ULTRA-HIGH WEATHER RESISTANCE STEEL PILES AND STRUCTURAL FOUNDATIONS WITH FLEXURAL STRENGTH

Abstract

The present invention relates to a lightweight, ultra-high-strength, weather-resistant steel pile for use as a steel foundation in structures such as, for example, solar installations. The lightweight, ultra-high-strength, weather-resistant steel pile comprises a thickness of 2.5 mm or less, cold-rolled into a steel pile with a reinforcement and a pair of opposing projections, each having internally formed discontinuities. The steel pile further comprises a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%.

Description

ULTRA-HIGH WEATHER RESISTANCE STEEL PILES AND STRUCTURAL FOUNDATIONS WITH BENDING RESISTANCE FIELD OF THE INVENTION This invention relates to thin strips of cast steel, methods for high friction rolling of thin strips of cast steel, and steel products manufactured from and by the same. BACKGROUND OF THE INVENTION In a double roll mill, molten metal is introduced between a pair of internally cooled, counter-rotating casting rolls, so that the metal casings solidify on the moving surfaces of the roll, and converge in the press between them to produce a solidified strip product, delivered downward from the press between the casting rolls. The term "presser" is used herein to refer to the general region in which the casting rolls are closest to each other. Molten metal is poured from a ladle through a metal supply system comprised of a trough and a central nozzle located above the presser to form a casting reservoir of molten metal, supported on the casting surfaces of the rollers above. of the presser and extended along the presser. This cast tank is normally contained between refractory side plates or dams held in sliding engagement with the end surfaces of the rollers so as to contain the two ends of the tank against the drain. BRIEF DESCRIPTION OF THE INVENTION To obtain a desired thickness, the thin steel strip can be passed through a rolling mill to hot roll the thin steel strip. While hot rolling is carried out, the thin strip of steel is generally lubricated to reduce rolling roller friction, which in turn reduces rolling load and roll wear, as well as providing a smoother surface finish. Lubrication is used to provide a low friction condition. A low friction condition is defined as one in which the coefficient of friction (μ) for the grip between rollers is less than 0.20. After hot rolling, the thin steel strip undergoes a cooling process. In a low friction condition, after undergoing a pickling or acid etching process to remove oxidation scale, large above austenitic grain boundary depressions have been observed on the hot rolled outer surfaces of cooled thin steel strips. In particular, while thin strips of steel tested using dye penetrant techniques appeared defect-free, after acid pickling of the same thin strips of steel, the former austenitic grain contours are acid etched to form contour depressions. of the previous austenitic grain. This etching may also cause a defect phenomenon to occur along the previously etched austenitic grain contours and resulting depressions. The resulting defects and separations, generally referred to as separations, can extend at least 5 microns deep, and in certain cases 5 to 10 microns deep. Also applicable to the present description, weathering steels are commonly alloy steels of low resistance to atmospheric corrosion. In the presence of moisture and air, low-alloy steels rust at a rate that depends on the level of exposure to oxygen, moisture, and atmospheric contaminants to the metal surface. When steel rusts, it can form a layer of rust commonly called corrosion. As the oxidation process progresses, the oxide layer forms a barrier to the ingress of oxygen, moisture and contaminants, and the rate of scale formation is reduced. With weathering steel, the oxidation process begins in the same way, but specific alloying elements in the steel produce a stable protective oxide layer that adheres to the base metal, and is much less porous than the weathering layer. Rust commonly formed on a non-weather resistant steel. The result is a much lower corrosion rate than would be found in ordinary non-weathering structural steel. Weathering steels are defined in ASTM A606, Standard Specification for High-Strength, Low-Alloy, Hot-Rolled and Cold-Rolled Steel, Sheet and Strip with Improved Resistance to Atmospheric Corrosion (Standard Specification for Steel, Sheet and Strip, High Strength, Low-Alloy, Hot Rolled and Coid Rolled with Improved Atmospheric Corrosion Resistance). Weathering steels are supplied in two types: Type 2, which contains at least 0.20% copper based on melting or heat analysis (0.18% Cu minimum to check the product); and Type 4, which contains additional alloying elements to provide a corrosion index of at least 6.0 as calculated by ASTM G101, Standard Guide for Estimating Atmospheric Corrosion Resistance of Low Alloy Steels. the Atmospheric Corrosion Resistance of Low-Alloy Steels), and provides a level of corrosion resistance significantly better than that of carbon steels with or without the addition of copper. Prior to the present invention, weathering steels were commonly limited to yield strengths less than 700 MPa and tensile strengths less than 1000 MPa. Also, prior to the present invention, the strength properties of weathering steels were commonly achieved by age hardening. United States Patent No. 10,174,398, incorporated herein by reference, is an example of a weathering steel achieved by age hardening. Due to strength limitations and corrosion limitations, steels, such as G100 or Gr70 steels, have not been very suitable for many products such as, for example, piles or steel foundations driven into the ground for use. in solar installations and / or in the highway industry such as, for example, support railings, signs, or the like. As used herein, a solar installation is a structure for supporting solar cells, such as in a solar farm of photovoltaic power stations designed to supply solar energy for use in an electrical grid or the like. The corrosive nature of groundwater and soil compositions requires material thicknesses exceeding 2.5 mm to maintain the integrity required for these structural elements. Accordingly, hot-dip galvanized steels were turned for such uses. Hot-dip galvanized steels are coated with zinc for improved corrosion resistance of the underlying material properties. In accordance with the above, it has been the convention of the solar industry to rely on piles designed from 50 ksi W6 or W8 double T beams for structural piles. However, the zinc coating reacts negatively with groundwater and soil compositions creating the potential to contaminate them. The zinc coating also provides a limited degree of protection. Once zinc oxidation deteriorates the zinc coating, metal oxidation still sets in, deteriorating the structural integrity of the underlying material and / or requiring greater thicknesses of material to maintain the integrity required for these structural elements. In accordance with the above, the present description proposes to provide a steel pile or foundation design produced from an ultra-high weathering and lightweight steel, which replaces the current material that is based on steel piles or foundations. . Specifically, the present disclosure proposes to provide a lightweight steel pile or foundation having shapes produced from a thin strip of molten metal. The forms of the present description propose to increase the strength and durability of the pile or steel foundation to withstand the deformation resulting from the force required to bring the structural elements to the ground and / or serve as structural elements for exterior above-ground structures, such as such as, for example, solar installations, support railings, signs or the like. In particular, the present disclosure proposes to provide a cold rolled steel pile or foundation formed from a thin strip of cast steel having a thickness of 2.5 mm or less, 2.0 mm or less, or 1.6 mm or less or a cast steel pile or foundation as a thin form of cast steel with a material thickness of 2.5 mm or less, 2.0 mm or less, or 1.6 mm or less. The steel pile or foundation is produced from a thin strip of molten steel that has been formed by cold rolling using one or more rolling mill stands. Additionally, a drilling system, a CNC plasma system, and / or a roller system, or the like, may also depend on the provision of through holes, slots, and / or spot welds, as noted below. The present disclosure also proposes to provide a cold rolled steel pile or foundation formed from a thin strip of cast steel that does not require an independently applied protective coating such as, for example, a zinc coating as provided on structural elements. hot dip galvanized. As used herein, independently applied coatings are protective coatings that may be a surface protector that is independent of the composition of the steel. Some examples of such independently applied protective coatings include a zinc coating, a galvanized coating (e.g., a hot dip galvanized coating), an aluminum-silicon corrosion resistant coating, or the like. More importantly, the steel piles or foundations of the present disclosure produce the corrosion resistance, as set forth below, without the aid of an independently applied coating. Inherently, by definition, the ultra-high weathering steel described herein possesses the required corrosion resistance that would otherwise be relied upon by hot-dip galvanizing. Therefore, the weathering steel of the present invention would not require or possess a zinc coating, a hot dip galvanized coating, or the like, could not be applied. ΜΛ / IOU In a set of examples, the present disclosure proposes to provide an ultra-high weathering and lightweight steel formed by shifting the peritectic point away from the carbon region and / or increasing a peritectic point transition temperature of the composition. Specifically, moving the peritectic point away from the carbon region and / or increasing a peritectic point transition temperature of the composition appears to inhibit defects and produces a high strength martensitic steel sheet that is free of defects. In the present example, the addition of nickel is based on where the addition of nickel must be sufficient to shift the “peritectic point” away from the carbon region that would otherwise be present in the same composition without the addition. of nickel. Also disclosed are products produced from an ultra-high weathering steel that is of various shapes, as further described herein, and that has improved strength properties that were not previously available. In another set of examples, the present disclosure proposes removing previous austenitic grain boundary depressions, but maintaining a spot pattern. In the present set of examples, the thin strip of molten steel undergoes a high friction rolling condition where the grain boundary depressions form a spot pattern on at least the surface of the thin strip of molten steel. Specifically, the present example proposes to form the spot pattern of the above austenitic grain boundary depressions by removing the previous austenitic grain boundary depressions from the surface and improving the formability of the steel strip or steel product. By improving the formability of steel strip products that are of various shapes, as further described herein, and that have improved strength properties become available that were not available previously. The present example is not only applicable with the ultra-high weathering steel mentioned above, but can additionally be applied with martensitic steels, other weathering steels and / or steel strips or products that have contour depressions. of the previous austenitic grain. In yet another set of examples, the present disclosure proposes to eliminate grain boundary depressions and spot patterns formed therefrom. In the present set of examples, the thin strip of molten steel undergoes surface homogenization, thereby eliminating the spot pattern. As a result, the thin strip of cast steel has a surface not only free of previous austenitic grain boundary depressions but additionally free of the spot pattern produced as a result of the high friction rolling condition, to provide, in some examples, a surface of thin strip of cast steel having a surface roughness (Ra) that is not greater than 2.5 pm. The present examples are not only applicable with the ultra-high weathering steel mentioned above, but can also be applied additionally with martensitic steels, other weathering steels and / or steel strips or products that have contour depressions. of the previous austenitic grain. Ultra-high weather resistance steel First, described herein is an ultra-high weathering and lightweight steel sheet, made by the steps comprising: (a) preparing a mass of molten steel comprising: (i) by weight, between 0.20 % and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium , less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) solidify at a heat flux greater than 10.0 MW / m2 in a steel sheet less than or equal to 2.5 mm thick and cool the sheet in a non-oxidizing atmosphere to below 1080°C and above an Ars temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when hot rolling; and (c) rapidly cooling to form a steel sheet with a microstructure having at least 75% martensite by volume, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and a elongation of between 1% and 10%. Here and elsewhere in this description, elongation refers to total elongation. “Rapid cooling” means cooling at a rate greater than 100°C / s to between 100 and 200°C. Rapidly cooling the present compositions, with an addition of nickel, reaches up to more than 95% of the steel strip in the martensitic phase. In one example, quenching forms a steel sheet with a microstructure having a volume of at least 95% martensite. The addition of nickel must be sufficient to shift the “peritectic point” away from the carbon region that would otherwise be present in the same composition without the addition of nickel. Specifically, it is considered that the inclusion of nickel in the composition contributes to the displacement of the peritectic point away from the carbon region and / or increases the transition temperature of the peritectic point of the composition, which appears to inhibit defects and delivers a plate of High strength martensitic steel that is free of defects. In one example, ultra-high weathering and lightweight steel sheet can also be hot rolled to a reduction of between 15% and 50% before being rapidly cooled. The carbon levels in the present steel sheet are preferably not below 0.20% in order to inhibit peritectic cracking of the steel sheet. The addition of nickel is provided to further inhibit peritectic cracking of the steel sheet, but makes it so independent of relying on carbon composition alone. The impact of nickel on the corrosion rate is reflected in the following equation to determine the calculation of the corrosion rate: Cu*26.01 + N¡*3.88 + Cr*1.2 + S¡*1.49 + P*17.28 - Cu*N¡ *7.29 - Ni*P*9.1 - Cu*Cu*33.39 (where each element is a percentage by weight). The melt can be solidified at a heat flux greater than 10.0 MW / m2 in a steel sheet with a thickness less than 2.5 mm, and the sheet can be cooled in a non-oxidizing atmosphere to below 1080°C and above the temperature of Plows at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when hot rolling. A non-oxidizing atmosphere is an atmosphere commonly of an inert gas such as nitrogen or argon, or a mixture thereof, which contains less than about 5% oxygen by weight. In another example, the sheet may be cooled in a non-oxidizing atmosphere below 1100°C and above the Ars temperature at a cooling rate greater than 15°C / s before quenching and / or before rolling. hot, when hot rolled. In some examples, martensite in the steel sheet can be formed from an austenitic grain size greater than 100 pm. In other examples, the martensite in the steel sheet can be formed from an austenitic grain size greater than 150 pm. The steel sheet is rapidly cooled to form a steel sheet with a microstructure having at least 75% martensite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation between 1% and 10%. In other examples, the steel sheet is rapidly cooled to form a steel sheet with a microstructure having at least 75% martensite plus bainite. In a specific example, quenching forms a steel sheet with a microstructure that is at least 95% martensite plus bainite by volume. In some examples, the steel sheet can be hot rolled with a reduction of up to 15% to 35% before being rapidly cooled. In other examples, the steel sheet may be hot rolled to a reduction of between 15% and 50% before being rapidly cooled. The molten steel used to produce the ultra-high weathering steel sheet is removed silicon (i.e. deoxidized silicon) comprising between 0.10% and 0.50% by weight of silicon. The steel sheet may further comprise by weight less than 0.008% aluminum or less than 0.006% aluminum. The melt may have a free oxygen content of between 5 to 70 ppm or between 5 and 60 ppm. The steel sheet may have a total oxygen content greater than 50 ppm. The inclusions comprise MnOSiCte commonly with 50% less than 5 pm in size and have the potential to improve the microstructure evolution and therefore the mechanical properties of the strip. Also described is a method for manufacturing an ultra-high weathering and lightweight steel sheet, which comprises the steps to: (a) prepare a mass of molten steel comprising: (i) by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than 0.12% niobium, less than 0.5% of molybdenum, between 0.5% and 1.5% of nickel, and removed silicon with a content of less than 0.01% of aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) forming the melt in a casting tank supported on casting surfaces of a pair of cooled casting rolls having a presser between them; (c) rotate the casting rollers in the opposite direction and solidify at a heat flux greater than 10.0 MW / m2 producing a steel sheet with a thickness less than 2.5 mm and cool the sheet in a non-oxidizing atmosphere to below 1080°C and above the Ars temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when hot rolled, and (d) quenching to form a sheet steel with a microstructure that has at least 75% martensite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10%. In a specific example, quenching forms a steel sheet with a microstructure that is at least 95% martensite plus bainite by volume. The sheet may be cooled in a non-oxidizing atmosphere to below 1100°C and above an Ara temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when rolled. hot. The steel sheet composition cannot be made with carbon levels below 0.20% because it is inoperative with peritectic cracking of the steel sheet. In one example, lightweight, ultra-high weathering steel sheet can be hot rolled to a reduction of between 15% and 50% before being rapidly cooled. Furthermore, the method of manufacturing an ultra-high weathering and lightweight steel sheet may comprise the step of tempering the steel sheet at a temperature of between 150°C and 250°C for 2 to 6 hours. The melt may have a free oxygen content of between 5 to 70 ppm or between 5 and 60 ppm. The steel sheet may have a total oxygen content greater than 50 ppm. The melt can be solidified at a heat flux greater than 10.0 MW / m2 in a steel sheet with a thickness less than 2.5 mm, and cooled in a non-oxidizing atmosphere below 1080°C and above an Ar3 temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when hot rolling. In another example, the sheet may be cooled in a non-oxidizing atmosphere below 1100°C and above an Ara temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling. , when hot rolled. In some embodiments, the martensite in the steel sheet may come from an austenitic grain size greater than 100 pm. In other embodiments, the martensite in the steel sheet can come from an austenitic grain size greater than 150 pm. The manufacturing method of ultra-high weathering and lightweight steel sheet may further comprise hot rolling of the steel sheet to a reduction of between 15% and 35% and then rapidly cooling to form a steel sheet with a microstructure that has at least 75% by volume of martensite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10 %. In some embodiments, the method of manufacturing a lightweight ultra-high strength steel sheet may further comprise hot rolling the steel sheet to a reduction of between 15% and 50% and thereafter rapidly cooling to form a steel sheet with a microstructure that has at least 75% by volume of martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10%. Furthermore, the method of manufacturing a hot-rolled lightweight ultra-high strength steel sheet may comprise hot rolling the steel sheet at a reduction of between 15% and 35% and, thereafter, rapidly cooling to form a steel sheet with a microstructure that has at least 75% by volume of martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10 %. In specific examples of the above, hot rolling of the steel sheet and subsequently quenching forms a steel sheet with a microstructure having by volume at least 95% martensite plus bainite. Also described is a steel pile comprising a reinforcement and one or more projections formed by cold rolling from a carbon alloy steel sheet having a composition comprising, by weight, between 0.20% and 0.35% carbon. , less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal ΜΛ / IOU at 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum where the carbon alloy steel sheet has a microstructure that has at least 75% by volume of martensite or martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, an elongation of between 1% and 10%, and that has a corrosion index of 6.0 or greater. High Friction Rolled High Weathering Steel Second, in a set of examples, a thin strip of cast carbon alloy steel having a casting thickness less than or equal to 2.5 mm is described herein. These examples do not only apply to the ultra-high weathering steel mentioned above, but can also be applied to martensitic steels, other weathering steels and / or steel strips or products that have contour depressions. earlier austenitic grain. The thin strip of carbon alloy cast steel may comprise, by weight, between 0.20% and 0.40% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum, and the remaining iron and impurities resulting from fusion. After high friction hot rolling, the thickness of the thin strip of carbon alloy cast steel is reduced by 15% to 50% of the casting thickness. The hot-rolled steel strip comprises a pair of opposing high-friction hot-rolled surfaces primarily free, substantially free, or free of prior austenitic grain boundary depressions and having a spot pattern. In some embodiments, the steel strip comprises a microstructure having by volume at least 75% martensite or at least 75% martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%. In some examples, the steel strip is a weathering steel with a corrosion rating of 6.0 or greater. In some examples, the pair of opposing high-friction hot-rolled surfaces are substantially free of prior austenitic grain boundary depressions. In some examples, the pair of opposing high-friction hot-rolled surfaces are substantially free of prior austenitic grain boundary depressions. Also described is a method of manufacturing a hot-rolled carbon alloy steel strip comprising by weight, between 0.20% and 0.40% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10 % and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and silicon removed with a lower content than 0.01% aluminum, and the remaining iron and impurities resulting from the fusion, the method comprising the steps to: (a) prepare a mass of molten steel; (b) forming the melt in a casting tank supported on casting surfaces of a pair of cooled casting rolls having a presser between them; (c) rotate the casting rollers in the opposite direction and solidify at a higher heat flux ΜΛ / IOU than 10.0 MW / m2the melt in a steel strip less than or equal to 2.5 mm thick supplied downward from the press and cool the strip in a non-oxidizing atmosphere to below 1080°C and above the temperature of Ars at a cooling rate greater than 15°C / s; (d) high friction hot rolling of the thin strip of cast steel to a hot rolled thickness of between 15% and 50% reduction from the cast thickness which produces a mainly free, practically free or hot rolled strip of steel free of previous austenitic grain boundary depressions and having a spot pattern. The thin strip of hot-rolled high-friction cast steel primarily free, substantially free, or free of above austenitic grain boundary depressions and having a spot pattern may be a weathering steel with a corrosion index of 6.0 or elderly. Furthermore, the high friction hot rolled steel strip may comprise a microstructure having, by volume, at least 75% martensite or at least 75% martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%. High-friction rolled high-strength maraging steel Third, in another set of examples, described herein is a thin strip of cast carbon alloy steel comprising a pair of opposing high-friction hot-rolled surfaces that have been surface homogenized, after being rolled in a uniform manner. high friction. These present examples are not only applicable with the ultra-high weathering steel mentioned above, but may additionally be applied with martensitic steels, other weathering steels, and / or steel strips or products that have depressions of previous austenitic grain contour. After surface homogenization, the pair of opposing high-friction hot-rolled surfaces are free of the spotted grain boundary depressions that were previously formed as a result of the high-friction rolling process. In some embodiments, the thin strip of cast carbon alloy steel may further comprise a microstructure having, by volume, at least 75% martensite or at least 75% martensite plus bainite with a yield strength of between 700 and 1600. MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%. In some embodiments, the steel strip comprises a microstructure having, by volume, at least 90% martensite or at least 90% martensite plus bainite. In some embodiments, the steel strip of claim 1 comprises a microstructure having, by volume, at least 95% martensite or at least 95% martensite plus bainite. Exemplary homogenized steel strips within the scope of this disclosure may comprise, by weight, between 0.20% and 0.40% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon containing less than 0.01% of aluminum, and the remaining iron and impurities resulting from the fusion. Methods for manufacturing hot rolled carbon alloy steel strip are also described. The method may comprise steps to: ΜΛ / IOU (a) prepare a mass of molten steel; (b) forming the melt in a casting tank supported on casting surfaces of a pair of cooled casting rolls having a presser between them; (c) rotate the casting rollers in the opposite direction and solidify at a heat flux greater than 10.0 MW / m2 the melt into a strip of steel less than or equal to 2.5 mm thick supplied downward from the press and cool the strip in a non-oxidizing atmosphere down to below 1080°C and above the Ara temperature at a cooling rate greater than 15°C / s; d) high friction rolling the thin strip of cast steel to a hot rolled thickness of between 15% and 50% reduction of the cast thickness which produces a hot rolled strip of steel free of previous austenitic grain boundary depressions and that it has a pattern of spots; and (e) homogenize the surface of the high-friction hot-rolled steel strip to eliminate the stain pattern. The high friction hot rolled homogenized cast steel thin strip may comprise a microstructure having, by volume, at least 75% martensite or at least 75% martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%, thus providing a high-strength martensitic steel. Furthermore, the high friction hot rolled homogenized steel strip may comprise, by weight, between 0.20% and 0.40% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% of silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon containing less than 0.01% aluminum , and the remaining iron and impurities resulting from the fusion. The present disclosure further proposes how each of the thin strips of cast steel, the above compositions and / or the above properties, as described, can be based on an ultra-high weathering steel pile. Specifically, in one example, an ultra-high weathering steel pile comprises a plurality of side walls, each side wall having a thickness of about 2.5 mm or less, 2.0 mm or less, or 1.6 mm or less. The pile can be formed from a steel strip. Specifically, the pile may be formed from a strip of cast steel. The pile can be formed from a strip of molten steel by hot rolling. Furthermore, the pile can be formed by cold rolling. The pile may have a composition comprising, by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and silicon removed with a content of less than 0.01% aluminum, and the remaining iron and impurities resulting from the merger. The pile may further comprise, or have, a corrosion rate of 6.0 or greater, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and / or an elongation of between 1%. and 10%. In some examples, the pile composition includes an amount of nickel sufficient to displace a peritectic point away from the carbon region and / or increase a transition temperature of the peritectic point to form a carbon alloy steel strip having a microstructure of at least 75% by volume of martensite or martensite plus bainite. In some examples, the pile may be formed from a steel strip where the cast thickness of the steel strip is hot rolled having a hot rolled thickness of between 15% and 50% reduction of the cast thickness. Hot rolled material can be high friction rolled to provide a high high friction rolling thickness. Various characteristics and forms for ultra-high strength weathering steel are further described herein. These features may be provided in combination or independently of each other. In some examples, the ultra-high weathering steel pile may be a C channel in which the plurality of side walls is a band and one or more projections. More specifically, the ultra-high weathering steel pile may be a hemmed C-channel and / or a corrugated C-channel in which the plurality of side walls are a reinforcement and one or more projections. In some examples, the ultra-high weathering steel pile may be a tube in which the plurality of side walls form the tube. More specifically, the ultra-high weathering steel pile can be a square tube or a rectangular tube. Furthermore, the ultra-high weathering steel pile may be a square tube or a rectangular tube, generally, wherein one or more of the plurality of side walls further comprise one or more corrugations. The plurality of side walls does not comprise an independently applied coating. The plurality of side walls are not galvanized. At least one side wall of the plurality of side walls may be a trim. More specifically, said one or more projections of the edged C channel may be a single trim. A first layer and a second layer of each individual trim of said one or more projections may be secured to each other by one or more spot welds. The first layer of one or more protrusions can transition to the second layer through a teardrop transition. Additionally, or alternatively, at least one of the plurality of side walls may comprise one or more corrugations. In some examples, the reinforcement of a C channel may comprise one or more corrugations. Additionally, or alternatively, said one or more projections of a channel C may comprise one or more corrugations. More specifically, the ultra-high weathering steel pile may comprise a reinforcement and a pair of opposing projections each having one or more discontinuities formed therein. In one example, the reinforcement may comprise a discontinuity that is a V-shaped transition. The V-shaped transition may be placed centrally on the reinforcement relative to the height of the pile. Such a pile may be referred to as Channel M. Additionally, or alternatively, one or both projections of the pair of opposing projections may comprise a discontinuity that is a V-shaped transition. The V-shaped transition of the projections may be placed centrally above the projection in relation to the width of the pile. In some examples, the discontinuities may be one or more corrugations that are arcs. The arches can be real arches. Alternatively, the arcs may comprise one or more planar portions. Said one or more flat parts may be at least 1x the thickness of the material. In one example, the reinforcement may comprise two corrugations that are arches and which may be uniformly spaced on the reinforcement relative to the height of the pile. Additionally, or alternatively, one or both projections of the pair of opposing projections may comprise one or more corrugations that are arcs. In each of the above examples, one or both projections of the pair of opposing projections may comprise a return flange. The return flange may return at an oblique angle to both the reinforcement and the corresponding boss. As examples of the above, the height of the ultra-high weathering steel pile, a height of the pile extending the reinforcement may vary between 10 and 30 cm (4 and 12 inches) and a width of the pile extending each The protrusion of the pair of opposing protrusions can vary between 5 and 20 cm (2 and 8 in). In other examples of the above, the height of the ultra-high weathering steel pile can vary between 5 and 35 cm (2 and 14 inches) and the width can vary between 2.5 and 25 cm (1 and 10 inches). . In some examples, an ultra-high weathering steel pile comprises a thickness of about 2.5 mm or less, 2.0 mm or less, or 1.6 mm or less. The pile may be formed from a thin strip of molten steel that is formed by cold rolling into the steel pile having a plurality of side walls with a corrosion index of 6.0 or greater. The ultra-high weathering steel pile may further comprise a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%. The composition of the ultra-high weathering steel pile may include an amount of nickel sufficient to displace a peritectic point away from the carbon region and / or increase a transition temperature of the peritectic point to form a steel strip of carbon alloy having a microstructure of at least 75% by volume of martensite or martensite plus bainite. In one example, the ultra-high weathering steel pile has a material composition comprising, by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and silicon removed with a content of less than 0.01% aluminum, and the remaining iron and impurities resulting from the fusion. A solar installation is also described. The solar installation may comprise an ultra-high weathering steel pile comprising a plurality of side walls and / or a reinforcement and a pair of opposing projections each having one or more discontinuities formed therein, each side wall , reinforcement, and projections may have a thickness of about 2.5 mm or less, 2.0 mm or less, or 1.6 mm or less. The ultra-high weathering steel pile of the solar installation may comprise, by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content less than 0.01 % aluminum, and the remaining iron and impurities resulting from the fusion. The ultra-high weathering steel pile of the solar installation can comprise a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10 %. In this example, a partial length of the ultra-high weathering steel pile is brought to grade and one or more solar cells are supported above grade by the ultra-high weathering steel pile. the weather According to ΜΛ / IOU above, the ultra-high weathering steel pile of the solar installation may additionally, or alternatively, have many characteristics as described above and in the rest of the description. Examples of ultra-high weathering steel piles can also be stored and / or transported in a nesting configuration. An ultra-high weathering steel pile nesting configuration may comprise a row of steel piles having a first, second and third steel pile, each of which comprises a stiffener and a pair of opposing bosses. , each has discontinuities formed inside, where a projection of the pair of opposite projections of the first steel pile overlaps and interlocks with a projection of the pair of opposite projections of the second steel pile and a projection of the pair of opposite projections of the third steel pile overlaps and interlocks with another projection of the pair of opposing projections of the second steel pile. The nesting configuration may further comprise a second row of steel piles having a fourth, fifth and sixth steel piles, each of which comprises a reinforcement and a pair of opposing projections, each of which has discontinuities formed at the same time. interior, where the fourth, fifth and sixth steel piles are placed respectively as the first, second and third steel piles and are stacked on top of the first, second and third steel piles forming a two-row pile. In some examples, the nesting configuration may comprise multipole rows with multiple piles therein, such as, for example, at least five rows of multiple steel piles. BRIEF DESCRIPTION OF THE FIGURES The invention can be illustrated and explained in more detail with reference to the attached figures, in which: Figure 1 illustrates a strip casting facility incorporating an in-line hot rolling mill and a folder. Figure 2 illustrates details of the double roll strip mill. Figure 3 is a micrograph of a steel sheet with a microstructure that has at least 75% martensite. Figure 4 is a phase diagram illustrating the effect of nickel to shift the peritectic point away from the carbon region. Figure 5 is a process flow diagram according to one or more aspects of the present description. Figure 6 is an image showing a hot-rolled steel strip surface of high friction condition after a surface homogenization process. Figure 7 is an image showing a hot-rolled steel strip surface of high friction condition having a spot pattern that has not been homogenized. Figure 8 is a friction coefficient model diagram created to determine the friction coefficient for a particular pair of operating rolls, specific rolling force and corresponding reduction. Figure 9 is a continuous cool transformation (CCT) diagram for steel. Figure 10 is a cross section of a rimmed C-channel shape of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 11 is a perspective view of the steel pile or foundation of Figure 10 formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 12 is a cross section of a corrugated C-channel shape of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 13 is a cross section of a corrugated C-channel shape of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 14 is a cross section of a square tube with reinforcing elements of a steel pile or steel foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 15 is a cross section of a rectangular tube with reinforcing elements of a steel pile or steel foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 16 is a graphical representation illustrating test results for a lightweight ultra-high weathering steel pile material of the present disclosure. Figure 17 is a graphical representation illustrating test results for a lightweight ultra-high weathering steel pile material of the present disclosure. Figure 18 is a cross section of an M channel shape of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 19 is a graphical representation illustrating test results for a lightweight ultra-high weathering steel pile material of the present disclosure. Figure 20 is a cross-sectional view of a C-channel shape of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 21 is a graphical representation illustrating test results for a lightweight ultra-high weathering steel pile material of the present disclosure. Figure 22 is a cross section of a C-channel shape of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 23 is a graphical representation illustrating test results for a lightweight ultra-high weathering steel pile material of the present disclosure. Figure 24 is a graphical representation illustrating test results for a lightweight ultra-high weathering steel pile material of the present disclosure. Figure 25 is a reproduction of a top portion of a UHSW steel pile of the present description driven into the ground. Figure 26 is a reproduction of a top portion of a prior art wide boss beam brought to the ground. Figure 27 is a graphical representation illustrating the allowable point load at the free end of a fixed cantilever for the pile or structural foundation examples. Figure 28 is a graphical representation illustrating the free end deviation at allowable point load observed for the pile or structural foundation examples. Figure 29 is a cross section of a form of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 30 is a cross section of a steel pile or foundation formed by cold rolling from a thin strip of molten steel in accordance with one or more aspects of the present disclosure. Figure 31 is an example of a steel pile or steel foundation nesting configuration of the present disclosure. DETAILED DESCRIPTION OF THE INVENTION Described herein, in one example, is a lightweight ultra-high weathering steel sheet. An ultra-high weathering and lightweight steel sheet can be manufactured from a melt. The melt can be processed through a double roll mill. In one example, the ultra-high weathering and lightweight steel sheet can be manufactured by the steps comprising: (a) preparing a mass of molten steel comprising: (i) by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5 % molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) solidify at a heat flux greater than 10.0 PM / m2 producing a steel sheet with a thickness less than 2.5 mm and cool in a non-oxidizing atmosphere to below 1080°C and above an Ara temperature at a higher cooling rate than 15°C / s before quenching and / or before hot rolling, when hot rolling; and (c) rapidly cooling to form a steel sheet with a microstructure having at least 75% by volume of martensite or martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10%. In one example, ultra-high weathering and lightweight steel sheet can also be hot rolled to a reduction of between 15% and 50% before quenching. The sheet may be cooled in a non-oxidizing atmosphere to below 1100°C and above an Ara temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when rolled. hot. The Ara temperature is the temperature at which austenite begins to transform into ferrite during cooling. In other words, the Ara temperature is the transformation point of austenite. In each example, the nickel shifts the peritectic point away from the carbon region and / or increases a peritectic point transition temperature of the steel sheet composition to provide a steel sheet that is free of defects. The impact of nickel on the corrosion rate is reflected in the following equation to determine the corrosion rate calculation: Cu*26.01 + Ni*3.88 + Cr*1.2 + S¡*1.49 + P * 17.28 Cu*N¡*7.29 - Ni*P*9.1 - Cu*Cu*33.39 (where each element is a percentage by weight). Also described herein are thin strips of cast steel having hot-rolled outer side surfaces characterized in that they are primarily free, substantially free, or free of previous austenitic grain boundary depressions but having spots, or elongated surface structures, such as as in the examples of high-strength, high-friction laminated martensitic steel. Methods or processes for producing the same are also described herein. These examples do not apply only to the ultra-high weathering steel mentioned above, but can additionally be applied to martensitic steels, other weathering steels and / or steel strips or products that have contour depressions. earlier austenitic grain. Further described herein are thin strips of steel having hot-rolled outer side surfaces characterized in that they are primarily free, substantially free, or free of prior austenitic grain boundary depressions and free of stains, or elongated surface structures, such as in the examples of a high friction laminated high weathering steel. Methods or processes for producing the same are also described herein. These examples do not apply only to the ultra-high weathering steel mentioned above, but can additionally be applied to martensitic steels, other weathering steels and / or steel strips or products that have contour depressions. earlier austenitic grain. As used herein, primarily free means less than 50% of each opposing hot-rolled outer side surface contains prior austenitic grain contours or prior austenitic grain boundary depressions after acid etching (pickling). At least substantially free of all prior austenitic grain boundaries or prior austenitic grain boundary depressions means that 10% or less of each opposing hot-rolled outer lateral surface contains prior austenitic grain boundary depressions or austenitic grain boundary depressions. above after acid etching (pickling). Such depressions form etched grain contour depressions after acid etching (also known as etching) to make the previous austenitic grain contours visible at 250x magnification. In other cases, free means that each opposing hot-rolled outer lateral surface is free, that is, completely free of, previous austenitic grain boundary depressions, which includes being free of any previous austenitic grain boundary depressions after of acid etching. It is noted that the previous austenitic grain boundaries may still exist within the strip material after hot rolling where the grain boundary depressions and separations on the surface have been removed by the techniques described herein ( for example, where hot rolling occurs at a temperature above the Ars temperature using roll grip friction coefficients equal to or greater than 0.20). Figures 1 and 2 illustrate successive parts of the strip mill for continuously melting a steel strip, or steel sheet, of the present invention. A double roll mill 11 can continuously produce a strip of molten steel 12, which passes in a transit path 10 through a guide table 13 to a pressure roll holder 14 having pressure rollers 14A. Immediately after leaving the pressure roller holder 14, the strip passes to a hot rolling mill 16 having a pair of operating rolls 16A and backing rolls 16B, where the molten strip is hot rolled to reduce a desired thickness. The hot rolled strip passes over a receiving table 17 where the strip enters an intensive cooling section by water jets 18 (or other suitable means). The rolled and cooled strip then passes through a pressure roller holder 20 comprising a pair of pressure rollers 20A and then to a folder 19. As shown in Figure 2, the double roll mill 11 comprises a main machine frame 21, which supports a pair of laterally positioned casting rolls 22 having casting surfaces 22A. Molten metal is supplied during a casting operation from a ladle (not shown) to a tundish 23, through a refractory casing 24 to a movable distributor or tundish 25, and then from the movable distributor or tundish 25 through a metal supply nozzle 26 between the casting rollers 22 above the presser 27. The molten metal supplied between the casting rollers 22 forms a casting reservoir 30 above the presser supported on the casting rollers. The casting tank 30 is held at the ends of the casting rolls by a pair of side dams or closure plates 28, which can be pushed against the ends of the casting rolls by a pair of thrusters (not shown) include hydraulic cylinder units (not shown) connected to side plate holders. The upper surface of the casting tank 30 (generally referred to as the "meniscus" level) which is normally located above the lower end of the supply nozzle such that the lower end of the supply nozzle is immersed within the casting tank 30. The casting rolls 22 are cooled internally with water such that the casings solidify on the moving surfaces of the casting roll as they pass through the casting tank, and as they converge at the presser 27 between them to produce the molten strip 12, which is supplied downward from the press between the casting rollers. The double roll mill may be of the type illustrated and described in detail in U.S. Pat. nos. 5,184,668, 5,277,243, 5,488,988, and / or U.S. Patent Application no. 12 / 050,987, published as no. of U.S. Publishing 2009 / 0236068 A1. Reference is made to those patents and publications which are incorporated by reference for suitable construction details of a double roll mill which may be used in an example of the present invention. After the thin strip of steel is formed (cast) using any desired process, such as the strip casting process described above in conjunction with Figures 1 and 2, the strip can be hot rolled and cooled to form a strip. desired thin steel having hot rolled opposing outer side surfaces at least mainly free, substantially free or free of previous austenitic grain boundary depressions. As illustrated in Figure 1, the inline hot rolling mill 16 provides a 15% to 50% reduction of the strip coming from the rolling mill. At receiving table 17, cooling may include a water cooling section to control cooling rates of the austenite transformation to achieve desired microstructure and material properties. Figure 3 shows a micrograph of a steel sheet with a microstructure having at least 75% martensite from a previous austenitic grain size of at least 100 pm. In some examples, the steel sheet is rapidly cooled to form a steel sheet with a microstructure having at least 90% by volume of martensite or martensite and bainite. In another example, the steel sheet is rapidly cooled to form a steel sheet with a microstructure having at least 95% by volume of martensite or martensite and bainite. In each of these examples, the steel sheet may further be hot rolled to a reduction of between 15% and 50% before quenching. Referring now to Figure 1, a hot box 15 is illustrated. As shown in Figure 1, after the strip has been formed, it can move to an environmentally controlled box, called hot box 15, where it continues to cool. passively before being hot rolled to its final gauge through a hot rolling mill 16. The environmentally controlled box, which has a protective atmosphere, is maintained until entering the hot rolling mill 16. Inside the hot box, the strip is moves on the guide table 13 to the pressure roller holder 14. In the examples of the present description, undesirable thermal attack may occur on the hot box 15. Based on whether thermal attack has occurred on the hot box, the strip may hot rolled under a high friction rolling condition based on the parameters defined in more detail below. In particular cases, methods for forming a thin strip of steel further include hot rolling of the thin strip of steel using a pair of opposing operating rolls that generate a high coefficient of friction (μ) sufficient to generate rolled opposite outer side surfaces. hot melting of thin strip of steel characterized by being primarily free, substantially free, or free of previous austenitic grain boundary depressions, and characterized by having an elongated surface structure associated with surface spot patterns formed under shear through plastic deformation. In certain cases, the pair of opposing operating rollers generates a coefficient of friction (μ) equal to or greater than 0.20, 0.25, 0.268, or 0.27, each with or without the use of lubrication at a temperature above the Ars temperature. . It will be noted that the coefficient of friction can be increased by increasing the surface roughness of the surfaces of the operating rollers, eliminating the use of any lubrication, reducing the amount of lubrication used, and / or choosing to use a particular type of lubrication. Other mechanisms may also be used to increase the friction coefficient as may be known to those skilled in the art, in addition to or independently of the mechanisms described above. The above process is referred to herein generally as high friction rolling. As previously mentioned, it will be noted that high friction rolling can be achieved by increasing the surface roughness of the surfaces of one or more of the operating rolls. Referred to herein generally as surface texturing of the operating roll. The surface texturing of the operating roll can be modified and measured by several parameters for use in a high friction rolling application. For example, the average roughness (Ra) of an operating roll profile can provide a reference point for generating the coefficient of friction required for interroll grip as indicated in the examples above. In order to achieve high friction lamination by surface texturing of the operating roll in one example, freshly ground and textured operating rolls may have a Ra between 2.5 pm and 7.0 pm. Freshly ground and textured operating rolls are referred to herein more generally as new operating rolls. In a specific example, the new operating roller may have a Rade between 3.18 pm and 4.0 pm. The average roughness of a new operating roller may decrease during use, or with wear. Therefore, the operating roll(s) used may also depend on the production of the high friction rolling conditions noted above as long as the roll(s) ) operating(s) used have, in one example, a Ra of between 2.0 pm and 4.0 pm. In a specific example, the operating roll(s) used may have a Ra between 1.74 pm and 3.0 pm simultaneously achieving the high friction rolling conditions noted above. Additionally, or alternatively, the average surface roughness depth (Rz) of the operating roll profile may also depend on an identifier to achieve the high friction rolling conditions observed above. The new operating roller(s) may have an Rz between 20 pm and 41 pm. In a specific example, the new operating roller(s) may have an Rz between 21.90 pm and 28.32 pm. The operating roll(s) used can be based on the high friction rolling conditions noted above in an example as long as they maintain an Rz of between 10 pm and 20 pm before retire from service. In a specific example, the operational roller(s) used have an Rz of between 13.90 pm and 20.16 pm before being removed from service. Still, the above parameters can be further defined by the average separation between the peaks across the profile (Sm). The new operational roll(s) based on the production of the high friction rolling condition may comprise an Sm between 90 pm and 150 pm. In a specific example, the new operating roll(s) that are based on the production of the high friction rolling condition comprise an Sm of between 96 pm and 141 pm. The operating roll(s) used may be based on the high friction rolling conditions noted above in an example as long as they maintain an Sm of between 115 pm and 165 pm. Table 1, shown below, illustrates measured test data for surface texturing of the operating roll that is based on producing a high friction rolling condition, by position on the operating roll, and also provides a comparison between the new parameters of the operating roller and the parameters of the used operating roller, before the used operating roller is removed from service: TABLE 1 New rollers Used rollers Delta (Δ) Roller Position Ra Sm Rz Ra Sm Rz Ra Sm Rz Upper roller Cto. PO* 3.64 128 25.74 2.56 121 17.30 Upper roller Cto. PO* 3.88 125 24.44 3.02 128 17.64 Upper roller Cto. PO* 3.80 112 23.54 2.78 128 19.06 Upper roller Cto. PO avg. 3.77 121.67 24.57 2.79 125.67 18.00 0.99 -4.00 6.57 Upper roller Ctr.** 3.48 119 24.1 2.76 154 18.46 Upper roller Ctr.** 3.44 112 - 2.36 134 17.46 Upper roller Ctr.** 4.06 117 26.12 2.64 121 16.36 Upper roller Ctr. avg.** 3.66 116.00 25.11 2.59 136.33 17.43 1.07 -2033 7.68 Upper roller Cto. PA*** 3.46 121 25.12 2.44 150 17.22 Upper roller Cto. PA 3.40 106 25.46 3.02 160 18.00 Upper roller Cto. PA 3.62 129 25.36 2.87 15 20.16 Upper roller Cto. DS avg. 3.49 118.67 25.31 2.77 153.67 18.46 0.73 -35.00 6.85 Upper roller General Avg. 3.61 118.83 29.72 2.45 140.44 16.94 Lower roller Cto. PO 3.84 126 28.32 2.32 142 16.44 Lower roller Cto. PO 3.52 112 24.44 2.34 133 15.94 TABLE 1 (cont.) New rollers Used rollers Delta (Δ) Lower roller Cto. PO 3.52 122 24.28 2.40 133 16.34 Lower roller Cto. PO avg. 3.63 120.00 25.68 2.35 136 16.24 1.27 -16.00 9.44 Lower roller Ctr. 3.18 96 21.9 2.34 153 15.82 Lower Roller Ctr. 3.66 109 24.68 2.32 154 15.64 Lower Roller Ctr. 3.84 127 25.94 2.06 141 13.54 Lower Roller Ctr. Avg. 3.56 110.67 24.17 2.24 149.33 15.00 1.32 -38.67 9.17 Lower roller Cto. PA 3.34 112 25.08 1.92 145 20.02 Lower roller Cto. PA 3.30 125 22.12 1.74 115 12.90 Lower roller Cto. PA 4.00 141 26.38 2.30 165 16.60 Lower roller Cto. BP avg. 3.55 126.00 24.53 1.99 141.67 16.51 1.56 15.67 8.02 Bottom Roller Overall Avg. 3.58 118.89 24.79 2.19 142.33 15.92 * “Cto. PO” is the Room area in the Operator's Part; and “Prom.” is average ** “Ctr.” is the center of the strip; and “Prom.” is average * “Cto. PA” is the Quarter area in the Drive Part; and “Prom.” it's average To determine whether high friction rolling is applicable for the examples of the present disclosure, it may be dependent on whether thermal attack has occurred in the hot box. Thermal attack is a by-product, or consequence, of the casting process that exposes previous austenitic grain boundary depressions on the surface of the steel strip. As noted above, earlier austenitic grain boundary depressions may be susceptible to causing the aforementioned defect phenomenon along earlier austenitic grain boundary depressions etched with additional acid etching. Specifically, thermal attack reveals ΜΛ / I OU anterior austenitic grain boundary depressions in a steel strip by the formation of grooves at the intersections of the anterior austenitic grain boundary depressions and the surface when the steel is exposed to a high temperature in an inert atmosphere, just like the hot box. These grooves make visible the previous austenitic grain contour depressions on the surface. Accordingly, the present process examples identify high friction rolling as the step to produce the desired steel properties after thermal attack in the hot box. Regardless of the presence of thermal attack and evidence of previous austenitic grain boundary depressions, a high friction lamination can be provided to increase recrystallization of the thin strip of steel. Figure 5 is a flow chart illustrating the process for applying high friction lamination and / or surface homogenization. In the present examples, determining whether the steel strip or steel product undergoes high friction rolling depends on whether undesirable thermal attack has occurred in the hot box 510. If thermal attack has not occurred in the hot box, high friction rolling is not necessary and there is no (1) staining of the above austenitic grain boundary depressions, (2) increasing the formability of the steel product such as, for example, in an ultra-high strength steel. to weathering, and / or (3) improve resistance to hydrogen embrittlement (H2). However, high friction rolling may still be intended to achieve recrystallization 520 or to produce a microstructure as otherwise described herein even if no thermal attack has occurred in the hot box. If thermal attack has occurred in the hot box 510, high friction rolling 530 is performed to (1) stain the previous austenitic grain boundary depressions, (2) increase the formability of an ultra-high tensile strength steel. weathering, and / or (3) improve the resistance to hydrogen embrittlement (H2) by removing previous austenitic grain boundary depressions and eliminating weak spots that form as defects after a 120-hour corrosion test. In an example of the present disclosure, a 550 ultra-high weathering steel is produced, with a spot pattern. In another embodiment of the present disclosure, the stain pattern is eliminated, thereby improving resistance to pitting corrosion 540, such as that required in automotive applications. Such an embodiment produces, for example, a high-strength martensitic steel 560. The stain pattern can be removed by a surface homogenization process. Figure 5 further illustrates a surface homogenization process 540. The applicability of the surface homogenization process is described in more detail below in connection with the present description. Representative examples are also described in more detail below. Ultra-high weather resistance steel In some embodiments, an ultra-high weathering steel sheet can be manufactured from a melt. The melt can be processed through a double roll mill. In one example, the ultra-high weathering resistance steel sheet can be manufactured by the steps comprising: (a) preparing a mass of molten steel comprising: (i) by weight, between 0.20% and 0.35% of carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% of molybdenum, between 0.5% and 1.5% of nickel, and removed silicon with a content of less than 0.01% of aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) solidify at a heat flux greater than 10.0 PM / m2 producing a steel sheet with a thickness less than 2.5 mm and cool in a non-oxidizing atmosphere to below 1080°C and above the Ars temperature at a rate of cooling greater than 15°C / s before quenching and / or before hot rolling, when hot rolling; and (c) rapidly cooling to form a steel sheet with a microstructure having at least 75% by volume of martensite or martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10%. In one example, ultra-high weathering and lightweight steel sheet can also be hot rolled to a reduction of between 15% and 50% before quenching. The sheet may be cooled in a non-oxidizing atmosphere to below 1100°C and above the Ars temperature at a cooling rate greater than 15°C / s before quenching and / or before hot rolling, when It is hot rolled. The Ars temperature is the temperature at which austenite begins to transform into ferrite during cooling. In other words, the Ars temperature is the transformation point of austenite. In each example, the nickel shifts the peritectic point away from the carbon region and / or increases a peritectic point transition temperature of the steel sheet composition to provide a steel sheet that is free of defects. The impact of nickel on the corrosion rate is reflected in the following equation to determine the corrosion rate calculation: Cu*26.01 + N¡*3.88 + Cr*1.2 + Si'1.49 + P'17.28 - Cu*N¡* 7.29 - Ni*P*9.1 - Cu*Cu*33.39 (where each element is a percentage by weight). The present examples of steel sheets provide an addition of nickel to further prevent peritectic cracking while simultaneously maintaining or improving hardenability. In particular, nickel is added between 0.5% and 1.5%, by weight. The addition of nickel is considered to prevent the strip shell from bulging due to volume change in the peritectic region during phase transformation on the casting rolls and thus improves uniform heat transfer during solidification. of the strip. The addition of nickel is considered to shift the peritectic point away from the carbon region and / or increase the peritectic point transition temperature of the composition to form a steel sheet that is free of defects. The phase diagram in Figure 4 illustrates this. In particular, the phase diagram in Figure 4 illustrates the impact of each of 0.0 wt% nickel 100, 0.2 wt% nickel 110, and 0.4 wt% nickel 120. As illustrated In Figure 4, the peritectic points, P100, Pno, and P120, found at the intersection of the liquid + delta 90 phase, the delta + gamma 50 phase, and the liquid + gamma 60 phase, shift a percentage by mass lower carbon (C) at a higher temperature as nickel increases. The carbon content, on the other hand, makes the steel strip susceptible to defects at low temperatures in a steel strip that has high yield strengths. The addition of nickel shifts the peritectic point away from the carbon region and / or increases the peritectic point transition temperature of the steel sheet to provide a defect-free martensitic steel strip with high yield strengths. The impact of nickel on the corrosion rate is reflected in the following equation to determine the corrosion rate calculation: Cu*26.01 + N¡*3.88 + Cr*1.2 + Si*1.49 + P*17.28 - Cu*N¡* 7.29 - Ni*P*9.1 - Cu*Cu*33.39 (where each element is a percentage by weight). Table 2, shown below, shows several examples of composition of an ultra-high resistance to weathering and light steel sheet, of the present description. Table 2 ΜΛ / t / ZUZZ / U4Z I OU Example No. 1 No. 2 No. 3 No. 4 % by weight S 0.2272 0.2212 0.2835 0.2733 Mn 0.91 0.94 0.91 1 Si 0.22 0.2 0.21 0.2 S 0.001 0.0006 0.0011 0.001 8 P 0.015 0.011 0.011 0.014 Cu 0.34 0.16 0.19 0.32 Cr 0.25 0.15 0.15 0.18 Ni 0.66 0.75 1.01 0.78 V 0.004 0.003 0.002 0.005 Nb 0.002 0.002 0 0.004 Ca 0 0.0001 0.0004 0 Al 0.00008 0.0003 0.0016 0.0021 LecoN 0.0066 0.0029 0.0039 0.0048 CEAWS 0.54 0.507 0.585 0.592 Mn / S 910 1567 827 556 Mn / Si 4.1 4.7 4.3 5 corrosion rate 6.71 6.01 6.84 6.77 In Table 2, LecoN is the measured nitrogen (N2), weight percent, and CEAWS is the measured carbon equivalent (CE - carbon equivalent), weight percent. Other elements that rely on hardenability produce the opposite effect by moving the peritectic point closer to the carbon region. Such elements include chromium and molybdenum which are intended to increase hardenability, but ultimately cause peritectic cracking. By adding nickel, hardenability is improved and peritectic cracking is reduced to provide a fully quenched martensitic grade steel strip with high strength. In the present compositions, the addition of nickel may be combined with limited amounts of chromium and / or molybdenum, as described herein. As a result, nickel reduces any impact that these hardening elements may have in producing peritectic cracking. However, in one example, the additional nickel would not combine with an intended addition of boron. A target addition is 5 ppm boron or more. In other words, in one example, the nickel addition would be used in combination with virtually no boron, or less than 5 ppm boron. Additionally, the ultra-high weathering and lightweight steel sheet can be manufactured by further tempering the steel sheet at a temperature between 150°C and 250°C for 2 to 6 hours. Tempering the steel sheet provides improved elongation with minimal loss of strength. For example, a steel sheet that has a yield strength of 1250 MPa, a tensile strength of 1600 MPa and an elongation of 2% was improved to a yield strength of 1250 MPa, tensile strength of 1525 MPa and an elongation of 5% after annealing as described herein. The ultra-high weathering and lightweight steel sheet can be silicon removed with a content of less than 0.008% aluminum or less than 0.006% aluminum. The melt may have a free oxygen content of between 5 to 70 ppm or between 5 and 60 ppm. The steel sheet may have a total oxygen content greater than 50 ppm. Inclusions include MnOSiOz commonly with 50% less than 5 pm in size and have the potential to improve the microstructure evolution and therefore the mechanical properties of the strip. The melt can be solidified at a heat flux greater than 10.0 MW / m2 in a steel sheet with a thickness less than 2.5 mm, and cooled in a non-oxidizing atmosphere below 1080°C and above an Ara temperature at a cooling rate greater than 15°C / s. A non-oxidizing atmosphere is an atmosphere commonly of an inert gas such as nitrogen or argon, or a mixture thereof, containing less than about 5% oxygen by weight. In some embodiments, the martensite in the steel sheet can be formed from an austenitic grain size greater than 100 pm. In other embodiments, the martensite in the steel sheet can be formed from an austenitic grain size greater than 150 pm. Rapid solidification at thermal fluxes greater than 10 MW / m2 allows the production of an austenitic granulometry that is sensitive to controlled cooling to allow the production of a defect-free sheet. The steel sheet can further be hot rolled to a reduction of between 15% and 50% and then rapidly cooled to form a steel sheet with a microstructure having at least 75% martensite plus bainite, a limit of elasticity of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10%. Additionally, the steel sheet can be hot rolled with a reduction of up to 15% to 35% and, shown below, rapidly cooled to form a steel sheet with a microstructure that has at least 75% martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10%. In one example, the steel sheet is hot rolled to a reduction of between 15% and 50% and then rapidly cooled to form a steel sheet with a microstructure having at least 90% by volume of martensite. or martensite and bainite. In yet another example, the steel sheet is hot rolled to a reduction of between 15% and 50% and, thereafter, rapidly cooled to form a steel sheet with a microstructure that has at least 95% by volume of martensite or martensite and bainite. Many products can be produced from ultra-high strength weathering (UHSW) steel sheet of the type described herein. An example of a product that can be produced from a lightweight, ultra-high weathering steel sheet includes a steel pile. More specifically, piles, or foundations, for solar installations, are examples of uses for a product produced from a lightweight, ultra-high weather-resistant steel sheet. As used herein, a solar installation is a structure for supporting solar cells, such as in a solar farm of photovoltaic power stations designed to supply solar energy for use in an electrical grid. The highway industry has a similar demand for foundations such as, for example, to support support railings, signage or the like. The steel pile or foundation can be produced from a thin strip of molten steel that has been formed by cold rolling using one or more rolling mill stands. Additionally, a drilling system, a CNC plasma system, and / or a roller system, or the like, may also rely on the provision of through holes, slots, continuous welds, partial welds, and / or spot welds, such as indicated below. In one example, a steel pile comprises a reinforcement and one or more bosses formed by cold rolling from carbon alloy steel strip of the varieties described above. Figures 10, 12 to 15, 22, 24 and 26 illustrate cross-sectional examples of UHSW steel piles formed by cold rolling from a thin strip of molten steel. In Figure 10, the UHSW steel pile 100 is a C channel comprising a reinforcement 110, a first projection 120, and a second projection 130 and is an example referred to herein as a bound C channel, or NXW foundation. The web 110 extends a height Hwo of the steel pile 100 and transitions to a curved transition 140 towards the first projection 120 at a first end 112 of the reinforcement 100. The reinforcement 100 further transitions to a curved transition 150 towards the second projection 130 on a second end 113 of the reinforcement 100, opposite the first end 112 of the reinforcement 110. In the present example, each curved transition 140, 150 has a respective radius Ruó, Riso, each forming an arc extending 90 degrees . Accordingly, each projection 120,130 is perpendicular to the reinforcement 110. In Figure 10, the first projection 120 is parallel to and opposite the second projection 130. Both the first projection 120 and the second projection 130 extend a width Wwo of the steel pile 100 of reinforcement 110 and in the same direction. In Figure 10, the first projection 120 and the second projection 130 comprise a trim structure. With specific reference to the first projection 120, the trim structure is a single trim comprising a first layer 122 and a second layer 124 wherein the first layer 122 extends from the curved transition 140 in a direction of the width Wwo of the pile pile. 100 steel to a 160 teardrop transition. The 160 teardrop transition is an open fitting that transitions to a closed fitting. The teardrop transition 160 advances inward from the steel pile 100 in a direction of both the width Wwo and the height Hwo of the steel pilot towards the second opposite protrusion 130. In a specific example, the first layer 122 advances towards a first leg 162 of the teardrop transition 160 at an angle Áwo of 45 degrees, relative to the direction of the width of the steel pile Wwo. From the first leg 162, the teardrop transition 160 advances through an arc to the second layer 124. The second layer 124 is placed on an outer side of the first layer 122 in a closed fitting. The second layer 124 is spliced ​​with the first layer 122 and moves in ΜΛ / I OU parallel to the first layer 122. In Figure 10, the second layer 124 extends the width W100 of the steel pile to the curved transition 140. Additionally, the teardrop transition 160 is kept within the height of the steel pile. Hwo steel, as defined by the trim sections of each respective first boss 120 and second boss 130. Still referring to Figure 10, and similar to, but opposite to, the first projection 120, the second projection 130 comprises a trim structure. The trim structure of the second projection comprises a first layer 132 and a second layer 134 wherein the first layer 132 extends from the curved transition 150 in a direction of the width Wwo of the steel pile 100 to a teardrop transition 170. The teardrop transition 170 is an open fitting that transitions to a closed fitting as follows. In a specific example, the first layer 132 advances toward a first leg 172 of the teardrop transition 170 at an angle of 45 degrees relative to the width direction of the steel pile W100. From the first leg 172, the teardrop transition 170 advances through an arc to the second layer 134. The second layer 134 is placed on an outer side of the first layer 132 in a closed fitting. The second layer 134 is butted to the first layer 132 and moves parallel to the first layer. In Figure 10, the second layer 134 extends the width Wwo of the steel pile to the curved transition 150. The teardrop transition 170 is maintained within the height Hwo of the steel pile, as defined by the trim sections of each respective first projection 120 and the second projection 130. In the example of Figure 10, the thickness T of the steel sheet, which forms the steel pile 100, is 1.575 mm (0.062 inches). Therefore, the trim sections are 0.124 mm (3.15 mm). In some examples, the thickness of the steel sheet, which forms the steel pile 100, may be 2 mm or less. In other examples, the thickness of the steel sheet, which forms the steel pile 100, may be 2.5 mm or less. Figure 11 illustrates a perspective view of the steel pile 100 of Figure 10 at the first projection 120. The steel pile 100 has a length Lwo in which the reinforcement 110, the first projection 120, and the second projection 130 extend the length of the steel pile Lwo. One or more spot welds 180 may be provided on the first projection 120 and the second projection 130 in order to maintain the first layer 122, 132 in abutting relationship with the second layer 124, 134, respectively (as illustrated in Figure 10). 180 spot welds can be spaced between 6” and 24” (15.2 cm and 61 cm) along the entire length Lwo of the steel pile. Spot welds 180 can also be centered relative to width Wwo or offset of steel pile width relative to steel pile width Wwo. Additionally, the spot welds 180 may be spaced consistently or the spot weld spacing 180 may be variable along the entire length Lwo of the steel pile. In one example, a first spot weld is 1.25 cm (0.50") from a first end 102 of the steel pile and is uniformly spaced 33.5 cm (13.22") along the entire length Lwo of the remaining steel pile. The spot welds 180 may also be centered relative to the steel pile width Wwo or offset relative to the steel pile width Wwo, or a combination thereof. In one example, the tack welds are placed 6.8 cm (2.68'j) from the outermost tangent of a respective teardrop transition 160, 170. Still referring to Figure 11, the first projection 120 and / or the second projection 130 can ΜΛ / t / ZUZZ / U4Z I OU additionally comprise one or more through holes 190 and / or one or more slots 192. The through holes 190 and slots 192 may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or similar. One or more through holes 190 and / or one or more slots 192 may additionally or alternatively be provided in the reinforcement 110. This perspective view is also representative of a perspective view of the steel pile profiles of Figures 12 to fifteen. In the example of the UHSW steel pile 100 of Figures 10 to 11, the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to 1.6 mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The C channel profile in Figure 11 is produced from the width of the steel sheet and therefore has a total material length in cross section of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third the width of the steel sheet. For edged projections, the material thickness T is maintained in each layer. However, by splicing the first layer 122, 132 and the second layer 124, 134, and although the thickness of the material remains as T, the thickness of the projection has doubled as reflected by Tx2 in Figure 10. In Figure 10, the double boss thickness TX2 extends from the teardrop transition 160 to the curved transition 140. In the example of Figure 10, the height H100 of the steel pile is greater than the width Wk» of the steel pile . In the example of Figure 10, the steel pile 100 is symmetrical about an axis bisecting the height Hwo of the steel pile 100. A typical UHSW steel pile of Figure 10 may be, for example, a C channel ( with or without corrugations) 6x4, 6x6, 8x4.5, 8x5, 8x6, 8x8, 10x8,10x10, 12x8,12x10,12x12, 14x10,14x12,14x14 (in inches), and any value in between or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). ). Turning now to Figure 12, a C-channel UHSW steel pile 200 is illustrated. Channel C comprises a stiffener 210, a first boss 220, and a second boss 230 and is an example referred to herein as a channel. C corrugated or NCW pile. The reinforcement 210 extends to a height H200 of the steel pile 200 and transitions to a curved transition 240 at the first projection 220 at a first end 211. The reinforcement 210 also transitions to a curved transition 250 at the second projection 230 at a second end 212. In the present example, each curved transition 240, 250 has a respective radius R240, R250. Each spoke R240, R250 forms an arc greater than 90 degrees. Furthermore, each projection 220, 230 remains generally perpendicular to the reinforcement 210. The reinforcement 210 further comprises one or more reinforcement corrugations. In Figure 12, the reinforcement 210 comprises a first reinforcement corrugation 213 and a second reinforcement corrugation 214. In order to form the reinforcement corrugations, an outer surface 215 of the reinforcement 210 is displaced from one or more interior surfaces 216 of the reinforcement 210, in one direction width W200 ΜΛ / I OU of the steel pile. Both the outer surface 215 and each inner surface 216 extend in a direction of the height H200 of the steel pile where the outer surface 215 and each inner surface 216 are perpendicular to the first projection 220 and / or the second projection 230. outer surface 215 and each inner surface 216 form the majority of the reinforcement 200 such that the reinforcement is referred to as remaining generally perpendicular to the first projection 220 and / or the second projection 230. Each curved transition 240, 250 extends from a respective first projection 220 or second projection 230 along the arc formed by radius R240, R250, respectively. As noted above, the arc of each curved transition 240, 250 extends more than 90 degrees to form the reinforcement corrugation on a respective inner surface 216 which then transitions to the outer surface 215. The outer surface 215 is It is located centrally on the reinforcement 210, in relation to the height H200 of the steel pile. In Figure 12, the arc formed by radius R240 and the arc formed by radius R250 each comprise a tangent that aligns with the outer surface 215 in the direction of the height H200 of the steel pile. The reinforcing corrugations 213, 214 of the UHSW steel pile of Figure 12 comprise a surface that is perpendicular to the first projection 220 and the second projection 230. From each respective curved transition 240, 250, the reinforcement 210 is recessed, forming the two reinforcing corrugations 213, 214. Each reinforcing corrugation then returns to the full width W200 and is connected by the outer surface 215 of the reinforcement 210. Instead, and as illustrated by the boss corrugations 222, 232, shown below , the corrugation can be completely formed by an arch. Still referring to Figure 12, the first projection 220 may also comprise one or more corrugations. In the example of Figure 12, the first boss 220 comprises a boss corrugation 222 formed centrally along the width W200 of the steel pile. The boss corrugation 222 is an arc formed by a radius R222 that extends inwardly from between the first outer surface 224 and a second outer surface 226 of the boss 220. Opposite the reinforcement 210, a first flange 228 extends from the first projection 220 in a curved transition 260. The first flange extends in a direction of the height H200 of the steel pile and is parallel to the inner surface 216 and the outer surface 215 of the reinforcement 210. The first flange 228 may further comprise a transition curved 280 within a return section 229. The return section 229 extends inwardly from the first flange 228 towards the reinforcement 210. The return section 229 is parallel to the first outer surface 224 and the second outer surface 226 of the salient 220. Like the first projection 220, the second projection 230 may also comprise one or more corrugations. In the example of Figure 12, the second boss 230 comprises a boss corrugation 232 formed centrally along the width W200 of the steel pile. The boss corrugation 232 is an arc formed by a radius R232 that extends inwardly from between the first outer surface 234 and a second outer surface 236 of the boss 230. Opposite the reinforcement 210, a second flange 238 extends from the second projection 230 in a curved transition 270. The second flange extends in a direction of the height H200 of the steel pile and is parallel to the inner surface 216 and the outer surface 215 of the reinforcement 210. The second flange 228 may further comprise a transition curved 290 within a return section 239. The return section ΜΛ / t / ZUZZ / U4Z I OU return 239 extends inwardly from the flange 228 towards the reinforcement 210. The return section 239 is parallel to the first exterior surface 234 and the second exterior surface 236 of the second projection 230. In In the example of Figure 12, the thickness T of the steel sheet, which forms the steel pile 200, is 1.575 mm (0.062 inches (")). In some examples, the thickness of the steel sheet, which forms the steel pile 200, may be 2 mm or less. In other examples, the thickness of the steel sheet, which forms the steel pile 200, may be 2.5 mm or less. The first projection 220 and / or the second projection 230 of the UHSW steel pile 200 of Figure 12 may additionally comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. One or more through holes and / or one or more slots may be provided, or alternatively, in the reinforcement 210. In the example of the UHSW 200 steel pile in Figure 12 the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to to 1.6mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The C channel profile in Figure 11 is produced from the width of the steel sheet and therefore has a total material length in cross section of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third the width of the steel sheet. In corrugations, the thickness T of the material is maintained at each layer and transition. In the example in Figure 12, the height H200 of the steel pile is greater than the width W200 of the steel pile. In the example of Figure 12, the steel pile 200 is symmetrical about an axis bisecting the height H200 of the steel pile 200. A typical UHSW steel pile of Figure 12 may be, for example, a C channel ( with or without corrugations) 6x4, 6x6, 8x4.5, 8x5, 8x6, 8x8, 10x8, 10x10, 12x8 12x10, 12x12, 14x10, 14x12, 14x14 (in inches), and any value in between or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). ). Referring now to Figure 13, a UHSW steel pile 300 is illustrated which is a C channel comprising a reinforcement 310, a first projection 320, and a second projection 330, and is another example of a corrugated C channel, or NCW pile. Like the steel pile of Figure 12, the reinforcement 310 of the steel pile 300 of Figure 13 extends a height H300 of the steel pile 300 and transitions to a curved transition 340 within the first projection 320 in a first end 311. The gusset 310 also transitions to a curved transition 350 within the second projection 330 at a second end 312. Each curved transition 340, 350 has a radius R340, R350, respectively. In Figure 13, the reinforcement 310 comprises a single reinforcement corrugation 313. The single reinforcement corrugation 313 is placed centrally relative to the height of the steel pile H300. This contrasts with Figure 12 where the reinforcement 210 comprises a first reinforcement corrugation ΜΛ / I OU 213 and a second reinforcing corrugation 214. To form the reinforcing corrugation of Figure 13, an outer surface 315 of the reinforcement 310 is offset from an inner surface 316 of the reinforcement 310, in a direction of the width W300 of the steel pile. Both the outer surface 315 and the inner surface 316 extend in a direction of the height H300 of the steel pile where the outer surface 315 and the inner surface 316 are perpendicular to the first projection 320 and / or the second projection 330. outer surface 315 and each inner surface 316 form the majority of the reinforcement 300 such that the reinforcement is referred to as remaining generally perpendicular to the first projection 320 and / or the second projection 330. Each curved transition 340, 350 extends from a respective first projection 320 or a second projection 330 along the arc formed by radii R340, R350, respectively. Also, unlike Figure 12, the arc of the curved transition 340, 350 of Figure 13 only extends 90 degrees, since the single reinforcing corrugation 313 is placed centrally above the reinforcement 310 and is independent of the curved transitions 340, 350. The single reinforcing corrugations 313 of the UHSW steel pile of Figure 13 comprise an interior surface 316 that is perpendicular to the first projection 320 and the second projection 330. The interior surface 316 may additionally, or alternatively, be referred to as being recessed, relative to the reinforcement 310, or the outer surface 315 of the reinforcement 310. Instead, and as illustrated by the protrusion corrugations 322, 332, shown below, the corrugation can be formed completely by an arch. Still referring to Figure 13, the first projection 320 may also comprise one or more corrugations. In the example of Figure 13, the first boss 320 comprises a boss corrugation 322 formed centrally along the width W300 of the steel pile. The protrusion corrugation 322 is an arc formed by a radius R322 extending inwardly from between a first outer surface 324 and a second outer surface 326 of the protrusion 320. The first flange 328 may comprise a curved transition 380 within a section return section 329. The return section 329 extends inwardly from the first flange 328 towards the reinforcement 310. The return section 329 is parallel to the first exterior surface 324 and the second exterior surface 326 of the projection 320. Like the first projection 320, the second projection 330 may also comprise one or more corrugations. In the example of Figure 13, the second boss 330 comprises a boss corrugation 332 formed centrally along the width W300 of the steel pile. The boss corrugation 332 is an arc formed by a radius R332 that extends inwardly from between the first outer surface 334 and a second outer surface 336 of the boss 330. Opposite the reinforcement 310, a second flange 338 extends from the second projection 330 in a curved transition 370. The second flange extends in a direction of the height H300 of the steel pile and is parallel to the inner surface 316 and the outer surface 315 of the reinforcement 310. The second flange 328 may further comprise a transition curved 390 within a return section 339. The return section 339 extends inwardly from the flange 328 toward the gusset 310. The return section 339 is parallel to the first outer surface 334 and the second outer surface 336 of the second projection 330. In the example of Figure 13, the thickness T of the steel sheet that forms the steel pile 300 is 1.575 mm (0.062 inches (")). In some examples, the thickness of the steel sheet that forms ΜΛ / t / ZUZZ / U4Z I OU 300 steel pile can be 2 mm or less. In other examples, the thickness of the steel sheet forming the steel pile 300 may be 2.5 mm or less. The first projection 320 and / or the second projection 320 of the UHSW steel pile 300 of Figure 13 may additionally comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. Additionally or alternatively, one or more through holes and / or one or more slots may be provided in the gusset 310. In the example of the UHSW 300 steel pile in Figure 13, the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to 1.6 mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The C channel profile in Figure 11 is produced from the width of the steel sheet and therefore has a total material length in cross section of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third the width of the steel sheet. In corrugations, the thickness T of the material is maintained at each layer and transition. In the example in Figure 13, the height H300 of the steel pile is greater than the width W300 of the steel pile. In the example of Figure 13, the steel pile 300 is symmetrical about an axis that bisects the height H300 of the steel pile 300. A typical UHSW steel pile of Figure 13 may be, for example, a C channel ( with or without corrugations) of 6x4, 8x4.5, 8x5, 8x6, 10x8, 12x8, 12x10, 14x10, 14x12 (in inches) or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). ). Referring now to Figure 14, a UHSW 400 steel pile having a tubular cross section is illustrated. The steel pile 400 in Figure 14 is square. The steel pile 400 comprises a first side wall 410, a second side wall 420, a third side wall 430, and a fourth side wall 440. The first side wall 410 is generally parallel to the third side wall 430. The second side wall 420 is generally parallel to the fourth side wall 440. Additionally, the first side wall 410 and the third side wall 430 are generally perpendicular to the second side wall 420 and the fourth side wall 440. As used in the present context, "generally ” refers to the sidewall configuration with the exceptions of corrugations, as described below. The height H400 and width W400 of the steel pile 400 in Figure 14 are equal, forming a cross section that is generally square. Again, as used in the present context, “generally” refers to the configuration of the wall with the exceptions of corrugations. In other words, the overall dimension of each side wall of the 400 steel pile, in cross section, is the same. A curved transition is provided between each side wall. More specifically, a first curved transition 450 is provided between the first side wall 410 and the second side wall 420; a second curved transition 460 is provided between the second side wall 420 and the third wall ΜΛ / I OU lateral 430; a third curved transition 470 is provided between the third side wall 430 and the fourth side wall 440; and a fourth curved transition 470 is provided between the fourth side wall 440 and the first side wall 410. Each curved transition 450, 460, 470 and 480 is an arc formed by respective radii R450, FUeo, R470 and R480. Each one or more of the side walls of the steel pile 400 of Figure 14 may comprise one or more corrugations. In the example of Figure 14, each side wall 410, 420, 430, 440 comprises a corrugation 412, 422, 432, 442, respectively. In Figure 14, each sidewall and corrugation have the same configuration and size. Therefore, the cross section of Figure 14 is symmetrical along any plane extending in the longitudinal axis Xax¡s. Like the reinforcement corrugations of Figures 12 to 13, each corrugation 412, 422, 432, 442 comprises an interior surface 413, 423, 433, 443, respectively, offset from and parallel to the exterior surfaces 411,421,431,441 of a side wall 410, 420, 430, 440, respectively. In the example of Figure 14, oblique side walls 480 are provided to make the transition from the inner surface to the outer surface. In Figure 14, each interior surface comprises opposing oblique side walls 414, 424, 434, 444. It may provide an arc to transition between each surface, between each surface and an oblique side wall, or the like. As previously indicated, the corrugation serves as a reinforcement for the steel pile. In Figure 14, each corrugation 412, 422, 432, 442 extends inwardly. In other examples, each of the corrugations may extend outward, alternatively, or form opposite halves. In some examples, one or more of the side walls may comprise multiple corrugations such as, for example, the reinforcement corrugations of Figure 10. Additionally, or alternatively, the corrugation may be formed entirely by an arc, such as the boss corrugations as illustrated in Figures 12 to 13. The corrugations may be a combination of the corrugations described with respect to Figure 14 and corrugations formed entirely by an arch. In the example of the UHSW 400 steel pile in Figure 14, the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to 1.6 mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The tube profile in Figure 14 is produced from the width of the steel sheet and therefore has a total cross-sectional material length of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third the width of the steel sheet. Additionally, a weld, rivet, overlap and / or joint may be provided to close the tubular steel pile of Figure 14 when formed from a steel sheet. The welds can be a continuous weld, partial welds and / or spot welds. The weld(s), rivet(s), overlay(s), and / or joint(s) may be placed on an arch, on a corrugation, on an interior surface, on an exterior surface, and / or on an oblique side wall. A typical UHSW steel pile in Figure 14 can be, for example, a steel tube (with or without corrugations) of 4x4, 6x6, 8x8, 12x12 (in inches), and any value in between or ΜΛ / t / ZUZZ / U4Z I OU of strength of the steel pile, comparatively with the previous steel piles. Specifically, as tested, previous steel piles of comparable dimensional characteristics were worn and structurally failed where the steel pile of the present disclosure provides a 25% RPM increase. Furthermore, previous steel piles were not additionally weather-resistant steel in the absence of a galvanized or zinc surface. Therefore, the above steel piles are susceptible to corrosion due to their placement in outdoor conditions, including soil and earth conditions, or require additional treatment such as, for example, galvanization. Again, the present steel pile provides the corrosion rate necessary to withstand these conditions. The present strength properties and corrosion properties have not been seen before in combination for such a product. The lined protrusions of the lined C channel, as described above and illustrated in Figure 10, the corrugated reinforcement and the protrusions of the corrugated C channel, as described above and illustrated in Figures 12 to 13, and the corrugated tubes , as described previously and illustrated by Figures 14 to 15, also increase the rigidity of the steel pile to prevent buckling and / or withstand the driving forces as indicated above. By providing the features and shapes of hemmed C-channel, corrugated C-channel and corrugated tubes, the material thickness of the thin cast steel strip forming the ultra-high weathering steel pile can be further maintained at 2.5 mm or less, 2.0 mm or less, or 1.6 mm or less, as described herein. Reducing the thickness of the material further helps reduce the drive force required to drive the ultra-high-strength weathering steel pile into the ground surface (e.g., soil or soil) by reducing cross-shear strength. between the ultra-high weathering steel pile and the ground surface. Additionally, because the ultra-high weathering steel pile does not have an independently applied coating for corrosion resistance, such coating is not susceptible to being stripped or removed during the installation process when it comes into contact with with the soil surface and / or that may otherwise negatively impact water and / or soil conditions by reacting with it. As used herein, independently applied coatings are protective coatings that may be a surface protector that is independent of the composition of the steel. Some examples of such independently applied protective coatings include a zinc coating, a galvanized coating (e.g., a hot dip galvanized coating), an aluminum-silicon corrosion resistant coating, or the like. More importantly, the steel piles or foundations of the present disclosure produce the corrosion resistance, as set forth below, without the aid of an independently applied coating. Inherently, by definition, weathering steels, including the ultra-high-strength weathering steel described herein, possess the required corrosion resistance of the applied coating process regardless of the hot-dip galvanizing that is applied. would occur otherwise. Therefore, the weathering steel of the present disclosure would not require or possess a zinc coating, a hot dip galvanized coating or the like. ΜΛ / t / ZUZZ / U4Z I OU An additional test was performed to evaluate the corrosion rate of UHSW steel compared to that of a galvanized (“HDG”) steel for varied geometry, burial duration, and simulated aging. Tables 3-4, shown below, illustrate the results of these tests. The materials were tested in moderately salty, low-resistivity soil, which was also designated as “very corrosive.” The geometry of the material tested included small angled stakes and full-size cold-rolled C-shaped piles. The material designated as “applied current” was given a voltage sufficient to artificially induce corrosion for approximately 24 hours, in an attempt to simulate the longer-term effects of the installation. Under this comparative analysis, the measurement speeds of the UHSW steel material varied from 77% to 99% of the speeds measured for the HDG steel material. Table 3 ID Material Surface area (in2) Corrosion current (mA) Corrosion rate (mpy) 1 UHSW Stake 100.04 40.00 28.20 2 UHSW Stake 100.04 40.00 28.20 3 HDG Stake 100.04 40.00 36.50 4 HDG Stake 100.04 35.00 3 1.90 5 Pile C UHSW 2171.00 110.00 3.60 6 Pile C UHSW 2270.00 120.00 3.70 7 Pile C HDG 3697.00 150.00 3.70 8 UHSW (applied current) 100.40 35.00 24.70 9 HDG (applied current) 100.40 35.00 31.90 Table 4 Material Average factor, corrosion rate (mpy) Ratio, UHSW / HDG Factors averaged / unitless) UHSW Stake 28.20 0.82 HDG Stake 34.20 Pile C UHSW 3.65 0.99 Pile C HDG 3.70 UHSW (applied current) 24.70 0.77 HDG 31.90 The above calculations of comparative testing and structural capacity illustrate that steel piles produced from a thin strip of cast steel performed better than hot-dip galvanized steel piles, as well as steel piles from the former. The UHSW steel pile of the present description provides greater resistance to corrosion and much thinner material thicknesses. These improvements are preserved, simultaneously maintaining desirable strength and elongation properties that allow UHSW steel piles to resist deformation while being driven into the ground. As also illustrated by the material thicknesses, UHW steel piles are produced at much lower weights than previous steel piles. Specifically, compared to a steel pile constructed from a W6x7 T-beam, weighing 0.97 kilograms (kg) per meter (7 pounds (Ibs) per foot), or from a W6x9 T-beam, weighing 1.24 kilograms (kg) per meter (9 pounds (Ibs) per foot), UHSW hemmed C channel, or an NXW pile, of a comparative general cross section weighs 0.69 kilograms (kg) per meter (5 pounds (lbs) per foot) and the UHSW corrugated C channel, or NCW pile, of comparative cross section weighs 0.48 kilograms (kg) per meter (3.5 pounds (Ibs) per foot). The UHW steel piles of the present description are also provided without a hot dip galvanized coating or zinc coating. The UHW steel piles of the present description thus eliminate any undesirable interaction between soil or groundwater and a zinc coating that is otherwise present with an HDG steel pile. Other alternatives to a steel pile that does not have an independently applied coating, such as the other non-galvanized steel piles tested herein, were significantly better performed by the UHSW steel pile of the present disclosure. Even with a galvanized coating, HDG steel pile structural capacity and service life fails to exceed the structural capacity and service life of a thinner UHW steel pile. The time for the galvanic layer to completely corrode is calculated using the thickness divided by the corrosion rate. The remaining time is then multiplied by the corrosion rate of the steel to determine the thickness of the final material. For example, consider a G235 sheet metal component with a thickness of 0.31 cm (0.124”): If the standard corrosion rate relationship between the zinc layer and the base metal is applied in the corrosive soil condition, and Calculates that a corrosion rate of zinc coating of G235 galvanized steel (0.0053 cm / side (2.1 mils / side)) is 0.007 cm / a (0.00037y), so a corrosion rate of base steel should be approximately 0.0053 cm / a (0.00217y), with a useful life of 30 years, the total reduction, per side, is calculated as follows: 0.0021 / side 0.0003 / year / side 0.0021 / year / side * 23 years * 2 sides = 0.0966 ΜΛ / t / ZUZZ / U4Z I OU The total metal loss will be approximately 0.25 cm (0.1008”), and this would leave a component 0.058 cm (0.0232” thick at the end of life. Assuming that UHSW material with a thickness of 0.0157 cm (0.062'j) corrodes at the same rate as zinc, the final thickness is more simply calculated as follows after the first two years: 0.3 mils / year / side *30 years *2 sides = 18 mils resulting in a material thickness of 0.111 cm (0.0440”) at the end of 30 years. This mild corrosivity case demonstrates how the material can outperform zinc + carbon steel structures for longevity, and the significantly increased strength compared to carbon steel allows for significantly higher capacities in virtually any loading scenario. In addition to the material property testing as illustrated above, three-point bending tests were also performed to evaluate the strength of the respective cross sections for the piles described herein. Specifically, three-point bending tests illustrate sustained and comparatively improved flexural strength derived from the particular characteristics of the pile shapes, or cross sections thereof. The comparatively improved flexural strength can be attributed to the particular characteristics of the pile shapes, or cross sections thereof, in view of forming each tested pile from the same thin cast steel strip material having a thickness less than or equal to 1.6 mm. The applied bending test was performed by the University of Nebraska-Lincoln. In the tests, the lengths of the tested piles were held by three collars at each end (left and right) and one in the middle. The piles were held on the ends by five bolts. Two bolts were placed on the upper and lower bosses each, and one bolt secured to the pile reinforcement to the collar. The center collar was attached to the pile using a single bolt in the pile reinforcement. Each of the end collars were further attached to separate steel plates positioned beneath the pile and in a certain manner that allows twisting to occur and the pile to flex downward. Specifically, the plates were supported on two steel tubes that act as rollers to make the plates move. The load was applied to the pile using a rammer and measured with a load cell placed between the rammer and the center collar. Four chain potentiometers were also used to measure deflection at various points throughout the test. Two chain potentiometers were placed to measure the deviation from the mean height of the reinforcement. These potentiometers were placed at the bottom of the lower bosses at points on the side of the end collars. The remaining two potentiometers measure the deflection near the center of the pile. One was attached to the central collar at the mid-height of the pile boss. The other was attached directly to the pile at the same location. As a reference value for a sustained bending strength, a pile 300 having the cross section of Figure 13 was subjected to the above bending test. While pile 300 of Figure 13 produced a measured flexural strength, improvements have been made and additional shapes with higher flexural strength have been developed, the cross sections for which are illustrated by ΜΛ / t / ZUZZ / U4Z I OU the piles 600, 700 and 800 of Figures 18, 20 and 22, respectively, and are further described below. In the bending test, the tested pile 300 of Figure 13 has a height of 20.3 cm (8 in.), a width Waoode 15.2 cm (6 in.), and a material thickness T of 0.062 in. (0.1575 mm). ). Figure 16 illustrates a load deflection curve for pile 300 of Figure 13 with results derived from tests designated S2, S3 and S6. Figure 17 illustrates a load deflection curve for pile 300 of Figure 13 with results from a test designated S7. In test S7, all the connections of the chain potentiometer were moved and connected to the bottom boss for the offset readings. Four inclinometers were also used for each of the tests. The inclinometers were placed over each collar with the additional inclinometer placed over a pile reinforcement 300 adjacent to the center collar. Inclinometers measured the twist of the collars and element and were used to ensure that the piles were loaded close to the reinforcement. Load placement was initiated until the pile achieved failure without exceeding a twist greater than 3.5 degrees at any of the inclinometer positions. The slope of the curves in each of Figures 17 to 18 corresponds to a modulus of rupture of approximately 15 in.4 for a steel elastic modulus (E) of 26,000 ksi - 290,000 ksi (179 GPa - 200 GPa). Table 5, shown below, illustrates the maximum load and the load at the onset of nonlinearity for the examples corresponding to pile 300 in Figure 13. Table 5 ΜΛ / t / ZUZZ / U4Z I OU Pile 300 (NCW) 8*6 Load at the beginning of nonlinearity (Ibs) Deviation at the beginning of nonlinearity (in.) Maximum load (Ibs) Deviation at maximum load (in.) S2 7900 0.289 8237 0.369 S3 5184 0.238 6814 0.334 S6 6430 0.264 8202 0.35 S7 5640 0.091 8819 0.257 Average 6289 0.221 8018 0 Table 6, shown below, illustrates the elastic stiffness observed during testing for the examples corresponding to pile 300 in Figure 13. Because the deflection sensors were located in the reinforcement for S2-S6, very high strains were reported. (probably due to asymmetric pile rotation and local deformations near the central collar). Table 6 Pile 300 (NCW) 8*6 Stiffness (k / in.) 1 calculated (in4) Moment at the beginning of nonlinearity (kp*in.) Moment at maximum load (kp*in.) S2 22.9 6.8 142 148 S3 20.2 6.0 93 123 S6 23.0 6.9 116 148 S7 62.0 18.5 102 159 Average 32.0 9.55 113 144 ΜΛ / 1 OU Table 7, shown below, illustrates the deflection at 50% load for the examples corresponding to pile 300 in Figure 13. Table 7 Pile 300 (NCW) 8*6 Deviation at 50% load S2 0.18 S3 0.169 S6 0.178 S7 0.068 Average 0.149 Additional shapes were developed to further improve the above properties in relation to their cross-sectional characteristics. Cross sections for these additional shapes are illustrated by piles 600, 700 and 800 of Figures 18, 20 and 22, respectively, with the results of comparative tests illustrated in Figures 19, 21 and 23 to 24 and Tables 8-10, 11-13 and 14-19, respectively. Referring now to Figure 18, there is illustrated a UHSW steel pile 600 that is a variation of a channel C comprising a reinforcement 610, a first projection 620 and a second projection 630. More specifically, the present example is a variation of the corrugated hemmed C channel, or NCW pile, of Figure 13. The UHSW steel pile 600 of the present example is called an M channel (e.g., M8x6, or the like). Like the steel pile of Figure 13, the reinforcement 610 of the steel pile 600 of Figure 18 extends a height Ηβοο of the steel pile 600 and transitions to a curved transition 640 within the first projection 620 in a first end 611. The gusset 610 also transitions to a curved transition 650 within the second projection 630 at a second end 612. Each curved transition 640, 650 has a radius R64o, Reso, respectively. Each curved transition 640, 650 extends from a respective first projection 620 or second projection 630 along the arc formed by radii Re4o, Reso, respectively. The arc of the curved transition 640, 650 of Figure 22 extends 90 degrees. In Figure 18, the reinforcement 610 comprises a discontinuity that is a V-shaped transition 613. The V-shaped transition 613 extends in the same direction as each projection 620, 630 relative to the reinforcement 610. This is in contrast to, and is compared to the single reinforcing corrugation 313 of the pile 300 of Figure 13. The V-shaped transition 613 is placed centrally relative to the Heco height of the steel pile. The apex 616 of the V-shaped transition 613 moves from an outer surface 615 of the reinforcement 610, in the same direction as the projections extend the width of the Weoo steel pile. The apex 616 may additionally, or alternatively, be referred to as being recessed relative to the fabric 610 or recessed relative to the outer surface 615 of the reinforcement 610. The opposite sides 617, 618 of the V-shaped transition meet at oblique angles. in relation to the reinforcement 610. In one example, the opposite sides 617, 618 are at right angles to each other. Still referring to Figure 18, the first projection 620 may also comprise one or more discontinuities in which the discontinuities are V-shaped transitions. In the example of Figure 18, the first projection 620 comprises a V-shaped transition 622 formed centrally along the width of the Weoo steel pile. In some examples, corrugations, arches and / or V-shaped transitions may be interchanged and / or combined on or between the bosses and reinforcements of a single pile. In Figure 18, the V-shaped transition 622 extends inwardly from a first outer surface 624 and a second outer surface 626 of the projection 620. Opposite the reinforcement 610, a first flange 628 extends from the first projection 620 in a curved transition 660. The first flange extends in a direction of the height Heoo of the steel pile and is parallel to the outer surface 615 of the reinforcement 610. The first flange 628 may further comprise a curved transition 680 in a first return 629A . The first return 629A extends inwardly from the first flange 628 toward the gusset 610. The first return 629A is parallel to the first outer surface 624 and the second outer surface 626 of the projection 620. A second return 629B may also be provided that returns in one direction of the gusset 620. It is noted herein that the second return 629B may return in the opposite direction (e.g., toward the opposite projection). It is also noted herein that the second return 629B may return at an oblique angle relative to the first return 629A. In the present example, the second return 629B is at a 90 degree angle relative to the first return 629A. A pile that has a second return can be described more generally as having a triple edge. Like the first projection 620, the second projection 630 may also comprise one or more discontinuities where the discontinuities have V-shaped transitions. In the example of Figure 18, the second projection 630 comprises a V-shaped transition 632 formed centrally along the Weoo width of the steel pile. In some examples, corrugations, arches and / or V-shaped transitions may be interchanged and / or combined on or between the bosses and reinforcements of a single pile. In Figure 18, the V-shaped transition 632 extends inwardly from a first outer surface 634 and a second outer surface 636 of the projection 630. Opposite the reinforcement 610, a first flange 638 extends from the second projection 630 in a curved transition 670. The first shoulder extends in a direction of the height Heoo of the steel pile and is parallel to the outer surface 615 of the reinforcement 610. The first shoulder 638 may further comprise a transition ΜΛ / t / ZUZZ / U4Z I OU curved 690 in a first return 639A. The first return 639A extends inwardly from the first flange 638 toward the gusset 610. The first return 639A is parallel to the first outer surface 634 and the second outer surface 636 of the projection 630. A second return 639B may also be provided that returns in one direction of the reinforcement 630. In the example of Figure 18, the thickness T of the steel sheet forming the steel pile 600 is 1.575 mm (0.062 inches (")). In some examples, the thickness of the steel sheet forming the steel pile 600 may be 2 mm or less. In other examples, the thickness of the steel sheet forming the steel pile 600 may be 2.5 mm or less. The first projection 620 and / or the second projection 630 of the UHSW steel pile 600 of Figure 18 may further comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. Additionally or alternatively, one or more through holes and / or one or more slots may be provided in the gusset 610. In the example of the UHSW 600 steel pile in Figure 18 the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to to 1.6mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The M channel profile in Figure 18 is produced from the width of the steel sheet and therefore has a total material length in cross section of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third the width of the steel sheet. In V-shaped transitions, the thickness T of the material is maintained in each layer and transition. In the example in Figure 18, the height Heoo of the steel pile is greater than the width Weoo of the steel pile. In the example of Figure 18, the steel pile 600 is symmetrical about an axis that bisects the height Heoo of the steel pile 600. A typical UHSW steel pile of Figure 18 may be, for example, an M6x4, M8x4 .5, M8x5, M8x6, M10x8, M12x8 M12xl0, M14xl0, M14xl2 (in inches), or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). ). In order to illustrate the flexural strength, a pile 600 of Figure 18 was subjected to the same bending test as described above, with respect to Figure 13. In the bending tests, the tested pile 600 of Figure 18 has a height Heoo of 20.3 cm (8 inches), a width Weoo of 15.2 cm (6 inches), and a material thickness T of 0.062 inches (“) (0.1575 mm). Figure 19 illustrates a load deflection curve for pile 600 of Figure 18 with results derived from tests designated S2, S3 and S4. The sensors were placed on the reinforcement for tests S2-S4. The material delivered does not look like in the test results. Rather, a local bearing failure occurred before the material was delivered. Also, no true local buckling of the boss or any other buckling was observed. The slope of the curves in each of Figures 19 corresponds to a moment of inertia of 20.8 in4 to 18.6 in4 for a steel elastic modulus (E) of 26,000 ksi to 29,000 ksi (179 GPa - 200 GPa). Table 8, shown below, illustrates the maximum load and the load at the onset of nonlinearity for the examples corresponding to pile 600 in Figure 18. Table 8 Pile 600 M8*6 Load at the beginning of nonlinearity (Ibs) Deviation at the beginning of nonlinearity (in.) Maximum load (Ibs) Deviation at maximum load (in.) S2 5684 0.0946 10815 0.339 S3 6518 0.0922 12309 0.441 S4 7769 0.1 11300 0.301 Average 6657 0.0956 11475 0.360 Table 9, shown below, illustrates the elastic stiffness observed during the test. Table 9 Pile 600 M8*6 Stiffness (k / in) Calculated I (in4) Moment at onset of nonlinearity (kip*in) Moment at maximum load (kip*in) S2 60.1 18.0 102 195 S3 70.7 21.1 117 222 S4 77.7 23.2 140 203 Average 69.5 20.8 120 207 Table 10, shown below, illustrates the deflection at 50% load for the examples corresponding to pile 600 in Figure 22. Table 10 Pile 600 M8*6 Deviation at 50% load S2 0.090 S3 0.081 S4 0.069 Average 0.080 Referring now to Figure 20, a UHSW steel pile 700 is illustrated which is a C channel comprising a reinforcement 710, a first projection 720, and a second projection 730, and is a variation of the corrugated C channel, or pile of NCW. Like the steel pile of Figure 13, the reinforcement 710 of the steel pile 700 of Figure 20 extends to a height H700 of the steel pile 700 and transitions to a curved transition 740 within the first projection 720 at a first end 711. The gusset 710 also transitions to a curved transition 750 into the second projection 730 at a second end 712. Each curved transition 740, 750 has a radius R740, R750, respectively. Each curved transition 740, 750 extends from a respective first projection 720 or second projection 730 along the arc formed by radii R740, R750, respectively. The arc of the curved transition 740, 750 of Figure 24 extends 90 degrees. In Figure 20, the reinforcement 710 comprises one or more discontinuities that can be characterized as corrugations that are arcs having a radius. Specifically, the first flange 720 comprises a first arc 714 formed by a radius R714 and a second arc 716 formed by a radius R716. In the example of Figure 20, the first arch 714 and the second arch 716 are evenly spaced across the width of the steel pile W700. The radius R714,716 extends inwardly from an outer surface 715 of the reinforcement 710. The first projection 720 may also comprise one or more discontinuities that may be characterized as corrugations. In the example of Figure 20, the first boss 720 comprises a boss corrugation 722 formed centrally along the width W700 of steel pile. The boss corrugation 722 is an arc formed by a radius R722 that extends inwardly from between a first outer surface 724 and a second outer surface 726 of the boss 720. Opposite the reinforcement 710, a first flange 728 extends from the first projection 720 in a curved transition 760. The first shoulder extends in a direction of the height H700 of the steel pile and is parallel to the inner surface 716 and the outer surface 715 of the reinforcement 710. The first shoulder 728 may further comprise a transition curved 780 inwardly of a return section 729. The return section 729 extends inwardly from the first flange 728 towards the reinforcement 710. The return section 729 is parallel to the first outer surface 724 and the second outer surface 726 of the 720 protrusion. Like the first projection 720, the second projection 730 may also comprise one or more discontinuities that may be characterized as corrugations. In the example of Figure 20, the second boss 730 comprises a boss corrugation 732 formed centrally along the width W700 of the steel pile. The boss corrugation 732 is an arc formed by a radius R732 that extends inwardly from between the first outer surface 734 and a second outer surface 736 of the boss 730. Opposite the reinforcement 710, a second flange 738 extends from the second projection 730 in a curved transition 770. The second flange extends in a direction of the steel pile height H700 and is parallel to the inner surface 716 and the outer surface 715 of the reinforcement 710. The second flange 728 may further comprise a transition curved 790 into a return section 739. The return section 739 extends inwardly from the flange 728 towards the reinforcement 710. The return section 739 is parallel to the first outer surface 734 and the second outer surface 736 of the second projection 730. In the example of Figure 20, the thickness T of the steel sheet forming the steel pile 700 is 1.575 mm (0.062 inches (")). In some examples, the thickness of the steel sheet forming the steel pile 700 may be 2 mm or less. In other examples, the thickness of the steel sheet that ΜΛ / t / ZUZZ / U4Z I OU form 700 steel pile can be 2.5 mm or less. The first projection 720 and / or the second projection 730 of the UHSW steel pile 700 of Figure 20 may further comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. Additionally or alternatively, one or more through holes and / or one or more slots may be provided in the gusset 710. In the example of the UHSW 700 steel pile in Figure 20 the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to to 1.6mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The C channel profile in Figure 20 is produced from the width of the steel sheet and therefore has a total material length in cross section of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third of the W700 width of the steel sheet. In the example in Figure 20, the height H700 of the steel pile is greater than the width W700 of the steel pile. In the example of Figure 20, the steel pile 700 is symmetrical about an axis that bisects the height H700 of the steel pile 700. A typical UHSW steel pile of Figure 20 may be, for example, a C6x4, C8x4 , C8x4.5, C8x5, C8x6, C10x8, C12x8, C12x10, C14x10, C14x12 (in inches), or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). ). To illustrate the flexural strength, multiple piles 700 having the cross section of Figure 20 were subjected to the same flexural test as described previously, in relation to Figures 13 and 18. In a first flexural test , the tested pile 700 of Figure 20 has a height H700 of 20.3 cm (8 inches), a width W700 of 10 cm (4 inches), and a material thickness T of 0.062 inches (“”) (0.1575 mm) and which is called 08x4. Figure 21 illustrates a load deflection curve for the 08x4 pile in Figure 20 with results derived from tests labeled S1, S2, S3, S4, and S5. The sensors were located in the reinforcement for tests S1-S5. No local buckling was observed until failure. The slope of each curve in Figure 21 corresponds to a moment of inertia of 6.2 to 5.6 in4 for a steel elastic modulus (E) of 26,000 ksi - 29,000 ksi (179 GPa - 200 GPa), respectively. Table 11, shown below, illustrates the maximum load and the load at the onset of nonlinearity for the 08x4 pile 700 of the specimens in Figure 20. Table 11 Pile 700 C8*4 Load at the beginning of nonlinearity (Ibs) Deviation at the beginning of nonlinearity (in.) Maximum load (Ibs) Deviation at maximum load (in.) S1 6334 0.168 7083 0.25 S2 6291 0.253 6475 0.546 S3 5045 0.287 6817 0.73 S4 4660 0.212 6916 0.439 S5 6490 0.347 7092 0.543 Average 5764 0.253 6876 0.502 Table 12, shown below, illustrates the elastic stiffness observed during testing for the C8x4 pile 700 of the specimens in Figure 20. Table 12 Pile 700 C8*4 Stiffness (k / in) Calculated I (in4) Moment at onset of nonlinearity (kip*in) Moment at maximum load (kip*in) S1 37.7 11.3 114 127 S2 24.9 7.4 113 117 S3 17.6 5.3 91 123 S4 22.0 6.6 84 124 S5 18.7 5.6 117 128 Average 20.8 6.2 101 123 Table 13, shown below, illustrates the deflection at 50% load for the C8x4 pile 700 of the specimens in Figure 20. Table 13 Pile 700 C8*4 Deviation at 50% load S1 0.118 S2 0.160 S3 0.186 S4 0.150 S5 0.170 Average 0.167 Referring now to Figure 22, a UHSW steel pile 800 is illustrated which is a C channel comprising a reinforcement 810, a first boss 820, and a second boss 830, and is a variation of the corrugated C channel pile, or pile. NCW, and the C channel pile 700 of Figure 20. The cross section of the steel pile 800 of Figure 22 is significantly the same as the cross section of the steel pile 700 of Figure 20 with the exception of the addition of the second returns 829B and 839B to pile 800 of Figure 22. Otherwise, similar to pile 700 of Figure 20, pile 800 has a reinforcement 810 that extends a height Hsoo from the steel pile 800 and transitions to a curved transition 840 within the first projection 820 at a first end 811. The brace 810 also transitions to a curved transition 850 within the second projection 830 at a second end 812. Each curved transition 840, 850 has a radius Rs4o, Rsso, respectively. Each curved transition 840, 850 extends from a first projection 820 or second projection 830 along the arc formed by radii Rsw, Rsso, respectively. The arc of the curved transition 840, 850 of Figure 22 extends 90 degrees. In Figure 22, reinforcement 810 comprises one or more discontinuities that can be characterized as corrugations that are arcs having a radius. Specifically, the first projection 820 comprises a first arc 814 formed by a radius Rsm and a second arc 816 formed by a radius Rsie. In the example of Figure 22, the first arc 814 and the second arc 816 are spaced uniformly along of the width Wsoo of the steel pile. The radius Reu,sie extending inwardly from an outer surface 815 of the reinforcement 810. The first projection 820 may also comprise one or more discontinuities that may be characterized as corrugations. In the example of Figure 22, the first boss 820 comprises a boss corrugation 822 formed centrally along the width Wsoo of the steel pile. The boss corrugation 822 is an arc formed by a radius Rb22 that extends inwardly from between a first outer surface 824 and a second outer surface 826 of the boss 820. Opposite the reinforcement 810, a first flange 828 extends from the first projection 820 to a curved transition 860. The first shoulder extends in a direction of the height Hsoo of steel pile and is parallel to the inner surface 816 and the outer surface 815 of the reinforcement 810. The first shoulder 828 may further comprise a transition curved 880 within a first return 829A. The first return 829A extends inwardly from the first flange 828 toward the gusset 810. The first return 829A is parallel to the first outer surface 824 and the second outer surface 826 of the boss 820. A second return 839B may also be provided. Like the second return 629B of the pile 600 of Figure 18, the second return 829B may return in one direction of the reinforcement 820. More specifically, the second return 829B returns at an oblique angle to the first return 829A and towards the second projection 820 It is noted herein that the second return 829B may return in the opposite direction (e.g., toward the opposite projection). It is also noted herein that the second return 829B may return at an angle of 90 degrees relative to the first return 829A. A pile that has a second return can be described more generally as having a triple edge. Like the first projection 820, the second projection 830 may also comprise one or more discontinuities that may be characterized as corrugations. In the example of Figure 22, the second boss 830 comprises a boss corrugation 832 formed centrally along the width Wsoo of steel pile. The projection corrugation 832 is an arc formed by a radius Rs32 that ΜΛ / t / ZUZZ / U4Z I OU extends inwardly from between the first outer surface 834 and a second outer surface 836 of the projection 830. Opposite the reinforcement 810, a second flange 838 extends from the second projection 830 to a transition curved 870. The second flange extends in a direction of the steel pile height Hsoo and is parallel to the inner surface 816 and the outer surface 815 of the reinforcement 810. The second flange 828 may further comprise a curved transition 890 within a first return 839A. The first return 839A extends inwardly from the flange 828 toward the gusset 810. The first return 839A is parallel to the first outer surface 834 and the second outer surface 836 of the second projection 830. A second return 839B may also be provided. Like the second return 639B of the pile 600 of Figure 18, the second return 839B may return in one direction of the reinforcement 830. More specifically, the second return 839B returns at an oblique angle to the first return 839A and towards the second projection 830 . In the example in Figure 22, the thickness T of the steel sheet that forms the steel pile is 1.575 mm (0.062 inches (“)). In some examples, the thickness of the steel sheet forming the steel pile 800 may be 2 mm or less. In other examples, the thickness of the steel sheet forming the steel pile 800 may be 2.5 mm or less. The first projection 820 and / or the second projection 830 of the UHSW steel pile 800 of Figure 22 may additionally comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. Additionally or alternatively, one or more through holes and / or one or more slots may be provided in the gusset 810. In the example of the UHSW 800 steel pile in Figure 22, the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to 1.6 mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The C channel profile in Figure 22 is produced from the width of the steel sheet and therefore has a total material length in cross section of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third the width of the steel sheet. In the example in Figure 22, the height Hsoo of the steel pile is greater than the width Wsoo of the steel pile. In the example of Figure 22, the steel pile 800 is symmetrical about an axis that bisects the height Hsoo of the steel pile 800. A typical UHSW steel pile of Figure 22 may be, for example, a C6x4, C8x4 , C8x4.5, C8x5, C8x4.5, C8x5, C8x6, C10x8, C12x8, C12x10, C14x10, C14x12 (in inches), or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 1035.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). To illustrate the flexural strength, the multiple piles 800 of Figure 22 were subjected to the same flexural test as described above, in relation to Figures 13, 18 and 20. In ΜΛ / t / ZUZZ / U4Z I OU In a first bending test, the tested pile 800 of Figure 24 has a height Hsoo of 20.3 cm (8 inches), a width Wsoo of 12.7 cm (5 inches), and a thickness T of 0.062 inch (“) (0.1575 mm) material and is called C8x5. Figure 23 illustrates a load deflection curve for the C8x5 pile 800 of Figure 22 with results derived from tests designated S1, S2, S3, S4, and S5. The sensors were placed on the booster for tests S1-S5. No local buckling was observed until failure. The slope of the curves in each of Figures 23 corresponds to a moment of inertia of 11.8 in4 to 13.2 in4 for a steel elastic modulus (E) of 26,000 ksi - 290,000 ksi (178 GPa - 200 GPa), respectively. Table 14, shown below, illustrates the maximum load and the load at the onset of nonlinearity for the specimens corresponding to the C8x5 pile 800 in Figure 22. Table 14 ΜΛ / t / ZUZZ / U4Z I OU Pile 800 C8*5 Load at the beginning of nonlinearity (Ibs) Deviation at the beginning of nonlinearity (in.) Maximum load (Ibs) Deviation at maximum load (in.) S1 13552 0.374 13552 0.374 S2 13443 0.351 14624 0.548 S3 10200 0.322 11876 0.52 S4 11283 0.232 13642 0.42 S5 13511 0.243 13840 0.284 Average 12398 0.304 13507 0.429 Table 15, shown below, illustrates the elastic stiffness observed during the test for the specimens corresponding to the C8x5 pile 800 in Figure 22. Table 15 Pile 800 C8*5 Stiffness (k / in) Calculated I (in4) Moment at onset of nonlinearity (kip*in) Moment at maximum load (kip*in) S1 61.0 18.3 244 244 S2 74.7 22.3 242 263 S3 46.8 14.0 184 214 S4 46.6 13.9 203 246 S5 75.9 22.7 243 249 Average 61 18.2 218 243 Table 16, shown below, illustrates the deflection at 50% load for the specimens corresponding to the C8x5 pile in Figure 22. Table 16 Pile 800 C8*5 Deviation at 50% load S1 0.111 S2 0.090 S3 0.109 S4 0.121 S5 0.089 Average 0.104 In a second bending test, the tested pile 800 of Figure 22 has a height Hsoo of 20.3 cm (8 inches), a width Wsoo of 11.4 cm (4.5 inches), and a material thickness T of 0.062 inches (“) (0.1575 mm) and is called C8x45. Figure 24 illustrates a load deflection curve for the C8x4.5 pile 800 of Figure 22 with results derived from tests designated S1, S2, S3, and S4. The sensors were placed on the booster for tests S1-S4. No local buckling was observed until failure. Table 17, shown below, illustrates the maximum load and the load at the onset of nonlinearity for the specimens corresponding to the C8x4.5 pile 800 in Figure 22. Table 17 Pile 800 C8*4.5 Load at the beginning of nonlinearity (Ibs) Deviation at the beginning of nonlinearity (in.) Maximum load (Ibs) Deviation at maximum load (in.) S1 8112 0.294 10183 0.589 S2 9405 0.226 9852 0.3 S3 10000 0.422 10723 0.61 S4 9822 0.123 15459 0.456 Average 9703 0.324 11554 0.489 Table 18, shown below, illustrates the elastic stiffness observed during the test of the specimens corresponding to the C8x4.5 pile 800 in Figure 22. Table 18 Pile 800 C8*4.5 Stiffness (k / in) Calculated I (in4) Moment at the beginning of nonlinearity (kip*in) Moment at maximum load (kip*in) S1 44.1 13.2 146 183 S2 45.7 13.7 169 177 S3 32.9 9.8 180 193 S4 54.6 16.3 177 278 Average 44 13.2 168 208 M A / t / ZUZZ / U4Z I OU Table 19, shown below, illustrates the deflection at 50% load for the specimens corresponding to the C8x4.5 pile 800 in Figure 22. Table 19 Pile 800 C8*4.5 Deviation at 50% load S1 0.092 S2 0.103 S3 0.152 S4 0.09 Average 0.109 As illustrated by the examples above, flexural strength is significantly impacted by shape details for a steel pile made from a thin strip of cast steel. Specifically, the V-shaped transition 613 of the pile 600 of Figure 18 significantly increases the flexural strength compared to the corrugation 313 of the pile 300 of Figure 13. In addition, multiple corrugated arches 714, 716 of the pile 700 of the Figure 20 also increased the flexural strength compared to corrugation 313 of pile 300 of Figure 13. Finally, adding second returns, such as second returns 838B, 839B of pile 800 of Figure 22, increased the flexural strength. bending compared to a comparable pile 700 of Figure 20. Therefore, it has been determined that these characteristics as described herein further increase the capacities of a steel pile made from a UHSW steel pile in the present document. The above flexural tests, in addition to the property characteristics, illustrate steel piles, and corresponding shapes, that produce a combined toughness and stiffness that can experience the abuse of being driven into the ground while simultaneously maintaining a thickness less than or equal to 2.5 mm, less than or equal to 2.0 mm, or even less than or equal to 1.6 mm. Such a lower thickness also provides a steel pile that is easier to drive into the ground with significantly lower resistance than piles made from much thicker material. In other words, the present UHSW steel pile, and the shapes thereof, provide a product that not only exhibits hardness but also exhibits stiffness at a lower material thickness. On the contrary, prior art piles exhibit greater fragility as hardness increases. This dynamic is best illustrated by the comparative examples in Figures 25 to 26. Figure 25 is a reproduction of a photographic image of a UHSW 300 steel pile of the present description that has been driven into bedrock. The steel pile 300 of Figure 25 has the cross section of the steel pile 300 of Figure 13. Instead, Figure 26 is a reproduction of a photographic image of a steel pile 301 produced from a boss beam wide grade 50 carried to the same bedrock. As illustrated by the reproductions, the UHSW steel pile did not undergo any deformation at a top of the pile, where the force was applied to drive the pile into the soil. In contrast, the grade 50 wide boss beam had significant deformation or damage at the top of the pile, where the force was applied to drive the pile into the ground. This illustrates deficiencies found in prior art piles that are not shown by the UHSW steel pile described herein having a smaller thickness. In order to further illustrate the characteristics of the UHSW steel pile of the present description, the free end point load and free end deflection in the allowable point load of a UHSW steel pile (C8x5 as shown) are illustrated. indicated above). Furthermore, these properties for the UHSW steel pile are comparatively illustrated with prior art wide boss beam piles (Grade 50 W6x7 and Grade 50 W6.9) in Figures 27 to 28, respectively. The graph in Figure 27 illustrates the allowable point load at the free end of a fixed cantilever for each pile. The graph in Figure 28 illustrates the free end deflection at the indicated allowable point load for each pile. These data represent the impact of a potential wind load, or force, applied to a free end of a steel pile extending from the ground. Figures 27 to 28 illustrate, in addition to the properties indicated above, the UHSW steel pile of the present description comparatively meets, and even exceeds, the performance of prior art piles with a lower material thickness. The properties of Figures 27 to 28 are reproduced below in Table 20 and Table 21. Additionally, Tables 20 and 21 illustrate the same respective properties for additional prior art wide boss beams and additional UHSW steel piles , as identified throughout these descriptions. ΜΛ / t / ZUZZ / U4Z I OU Table 20 Allowable Point Load Span Length W6x9 W6x8.5 W6x7 W8x10 NCW- 1000 C8x5 C8x4 M8x6 (Feet) (k) (k) (k) (k) (k) (k) (k) (k) 4 3.9 3.5 2.7 5.5 1.7 3,469 3.5 4.1 5 3.1 2.8 2.1 4.4 1.3 2,775 2.8 3.3 6 2.6 2.3 1.8 3.6 0.8 2,282 2.3 2.8 7 2.2 2.0 1.5 3.1 0.5 1,811 1.8 2.4 8 1.9 1.7 1.3 2.7 0.3 1,431 1.4 2.0 Table 21 Deviation in allowable point load Span length W6x9 W6x8.5 W6x7 W8x10 C8x5 (Feet) (in) (in) (in) (in) (in) 4 0.301 0.298 0.283 0.226 0.305 5 0.471 0.465 0.442 0.353 0 .476 6 0.678 0.669 0.636 0.508 0.674 7 0.922 0.911 0.865 0.691 0.834 8 1.205 1.190 1.130 0.903 0.983 As illustrated by the many examples above, the various characteristics of steel pile shapes provide improved properties. It will be noted herein that the respective characteristics of each form of steel pile are interchangeable and / or combinable between each of the steel pile examples herein. Specifically, the bending tests above illustrate several characteristics that increase the strength of the steel pile when subjected to bending tests. Examples of features to increase the flexural strength of the steel pile were determined to include the V-shaped transition found in either of the reinforcement and / or the projections and / or the second return. It has also been determined that the flexural strength attributed to each of these characteristics must be additionally balanced across the cross section of the steel pile, otherwise the steel pile of the present disclosure may bend, deform, or fail. due to localized bearing failure (as illustrated by the above examples where a true local buckling or other buckling failure did not occur or was reached before reaching a localized bearing failure) without reaching its full potential. Accordingly, additional pile examples 900 and 1000 are provided below to illustrate the many additional variations to steel pile forms that can be made by exchanging and / or combining features across the many pile forms. described previously. Figure 29 illustrates a UHSW steel pile 900 that is a variation of the channel M of Figure 18. The steel sheet 900 of Figure 29 comprises a reinforcement 910, a first projection 920, and a second projection 930. The reinforcement 910 of the steel pile 900 of Figure 29 extends to a height H900 of the steel pile 900 and transitions to a curved transition 940 at the first projection 920 at a first end 911. The reinforcement 910 also transitions to a transition curved 950 within the second projection 930 at a second end 912. Each curved transition 940, 950 has a radius R940, R950, respectively. Each curved transition 940, 950 extends from a respective first projection 920 or second projection 930 along the arc formed by radii R940, R550, respectively. The arc of the curved transition 940, 950 of Figure 33 extends at an angle of 90 degrees. In Figure 29, the reinforcement 910 comprises a discontinuity that is a V-shaped transition 913. The V-shaped transition 913 extends in the same direction as each projection 920, 930 relative to the reinforcement 910. The of V 913 is placed centrally in relation to the height H900 of the steel pile. The apex 916 of the V-shaped transition 913 moves from an outer surface 915 of the reinforcement 910, in the same direction as the projections extend the width of the steel pile W900. The opposite sides 917, 918 of the V-shaped transition are at oblique angles relative to the gusset 910. In one example, the opposite sides 917, 918 are at a right angle to each other. Still referring to Figure 29, the first projection 920 and the second projection 930 may also comprise one or more discontinuities. Unlike the example of Figure 18, where the projection discontinuities are V-shaped transitions, the discontinuities of pile 900 of Figure 29 can be characterized as corrugations that are arcs. In the example of Figure 29, the first boss 920 comprises a boss corrugation 922 formed centrally along the width W900 of steel pile. The boss corrugation 922 is an arc formed by a radius R922 that extends inwardly from between a first outer surface 924 and a second outer surface 926 of the boss 920. Opposite the reinforcement 910, a first flange 928 extends from the first projection 920 in a curved transition 960. The first shoulder extends in a direction of the height H900 of steel pile and is parallel to the inner surface 916 and the outer surface 915 of the reinforcement 910. The first shoulder 928 may further comprise a transition curved 980 in a first return 929A. The first return 929A extends inwardly from the first flange 928 toward the gusset 910. The first return 929A is parallel to the first outer surface 924 and the second outer surface 926 of the projection 920. A second return 939B may also be provided. The second return 929B may return in one direction of the gusset 920. More specifically, the second return 929B returns at an oblique angle to the first return 929A and towards the second projection 920. It is noted herein that the second return 929B may return in the opposite direction (for example, towards the ΜΛ / t / ZUZZ / U4Z I OU opposite salient). It is also noted herein that the second return 929B may return at an angle of 90 degrees relative to the first return 929A. A pile that has a second return can be described more generally as having a triple edge. Like the first projection 920, the second projection 930 may also comprise one or more discontinuities that may be characterized as corrugations. In the example of Figure 29, the second projection 930 comprises a projection corrugation 932 formed centrally along the width W900 of the steel pile. The boss corrugation 932 is an arc formed by a radius R932 extending inwardly from between the first outer surface 934 and a second outer surface 936 of the boss 930. Opposite the gusset 910, a second flange 938 extends from the second projection 930 in a curved transition 970. The second flange extends in a direction of the height H900 of the steel pile and is parallel to the inner surface 916 and the outer surface 915 of the reinforcement 910. The second flange 928 may further comprise a transition curved 990 within a first return 939A. The first return 939A extends inwardly from the flange 928 toward the gusset 910. The first return 939A is parallel to the first outer surface 934 and the second outer surface 936 of the second projection 930. A second return 939B may also be provided. The second return 939B may return in one direction from the gusset 930. More specifically, the second return 939B returns at an oblique angle to the first return 939A and towards the second projection 930. In the example of Figure 29, the thickness T of the steel sheet forming the steel pile 900 is 1.575 mm (0.062 inches (")). In some examples, the thickness of the steel sheet forming the steel pile 900 may be 2 mm or less. In other examples, the thickness of the steel sheet forming the steel pile 900 may be 2.5 mm or less. The first projection 920 and / or the second projection 930 of the UHSW steel pile 900 of Figure 29 may additionally comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. One or more through holes and / or one or more slots may be provided, additionally or alternatively, in the network 910. In the example of the UHSW 900 steel pile in Figure 29 the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to to 1.6mm. The constant thickness T is maintained throughout each of the characteristics described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The steel pile profile 900 in Figure 29 is produced from the width of the steel sheet and therefore has a total cross-sectional material length of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third of the width of the steel sheet. In the transition and V-shaped corrugations, the thickness T of the material is maintained in each layer and transition. In the example in Figure 29, the height H700 of the steel pile is greater than the width W700 of the steel pile. In the example of Figure 29, the steel pile 900 is symmetrical about an axis that bisects the height H900 of the steel pile 900. A typical UHSW steel pile of Figure 29 may be, for example, a 6x4, 8x4 .5, 8x5, 8x6, 10x8, 12x8 12x10, 14x10, ΜΛ / t / ZUZZ / U4Z I OU 14x12 (in inches), or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ) In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the projections, or width, may be in the range of 2.5-25 cm (1-10 inches). Referring now to Figure 30, a UHSW steel pile 1000 comprises a reinforcement 1010, a first projection 1020, and a second projection 1030 and, more specifically, is a variation of the corrugated channel M of Figure 18. Like the steel pile of Figure 18, the reinforcement 1010 of the steel pile 1000 of Figure 30 extends a height H1000 of the steel pile 1000 and transitions to a curved transition 1040 within the first projection 1020 at a first end 1011 The gusset 1010 also transitions to a curved transition 1050 within the second projection 1030 at a second end 1012. Each curved transition 1040, 1050 has a radius Rw4o, Rwso, respectively. Each curved transition 1040, 1050 extends from a respective first projection 1020 or second projection 1030 along the arc formed by radii Rw4o, Rwso, respectively. The arc of the curved transition 1040, 1050 of Figure 30 extends 90 degrees. In Figure 30, the reinforcement 1010 comprises a discontinuity that is a V-shaped transition 1013. The V-shaped transition 1013 extends in the same direction as each projection 1020, 1030 relative to the reinforcement 1010. The of V 1013 is placed centrally in relation to the height of the steel pile. The apex 1016 of the V-shaped transition 1013 moves from an outer surface 1015 of the reinforcement 1010, in the same direction as the projections extend the width of steel pile Wwoo. The opposite sides 1017, 1018 of the V-shaped transition are at oblique angles relative to the gusset 1010. In one example, the opposite sides 1017, 1018 are at a right angle to each other. Still referring to Figure 30, the first projection 1020 may also comprise one or more discontinuities in which the discontinuities are V-shaped transitions. In the example of Figure 30, the first projection 1020 comprises a V-shaped transition 1022 formed centrally along the width Wwoo of the steel pile. In some examples, corrugations, arches and / or V-shaped transitions may be interchanged and / or combined on or between the bosses and reinforcements of a single pile. In Figure 30, the V-shaped transition 1022 extends inwardly from a first outer surface 1024 and a second outer surface 1026 of the projection 1020. Opposite the reinforcement 1010, a first flange 1028 extends from the first projection 1020 in a curved transition 1060. The first flange extends in a direction of the height Hwoo of the steel pile and is parallel to the outer surface 1015 of the reinforcement 1010. The first flange 1028 may further comprise a curved transition 1080 at a first return 1029A. The first return 1029A extends inwardly from the first flange 1028 toward the gusset 1010. The first return 1029A is parallel to the first outer surface 1024 and the second outer surface 1026 of the boss 1020. A second return 1039B may also be provided. The second return 1029B may return in one direction of the gusset 1020. More specifically, the second return 1029B returns at an oblique angle to the first return 1029A and towards the second projection 1020. It is noted herein that the second return 1029B may return in the opposite direction (for example, towards the opposite ledge). Also ΜΛ / t / ZUZZ / U4Z I OU It is noted herein that the second return 1029B may return at an angle of 90 degrees relative to the first return 1029A. A pile that has a second return can be described more generally as having a triple edge. Like the first projection 1020, the second projection 1030 may also comprise one or more discontinuities where the discontinuities are V-shaped transitions. In the example of Figure 30, the second projection 1030 comprises a V-shaped transition 1032 formed centrally along the width Wwoo of the steel pile. In some examples, corrugations, arches and / or V-shaped transitions may be interchanged and / or combined on or between the bosses and reinforcements of a single pile. In Figure 30, the V-shaped transition 1032 extends inwardly from a first outer surface 1034 and a second outer surface 1036 of the projection 1030. Opposite the reinforcement 1010, a first flange 1038 extends from the second projection 1030 in a curved transition 1070. The first shoulder extends in a direction of the height Hwoo of the steel pile 1070 and is parallel to the outer surface 1015 of the reinforcement 1010. The first shoulder 1038 may further comprise a curved transition 1090 within a first shoulder 1039A. The first return 1039A extends inwardly from the flange 1028 toward the gusset 1010. The first return 1039A is parallel to the first outer surface 1034 and the second outer surface 1036 of the second projection 1030. A second return 1039B may also be provided. The second return 1039B may return in a direction of the gusset 1030. More specifically, the second return 1039B returns at an oblique angle to the first return 1039Ay towards the second projection 1030. In the example in Figure 30, the thickness T of the steel sheet that forms the steel pile is 1.575 mm (0.062 inches (“)). In some examples, the thickness of the steel sheet forming the steel pile 1000 may be 2 mm or less. In other examples, the thickness of the steel sheet forming the steel pile 1000 may be 2.5 mm or less. The first projection 1020 and / or the second projection 1030 of the UHSW steel pile 1000 of Figure 30 may additionally comprise one or more through holes and / or one or more slots. Through holes and slots may be provided to attach elements to the steel pile such as, for example, a solar installation, road barriers or the like. Additionally or alternatively, one or more through holes and / or one or more slots may be provided in the gusset 1010. In the example of the UHSW 1000 steel pile in Figure 30, the UHSW steel pile comprises a constant thickness T. The constant thickness may be less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to 1.6 mm. The constant thickness T is maintained across each of the features as described above. More specifically, constant thickness is a product formed by cold rolling UHSW steel pile from a steel sheet. In an example, the width of the steel sheet is 50”. The pile profile 1000 of Figure 30 is produced from the width of the steel sheet and therefore has a total cross-sectional material length of 50” or less. More specifically, the total length of the material in cross section may be one-half or one-third of the width of the steel sheet. In V-shaped transitions, the thickness T of the material is maintained in each layer and transition. In the example in Figure 30, the height Hiooo of the steel pile is greater than the width Wwoo of the steel pile. In the example in Figure 30, the steel pile ΜΛ / t / ZUZZ / U4Z I OU 1000 is symmetrical about an axis bisecting the height H1000 of the steel pile 1000. A typical UHSW steel pile in Figure 30 may be, for example, a 6x4, 8x4.5, 8x5, 8x6, 10x8, 12x8, 12x10, 14x10, 14x12 (in inches), or similar. In the examples, the gusset, or height, may be in a range of 15.2-30 cm (6-12 inches) and the overhangs, or width, may be in a range of 5-20 cm (2-8 inches). ). In other examples, the gusset, or height, may be in the range of 10-35.5 cm (4-14 inches) and the overhangs, or width, may be in the range of 2.5-25 cm (1-10 inches). ). As described with respect to each of the shapes above an arch may comprise one or more plane sections or plane parts in a transition. For example, the reinforcing corrugation 313 of Figure 13 is a plane placed between several true arches where the corrugation 313 of Figure 13 transitions from the reinforcement 310. As used herein, the term is understood to be Arc may include one or more flat parts as you transition. The flat parts can separate two 45° arcs separated by a plane to form a 90° arc. Alternatively, each of the arcs as described herein may be a true arc. A true arc is an arc that does not include a plane. In other words, in the present description an arc may be relied upon to define a curved transition which may be a combination of arcs and flat parts and a true arc defines curved transitions which are curvatures, alone. Each of the above-mentioned arcs may alternatively be a true arc. The flat parts of an arc, or transition, are often relied upon as a practical cold-roll formed component where it is necessary to include a plane in an arc to complete or to facilitate the cold-roll forming process. These flat parts additionally provide stiffening characteristics to the discontinuities. Typically, a plane 1 x the thickness T (e.g., 1 times the thickness, or equal to the thickness) of the material in each of the above examples may be provided at each arc transition (e.g., arch entrance, at every 45° of the arc, the exit of the arc, etc.). However, in some cases the planar portions, themselves, may conform to the discontinuity further defined herein. Specifically, and as noted above, the reinforcing corrugation 313 of Figure 13 is simply a plane in excess of 1x the thickness T of the material between multiple arches. Additionally, the V-shaped discontinuity also comprises flat portions such as the opposite sides 617, 618 of the V-shaped discontinuity of Figure 18. Additionally, an arc may be provided between the flat portions that are the opposite sides 617, 618 of the V-shaped discontinuity. Therefore, it can be said that each discontinuity (e.g. arc, V-shaped transition, curved transition, etc.) can comprise one or more planar parts that are at least 1x the thickness T of the material except when based on a true arch herein. Therefore, in some examples a discontinuity of a reinforcement and / or projection may be a combination of a true arc, a plane, a true arc, a plane and so on where the plane is at least 1x the thickness. In some examples, the plane may be greater than 1 x (e.g., at least 2x, at least 3x, at least 4x, at least 5x, etc.) the thickness, thus providing additional shaping to the discontinuity between true arcs. of the transition. In other examples, a discontinuity of a reinforcement and / or a projection may be a true arch, alone. In still other examples, a discontinuity of a buttress and / or boss may be a combination of a true arch and an arch having flat portions. The UHW steel piles of the present disclosure also provide improvements for packaging and shipping. Figure 35 illustrates a nesting configuration for a channel shape of an example of the UHSW steel pile of the present description. The way this specific example is based is the way it is described and illustrated in relation to Figure 29 of the present description. It is noted herein that additional forms described herein may also be based on such a nesting configuration. The nesting configuration of Figure 31 includes three piles 1110, 1120 and 1130 placed in an overlapping and interlocking configuration with each other. The first pile 1110 is placed with reinforcement in a vertical configuration with the second pile 1120 placed with reinforcement in an inverted configuration, while a third pile 1130 is placed with reinforcement in a vertical configuration. One projection of the first pile overlaps one projection of the second pile 1120, while one projection of the third pile 1130 overlaps the other projection of the second pile 1120 in the nesting configuration. Additional piles can be added to the nesting configuration for transportation and multiple nesting configurations can be additionally stacked. Stacked nesting configurations can be provided on pallets for additional mobility. The ability to provide a nesting configuration in combination with the lower material thickness provides greater loading efficiency by reducing weight and space requirements for transportation. Specifically, up to twice the number of steel piles of the present disclosure may be provided per transport vehicle compared to conventional piles. Furthermore, because the nesting configuration has an interlocking arrangement between the piles, the nesting configuration increases the stability of the load being carried. In summary, some examples of ultra-high weathering steel pile comprise a cast material having a thickness less than or equal to 2.5 mm, less than or equal to 2.0 mm, or less than or equal to 1.6 mm. Cast stock is a thin sheet of cast steel formed by cold rolling within a steel pile having reinforcement and one or more bosses with a corrosion rating of 6.0 or greater. The ultra-high weathering steel pile may further comprise a material yield strength of between 700 and 1600 MPa, a material tensile strength of between 1000 and 2100 MPa, and a material elongation of between 1 % and 10%. The material composition of the ultra-high weathering steel pile may include an amount of nickel sufficient to displace a peritectic point away from the carbon region and / or increase a transition temperature of the peritectic point to form a strip of carbon alloy steel having a microstructure of at least 75% by volume of martensite or martensite plus bainite. A UHSW steel pile may be a steel pile comprising reinforcement and one or more projections, or in one of the ways described above, formed from a strip of carbon alloy steel having a composition comprising, by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum where the carbon alloy steel strip has a microstructure having at least 75% by volume of martensite or martensite plus bainite, a resistance to creep of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, an elongation of between 1% and 10%, and has a corrosion index of 6.0 or greater. In one example, the steel pile may be formed by cold rolling from a carbon alloy steel strip cast to a casting thickness less than or equal to 2.5 mm. In another example, the steel pile may be formed by cold rolling from a steel sheet less than or equal to 2.0 mm or less than or equal to 1.6 mm. In yet another example, the steel pile may be formed by cold rolling from a steel sheet ranging from 1.4 mm to 1.5 mm or 1.4 mm to 1.5 mm thick. The steel piles may be channels, such as C channels, M channels, box channels, double channels or the like. Steel piles may additionally or alternatively be I-shaped members, angles, structural T-connections, hollow structural sections, double angles, S-shapes, tubes or the like. Furthermore, many of these elements can be connected together, for example welded together, in order to form a single steel pile. It will be noted herein that additional products may be manufactured from lightweight, ultra-high weathering steel sheet. Additionally, it will be noted herein that additional products can be manufactured from an ultra-high strength weathering steel that is not produced by a double roll mill but, instead, an ultra-high strength product can be produced. discharge through other methods. Additional examples of an ultra-high weathering steel are provided below: A lightweight, ultra-high strength steel sheet, comprising: a carbon alloy steel strip cast to a casting thickness less than or equal to 2.5 mm, having a composition comprising: (i) by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less of or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon containing less than 0.01% aluminum, and (i) the remaining iron and impurities resulting from the fusion; wherein in the composition the nickel displaces a peritectic point away from the carbon region and / or increases a transition temperature of the peritectic point to form the carbon alloy steel strip having a microstructure having at least 75% by volume of martensite or martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10% that is free of defects. In an example of the above, ultra-high strength and lightweight steel sheet has a microstructure that has at least 75% by volume of martensite. In another example of the above, ultra-high strength and lightweight steel sheet has a microstructure that has at least 90% by volume of martensite. In yet another example of the above, ultra-high strength and lightweight steel sheet has a microstructure that is at least 95% martensite. In an example of the above, ultra-high strength and lightweight steel sheet comprises less than 5 ppm of boron. In an example of the above, ultra-high strength and lightweight steel sheet comprises between 0.05% and 0.12% niobium. In an example of the above, the martensite in the steel sheet comes from an austenitic grain size greater than 100 pm. In an example of the above, the martensite in the steel sheet comes from an austenitic grain size greater than 150 pm. In an example of the above, steel sheet may be hot rolled to a reduction of between 15% and 50% before being rapidly cooled. In an example of the above, carbon alloy steel sheet is hot rolled to a hot rolling thickness of between 15% and 35% reduction from the cast thickness before being quenched. In an example of the above, sheet steel is a weathering steel that has a corrosion index of 6.0 or greater. A method for manufacturing an ultra-high weathering and lightweight steel sheet, comprising the steps for: (a) prepare a mass of molten steel comprising: (i) by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less of or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, silicon removed with less than 0.01% aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) forming the melt in a casting tank supported on casting surfaces of a pair of cooled casting rolls having a presser between them; (c) rotate the casting rollers in the opposite direction and solidify at a heat flux greater than 10.0 MW / m2 the molten mass in a steel sheet less than 2.5 mm thick supplied downward from the press and cool the sheet in an atmosphere non-oxidizing up to below 1100°C and above the Ar3 temperature at a cooling rate greater than 15°C / s; and (d) rapidly cooling to form a steel sheet with a microstructure having at least 75% by volume of martensite or martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa and an elongation of between 1% and 10% where nickel shifts the peritectic point away from the carbon region and / or increases a transition temperature of the peritectic point to inhibit crack, or defect, formation in a sheet of high strength martensitic steel. In an example of the above, the microstructure has at least 75% by volume of martensite. In another example of the above, the microstructure has at least 90% by volume of martensite. In another example of the invention, the microstructure has at least 95% by volume of martensite. In an example of the above, carbon alloy steel sheet is formed with less than 5 ppm boron. In an example of the above, the carbon alloy steel sheet comprises between 0.05% and 0.12% niobium. In an example of the above, the martensite in the steel sheet comes from an austenitic grain size greater than 100 pm. In an example of the above, the martensite in the steel sheet comes from an austenitic grain size greater than 150 pm. In an example of the above, steel sheet is hot rolled to a hot rolling thickness of between 15% and 50% reduction from the cast thickness before being quenched. In an example of the above, steel sheet is hot rolled to a hot rolling thickness of between 15% and 35% reduction from the cast thickness before being quenched. In an example of the above, high strength steel sheet is free of defects. Also described is a steel pile comprising a reinforcement and one or more projections formed by cold rolling from a carbon alloy steel sheet cast to a casting thickness less than or equal to 2.5 mm having a composition that comprises, by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum where the carbon alloy steel sheet has a microstructure that has at least 75% by volume of martensite or martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, an elongation of between 1% and 10% and is free of defects. In an example of the above, ultra-high strength and lightweight steel sheet has a microstructure that has at least 75% by volume of martensite. In another example of the above, ultra-high strength and lightweight steel sheet has a microstructure that has at least 90% by volume of martensite. In yet another example of the above, ultra-high strength and lightweight steel sheet has a microstructure that is at least 95% martensite. In an example of the above, the carbon alloy steel sheet of the steel pile comprises less than 5 ppm boron. In an example of the above, the carbon alloy steel sheet of the steel pile comprises between 0.05% and 0.12% niobium. In an example of the above, the martensite in the steel pile comes from an austenitic grain size greater than 100 pm. In an example of the above, the martensite in the steel pile comes from an austenitic grain size greater than 150 pm. In an example of the above, steel sheet may be hot rolled to a reduction of between 15% and 50% before being rapidly cooled. In an example of the above, carbon alloy steel sheet is hot rolled to a hot rolling thickness of between 15% and 35% reduction from the cast thickness before being quenched. In an example of the above, carbon alloy steel sheet is a weathering steel that has a corrosion index of 6.0 or greater. High Friction Rolled High Weathering Steel In the following examples, a high friction laminated high weathering steel sheet is described. An example of an ultra-high weathering steel sheet is manufactured by the steps comprising: (a) preparing a mass of molten steel comprising: (i) by weight, between 0.20% and 0.40% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum , between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) solidify at a heat flux greater than 10.0 PM / m2 in a steel sheet less than or equal to 2.5 mm thick and cool the sheet in a non-oxidizing atmosphere to below 1080°C and above the Ara temperature at a cooling rate greater than 15°C / s before rapidly cooling; (c) high-friction rolling the thin strip of cast steel to a hot-rolled thickness of between 15% and 50% reduction from the cast thickness which produces a mainly free, practically free, or free hot-rolled strip of steel of earlier austenitic grain boundary depressions and having a spotty pattern; and (d) rapidly cooling to form a steel sheet with a microstructure having by volume at least 75% martensite or at least 75% martensite plus bainite, a yield strength of between 700 and 1600 MPa, a resistance to tensile of between 1000 and 2100 MPa and an elongation of between 1% and 10%. Here and elsewhere in this description, elongation means total elongation. “Rapid cooling” means cooling at a rate greater than 100°C / s to between 100 and 200°C. Rapidly cooling the present compositions, with an addition of nickel, achieves up to more than 95% of the steel strip in the martensitic phase. In one example, quenching forms a steel sheet with a microstructure having by volume at least 95% martensite or at least 95% martensite plus bainite. The addition of nickel must be sufficient to shift the “peritectic point” away from the carbon region that would otherwise be present in the same composition without the addition of nickel. Specifically, it is considered that the nickel in the composition contributes to the displacement of the peritectic point away from the carbon region and / or increases a transition temperature of the peritectic point of the composition, which appears to inhibit defects and results in a steel sheet of Ultra-high weather resistance that is free of defects. High friction rolling of an ultra-high weathering steel further improves the formability of the ultra-high weathering steel. A measure of formability is established by the ASTM A370 bending testing standard. In embodiments, the ultra-high strength weathering steel of the present disclosure will pass a 3T 180 degree bending test, and will do so consistently. In particular, high-friction rolling generates stains from previous austenitic grain boundary depressions under shear through plastic deformation. These elongated surface structures, characterized as the spot pattern, are desirable for the properties of an ultra-high weathering steel. Specifically, the formability of ultra-high weathering steel is improved by the spot pattern. The steel strip may further comprise by weight more than 0.005% niobium or more than 0.01% or 0.02% niobium. The steel strip may comprise by weight more than 0.05% molybdenum or more than 0.1% or 0.2% molybdenum. The steel strip may be removed silicon with a content of less than 0.008% aluminum or less than 0.006% aluminum. The melt may have a free oxygen content of between 5 to 70 ppm. The steel strip may have a total oxygen content greater than 50 ppm. Inclusions include MnOSiOz commonly with 50% less than 5 pm in size and have the potential to improve the microstructure evolution and therefore the mechanical properties of the strip. The melt can be solidified at a heat flux greater than 10.0 MW / m2 in a steel strip less than 2.5 mm thick, and cooled in a non-oxidizing atmosphere below 1080°C and above an Ara temperature at a higher cooling rate. than 15°C / s. A non-oxidizing atmosphere is an atmosphere commonly of an inert gas such as nitrogen or argon, or a mixture thereof, containing less than about 5% oxygen by weight. In some embodiments, the martensite in the steel strip may come from an austenitic grain size greater than 100 pm. In other embodiments, the martensite in the steel strip may come from an austenitic grain size greater than 150 pm. Rapid solidification at heat fluxes greater than 10 MW / m2 allows the production of an austenitic grain size that is sensitive to controlled cooling after subsequent hot rolling to allow the production of a defect-free strip. As noted above, the steel strip of the present set of examples may comprise a microstructure having martensite or martensite plus bainite. Martensite is formed in carbon steels by rapid cooling or quenching of austenite. Austenite has a particular crystal structure known as face-centered cubic (FCC). If allowed to cool naturally, austenite converts to ferrite and cementite. However, when the austenite is rapidly cooled, or quenched, the face-centered cubic austenite transforms into a highly deformed body-centered tetragonal (BCT) form of ferrite that becomes supersaturated with carbon. Shear deformations that cause large amounts of dislocations, which is a primary strengthening mechanism for steels. The martensitic reaction begins during cooling when the austenite reaches the martensite onset temperature and the original austenite becomes thermodynamically unstable. As the sample is quenched, an increasing percentage of the austenite transforms to martensite until the lowest transformation temperature is reached, at which time the transformation is complete. However, martensitic steels are susceptible to producing the above large austenitic grain boundary depressions observed on the hot-rolled outer surfaces of cooled thin steel strips formed from low-friction condition rolled steel. The stripping or acid etching step amplifies these imperfections causing defects and separations. High friction rolling is now introduced as an alternative to overcome the problems identified for a martensitic steel rolled in a low friction condition. High friction lamination produces a stain contour pattern. Spot contour patterns may be referred to herein generally as spot patterns. Besides, ΜΛ / t / ZUZZ / U4Z I OU alternatively spot contour patterns may be descriptively referred to as flange scale patterns. Just as ultra-high weathering steel is relied upon to produce product shapes and configurations, such as the piles described above, many products can be produced from rolled high-weathering steel sheet. high friction of the type described herein. As mentioned previously, an example of a product that can be produced from a high-friction laminated high-weathering steel sheet includes a steel pile. In one example, a steel pile comprises a reinforcement and one or more bosses formed by cold rolling from carbon alloy steel strip of the varieties described above. The steel pile may further comprise a length in which the reinforcement and said one or more projections extend the entire length. In use, the length of the steel pile is driven into the soil or earth to provide a structural foundation. The steel pile is driven into the soil or earth using a rammer, such as a piston or hammer. The tamper may be a part of and is at least driven by a pile driver. The rammer strikes or impacts the steel pile driving it into the soil or earth. Due to the impact, the above steel piles may buckle or deform under the impact of the rammer. In order to prevent buckling or damage to the above steel piles, the RPM or force of the pile driver is kept below a damage threshold. The present steel pile has illustrated a capacity for an increase in RPM or force applied to the steel pile without buckling or damage, the steel pile, as reflected by the strength properties of the steel pile, comparatively with the previous steel piles. Specifically, as tested, previous steel piles of comparable dimensional characteristics were tested and failed structurally where the steel pile of the present description provides a 25% RPM increase. Furthermore, the previous steel piles were not additionally weathered steel. Therefore, the above steel piles are susceptible to corrosion due to their placement in outdoor conditions, including soil and earth conditions. Again, the present steel pile provides the corrosion rate necessary to withstand these conditions. The present strength properties and corrosion properties present have not been seen before in combination for such a product. In one example, the steel pile may be formed from a strip of cast carbon alloy steel of the present examples in a casting thickness less than or equal to 2.5 mm. In another example, the steel pile may be formed from a steel strip of the present examples less than or equal to 2.0 mm. In another example, the steel pile may be formed from a steel sheet of the present examples that is between 1.4 mm to 1.5 mm or 1.4 mm or 1.5 mm thick. The steel piles may be channels, such as C channels, box channels, double channels or the like. Steel piles may additionally or alternatively be I-shaped members, angles, structural T-connections, hollow structural sections, double angles, S-shapes, tubes or the like. Furthermore, many of these elements can be connected together, for example welded together, to form a single steel pile. It will be noted herein that additional products may be manufactured from a high friction laminated ultra-high weathering steel sheet. High-friction rolled high-strength maraging steel In embodiments of the present description, a high strength martensitic steel sheet is also described. The examples of high strength martensitic steel sheets that follow may additionally comprise weathering characteristics. Therefore, the examples of high strength martensitic steel sheets can also be referred to as ultra-high weathering steel sheet for such properties. Martensitic steels are increasingly used in applications requiring high strength, for example in the automotive industry. Martensitic steel provides the strength needed by the automotive industry, simultaneously decreasing energy consumption and improving fuel economy. Martensite is formed in carbon steels by the rapid cooling or quenching of laaustenite. Austenite has a particular crystal structure known as face-centered cubic (FCC). If allowed to cool naturally, austenite converts to ferrite and cementite. However, when the austenite is rapidly cooled, or quenched, the face-centered cubic austenite transforms into a highly deformed body-centered tetragonal (BCT) form of ferrite that becomes supersaturated with carbon. The resulting shear strains produce large amounts of dislocations, which is a primary strengthening mechanism of steels. The martensitic reaction begins during cooling when the austenite reaches the martensite onset temperature and the original austenite becomes thermodynamically unstable. As the sample is quenched, an increasing percentage of the austenite transforms to martensite until the lowest transformation temperature is reached, at which point the transformation is complete. However, martensitic steels are susceptible to producing the above large austenitic grain boundary depressions observed on the hot-rolled outer surfaces of cooled thin steel strips formed from low-friction condition rolled steel. The stripping or acid etching step amplifies these imperfections, causing defects and separations. High friction rolling is now introduced as an alternative to overcome the problems identified for a low friction state rolled martensitic steel, however high friction rolling has also been observed to produce an undesirable surface finish. In particular, high friction lamination produces a blotchy contour pattern in combination with an uneven surface finish. Spot contour patterns may be referred to herein generally as spot patterns. Additionally, spot contour patterns may alternatively be referred to as flange scale patterns. The uneven surface finish, which has the stain patterns, then becomes susceptible to trapping acid and / or causing excess corrosion, such as when the thin strip of steel undergoes subsequent acid etching, thereby resulting in excessive amounts of perforations. Accordingly, for some steel strips or products, such as a martensitic steel sheet for use in an automotive application, additional surface treatment is warranted to provide a surface on which stain patterns and / or uneven surface surface finishes. To reduce or eliminate stain pattern and / or uneven surface finish, the thin strip ΜΛ / t / ZUZZ / U4Z I OU steel undergoes a surface homogenization process after hot rolling. Examples of a surface homogenization process include abrasive blasting such as, for example, by use of an abrasive wheel, shot blasting, sandblasting, wet abrasive blasting, other pressurized application of an abrasive, or the like. A specific example of a surface homogenization process includes an eco-pickled surface (referred to herein as “EPS” – eco-pickled surface). Other examples of a surface homogenization process include the forced application of an abrasive medium onto the surface of the steel strip to homogenize the surface of the steel strip. It can also rely on a pressurized component for forced application. For example, a fluid can propel an abrasive medium. A fluid, as used herein, includes liquid and air. Additionally, or alternatively, a mechanical device may provide forceful application. The surface homogenization process occurs after the thin strip of molten steel reaches room temperature. In other words, the surface homogenization process does not occur in an in-line process with the hot rolling mill. The surface homogenization process may occur at a location separate from, or offline from, the hot rolling mill and / or double casting rolls. In some examples, the surface homogenization process may occur after winding. As used herein, the surface homogenization process alters the surface to be free of a stain pattern or eliminates the stain pattern. A surface of a thin strip of steel that is free of a stain pattern or where the stain pattern has been removed is a surface that passes a 120-hour corrosion test without any surface pitting corrosion. Test samples that did not undergo a surface homogenization process fractured after 24 hours during a 120-hour corrosion test due to surface corrosion. Figure 6 is an image showing a high friction hot rolled steel strip surface homogenized using EPS. Comparatively, Figure 7 is an image showing a high-friction hot-rolled steel strip surface having a spot pattern that has not undergone a surface homogenization process. As noted previously, the stain pattern, unless removed by the surface homogenization process, can trap acid after acid etching and is therefore susceptible to over-perforation and / or corrosion. In summary and as used herein, a surface that has undergone surface homogenization is a surface that is free of the stain pattern previously formed by a high friction rolling condition. After hot rolling, the thin hot rolled steel strip is cooled. In each of the modalities, the steel strip undergoes the surface homogenization process after cooling. It is noted that cooling can be achieved in any known manner. In certain cases, when the thin steel strip is cooled, the thin steel strip is cooled to a temperature equal to or lower than an initial transformation temperature of the martensite Ms to thereby form the martensite from the previous austenite within the thin strip of steel. One modality of a high-strength martensitic steel sheet is manufactured by the steps that include: (a) preparing a mass of molten steel that comprises: (i) by weight, between 0.20% and 0.40% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less of 0.5% molybdenum, between 0.5% and 1.5% nickel, and removed silicon with a content of less than 0.01% aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) solidify at a heat flux greater than 10.0 MW / m2 in a steel sheet less than or equal to 2.5 mm thick and cool the sheet in a non-oxidizing atmosphere to below 1080°C and above the Ars temperature at a cooling rate greater than 15°C / s before rapidly cooling; (c) high friction rolling the thin strip of cast steel to a hot rolled thickness of between 15% and 50% reduction from the cast thickness which produces a hot rolled strip of steel free of austenitic grain boundary depressions former; (d) rapidly cooling to form a steel sheet with a microstructure having by volume at least 75% martensite or at least 75% martensite plus bainite, a yield strength of between 700 and 1600 MPa, a tensile strength between 1000 and 2100 MPa and an elongation of between 1% and 10%; and a high-friction hot-rolled steel strip homogenization surface I that produces a high-friction hot-rolled steel strip having a pair of opposing high-friction hot-rolled homogenized surfaces free of the spot pattern. Here and elsewhere in this description, elongation means total elongation. “Rapid cooling” means cooling at a rate greater than 100°C / s to between 100 and 200°C. Rapidly cooling the present compositions, with an addition of nickel, achieves up to more than 95% of the steel strip in the martensitic phase. In one example, quenching forms a steel sheet with a microstructure having by volume at least 95% martensite or at least 95% martensite plus bainite. The addition of nickel must be sufficient to shift the “peritectic point” away from the carbon region that would otherwise be present in the same composition without the addition of nickel. Specifically, it is considered that the nickel in the composition contributes to the displacement of the peritectic point away from the carbon region and / or increases a transition temperature of the peritectic point of the composition, which appears to inhibit defects and results in a steel sheet of high martensitic weather resistance that is free of defects. Additional variations of examples of a high-friction rolled high-strength maraging steel are presented below. In some examples, the steel strip may comprise a pair of opposing high friction hot rolled homogenized surfaces substantially free of prior austenitic grain boundary depressions and spot pattern. In yet another example, the steel strip may further comprise a pair of opposing high friction hot rolled homogenized surfaces primarily free of prior austenitic grain boundary depressions and a spot pattern. In each of these examples, the surfaces may have a surface roughness (Ra) that is not greater than 2.5 pm. In some examples, the thin steel strip may be further quenched at a temperature between 150°C and 250°C for 2 to 6 hours. Tempering the steel strip provides improved elongation with minimal loss of strength. For example, a steel strip that has a yield strength of 1250 MPa, tensile strength of 1600 MPa and an elongation of 2% was improved to a yield strength of 1250 MPa, tensile strength of 1525 MPa and a 5% elongation after ΜΛ / t / ZUZZ / U4Z I OU of the tempering as described herein. The steel strip may further comprise by weight more than 0.005% niobium or more than 0.01% or 0.02% niobium. The steel strip may comprise by weight more than 0.05% molybdenum or more than 0.1% or 0.2% molybdenum. The steel strip may be removed silicon with a content of less than 0.008% aluminum or less than 0.006% aluminum. The melt may have a free oxygen content of between 5 to 70 ppm. The steel strip may have a total oxygen content greater than 50 ppm. Inclusions include MnOSÍO2 commonly with 50% less than 5 pm in size and have the potential to improve the microstructure evolution and therefore the mechanical properties of the strip. The melt can be solidified at a heat flux greater than 10.0 MW / m2 in a steel strip less than 2.5 mm thick, and cooled in a non-oxidizing atmosphere below 1080°C and above an Ara temperature at a higher cooling rate. than 15°C / s. A non-oxidizing atmosphere is an atmosphere commonly of an inert gas such as nitrogen or argon, or a mixture thereof, containing less than about 5% oxygen by weight. In some embodiments, the martensite in the steel strip may come from an austenitic grain size greater than 100 pm. In other embodiments, the martensite in the steel strip may come from an austenitic grain size greater than 150 pm. Rapid solidification at heat fluxes greater than 10 MW / m2 allows the production of an austenitic grain size that is sensitive to controlled cooling after subsequent hot rolling to allow the production of a defect-free strip. A high friction rolled steel sheet can be provided for use in hot stamping applications. Generally, steel sheets based on use in hot stamping applications are of stainless steel compositions or require a corrosion-resistant aluminum-silicon coating. In a hot stamping application a corrosion resistant protective layer is desired while simultaneously maintaining high strength properties and favorable surface structural characteristics. The present high friction laminate compositions have achieved the desired properties without relying on stainless steel compositions or otherwise providing an aluminum-silicon corrosion resistant coating. Rather, the present high friction laminate compositions are based on a mixture of nickel, chromium and copper, as illustrated in the various examples above, for improved corrosion resistance. In the hot stamping application, the high friction rolled steel sheet undergoes an austenitizing condition between 900°C and 930°C for a period of between 6 minutes and 10 minutes. In one example, high friction rolled steel sheet undergoes an austenitizing condition at 900sC for a period of 6 minutes. In yet another example, the high friction rolled steel sheet undergoes an austenitizing condition at 900°C for a period of 10 minutes. In yet another example, the high friction rolled steel sheet undergoes an austenitizing condition at 930°C for a period of 6 minutes. In yet another example, the high friction rolled steel sheet undergoes an austenitizing condition at 930°C for a period of 10 minutes. Table 22, shown below, illustrates the properties of a high friction rolled steel sheet that are maintained above a minimum tensile strength of 1500 MPa, a minimum yield strength of 1100 MPa, and a minimum elongation of 3% for a hot stamping application. Table 22 Austenitization condition Tensile strength (MPa) Yield strength (MPa) Elongation (%) 900°C, 6 minutes 1546.98 1155.06 7.3 900°C, 6 minutes 1576.65 1154.37 7.0 900°C, 10 minutes 1591.14 1168.86 6.4 900°C , 10 minutes 1578.03 1152.30 6.6 930°C, 6 minutes 1566.30 1146.09 7.3 930°C, 6 minutes 1566.99 1178.52 6.5 930°C, 10 minutes 1509.03 1109.52 6.6 930° C, 10 minutes 1521.45 1129.53 6.4 ΜΛ / t / ZUZZ / U4Z I OU In these examples, a steel sheet provided for use in a hot stamping application may comprise a composition of any of the examples of the steel sheets described above, but is a steel sheet that may remain unquenched. Specifically, a steel sheet provided for use in a hot stamping application can be manufactured by the steps comprising: (a) preparing a mass of molten steel comprising: (i) by weight, between 0.20% and 0.40% of carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% of molybdenum, between 0.5% and 1.5% of nickel, and removed silicon with a content of less than 0.01% of aluminum, and (i) the remaining iron and impurities resulting from the fusion; (b) solidifying at a heat flux greater than 10.0 PM / m2 in a steel sheet less than or equal to 2.5 mm thick and cooling the sheet in a non-oxidizing atmosphere to below 1080°C and above an Ara temperature at a cooling rate greater than 15°C / s before rapid cooling; (c) high-friction rolling the thin strip of cast steel to a hot-rolled thickness of between 15% and 50% reduction from the cast thickness which produces a hot-rolled strip of hot-rolled steel that is primarily free, practically free, or free of earlier austenitic grain boundary depressions and having a spotty pattern; and (d) cooling to less than 100°C / s to form a steel sheet having a microstructure of primarily bainite. In other words, a steel sheet provided for use in a hot stamping application may be any of the examples of the steel sheets described above with the exception that the steel sheet does not cool rapidly and therefore Therefore, the microstructure that has mainly or significantly martensite or martensite plus bainite is not formed. Rather, the steel sheet provided for use in a hot stamping application is cooled to less than 100°C / s. Hot rolling, including low friction hot rolling and high friction hot rolling Hot rolling and, more specifically, low friction rolling and high friction rolling, as based on the above examples of the present disclosure, are further described below. The concepts described below can be applied to the examples provided above as necessary to achieve the properties of each respective example. Generally, in each of the hot rolling examples, the strip is passed through the hot rolling mill to reduce the casting thickness before the strip is cooled, such as to a temperature at which the austenite in the Steel is transformed into martensite in particular ways. In particular cases, the hot solidified strip (the molten strip) can be passed through the hot rolling mill while having an inlet temperature greater than 1050°C, and in certain cases up to 1150°C. After the strip leaves the hot rolling mill, the strip is cooled such as, in certain exemplary cases, to a temperature at which the austenite in the steel is transformed to martensite by cooling to a temperature equal to or less than the initial transformation temperature of martensite Ms. In certain cases, this temperature is ¿ 600°C, where the initial transformation temperature of martensite Ms depends on the particular composition. Cooling can be achieved by any of the known methods using any known mechanism(s), including those described above. In certain cases, cooling is rapid enough to prevent the onset of observable ferrite, which is also influenced by composition. In such cases, for example, the cooling is configured to reduce the temperature of the strip at a rate of approximately 100°C to 200°C per second. Hot rolling is performed using one or more pairs of opposing operating rolls. Operating rollers are commonly used to reduce the thickness of a substrate, such as a plate or strip. This is achieved by passing the substrate through a space placed between the pair of operating rollers, the space being less than the thickness of the substrate. The space is also called as a grip between rollers. During hot working, a force is applied to the substrate by the operating rollers, thereby applying a rolling force on the substrate to thereby achieve a desired reduction in the thickness of the substrate. In doing so, friction is generated between the substrate and each operating roller as the substrate moves through the gap. This friction is called interroller gripping friction. Traditionally, the desire is to reduce gripping friction during hot rolling of steel plates and strips. By reducing gripping friction (and therefore friction coefficient), rolling load and roller wear are reduced to prolong machine life. Various techniques have been employed to reduce the roll gripping friction and friction coefficient. In certain exemplary cases, the thin steel strip is lubricated to reduce the gripping friction of the roller. Lubrication may take the form of oil, which is applied to the rollers and / or the steel strip, or as an oxidation scale formed along the exterior of the steel strip prior to hot rolling. When using lubrication, hot rolling can occur in a low-friction condition, where the coefficient of friction (μ) for the grip between rolls is less than 0.20. In one example, the coefficient of friction (μ) is determined based on a hot rolling model developed by HATCH for a particular set of operating rolls. The model is shown in Figure 8, providing a reduction in the thickness of the thin steel strip in percentage along the X axis and the specific force “P” in kN / mm along the Y axis. The specific force P is the ΜΛ / t / ZUZZ / U4Z I OU normal (vertical) force applied to the substrate by the operating rollers. The model includes five (5) curves each representing a coefficient of friction and providing a relationship between reduction and operating roller forces. For each friction coefficient, predicted operating roller forces are obtained based on the measured reduction. In operation, during hot rolling, the target friction coefficient is preset by adjusting the lubrication of the operating roll, the target reduction is adjusted by the desired strip thickness required at the exit of the rolling mill to meet an order of specific customer and the actual force of the operating roller will be adjusted to achieve the target reduction. Figure 8 shows the typical forces required to achieve a target reduction for a specific friction coefficient. In certain example cases, the coefficient of friction is equal to or greater than 0.20. In other examples, the friction coefficient is equal to or greater than 0.25, equal to or greater than 0.268, or equal to or greater than 0.27. It is observed that these friction coefficients are sufficient, under certain conditions for austenitic steel (which is the steel alloy used in the examples shown in the figures), where during hot rolling, the steel is austenitic but is formed after cooling martensite that has previous austenite grains and previous austenitic grain boundary depressions present, at least mainly or practically eliminates the previous austenitic grain boundary depressions from the hot-rolled surfaces and to generate elongated surface features formed plastically by shear. As previously indicated, various factors or parameters can be altered to achieve a desired friction coefficient under certain conditions. It is noted that for the friction coefficient values ​​described above, for substrates having a thickness of 5 mm or less before hot rolling the normal force applied to the substrate during hot rolling can be 600 to 2500 tons while the substrate enters the pair of operating rollers and moves, or advances, at a speed of 45 to 75 meters per minute (m / min) where the temperature of the substrate entering the operating rollers is greater than 1050°C, and in certain cases up to 1150°C. For these friction coefficients, the operating rollers have a diameter of 400 to 600 mm. Of course, variations outside each of these parameter ranges may be employed as desired to achieve different coefficients of friction as desired to achieve the hot rolled surface characteristics described herein. In one example, hot rolling is performed under a high friction condition with a friction coefficient of 0.25 at 60 meters per minute (m / min) at a reduction of 22% with an operating roll force of approximately 820 tons. In another example, hot rolling is performed under a high friction condition with a friction coefficient of 0.27 at 60 meters per minute (m / min) at a reduction of 22% with an operating roll force of approximately 900 tons. As based on the examples of the present description, hot rolling of the thin steel strip is performed while the thin steel strip is at a temperature higher than the Ara temperature. The Ara temperature is the temperature at which austenite begins to transform into ferrite during cooling. In other words, the Ara temperature is the transformation point of austenite. Ara's temperature is located a few degrees below the temperature ΜΛ / t / ZUZZ / U4Z I OU Ara. Below the Ara temperature, alpha-ferrite is formed. These temperatures are shown on an exemplary CCT diagram in Figure 9. In Figure 9, Ars 170 represents the upper end-of-stability temperature for ferrite at equilibrium. Ars is the upper limit temperature for the end of stability for ferrite upon cooling. More specifically, the Ara temperature is the temperature at which austenite begins to transform into ferrite during cooling. In other words, the Ara temperature is the transformation point of austenite. Comparatively, Ai 180 represents the lower limit temperature for the end of stability for ferrite in equilibrium. Still referring to Figure 9, the ferrite curve 220 represents the transformation temperature that produces a 1% ferrite microstructure, the pearlite curve 230 represents the transformation temperature that produces a 1% pearlite microstructure, the curve of austenite 250 represents the transformation temperature that produces a 1% austenite microstructure, and the bainite (Bs) 240 curve represents the transformation temperature that produces a 1% bainite microstructure. As previously described in more detail, an initial martensite transformation temperature Ms is represented by the martensite curve 190 where martensite begins to form from the previous austenite within the thin strip of steel. Additionally, Figure 9 illustrates a 50% martensite curve 200 that represents a microstructure having at least 50% martensite. Additionally, Figure 9 illustrates a 90% martensite curve 210 that represents a microstructure having at least 90% martensite. In the exemplary CCT diagram shown in Figure 9, the initial transformation temperature of martensite Ms190 is shown. As it passes through the cooler, the austenite in the strip transforms into martensite. Specifically, in this case, cooling the strip below 600°C causes a transformation of the coarse austenite in which a distribution of fine iron carbides is precipitated within the martensite. Although the invention has been illustrated and described in detail in the previous figures and description, it should be considered as illustrative and not restrictive, it being understood that only illustrative modalities thereof have been shown and described, and that all changes and modifications are They are within the spirit of the invention described by the following claims that are intended to be protected. Additional features of the invention will become apparent to those skilled in the art upon consideration of the description. Modifications may be made without departing from the spirit and scope of the invention.

Claims

1. An ultra-high-strength weathering steel pile characterized in that it comprises: a reinforcement and a pair of opposing projections, each of which has discontinuities formed therein, a thickness of approximately 2.5 mm or less, and a composition comprising, by weight, (i) between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and silicon removed with a content of less than 0.01% aluminum, and (ii) the remaining iron and impurities resulting from melting; The pile has a corrosion index of 6.0 or higher, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%.

2. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the reinforcement discontinuity is a V-shaped transition.

3. The ultra-high weather resistance steel pile according to claim 2, further characterized in that the V-shaped transition is positioned centrally over the reinforcement relative to the pile height and the pile forms a channel M.

4. The ultra-high weather resistance steel pile according to claim 3, further characterized in that the discontinuity of each projection of the pair of opposing projections is a V-shaped transition.

5. The ultra-high weather resistance steel pile according to claim 4, further characterized in that the V-shaped transition of each projection of the pair of opposing projections is positioned centrally over each projection relative to the width of the pile.

6. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the height of the pile extending the reinforcement varies between 10 and 30 cm (4 and 12 inches) and the width of the pile extending each projection of the pair of opposing projections varies between 5 and 20 cm (2 and 8 inches).

7. The ultra-high weather resistance steel pile according to claim 2, further characterized in that the discontinuity of each projection of the pair of opposing projections is a corrugation that is an arch.

8. The ultra-high weather resistance steel pile according to claim 2, further characterized in that the discontinuity of each projection of the pair of opposing projections is a corrugation that is a true arch.

9. The ultra-high weather resistance steel pile according to claim 7, further characterized in that the arch of each projection of the pair of opposing projections is positioned centrally over each projection relative to the width of the pile. ML / t / ZUZZ / U4Z I OU 10. The ultra-high weather resistance steel pile according to claim 7, further characterized in that the arc of each projection of the pair of opposing projections includes one or more flat parts that are at least 1x the thickness.

11. The ultra-high weather resistance steel pile according to claim 2, further characterized in that it additionally comprises a triple edge.

12. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the thicknesses are 2.0 mm or less.

13. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the thicknesses are 1.6 mm or less.

14. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the reinforcement discontinuity is one or more corrugations that are arches.

15. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the reinforcement discontinuity is one or more corrugations that are true arches.

16. The ultra-high weather resistance steel pile according to claim 1, further characterized in that the arches include one or more flat parts that are at least 1x the thickness.

17. The ultra-high weather resistance steel pile according to claim 16, further characterized in that the reinforcement comprises two corrugations that are arches that are uniformly spaced in the reinforcement with respect to the height of the pile.

18. The ultra-high weather resistance steel pile according to claim 16, further characterized in that the discontinuity of each projection is one or more corrugations that are arches.

19. The ultra-high weather resistance steel pile according to claim 18, further characterized in that said one or more corrugations of the projections are centrally located on each projection in relation to the width of the pile.

20. The ultra-high weather resistance steel pile according to claim 19, further characterized in that the height of the pile extending the reinforcement is between 10 and 30 cm (4 and 12 inches) and the width of the pile extending each projection of the pair of opposing projections varies between 5 and 20 cm (2 and 8 inches).

21. The ultra-high weather resistance steel pile according to claim 19, further characterized in that each projection comprises a return flange.

22. The ultra-high weather resistance steel pile according to claim 21, further characterized in that each return flange returns at an oblique angle with respect to both the reinforcement and the corresponding projection.

23. The ultra-high weather resistance steel pile according to claim 22, further characterized in that the height of the pile extending the reinforcement varies between 10 and 30 cm (4 and 12 inches) and the width of the pile extending each projection of the pair of opposing projections ML / t / ZUZZ / U4Z I OU varies between 5 and 20 cm (2 and 8 inches).

24. A solar installation characterized in that it comprises: an ultra-high-strength weathering steel pile comprising: a reinforcement and a pair of opposing projections, each of which has discontinuities formed therein, a thickness of approximately 2.5 mm or less, and a composition comprising: (i) by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, between 0.5% and 1.5% nickel, and silicon removed with a content of less than 0.01% aluminum, and (ii) the remaining iron and impurities resulting from melting; The ultra-high weather resistance steel pile has a corrosion index of 6.0 or greater, an elastic limit of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%; and wherein a partial length of the ultra-high weathering strength steel pile is carried flush with the ground and one or more solar cells are supported above ground level by the ultra-high weathering strength steel pile.

25. An ultra-high weather resistance steel pile characterized in that it comprises: a reinforcement and a pair of opposing projections, each of which has discontinuities formed therein, a thickness of approximately 2.5 mm or less, a corrosion index of 6.0 or greater, a yield strength of between 700 and 1600 MPa, a tensile strength of between 1000 and 2100 MPa, and an elongation of between 1% and 10%.

26. The ultra-high weathering strength steel pile according to claim 25, further characterized in that it has a composition comprising: (i) by weight, between 0.20% and 0.35% carbon, less than 1.0% chromium, between 0.7% and 2.0% manganese, between 0.10% and 0.50% silicon, between 0.1% and 1.0% copper, less than or equal to 0.12% niobium, less than 0.5% molybdenum, silicon removed with an aluminum content of less than 0.01%, and an amount of nickel sufficient to displace a peritectic point away from the carbon region and / or increase a peritectic point transition temperature to form a carbon alloy steel strip having a microstructure of at least 75% by volume martensite or martensite plus bainite, and (ii) the remaining iron and impurities resulting from the melting.

27. A nesting configuration of ultra-high weather resistance steel piles, characterized in that it comprises: a row of steel piles having a first, second, and third steel piles, each of which comprises a reinforcement and a pair of opposing projections, each of which has internally formed discontinuities, wherein one projection of the pair of opposing projections of the first steel pile overlaps and interlocks with one projection of the pair of opposing projections of the second steel pile and one projection of the pair of opposing projections of the third steel pile overlaps and interlocks with another projection of the pair of opposing projections of the second steel pile.

28. The nesting configuration according to claim 27, further characterized in that it additionally comprises a second row of steel piles having a fourth, fifth, and sixth steel piles, each comprising a reinforcement and a pair of opposing projections, each having internally formed discontinuities, wherein the fourth, fifth, and sixth steel piles are stacked on top of the first, second, and third steel piles forming a two-row stack.

29. The nesting configuration according to claim 28, further characterized in that it comprises a stack of at least five rows of steel piles.