Use of a nickel-iron-chromium alloy having high resistance in carburising and sulphidising and chlorinating environments and simultaneously good processability and strength

Abstract

The invention relates to the use of a nickel-iron-chromium alloy having excellent high-temperature corrosion resistance as a semi-finished product in simultaneously carburising, sulphidising and chlorinating environments, said alloy comprising (in wt.%): 35.0 to 38% nickel, 26.0 to 30.0% chromium, > 0.7 to 1.50% silicon, 0.40 to 1.30% aluminium, 0.00 to 1.0% manganese, 0.0001 to 0.05% each of magnesium and / or calcium, 0.015 to 0.12% carbon, 0.001 to 0.150% nitrogen, 0.001 to 0.030% phosphorus, 0.0001 to 0.020% oxygen, a maximum of 0.010% sulphur, less than 1.0% molybdenum, less than 1.0 % cobalt, less than 0.5% copper, less than 1.0% tungsten, the remainder being iron and the usual process-related impurities, it being necessary to satisfy the following equation: Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*AI < 2.5 (1 a), where Ni, Si and AI are the concentration of the elements in question in wt.%.

Description

[0001]Use of a nickel-iron-chromium alloy with high resistance in carburizing, sulfidizing, and chlorinating environments and, at the same time, good workability and strength. The invention relates to the use of a nickel-iron-chromium alloy with good high-temperature corrosion resistance in highly corrosive environments, such as simultaneously carburizing, sulfidizing, and chlorinating environments, and improved workability, in particular weldability. Austenitic nickel-iron-chromium alloys with different nickel, chromium, and iron contents have long been used in furnace construction and in the chemical and petrochemical industries. For this application, good high-temperature corrosion resistance, even in carburizing and sulfidizing environments, and good high-temperature strength are required. In general, it should be noted that the high-temperature corrosion resistance of the alloys listed in Table 1 increases with increasing chromium content.increases. All of these alloys form a chromium oxide layer (Cr2O3) with an underlying, more or less continuous, silicon oxide layer. Small additions of elements with a strong oxygen affinity, such as yttrium or cerium, improve corrosion resistance. The chromium content is slowly consumed over the course of use in the application to build up the protective layer. Therefore, a higher chromium content increases the service life of the material, since a higher content of the element chromium, which forms the protective layer, delays the point at which the chromium content falls below the critical limit and oxides other than Cr2O3 form, such as iron-containing and nickel-containing oxides. A further increase in high-temperature corrosion resistance can be achieved by adding silicon or aluminum. Above a certain minimum content, these elements form a continuous layer beneath the chromium oxide layer and thus reduce the consumption ofChromium. In carburizing environments (CO, H2, CH4, CO2, H2O mixtures), carbon can penetrate the material, leading to the formation of internal carbides. These cause a loss of notched impact toughness. Transformation processes can also occur due to chromium depletion of the matrix. High resistance to carburization is achieved by materials with low carbon solubility and a low carbon diffusion rate. Nickel alloys are therefore generally more resistant to carburization than iron-based alloys, since both carbon diffusion and carbon solubility are lower in nickel than in iron. An increase in the chromium content results in greater carburization resistance through the formation of a protective chromium oxide layer, unless the oxygen partial pressure in the gas is insufficient to form this protective chromium oxide layer. At very low oxygen partial pressures, materials can be used thata layer of silicon oxide or the even more stable aluminum oxide, both of which can form protective oxide layers even at significantly lower oxygen contents. In carburizing, sulfidizing environments with low oxygen partial pressure (CO, H2, H2O, CO2, H2S mixtures), sulfur can penetrate the material, potentially leading to the formation of sulfides. The melting point can also drop to very low values ​​(635°C for the Ni-Ni3S2 eutectic, 988°C for the Fe-FeS eutectic). Nickel-iron-chromium alloys with high nickel content are often more sensitive in sulfidizing environments than nickel-iron-chromium alloys with high iron content. Here, too, a further increase in high-temperature corrosion resistance can be achieved by adding silicon or aluminum. In chlorinating environments with low oxygen partial pressure, volatile metal chlorides with high vapor pressures and / or low melting points can form and thus cause high corrosion ratesproduce. A high content of chromium and / or nickel improves corrosion resistance. DE 41 30 139 C1 describes a heat-resistant, hot-formable austenitic nickel alloy consisting of (in mass %) 0.05 to 0.15% carbon, 2.5 to 3.0% silicon, 0.2 to 0.5% manganese, max. 0.015% phosphorus, max. 0.005% sulfur, 25 to 30% chromium, 20 to 27% iron, 0.05 to 0.15% aluminum, 0.001 to 0.005% calcium, 0.05 to 0.15% rare earths, 0.05 to 0.20% nitrogen, with the remainder nickel and the usual impurities resulting from the melting process. The alloy described in DE 4130139 C1 is known under the designations "NiCr28FeSiCe", Alloy 45TM, Nicrofer 45TM or under the material number 2.4889 and is referred to below as "45TM". Alloy 45TM is very resistant to carburizing and sulfidizing media, which makes it suitable for use in waste incineration plants or coal gasification plants. Figure 1 shows the metallographicallyMeasured corrosion attack depth for various alloys after exposure to a gas containing H2S for 2100 hours in a PRENFLO coal gasification pilot plant in Fürstenhausen as a function of temperature for various alloys. Table 1 shows the composition of the alloys tested according to the state of the art. A high chromium and silicon content significantly reduces the corrosion attack depth. Due to the high silicon content of ≥ 2.5%, a silicon oxide layer can form beneath the protective chromium oxide layer, which results in the material's high corrosion resistance. 45TM, with 26 to 29% chromium and 2.5 to 3% silicon, exhibits the lowest corrosion attack depth at all temperatures, followed by AC66 with 26 to 28% chromium and a maximum of 0.3% silicon. However, alloy 45TM is very difficult to process. This is evident, for example, in cracking during hot forming. 45TM is also prone to cracking during welding.This makes a proper weld (using a filler metal in the composition range of the material to be welded), which would be sensible for corrosion protection reasons, impossible and complicates the practical use of the material. The reason for the increased hot cracking in austenitic FeCrNi weld metals with primary austenite solidification is the formation of low-melting phases due to silicon enrichment at the austenite grain boundaries (eutectic Fe-Fe2Si: 1212°C; eutectic NiSi-Ni3Si2: 964°C and NiSi: 996°C) as well as the expanding solidification range. Alloy AC66 (composition see Table 1), on the other hand, has sufficient weldability and processability, but is not as corrosion-resistant in a coal gasification plant, as Figure 1 shows. The demands on the material increase further when attack by chlorine is added to the carburizing, sulfidizing conditions, as is the case in coal gasification plants.Waste incineration plants, etc. For materials used in carburizing, sulfidizing, and chlorinating environments, especially atmospheres, a compromise must be made regarding composition. High-temperature strength is improved, among other things, by a high carbon content. High contents of solid-solution strengthening elements such as chromium, aluminum, silicon, molybdenum, and tungsten also improve high-temperature strength. US 6,623,869 B1 describes a metallic material containing the following components in mass%: not more than 0.2% carbon, 0.01 – 4% silicon, 0.05 – 2% manganese, not more than 0.04% phosphorus, not more than 0.015% sulfur, 10 – 35% chromium, 30 – 78% nickel, not less than 0.005% aluminum but less than 4.5% aluminum, 0.005 – 0.2% nitrogen, and one or both of 0.015 – 3% copper and 0.015 – 3% cobalt, the remainder being essentially iron. Wherein the value of 40 Si + Ni + 5 Al + 40 N + 10(Cu + Co) not less than 50, where the element symbols represent the alloy content of the respective elements. This metallic material exhibits excellent corrosion resistance in environments where metal dusting may occur and can therefore be used in furnace tubes, piping systems, heat exchanger tubes, etc. in oil refineries or petrochemical plants. It can significantly improve the durability and safety of the equipment. US 3,833,358 A describes an iron-based refractory alloy which offers high resistance to creep, thermal shock, thermal fatigue and intergranular oxidation as well as good weldability, essentially consisting of the following elements (in weight fractions): C 0.05 - 0.20 Ni 30 - 40 Cr 20 - 30 Nb 0.2 - 2 N 0.04 - 0.2 Mn 0.6 - 2 Si 0.6 - 2 Ta 0 - 0.3 Ti 0 - 1 Mo 0 - 0.5 Al 0 - 0.05 Pb 0 - 0.01 Sn 0 - 0.01 Zn 0 - 0.01 Cu 0 - 0.25 and the remainder is essentially iron.Weight proportions of the above elements the following formulas 30 * C% + Ni% + 0.5 * Mn% + 16 * N% = Cr% + 0.5 * (Nb + 1 / 2 Ta)% + 3.5 * Ti% + 1.5 * Si% + Mo% + (11 + / - 2)% A = B + / - 20% with A = 30 * C% B = 2 * Ti% + 6 * (Nb + 1 / 2 Ta)%. US 3,865,581 A describes a heat-resistant alloy with hot formability, containing 0.01 to 0.5% C, 0.01 to 2.0% Si, 0.01 to 3.0% Mn, 22 to 80% Ni, and 10 to 40% Cr as the main components, along with one or both of 0.0005 to 0.20% B and 0.001 to 6.0% Zr, and further one or more of 0.001 to 0.5% Ce, 0.001 to 0.2% Mg, and 0.001 to 1.0% Be, the balance being iron and unavoidable impurities. It is suitable for use in furnace construction (burner tips, protective housings, thermocouple protection tubes, etc.). DE 1024719 A describes a method for adding cerium and / or lanthanum to a nickel-iron alloy. It is a hot-formable alloy characterized by the following composition: 0 to0.5% carbon, 10 to 60% of one or more of the elements chromium, molybdenum and tungsten, the amount of each of these elements not exceeding 30%, 0 to 73% iron, 0.02 to 1.10% cerium or lanthanum or both, the balance 4 to 70% nickel including impurities, provided that the rare earth metal content is balanced with the nickel content as follows: % nickel % cerium or lanthanum or both 4 about 0.02 to 1.10 10 about 0.02 to 1.05 20 about 0.02 to 0.90 30 about 0.02 to 0.75 40 about 0.02 to 0.60 50 about 0.02 to 0.45 60 about 0.02 to 0.30 70 about 0.02 to 0.15 In EP 0812926 A1 describes a nickel-based alloy whose strength increases with use, consisting of 0.06 - 0.14% carbon, 35 - 46% nickel, 22.5 - 26.5% chromium, 0 - 1.5% manganese, 0.5 - 2% silicon, 0.1 - 1% titanium, 0.05 - 2% aluminum, 1 - 3% molybdenum, 0.2 - 1% niobium, 0.1 - 1% tantalum, 0 - 0.3% tungsten, 0 - 0.008% boron, 0 - 0.05% zirconium andthe remainder being iron and incidental impurities. WO 2007 / 124996 A1 describes a reaction vessel for use in the production of hydrogen sulfide by reaction between sulfur and hydrogen, wherein the reaction vessel and, if applicable, connecting lines, fittings, and measuring and control elements are made partially or entirely of a material that is resistant to the reaction mixture and contains aluminum. In particular, the material contains the following components: 0-0.3% C, 0-2.5% Si, 0-2.5% Mn, 0-0.1% P, 0-0.3% S, 15.0-28.0% Cr, 0-1.0% Cu, 0-0.5% Fe, 1.0-5.0% Al, 0-2.5% Co, 0-1.5% Ti, 0-0.4% Y, and up to 70% Ni (% by weight). DE 10 2007 005 605 A1 describes an iron-nickel-chromium-silicon alloy, with (in wt.%) 34 to 42% nickel, 18 to 26% chromium, 1.0 to 2.5% silicon and additions of 0.05 to 1% Al, 0.01 to 1% Mn, 0.01 to 0.26% lanthanum, 0.0005 to 0.05% magnesium, 0.01 to 0.14% carbon, 0.01Up to 0.14% nitrogen, max. 0.01% sulfur, max. 0.005% boron, the remainder iron and the usual process-related impurities. This alloy is used in heating elements. US 5,021,215 A discloses a high-strength, heat-resistant steel with improved formability, which essentially consists of (wt%): C: 0.05 – 0.30%, Si: not more than 3.0%, Mn: not more than 10%, Cr: 15 – 35%, Ni: 15 – 50%, Mg: 0.001 – 0.02%, B: 0.001 – 0.01%, Zr: 0.001 – 0.10%, at least one of Ti: 0.05 – 1.0%, Nb: 0.1 – 2.0%, and Al: 0.05 – 1.0%, Mo: 0 – 3.0%, W: 0 – 6.0%, (Mo + 1 / 2 W = 3.0% or less), balance Fe and incidental impurities, wherein the impurities are oxygen and nitrogen. 50 ppm or less or 200 ppm or less, respectively, and the austenite grain size is limited to No. 4 or coarser. JPS 56163244 A describes the improvement of the hot workability and oxidation resistance of an austenitic steel byAdding a specific amount of C, Si, Mn, Ni, Cr, Al, B, a rare earth element, and Ca to the steel. This is achieved by producing an austenitic steel containing the following composition in wt%: <0.2% C, 1.5–3.5% Si, <2% Mn, 8–35% Ni, 15–30% Cr, <2% Al, 0.0005–0.005% B, 0.005–0.1% of a rare earth element, and 0.0005–0.02% Ca, or an additional 0.0005–0.03% Mg if required. The resulting austenitic steel is refined in an ordinary steelmaking furnace, and this molten steel is formed into a billet, which is then hot-rolled. US 7,118,636 B2 describes a nickel-iron-chromium alloy containing a hardening phase capable of maintaining a fine grain structure during forging and processing of the alloy at high temperatures. The alloy contains a sufficient amount of titanium, zirconium, carbon, and nitrogen to produce fine titanium and zirconium nitride.formed, even though, in the molten state of the alloy, these are close to their solubility limit. When an article is manufactured from such an alloy by thermomechanical processing, a dispersion of fine titanium and zirconium carbonitride precipitates forms during solidification of the melt and remains in the alloy during subsequent processing steps (at elevated temperatures) to prevent austenitic grain growth. The nickel-iron-chromium alloy contains less than 0.05 wt.% niobium, at least 0.05% zirconium, at least 0.05% carbon, at least 0.05% nitrogen, a carbon to nitrogen weight ratio of at least 1 to 2 to less than 1 to 1, sufficient titanium, zirconium and / or aluminum to be free of chromium carbides, and titanium, zirconium, carbon and nitrogen in sufficient quantities to form a uniform dispersion of fine titanium and zirconium carbonitride [(Ti x Zr 1-x ) (Cy N 1-y )] in a sufficientAmount near the solubility limit of the titanium and zirconium carbonitride precipitates in a molten state of the alloy. This nickel-iron-chromium alloy also consists of about 32 wt.% to about 38 wt.% iron, about 22 wt.% to about 28 wt.% chromium, about 0.10 wt.% to about 0.60 wt.% titanium, about 0.05 wt.% to about 0.30 wt.% zirconium, about 0.05 wt.% to about 0.30 wt.% carbon, about 0.05 wt.% to about 0.30 wt.% nitrogen, about 0.05 wt.% to about 0.5 wt.% aluminum, up to 0.99 wt.% molybdenum, up to about 0.01 wt.% boron, up to about 1 wt.% silicon, up to about 1 wt.% manganese, the balance nickel and incidental impurities. JPS 57134544 A describes the improvement of stress corrosion cracking resistance of oil drilling pipes by adding specific amounts of Mo, W, etc. to a high Cr-Ni steel as pipe material. For this purpose, an alloyed steel with a composition of < 0.10% C, < 1.0% Si, < 2.0% Mn, < 0.030% P, < 0.005% S, < 0.5% Al, 22.5 – 30% Cr, 25 – 60% Ni and Mo and / or W is used.which satisfies the equations Cr(%) + 10*Mo(%) + 5*W(%) ≥ 70% 4% ≤ Mo(%) + ½ W(%) < 8%. The steel is used for an oil well pipe used in the highly corrosive, harsh environment of an oil well, a natural gas well, etc. < 1% Cu and / or < 2% Co and / or < 0.10% of one or more of the rare earth elements, < 0.20% Y, < 0.10% Mg, < 0.10% Ca and < 0.5% Ti can be added to the alloy. Oil well pipes with superior stress corrosion cracking resistance in the highly corrosive environment of an oil well containing H2S, CO2 and Cl can be produced. The object underlying this invention is therefore to design the use of a wrought nickel-iron-chromium alloy which a) has good high-temperature corrosion resistance in a highly corrosive environment such as simultaneously carburising, sulphidising and chlorinating environments, comparable to that of alloy 45TM,b) has sufficient processability, in particular weldability, as similar as possible to that of alloy AC66, and c) has sufficient high-temperature strength at 500°C similar to that of alloy AC66. The object underlying this invention is achieved by the use of a nickel-iron-chromium alloy with excellent high-temperature corrosion resistance as a semi-finished product in simultaneously carburizing, sulfidizing and chlorinating environments, comprising (in mass%): 35.0 to 38% nickel, 26.0 to 30.0% chromium, > 0.7 to 1.50% silicon, 0.40 to 1.30% aluminum, 0.00 to 1.0% manganese, 0.0001 to 0.05% each of magnesium and / or calcium, 0.015 to 0.12% carbon, 0.001 to 0.150% nitrogen, 0.001 to 0.030% phosphorus, 0.0001 to 0.020% oxygen, maximum 0.010% sulfur, less than 1.0% molybdenum, less than 1.0% cobalt, less than 0.5% copper, less than 1.0% tungsten, balance iron and the usual process-relatedImpurities, whereby the following relationship must be fulfilled: Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*Al ≤ 2.5 (1a), where Ni, Si, and Al are the concentrations of the respective elements in mass%. Advantageous developments of the subject matter of the invention can be found in the associated subclaims. The nickel content is between 35.0 and 38.0%, with preferred contents being adjustable within the following ranges: - 35 or > 35.0 to < 38.0% - 35 or > 35.0 to 37 or < 37.0%. The spread range for the element chromium is between 26.0 and 30.0%, whereby preferred ranges can be set as follows: - > 26.0 to < 30.0% - 27.0 or > 27.0 to 30.0 or < 30.0% - 28.0 or > 28.0 to 30.0 or < 30.0% The silicon content is between > 0.7 and 1.50%. Preferably, silicon can be set in the alloy within the spread range as follows: - > 0.70 to < 1.50% - 0.80 or > 0.80 to 1.50 or < 1.50% - 0.90 or >0.90 to 1.50 or < 1.50% - 0.80 or > 0.80 to 1.50 or < 1.50% - 0.80 or > 0.80 to 1.45 or < 1.45%. The aluminum content is between 0.40 and 1.30%, whereby preferred aluminum contents can also be set as follows: - > 0.40 to < 1.30% - 0.50 or > 0.50 to 1.30 or < 1.30% - 0.50 or > 0.50 to 1.20 or < 1.20% - 0.50 or > 0.50 to 1.10 or < 1.10% - 0.60 or > 0.60 to 1.10 or < 1.10%. The same applies to the element manganese, which can be present in the alloy at 0.0 to 1.0%. Alternatively, the following range is also conceivable: - > 0.0 to < 1.00% - > 0.0 to 0.50 or < 0.50% - > 0.0 to 0.05 or < 0.05% - 0.005 or > 0.005 to 0.20 or < 0.20% - 0.005 or > 0.005 to 0.10 or < 0.10%. Magnesium and / or calcium are also present in amounts of 0.0001 to 0.05%. Preferably, these elements can be included in the alloy as follows: - 0.0001 to 0.030% - 0.0001 to 0.020% - 0.0002 to 0.015% -0.0010 to 0.010%. The alloy contains 0.015 to 0.12% carbon. This can preferably be adjusted within the alloy within the spread range as follows: - > 0.015 to < 0.12%. - 0.03 or > 0.03 to 0.10 or < 0.10% - 0.04 or > 0.04 to 0.10 or < 0.10% - 0.05 or > 0.05 to 0.10 or < 0.10% - 0.05 or > 0.05 to 0.09 or < 0.09%. This also applies to the element nitrogen, which is present in amounts between 0.001 and 0.150%. Preferred contents can be as follows: - > 0.001 to < 0.150% - 0.010 or > 0.010 to 0.140 or < 0.140% - 0.020 or > 0.020 to 0.140 or < 0.140% - 0.050 or > 0.050 to 0.140 or < 0.140%. The alloy also contains phosphorus in contents between 0.001 and 0.030%. Preferred contents can be as follows: - 0.001 to 0.015%. The alloy also contains oxygen in contents between 0.0001 and 0.020%, including in particular 0.0001 to 0.010%. The elementSulfur is present in the alloy at a maximum of 0.010%. Preferred contents can be as follows: - Sulfur max. 0.008%. Molybdenum is present in the alloy at a content of less than 1.0%. The molybdenum content can be further restricted as follows: - Mo max. 0.50 or < 0.50% - Mo max. 0.20 or < 0.20% - Mo max. 0.10 or < 0.10% - Mo max. 0.05 or < 0.05% - Mo max. 0.02 or < 0.02%. Furthermore, the alloy contains less than 1.0% cobalt. The cobalt content can be further restricted as follows: - Co max. 0.50 or < 0.50% - Co max. 0.20 or < 0.20% - Co max. 0.10 or < 0.10% - Co max. 0.05 or < 0.05% - Co max. 0.015 or < 0.015%. Furthermore, the alloy can contain less than 0.5% copper. The copper content can be further restricted as follows: - Cu max. 0.30 or < 0.30% - Cu max. 0.10 or < 0.10% - Cu max. 0.05 or < 0.05% - Cu max. 0.015 or < 0.015%. Tungsten is present in the alloy witha maximum content of 1.0%. The tungsten content can be further restricted as follows: - W < 1.0% - W max. 0.50 or < 0.50% - W max. 0.20 or < 0.20% - W max. 0.10 or < 0.10% - W max. 0.05 or < 0.05% - W max. 0.02 or < 0.02%. The remainder of the alloy consists of iron and the usual manufacturing impurities. The iron content can be further restricted as follows: - 28.0 or > 28.0 to 38.0% - 29.0 or > 29.0 to 38.0% - 30.0 or > 30.0 to 38.0 or < 38.0%. The following relationship between nickel, silicon, and aluminum must be satisfied to ensure sufficient resistance in carburizing, sulfidizing, and chlorinating environments: Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*Al ≤ 2.5 (1a), where Ni, Si, and Al are the concentrations of the respective elements in mass%. Preferred ranges can be set with Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*Al ≤ 1.5 (1b) Fc = - 1.2 + 0.29*Ni -4.6*Si - 4.4*Al ≤ 1.0 (1c) Additions of oxygen-affine elements such as cerium, lanthanum, yttrium, zirconium, and hafnium improve corrosion resistance. They do this by being incorporated into the oxide layer and blocking oxygen diffusion paths at the grain boundaries. If necessary, the alloy can contain 0.001 to 0.20% each of one or more of the elements cerium, lanthanum, yttrium, zirconium, and hafnium, provided the following formula is met: FRE = 0.714*Ce + 0.720*La + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.10 (2a) where Ce, La, Y, Zr, and Hf are the concentrations of the respective elements in mass %. Preferably, if at least one of the elements cerium, lanthanum, yttrium, zirconium and hafnium is present, FRE can be set as follows: FRE = 0.714*Ce + 0.720*La + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.075 (2b) FRE = 0.714*Ce + 0.720*La + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.065 (2c) Alternatively, if cerium and lanthanum are present at the same time, cerium can also beMisch metal (abbreviation CeMM) can be used in contents of 0.001 to 0.20%, where FRE must be modified as follows: FRE= 0.716*CeMM + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.10 (3a) where CeMM, Y, Zr and Hf are the concentration of the respective elements in mass%. Preferably, when adding cerium mischmetal, FRE can be set as follows: FRE = 0.716*CeMM + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.075 (3b) FRE = 0.716*CeMM + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.065 (3c) Preferably, cerium, lanthanum, cerium mischmetal, zirconium and hafnium can be contained in the alloy within the spread range as follows: - > 0.001 to < 0.20% - 0.001 or > 0.001 to 0.15 or < 0.15% - 0.001 or > 0.001 to 0.10 or < 0.10% - 0.001 or > 0.001 to 0.08 or < 0.08% - 0.001 or > 0.001 to 0.05 or < 0.05% - 0.001 or > 0.001 to 0.04 or < 0.04% - 0.01 or > 0.01 to 0.04 or < 0.04% Preferably, yttrium can be included in the alloy within the spread range as follows:will be: - > 0.001 to < 0.20% - 0.001 or > 0.001 to 0.15 or < 0.15% - 0.001 or > 0.001 to 0.10 or < 0.10% - 0.001 or > 0.001 to 0.08 or < 0.08% - 0.01 or > 0.01 to 0.08 or < 0.08% - 0.01 or > 0.01 to < 0.045%. The element titanium can optionally be present in the alloy in contents of 0.0 to 0.50%. Titanium can preferably be contained in the alloy within the spread range as follows: - > 0.0 to < 0.50% - > 0.0 to 0.50 or < 0.50% - 0.001 or > 0.001 to 0.20 or < 0.20% - 0.001 or > 0.001 to 0.15 or < 0.15% - 0.001 or > 0.001 to 0.10 or < 0.10% - 0.001 or > 0.001 to 0.05 or < 0.05% - 0.001 or > 0.001 to 0.04 or < 0.04% - 0.005 or > 0.005 to 0.20 or < 0.20%. - 0.010 or > 0.010 to 0.20 or < 0.20%. Niobium can optionally be included in the alloy in contents of 0.0 to 0.2%. Niobium can preferably be contained in the alloy within the range as follows: -> 0.0 to < 0.20% -> 0.0 to 0.15 or < 0.15% -> 0.0 to 0.10 or < 0.10% -> 0.0 to 0.05 or < 0.05% -> 0.0 to 0.02 or < 0.02% -> 0.001 or > 0.001 to 0.20 or < 0.20% -> 0.010 or > 0.010 to 0.20 or < 0.20%. Optionally, the alloy can also contain 0.0 to 0.20% tantalum. Preferred contents can be as follows: -> 0.0 to < 0.20% -> 0.0 to 0.10 or < 0.10% -> 0.0 to 0.05 or < 0.05%. Optionally, the element boron can be included in the alloy in amounts of 0.0001 – 0.008%. Preferred contents can be as follows: - Boron 0.0005 – 0.008% - Boron 0.0005 – 0.005% - Boron 0.0005 – 0.004%. Furthermore, the alloy can contain a maximum of 0.50% vanadium. - V < 0.50% - V max. 0.40 or < 0.50% - V max. 0.20 or < 0.20% - V max. 0.08 or < 0.10% - V max. 0.05 or < 0.05% Finally, the elements lead, zinc, and tin can be present as impurities in amounts as follows: Pb max. 0.002%, Zn max. 0.002%.Sn max. 0.002% The element beryllium can then be present as follows: Be less than 0.001%. The alloy according to the invention is preferably melted in an open furnace, followed by a VOD (Vacuum Oxygen Decarburization) or VLF (Vacuum Laddle Furnace) treatment. However, melting and pouring in a vacuum is also possible. The alloy is then poured into blocks, electrodes, or as a continuous cast to form a precursor. If necessary, the precursor is then annealed at temperatures between 900 and 1270°C for 0.1 to 70 hours. Furthermore, it is possible to remelt the alloy one or more times using ESU (electro-slag remelting) and / or VAR (vacuum arc remelting). The alloy is then formed into the desired semi-finished product. For this purpose, annealing is carried out at temperatures between 800 and 1290°C for 0.1 to 70 hours, followed by hot forming, possibly with intermediate annealing between 800 and 1290°C for 0.05 hours to 70 hours. The surface of theIf necessary, the material can be chemically and / or mechanically removed for cleaning purposes (even several times) during and / or at the end of hot forming. This can then be followed by cold forming with a degree of deformation of up to 98% into the desired semi-finished product shape, if necessary with intermediate annealing between 800 and 1250°C for 0.05 minutes to 70 hours, if necessary under a protective gas such as argon or hydrogen, followed by cooling in air, in a moving annealing atmosphere or in a water bath. This is followed by solution annealing in a temperature range of 800 to 1250°C for 0.05 minutes to 70 hours, if necessary under a protective gas such as argon or hydrogen, followed by cooling in air, in a moving annealing atmosphere or in a water bath. If necessary, chemical and / or mechanical cleaning of the material surface can be carried out during and / or after the final annealing. The semi-finished product produced by hot and / or cold rolling has, after solution annealing, a structure with a medium grain sizefrom 5 to 600 µm. The alloy according to the invention can be easily produced and used in the semi-finished forms of bars, sheets, forgings, longitudinally welded or seamless pipes, pipe accessories, valve parts, and flanges. The various semi-finished forms can be assembled into the required components or incorporated into the required components. Likewise, the alloy according to the invention can be used, if required, for build-up welding on metallic components of any type. The alloy according to the invention is particularly suitable as a component for applications with carburizing, sulfidizing, and chlorinating environments, particularly atmospheres. Due to its good high-temperature corrosion resistance and its good formability and weldability, the alloy according to the invention is suitable for use as a component in waste incineration plants, pyrolysis plants, refinery furnaces, the chemical industry, coal gasification plants, and inIndustrial furnace construction, activated carbon filters, waste pyrolysis, and precious metal recovery. Examples: Tests conducted: The assessment of high-temperature corrosion resistance in carburizing, sulfiding, and chlorinating environments was carried out by testing the material's resistance to exposure to a flowing synthetic gas atmosphere with these properties at elevated temperatures (at Dechema). For this purpose, samples measuring 20 x 8 x 4 mm³ were cut from the semi-finished product of the respective alloys, then drilled with a 3 mm diameter hole, and then wet-ground with SiC paper up to 1200 grit (grain size ~15 μm). The samples were degreased and cleaned in an ultrasonic bath with isopropanol. Each sample was suspended in the reaction vessel via this hole over a ceramic crucible to collect any flaking corrosion products. The mass of the flaking could be determined by weighing the crucible containing the corrosion products.can. The sum of the mass of the flaking and the mass change of the samples is the gross mass change of the sample. The specific mass change is the mass change relative to the surface of the samples. These are referred to below as mNet for the specific net mass change, mGross for the specific gross mass change, and mSpall for the specific mass change of the flaking oxides. A gas mixture consisting of 60% CO, 30% H2, 4% CO2, 1% H2S, 0.05% HCl, and 3.95% H2O flowed through the space of the reaction vessel. This mixture has a carburizing (60% CO), sulfidizing (1% H2S), and chlorinating (0.05% HCl) effect. Tests were carried out at 500°C. The test duration was 1056 hours each, divided into 11 cycles of 96 hours each. Each test included two samples per alloy. The values ​​given are the mean values ​​of these two samples. In the following tests, an alloy is considered to be resistant to carburizing andsulfidizing and chlorinating environments, which shows a gross mass gain of ≤ 2.0 mg / cm² (4) after 1056 hours. This is the case when the following relationship between nickel, silicon and aluminum is satisfied: Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*Al ≤ 2.5 (1a), where Ni, Si and Al and Si are the concentrations of the respective elements in mass%. Weldability is assessed by the extent to which hot cracks form during welding. The greater the risk of hot cracking, the worse the weldability of a material. To quantify their susceptibility to hot cracking, the various alloys were tested using the MVT (Modified Varestraint Transvarestraint) test at the BAM (Federal Institute for Materials Research and Testing). For this purpose, a sample measuring 100 mm x 40 mm x 10 mm is made from the alloy. In the MVT test, a TIG weld (TIG: Tungsten InertGas) at a constant feed rate. When the arc passes the center of the sample, a defined bending strain is applied to the sample. The samples were bent longitudinally to the welding direction (varestraint mode). During this bending phase, hot cracks form in a locally limited test zone on the MVT sample. The tests were carried out with 4% bending strain, a die speed of 2 mm / s, and a heat energy of 7.5 kJ / cm, each under pure argon 4.8. For evaluation, the lengths of all solidification cracks and remelting cracks visible on the sample under a light microscope at 25x magnification were determined and summed. Based on these results, the material can then be classified into the categories "hot crack resistant" (range 1), "increasing hot crack tendency" (range 2), and "hot crack prone" (range 3), as shown in Table 2. In the following tests, the alloys are considered to be goodWeldable alloys which, in the MVT test, are in range 1 "hot crack resistant" and in range 2 "increasing hot cracking tendency", since the weldable alloy according to the state of the art AC66 is in range 2. Alloys which are in the hot cracking risk (range 3) are generally difficult to weld. In particular, welding with a welding consumable of the same type (comparable composition to the material to be welded) is difficult or even impossible. The assessment of the high-temperature strength was determined by hot tensile tests. This is determined in a tensile test according to DIN EN ISO 6892-2 at the desired temperature. The yield strength Rp0.2, the tensile strength Rm and the elongation A until fracture are determined. The tests were carried out on round specimens with a diameter of 6 mm in the measuring range and an initial gauge length L0 of 30 mm. The yield strength Rp0.2 and the tensile strength Rm at 500°C should at least be the minimum values ​​for the alloy AC66 according to the state of the artAchieve the following values: - 500°C: Rp0.2 ≥ 95 MPa or Rm ≥ 115 MPa (5a, 5b) It would be desirable for them to be better than the minimum values ​​of the state-of-the-art alloy 45TM. - 500°C: Rp0.2 ≥ 150 MPa or Rm ≥ 500 MPa. (6a, 6b) The grain size is determined using a line-intercept method. Production To determine the properties of the components manufactured from the alloy, alloys melted on a laboratory scale in a vacuum furnace were used. Tables 3a and 3b show the analyses of the laboratory-scale melted batches together with some large-scale melted batches of AC66 (1.4877) and 45TM (2.4889) used for comparison. The batches according to the state of the art are marked with a T, the batches according to the invention with an E. The batches melted on a laboratory scale are marked with an L, the batches melted on an industrial scale with a G. The blocks of the batches melted on a laboratory scaleThe vacuum-melted alloys in Tables 3a and 3b were annealed between 900 and 1270°C for 8 hours and then hot-rolled to a final thickness of 13 or 6 mm by means of hot rolling and further intermediate annealing between 900 and 1270°C for 0.1 to 1 hour. The sheets produced in this way were solution-annealed between 800 and 1250°C for 1 hour. The samples required for the measurements were made from these sheets. For the industrially melted alloys, a sample was taken from a factory-produced sheet of the appropriate thickness during industrial production. The samples required for the measurements were made from these sheets. All alloy variants typically had a grain size of 50 to 190 µm. For the sample batches in Table 3a and b), the following properties are compared: - the high-temperature corrosion resistance in carburizing, sulfidizing and chlorinating environments - the weldability by means of MVT tests - theCreep resistance using hot tensile tests. The results are summarized in Table 4. Table 4 shows the results of the corrosion test in the form of gross mass change and spalling at 500°C after 1056 hours in an atmosphere of 60% CO, 30% H2, 4% CO2, 1% H2S, 0.05% HCl, and 3.95% H2O. All alloys tested have a chromium content of approximately 27 to 28%. The state-of-the-art alloy AC66, with only 0.2% silicon, shows by far the largest gross mass change of 10.92 mg / cm². The state-of-the-art alloy 45TM with 2.6% silicon and all tested batches melted on a laboratory scale with a silicon content greater than 1.0% show a gross mass change of less than or equal to 2.0 mg / cm² (2209, 250098, 250101, 250105, 250102 and 250107). If the aluminum content is also greater than 0.40%, a batch with a silicon content less than or equal to 1.0% can also show a gross mass change of less than or equal to2.0 mg / cm² if formula (1a) Fc ≤ 2.5 is simultaneously met. This is the case for batches 250084 (Si = 0.59% and Al = 0.95%), 250085 (Si = 0.90% and Al = 0.98%), 250106 (Si = 0.98% and Al = 0.80%), and 250108 (Si = 0.70% and Al = 0.86%). Batches 250084, 250106, 250105, 250108, and 250107 are in accordance with the invention, while batch 2209, with a silicon content greater than 1.50%, and batch 250098, with a nickel content of 44.0%, are not. Batch 250098 (Si = 1.20% and Al = 0.85%) shows a comparable or higher gross mass increase compared to batches 250106 (Si = 0.98% and Al = 0.80%) and 250101 (Si = 1.01% and Al = 0.75%), despite a significantly increased silicon content of 1.2%. Batch 250098 (Ni = 44.0%) has a significantly increased nickel content compared to batches 250106 (Ni = 35.6%) and 250101 (Ni = 38.2%). This shows that a higher nickel content worsens corrosion. The upper limit for nickel is therefore set at a maximum of40%. In the non-inventive batch 250100 (Ni = 38.2%, Si = 0.99%, and Al = 0.43%), with a gross mass increase (3.43 mg / cm²) significantly greater than 2.0 mg / cm², the aluminum content is somewhat too low, so that formula (1a) is not met, in contrast to batch 250101 (Ni = 38.2%, Si = 1.01%, and Al = 0.75%). In the non-inventive batches 250103 (Ni = 38.2, Si = 0.36% and Al = 0.82%) and 250099 (Ni = 38.4%, Si = 1.00% and Al = 0.20%), which also have a gross mass increase (8.01 mg / cm² and 5.35 mg / cm², respectively) significantly greater than 2.0 mg / cm², the silicon and aluminum content are outside the claimed limits and, in addition, formula (1a) is not met. The inventive alloys 250084 and 250106 still exhibit spalling. If formula (1c) Fc ≤ 1.0 is also met, these alloys no longer exhibit spalling (250107) and, surprisingly, also have a very low gross mass change at moderate silicon contents.of well below 1.0 mg / cm² in the range of 45TM with 2.6% silicon and 0.16% aluminum. Table 4 shows the weldability classification of the alloys using the MVT test. The state-of-the-art weldable alloy AC66 is in range 2. Alloy 45TM is classified in range 3 (hot cracking prone) and thus has a strong tendency to crack formation, which makes welding difficult and makes welding with a similar filler metal difficult or even impossible. Non-inventive batches with a silicon content greater than 1.50% (45TM, batches 2091, 2099, 2100, 2200, 2203, 2207, 2208, 2209) are all in range 3. Of the batches with a silicon content of around 1.4%, the batches with an aluminum content below 0.1% are in range 2 (batches 2093, 2101), while those with a higher aluminum content are already in range 3 (batches 2103, 2096, 2097, 2098). The batches with a silicon content of less than 1.3%are all in range 1 or 2 (AC66, batches 2095, 2102, 250084 to 250108). All laboratory batches according to the invention are in range 1 (batches 250084, 250106, 250105, 250108, and 250107) or range 2 (batch 250102). The results of the hot tensile tests at 500°C in the table show that for all alloys according to the invention melted on a laboratory scale, the yield strength Rp0.2 is greater than or equal to 153 MPa, thus significantly exceeding the minimum of 95 MPa for AC66. They also exceed the minimum of 150 MPa for 45TM, albeit not significantly (see formulas 5a and 6a). Likewise, the tensile strength Rm of all alloys according to the invention is greater than or equal to 192 MPa and thus also significantly greater than the minimum of 115 MPa for AC66 (see formula 5b). All hot tensile tests at 500°C showed an elongation of greater than 35%. The claimed limits for the alloys "E" according to the invention can therefore be explained in detail as follows: A relatively low nickel content (atA high iron content (balance) promotes low corrosion in carburizing, sulfidizing, and chlorinating environments. Therefore, a content of 40% is the upper limit for nickel. A nickel content that is too low (a high iron content (balance) at the same time) promotes sigma phase formation, especially with high chromium and silicon contents. Therefore, a nickel content of 35% is the lower limit. Chromium improves corrosion resistance in carburizing, sulfidizing, and chlorinating environments. Too low a chromium content means that the chromium concentration drops very quickly below the critical limit when the alloy is used in a highly corrosive environment, so that a continuous chromium oxide layer can no longer form. Therefore, 26% chromium is the lower limit for chromium when used in carburizing, sulfidizing, and chlorinating environments. Too high a chromium content promotes sigma phase formation in the alloy, especially at highChromium contents. Therefore, 30% chromium is considered the upper limit. Silicon improves corrosion resistance in carburizing, sulfidizing, and chlorinating environments. A minimum content of 0.40% is therefore necessary. Excessively high contents, in turn, impair weldability and promote sigma phase formation, especially at high chromium contents. The silicon content is therefore limited to 1.50%. A certain aluminum content improves corrosion resistance in carburizing, sulfidizing, and chlorinating environments. A minimum content of 0.40% is therefore necessary. Excessively high contents, in turn, impair weldability, especially at high chromium and silicon contents. The aluminum content is therefore limited to 1.30%. Manganese is useful for improving workability. Manganese is limited to 1.0% because this element reduces high-temperature corrosion resistance. Even very low magnesium contents and / orCalcium contents improve processing by binding sulfur, thereby avoiding the occurrence of low-melting NiS eutectics. A minimum content of 0.0001% is therefore required for magnesium and / or calcium. At excessively high contents, intermetallic Ni-Mg or Ni-Ca phases can occur, which in turn significantly impair processability. The magnesium and / or calcium content is therefore limited to a maximum of 0.05%. A minimum carbon content of 0.015% is necessary for good creep resistance. Carbon is limited to a maximum of 0.12%, as this element reduces processability above this content due to the excessive formation of primary carbides. A minimum nitrogen content of 0.001% is required, which improves processability and the high-temperature strength of the material. Nitrogen is limited to a maximum of 0.150%, as this element reduces theProcessability is reduced. The phosphorus content should be less than or equal to 0.030%, as this surface-active element impairs high-temperature corrosion resistance. A phosphorus content that is too low increases costs. The phosphorus content is therefore ≥ 0.001%. The oxygen content must be less than or equal to 0.020% to ensure the manufacturability of the alloy. An oxygen content that is too low increases costs. The oxygen content is therefore ≥ 0.0001%. The sulfur content should be set as low as possible, as this surface-active element impairs high-temperature corrosion resistance. A maximum of 0.010% sulfur is therefore specified. Molybdenum is limited to less than 1.0%, as this element reduces high-temperature corrosion resistance. Tungsten is limited to less than 1.0%, as this element also reduces high-temperature corrosion resistance. Cobalt can contain less than 1.0% in this alloy.Higher contents reduce high-temperature corrosion resistance. Copper is limited to less than 0.5%, as this element reduces high-temperature corrosion resistance. The following relationship between nickel, silicon, and aluminum must be met to ensure sufficient resistance in carburizing, sulfidizing, and chlorinating environments: Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*Al ≤ 2.5 (1a), where Ni, Si, and Al are the concentrations of the respective elements in mass%. The limit for Fc has been explained in detail in the previous text. If necessary, high-temperature corrosion resistance can be further improved with the addition of oxygen-affine elements. They do this by being incorporated into the oxide layer and blocking the oxygen diffusion paths at the grain boundaries. A minimum content of one or more of the elements cerium, lanthanum, cerium mischmetal, yttrium, and zirconium is required.and hafnium of 0.001% each are necessary to achieve the high-temperature corrosion resistance-enhancing effect. For cost reasons, the upper limit for each element is set at 0.20%. The following formula must be met: FRE = 0.714*Ce + 0.720*La + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.10 (2a) where Ce, La, Y, Zr, and Hf are the concentrations of the respective elements in mass%. This formula limits the total content of elements such as cerium, lanthanum, yttrium, zirconium, and hafnium. Contents with FRE > 1.0 can increase corrosion rates and impair workability. Titanium can be added if necessary. Titanium increases high-temperature strength. Above 0.50%, high-temperature corrosion behavior can be impaired, which is why 0.50% is the maximum value. Niobium can be added if necessary, as it also increases high-temperature strength. Higher contents increase costs significantly. The upper limit is therefore set at 0.20%.If necessary, the alloy can also contain tantalum, as tantalum also increases high-temperature strength. Higher contents increase costs considerably. The upper limit is therefore set at 0.20%. A minimum content of 0.001% is required to achieve an effect. If necessary, boron can be added to the alloy, as boron improves creep resistance. Therefore, a content of at least 0.0001% should be present. At the same time, this surface-active element impairs high-temperature corrosion resistance. A maximum of 0.008% boron is therefore specified. If necessary, vanadium is limited to a maximum of 0.50%, as this element reduces high-temperature corrosion resistance. If necessary, lead is limited to a maximum of 0.002%, as this element reduces high-temperature corrosion resistance. 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0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 0 , 0 on 1 0 r9703592039103019697989990003789394045681 5827 a , N - 0301 01 1 000001 020202020201 9001 0880900000 L 0 g 72 22 2 2 22 2 22 2 22 2 22 20001000001000101010101 r 53 555555 0 < h 1 1 5555555 e 22 2 22 2 2 22 2 2 d C 2 2 Y g ; ) n 1 . r u 0 z , t 0 N - f f f n H e s < : o t M r Z s n W k r E s E s E s E s E s E s E s E s E s E s E s E s a a a a L L L L E s E s E s E s E s Es E s E s E s E s E s E s E s is : t and 889888888888888888888887777 l i 2 2 2 2 2 2 2 2 2 2Wr rrrrrrrrr 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r 2 r ( C5 C5 C7 C3 CCCCCCCCCCCCCCCCCCCCCCC m g a s ng ) 7 ) 9 0 . 3 . 6 4 . 8 . 5559 . 9 . 8 . 9 . 9 . 8 . 2 . 2 . 4 . 0 . 0 . 8 . 8 8 5 9 8 9l 0 .l 0 .l 0 .l l 1 0 .l l 1 l 0 1 .l 0 .l 0 . . . . . . . l l 0 one l 0 l 0 l 0 l 0 l 0 l 0 l 0 l 0 l 1 l 1 l 0 l 0 l 0 l 0 l 0 l 0 Z gu 78 l0 n 88 AAAAAAAAAAAAAAAAAAAAAAAAAAAAAAAAA 449 8 4 4 4 0 4 4 4 9: nh 1 2. . . . . . . . . . 0 . 5 . 5 . 5 . 5 . 5 . 4 . 0 . 0 . 0 . 6 . 9 . 0 . 2 . 0 . 1 . 7 . 3 . 3 . i 0 i 0 i 1 i 1 i 1 i 2 i 1 i 1 i 1 i 1 i 2 i 1 i 1 i 1 i 1 i1 i b u r . ) a c i ( ( 0 i 1 i 1 i 1 i 0 i 0 i 1 i 1 i 1 i 1 i 0 i 1 i 1 e 6 MS4 S4 S5 S4 S4 S4 S5 S4 S4 S4 S5 S8 S4 S4 S8 S8 S8 S8 S S S S S S S S S S S 3 i e e l l g 3 z 6 e CT 58585485585 5 i 4 i 3 i 4 i 3 i 3 i 4 i 4 i 4 i 4 i 4 i 3 i 3 i 4 i 4 i 3 i3 i 3 i 3 i 3 i 3 i 3 i 3 i 3 i 4 i 3 i 3 i 3 i 3 i 3 e e l B A 4 N N N N N N N N N N N N N N N N N N N N N N N N N N N N N eb L l e e b GG L L L L L L L L L L L L L L L L L L L L L L L L L L L L L a l T l a a T T T E T E T E E T E 1 , 2 . 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N l l l l l 1 l l 1 l 0 .l .l .ll 0 l 0 l 0 l 0 l 0 l 0 l AND : 5 or 78 0 l 0 l 0 l 1 l 1 l 0 l 0 l 0 l 0 l 0 l 0 l 0 0 n 88 AAAAAAAAAAAAAAAAAAAAAAAAAAAAAAA 44 9 . 8 . 4 . 4 . 4 . 0 . 4 . 4 . 4 . 9 . 0 . 5 . 5. 5 . 5 . 5 . 4 . 0 . 0 . 0 . 6 . 9 . 0 . 2 . 0 . 1 . 7 . 3 . 3 . 4 , 0 h 1 2 el l , c i ( ( i 0 i 0 i 1 i 1 i 1 i 2 i 1 i 1 i 1 i 1 i 2 i 1 i 1 i 1 i 1 i 1 i 0 i 1 i 1i 1 i 0 i 0 i 1 i 1 i 1 i 1 i 0 i 1 i 1 e 6 MS4 S4 S5 S4 S4 S4 S5 S4 S4 S4 S5 S8 S4 S4 S8 S8 S8 S8 S5 S8 S5 S S S S S S S S e S z 6 2 e CT 85485585 i 4 i 3 i 4 i 3 i 3 i 4 i 4 i 4 i 4 i 4 i 3 i 3 i 4 i 4 i 3 i 3 i 3 i 3 i 3 i 3 i 3 i 3 i 3 i b H B A5 4i 3 i 3 i 3 i 3 i 3 4 NNNNNNNNNNNNNNNNNNNNN NNNNNNNN a T % TTETETEETE Figure description Figure 1: Corrosion attack depth of various alloys after aging for 2100 hours in a Prenflo pilot plant in a gas containing H2S as a function of temperature.

Claims

Claim 1. Use of a nickel-iron-chromium alloy with excellent high-temperature corrosion resistance as a semi-finished product in simultaneously carburizing, sulfiding, and chlorinating environments, comprising (in wt.%): 35.0 to 38% nickel, 26.0 to 30.0% chromium, > 0.7 to 1.50% silicon, 0.40 to 1.30% aluminum, 0.00 to 1.0% manganese, 0.0001 to 0.05% each of magnesium and / or calcium, 0.015 to 0.12% carbon, 0.001 to 0.150% nitrogen, 0.001 to 0.030% phosphorus, 0.0001 to 0.020% oxygen, maximum 0.010% sulfur, less than 1.0% molybdenum, less than 1.0% cobalt, less than 0.5% copper, less than 1.0% tungsten, the remainder iron, and the usual process-related impurities, wherein the following relationship must be satisfied: Fc = -1.2 + 0.29*Ni - 4.6*Si - 4.4*Al ≤ 2.5 (1a), where Ni, Si, and Al are the concentrations of the respective elements in mass %.

2. Use according to claim 1 with a nickel content of > 35.0 to < 38%. 3.Use according to one of claims 1 to 2 with a chromium content of > 26.0 to 30.0%.

4. Use according to any one of claims 1 to 3 with an aluminum content of ≥ 0.50% or > 0.50% to < 1.30%.

5. Use according to any one of claims 1 to 4 with a residual iron content of 28.0% or > 28.0% to 38.0%.

6. Use according to any one of claims 1 to 5 containing 0.001% to 0.20% of one or more of the elements cerium, lanthanum, yttrium, zirconium, and hafnium, wherein the following formula must be satisfied: FRE = 0.714*Ce + 0.720*La + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.10 (2a) where Ce, La, Y, Zr, and Hf are the concentrations of the respective elements in mass percent.

7. Use according to any one of claims 1 to 6, wherein, in the simultaneous presence of cerium and lanthanum, cerium mischmetal (abbreviated CeMM) is also used in contents of 0.001 to 0.20%, wherein FRE must be modified as follows: FRE = 0.716*CeMM + 1.124*Y + 1.096*Zr + 0.560*Hf ≤ 0.10 (3a) where CeMM, Y, Zr, and Hf are the concentrations of the respective elements in mass percent. 8.Use according to any one of claims 1 to 7, optionally with a titanium content of 0.0 to 0.50%.

9. Use according to any one of claims 1 to 8, optionally with a niobium and / or tantalum content of 0.0 to 0.50% each.

10. Use according to any one of claims 1 to 9, optionally with a boron content of 0.0001 to 0.008%.

11. Use according to any one of claims 1 to 10, further optionally containing a maximum of 0.50% vanadium.

12. Use according to any one of claims 1 to 12, wherein the impurities are adjusted to levels of max. 0.002% lead, max. 0.002% tin, max. 0.002% zinc.

13. Use according to any one of claims 1 to 12 with semi-finished products in the form of strip, sheet, wire, bar, forgings, longitudinally welded pipe, and seamless pipe.

14. Use according to any one of claims 1 to 13 as a component or in a component in the chemical industry.

15. Use according to any one of claims 1 to 13 as a semi-finished product or as a semi-finished product in a component in a waste incineration plant or in a waste pyrolysis plant.

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