Wear-resistant plate as well as preparation method and application thereof

Abstract

The invention provides a wear-resistant plate and a preparation method and application thereof, and belongs to the technical field of steel plate materials. The wear-resisting plate comprises a steel base body and a surface wear-resisting layer cladded on the base body, and powder raw materials of the surface wear-resisting layer comprise, by mass, 30%-72% of TiC, 4%-10% of Cr, 5%-25% of Ni, 0.3%-5% of Mo, 0.01%-1% of Mn, 0.1%-1.0% of Si, 0.3%-1.0% of B and the balance Fe. The powder raw material is in a sphere-like shape, and the particle size of the powder raw material is 42-150 [mu] m. Spherical-like powder is adopted, the stability of TiC in the cladding process is improved, the hardness, bonding strength, wear resistance and other comprehensive performance of the wear-resisting plate can be remarkably improved by accurately controlling the proportion of powder raw materials and cladding process parameters, the wear-resisting plate is more suitable for concrete pump truck wear plates and cutting rings, the service life of equipment is prolonged, cost is reduced, and the wear-resisting plate is suitable for large-scale production. The economic benefit is improved.

Description

Technical Field

[0001] This application relates to the field of steel plate material technology, and in particular to a wear-resistant plate, its preparation method and application. Background Technology

[0002] Wear-resistant steel plates are composite materials with a wear-resistant layer fused onto the surface of a steel substrate. They are widely used in high-wear environments in industries such as mining, metallurgy, cement, and power. With the development of industrial production, higher requirements are being placed on the wear resistance, corrosion resistance, service life, and cost-effectiveness of wear-resistant steel plates.

[0003] Currently, commonly used wear-resistant plates mainly include weld overlay wear-resistant plates, composite wear-resistant plates, and clad wear-resistant plates. Among them, clad wear-resistant plates have received widespread attention in industrial applications due to their advantages such as high bonding strength and good wear resistance. CN109183025B discloses a wear-resistant Cr8Mo2SiV steel part and its preparation method, as well as Ni-based wear-resistant alloy powder for Cr8Mo2SiV steel. This technology forms a wear-resistant layer on the surface of the steel substrate through laser cladding, which can achieve high hardness and high wear resistance. CN106367706B discloses a plasma spraying gradient wear-resistant plate, its preparation method, and its applications. This technology plasma sprays a layer of Fe50 iron-based self-fluxing alloy as a transition layer on the surface of a pretreated carbon steel substrate, and uses a dual-channel powder feeder to simultaneously feed powder on the surface of the transition layer, realizing a gradient distribution of ceramic phase content from the surface layer to the transition layer and even the substrate, increasing the adhesion of the coating.

[0004] Regarding wear-resistant layer materials, CN113319272B discloses a cermet powder material for the wear-resistant layer of a steel conveyor roller. This material is composed of a nickel-based alloy and NiCr-Cr3C2 cermet. The wear-resistant layer is prepared using laser cladding technology, which significantly improves its high-temperature resistance, wear resistance, and impact resistance. CN114774912A discloses a method for preparing a self-lubricating ceramic high-temperature wear-resistant coating by in-situ laser cladding. This method improves the surface wear resistance and corrosion resistance while also enhancing the surface's self-lubricating properties by adding self-lubricating materials to the coating. CN113774287A discloses a laser-clad pre-hardened cone crusher liner and its processing technology. This technology, through the design of the underlayer and wear-resistant layer, effectively suppresses the floating of casting defects in the substrate, increasing the coating's impact resistance and wear resistance.

[0005] However, traditional wear-resistant plates often use WC-Fe-Ni-Co type cemented carbide as the wear-resistant material, which is costly, and the high Fe content leads to poor corrosion resistance, affecting service life. Therefore, there is an urgent need to develop a new type of wear-resistant plate. By optimizing the material composition and preparation process, the wear resistance, bonding strength and service life of the wear-resistant plate can be improved to meet the high requirements of industrial production applications. Summary of the Invention

[0006] This application is made in view of the above-mentioned problems, and its purpose is to provide a wear-resistant plate, a method for preparing the same, and its application, wherein the wear-resistant plate has low cost and good wear resistance.

[0007] Specifically, the first aspect of this application provides a wear-resistant plate, comprising a steel substrate and a surface wear-resistant layer clad on the substrate. The powder raw material of the surface wear-resistant layer comprises, by mass percentage: TiC 30-72%, Cr 4-10%, Ni 5-25%, Mo 0.3-5%, Mn 0.01-1%, Si 0.1-1.0%, B 0.3-1.0%, with the balance being Fe. The powder raw material is spherical with a particle size of 42-150 μm.

[0008] Furthermore, it also includes a transition bonding layer, which is clad between the substrate and the surface wear-resistant layer. The transition bonding layer contains, by mass percentage: Cr 6-9%, Ni 10-15%, Mo 1.0-1.8%, B 0.3-1.0%, with the balance being Fe.

[0009] Furthermore, the thickness ratio of the transition bonding layer to the surface wear-resistant layer is 1:1.5-2.5.

[0010] A second aspect of this application provides a method for preparing the wear-resistant plate, comprising the following steps: S1: Mix the powders of the transition bonding layer and the surface wear-resistant layer separately; S2: Surface pretreatment of the steel substrate; S3: The steel substrate is sequentially coated with a transition bonding layer and a surface wear-resistant layer; S4: After the cladding is completed and cooled, micro-pits are constructed on the surface wear-resistant layer, and solid lubricant is filled in and sintered.

[0011] Further, in step S1, the mixing time is 6-8 h, and the spheroidization treatment is carried out for 40-50 min at a compressed air pressure of 0.20-0.30 MPa and a temperature of 2000-2800℃ to obtain spherical powder.

[0012] Further, in step S2, the steel substrate is sandblasted to a surface roughness Ra of 6.3-12.5 μm and then ultrasonically cleaned.

[0013] Further, during the cladding of the transition bonding layer described in step S3, the steel substrate is preheated to 280-320°C and carried out under a protective atmosphere of Ar gas and 2-4% N2; and / or The plasma cladding uses a current of 320-430 A and / or a voltage of 28-32 V and / or a scanning speed of 3.5-4.0 mm / s.

[0014] Further, step S3, surface wear-resistant layer cladding, involves cladding the surface wear-resistant layer in a pure Ar atmosphere after the interlayer temperature of the transition bonding layer has cooled to 150-180°C, with a current of 340-360 A and / or a voltage of 25-28 V and / or a scanning speed of 5.0-6.0 mm / s.

[0015] Furthermore, in step S4, the micro-pit construction involves shot peening the surface wear-resistant layer with a shot peening pressure of 0.4-0.6 MPa; and / or the solid lubricant is graphene.

[0016] A third aspect of this application provides the application of the aforementioned wear-resistant plate in concrete pump truck spectacle plates, cutting rings, crushers, and shredders.

[0017] The present invention has the following beneficial effects: (1) This invention addresses the low specific gravity of TiC by employing spherical powder. Spherical powder exhibits better flowability and uniformity, thereby improving the stability of TiC during the cladding process. Good flowability allows the powder to enter the molten pool more smoothly during cladding, avoiding uneven cladding caused by powder accumulation or blockage. The relatively large surface area of ​​the spherical powder facilitates full reaction with other components during cladding, forming compounds and structures with excellent wear resistance. These compounds and structures are uniformly distributed within the wear-resistant layer, significantly improving the wear resistance and corrosion resistance of the wear-resistant plate.

[0018] (2) The wear-resistant plate of the present invention uses TiC as the main wear-resistant component, which significantly reduces the cost compared with traditional WC-Fe-Ni-Co type cemented carbide. At the same time, the reasonable composition design enables the wear-resistant plate to have good corrosion resistance while ensuring wear resistance, further improving its applicability in complex industrial environments.

[0019] (3) In terms of the manufacturing process, the transition bonding layer plays a crucial role. The composition and thickness of the transition bonding layer work in conjunction with the surface wear-resistant layer to effectively alleviate the thermal and structural stresses between the steel substrate and the surface wear-resistant layer, thereby improving the bonding strength between the wear-resistant layer and the substrate. In addition, the micro-pit construction and filling of the surface wear-resistant layer with solid lubricant graphene further enhances the self-lubricating performance of the wear-resistant plate. Under high-load and high-wear working conditions, graphene can form a lubricating film on the friction surface, reducing the coefficient of friction and the wear rate, thereby extending the service life of the wear-resistant plate. Attached Figure Description

[0020] To more clearly illustrate the technical solutions in the embodiments of this drawing or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this drawing. For those skilled in the art, other drawings can be obtained based on the structures shown in these drawings without creative effort.

[0021] Figure 1 This is a schematic diagram of the structure of the product of the present invention.

[0022] The purpose, features, and advantages of this accompanying drawing will be further explained in conjunction with the embodiments and with reference to the accompanying drawing. Detailed Implementation

[0023] To make the objectives, technical solutions, and advantages of this application clearer, the following description and illustration are provided in conjunction with embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the scope of this application. All other embodiments obtained by those skilled in the art based on the embodiments provided in this application without inventive effort are within the scope of protection of this application.

[0024] Obviously, the following description is merely some examples or embodiments of this application. Those skilled in the art can apply this application to other similar scenarios without any inventive effort. Furthermore, it is understood that although the effort involved in such development may be complex and lengthy, for those skilled in the art related to the content disclosed in this application, any changes to design, manufacturing, or production based on the technical content disclosed in this application are merely conventional technical means and should not be construed as insufficient disclosure of the content of this application.

[0025] Unless otherwise specified, the terms "comprising" and "including" as used in this application can be open-ended or closed-ended. For example, "comprising" and "including" can mean that other components not listed may also be included, or that only the listed components may be included.

[0026] Unless otherwise specified, the term "or" is inclusive in this application. For example, the phrase "A or B" means "A, B, or both A and B". More specifically, the condition "A or B" is satisfied by any of the following conditions: A is true (or exists) and B is false (or does not exist); A is false (or does not exist) and B is true (or exists); or both A and B are true (or exist).

[0027] The first aspect of this application provides a wear-resistant plate, comprising a steel substrate and a surface wear-resistant layer clad on the substrate, wherein the powder raw material of the surface wear-resistant layer comprises, by mass percentage: TiC 30-72%, Cr 4-10%, Ni 5-25%, Mo 0.3-5%, Mn 0.01-1%, Si 0.1-1.0%, B 0.3-1.0%, with the balance being Fe; The powder raw material is spherical with a particle size of 42-150 μm.

[0028] The mass percentage of TiC can be any value or range from 30%, 35%, 40%, 50%, 60%, 70%, and 72%. When the mass percentage of TiC is less than 30%, the content of the hard phase in the wear-resistant layer is insufficient, which will lead to a significant decrease in the wear resistance of the wear-resistant plate and make it difficult to meet the requirements of high wear conditions. When the mass percentage of TiC is higher than 72%, on the one hand, the flowability of the powder will become worse, and problems such as agglomeration and blockage will easily occur during the cladding process, affecting the cladding quality; on the other hand, too much TiC may increase the brittleness of the wear-resistant layer, making it prone to cracking when subjected to impact or vibration, thus reducing the service life of the wear-resistant plate.

[0029] The mass percentage of Cr is any value or range from 4%, 6%, 8%, and 10%. Cr plays an important role in the wear-resistant layer, improving its corrosion resistance and oxidation resistance. An appropriate amount of Cr can form a dense oxide film on the surface of the wear-resistant layer, preventing external media from eroding it. When the Cr content is below 4%, the oxide film formation is insufficient, affecting the corrosion resistance of the wear-resistant layer. Conversely, when the Cr content is above 10%, it increases production costs and may also increase the hardness and brittleness of the wear-resistant layer, negatively impacting the overall performance of the wear-resistant plate.

[0030] The mass percentage of Ni is any value or range from 5%, 8%, 15%, 20%, 22%, to 25%. Ni can improve the toughness and fatigue resistance of the wear-resistant layer. It can refine the grains, improve the microstructure of the wear-resistant layer, and give it better deformation capacity and crack propagation resistance under external forces. When the Ni content is less than 5%, the toughness of the wear-resistant layer is insufficient, and it is prone to cracking and fracture during use. When the Ni content is more than 25%, the hardness of the wear-resistant layer will decrease, affecting the wear resistance and increasing the cost.

[0031] The mass percentage of Mo is any value or range from 0.3%, 1.5%, 3%, 4%, and 5%. Mo can improve the strength and high-temperature performance of the wear-resistant layer. It can form stable carbides, enhancing the hardness and wear resistance of the wear-resistant layer. Simultaneously, Mo can improve the stability of the wear-resistant layer at high temperatures, reducing thermal deformation and thermal fatigue. When the Mo content is below 0.3%, the improvement in wear-resistant layer performance is not significant. When the Mo content is above 5%, it increases the cost of the wear-resistant layer and may lead to a decrease in its toughness.

[0032] The mass percentage of Mn can be any value or range from 0.01%, 0.05%, 0.1%, 0.5%, 0.8%, to 1%. Mn acts as a deoxidizer and desulfurizer, improving the purity of the wear-resistant layer. It can also combine with sulfur to form MnS, reducing the adverse effects of sulfur on the wear-resistant layer's performance. When the Mn content is below 0.01%, the deoxidation and desulfurization effects are poor. When the Mn content is above 1%, it may lead to uneven hardness in the wear-resistant layer, affecting its wear resistance.

[0033] The mass percentage of Si is any value or range from 0.1%, 0.3%, 0.5%, 0.7%, 0.9%, to 1.0%. Si can improve the strength and hardness of the wear-resistant layer. It can form compounds with other elements, enhancing the microstructure of the wear-resistant layer. Simultaneously, Si can also improve the oxidation resistance of the wear-resistant layer. When the Si content is below 0.1%, its effect on improving the performance of the wear-resistant layer is limited. When the Si content is above 1.0%, it increases the brittleness of the wear-resistant layer, reducing its toughness and impact resistance.

[0034] The mass percentage of boron (B) is any value or range from 0.3%, 0.5%, 0.7%, 0.9%, to 1.0%. Boron can improve the hardness and wear resistance of the wear-resistant layer. It can form borides with high hardness, enhancing the wear resistance of the layer. When the B content is below 0.3%, the amount of borides formed is insufficient, and the improvement in wear resistance is not significant. When the B content is above 1.0%, it increases the brittleness of the wear-resistant layer, making it prone to cracking.

[0035] The balance is Fe, which serves as the matrix element, providing the basic strength and toughness of the wear-resistant layer. It works in conjunction with other elements to form a wear-resistant layer with excellent performance. The reasonable component ratio ensures that the wear-resistant plate, while maintaining wear resistance, also possesses good corrosion resistance, toughness, and fatigue resistance, meeting the application needs of various industrial fields.

[0036] In this embodiment, the powder raw material is spherical with a particle size of 42-150 μm. This particle size range offers several advantages. When the particle size is less than 42 μm, the specific surface area of ​​the powder is too large, making it prone to oxidation during the cladding process. This leads to increased impurities in the wear-resistant layer, affecting the performance of the wear-resistant plate. Furthermore, excessively small particle sizes also reduce the powder's flowability, hindering uniform conveying and cladding. Conversely, when the particle size is greater than 150 μm, the powder is difficult to fully melt during the cladding process, easily resulting in incomplete fusion, reducing the bonding strength between the wear-resistant layer and the substrate, and consequently affecting the overall quality and service life of the wear-resistant plate.

[0037] Spherical powder raw materials also exhibit good processability during preparation. During spheroidization, spherical powders are easier to mix uniformly and better maintain the stability of their shape and particle size distribution. This allows for more precise control of cladding parameters in subsequent cladding processes, ensuring consistent quality of the wear-resistant layer.

[0038] Furthermore, the composition design of this wear-resistant plate also considers the synergistic effects between various elements. For example, TiC works in combination with elements such as Cr and Ni to further improve the wear resistance and corrosion resistance of the wear-resistant layer. TiC, as the main wear-resistant phase, provides high hardness and wear resistance, while the oxide film formed by Cr protects the hard phases such as TiC from corrosion, and Ni enhances the toughness of the wear-resistant layer, preventing crack propagation during wear. Si and B also have a synergistic effect; Si increases the strength and hardness of the wear-resistant layer, while B increases its hardness and wear resistance. Together, they significantly improve the performance of the wear-resistant layer. Simultaneously, the deoxidizing and desulfurizing effects of Mn ensure that other elements perform better and reduce the adverse effects of impurities on the wear-resistant layer's performance. Mo, while improving the strength and high-temperature performance of the wear-resistant layer, works synergistically with other elements to ensure that the wear-resistant plate maintains good performance under different temperatures and operating conditions.

[0039] In this embodiment, the wear-resistant plate further includes a transition bonding layer, which is fused between the substrate and the surface wear-resistant layer. The transition bonding layer contains, by mass percentage: Cr 6-9%, Ni 10-15%, Mo 1.0-1.8%, B 0.3-1.0%, with the balance being Fe.

[0040] The Cr content in the transition bonding layer is 6-9%. An appropriate amount of Cr can significantly improve the corrosion resistance and oxidation resistance of the transition bonding layer. During the cladding process and in the actual use of the wear-resistant plate, Cr promotes the formation of a dense oxide film on the surface of the transition bonding layer. This oxide film acts as a strong barrier, effectively preventing external corrosive media from eroding the transition bonding layer and internal structure, thereby extending the service life of the wear-resistant plate. When the Cr content is below 6%, the oxide film formation is not complete and dense enough to provide sufficient protection; while when the Cr content is above 9%, it increases material costs and may lead to increased hardness and brittleness of the transition bonding layer, affecting its bonding performance with the steel substrate and the surface wear-resistant layer.

[0041] Ni, comprising 10-15% by mass, plays a crucial role in improving the toughness and fatigue resistance of the transition bonding layer. It refines the grain structure of the transition bonding layer, giving it better deformation capacity and crack propagation resistance under external impact or repeated fatigue loads. When the Ni content is below 10%, the transition bonding layer lacks toughness and is prone to cracking and fracture during use; when the Ni content is above 15%, it reduces the hardness of the transition bonding layer, affecting its support for the surface wear-resistant layer and increasing costs.

[0042] The mass percentage of molybdenum (Mo) is 1.0-1.8%. Mo can improve the strength and high-temperature performance of the transition bonding layer. During the cladding process and when the wear-resistant plate operates in high-temperature environments, Mo can form stable carbides, enhancing the hardness and wear resistance of the transition bonding layer. Simultaneously, Mo can also improve the stability of the transition bonding layer at high temperatures, reducing thermal deformation and thermal fatigue. When the Mo content is below 1.0%, the improvement in the performance of the transition bonding layer is not significant; when the Mo content is above 1.8%, it increases the cost of the transition bonding layer and may lead to a decrease in its toughness.

[0043] The mass percentage of boron (B) is 0.3-1.0%. B can improve the hardness and wear resistance of the transition bonding layer. It can form borides with high hardness, enhancing the wear resistance of the transition bonding layer. When the B content is below 0.3%, the amount of borides formed is insufficient, and the improvement in wear resistance is not significant; when the B content is above 1.0%, it increases the brittleness of the transition bonding layer, making it prone to cracking.

[0044] The balance element is Fe, which serves as the matrix element, providing basic strength and toughness for the transition bonding layer. It works in conjunction with elements such as Cr, Ni, Mo, and B to form a transition bonding layer with excellent performance. The rational composition ratio of the transition bonding layer effectively alleviates thermal and structural stresses between the steel substrate and the surface wear-resistant layer, improving the bonding strength between the wear-resistant layer and the substrate, thereby ensuring the stable performance of the wear-resistant plate under complex working conditions. In practical applications, this transition bonding layer design can significantly improve the overall performance and service life of the wear-resistant plate, meeting the stringent requirements of different industrial sectors for wear-resistant materials.

[0045] In this embodiment, the thickness ratio of the transition bonding layer to the surface wear-resistant layer is 1:1.5-2.5. When the thickness ratio of the transition bonding layer to the surface wear-resistant layer is less than 1:1.5, the transition bonding layer is relatively too thick, which may lead to uneven hardness distribution in the wear-resistant plate. An excessively thick transition bonding layer will, to some extent, weaken the dominant wear-resistant effect of the surface wear-resistant layer, preventing the wear-resistant plate from fully utilizing its wear resistance under high-wear conditions. Furthermore, an excessively thick transition bonding layer increases material costs and preparation time, reducing production efficiency.

[0046] An embodiment of the second aspect of this application provides a method for preparing the wear-resistant plate, comprising the following steps: S1: Mix the powders of the transition bonding layer and the surface wear-resistant layer separately; S2: Surface pretreatment of the steel substrate; S3: The steel substrate is sequentially coated with a transition bonding layer and a surface wear-resistant layer; S4: After the cladding is completed and cooled, micro-pits are constructed on the surface wear-resistant layer, and solid lubricant is filled in and sintered.

[0047] In this embodiment, the wear-resistant layer powder in step S1 is mixed using a powder mixer at a speed of 250-280 rpm under argon protection for 6-8 hours. Subsequently, an airflow vortex spheroidizer is used for spheroidization treatment at a compressed air pressure of 0.20-0.30 MPa and a temperature of 2000-2800℃ for 40-50 minutes, resulting in spherical or pebble-like powder. This step is crucial for preventing TiC flotation, as TiC is lightweight and prone to flotation during cladding without proper treatment, leading to uneven composition of the wear-resistant layer and affecting its wear resistance. Argon, as an inert gas, prevents oxidation of the powder during mixing, ensuring its purity. A suitable speed (250-280 rpm) ensures thorough and uniform mixing of various powder raw materials, laying a good foundation for the subsequent cladding process. Subsequently, a spheroidizing process is performed using an airflow vortex spheroidizing machine. Under specific compressed air pressure (0.20-0.30 MPa) and temperature (2000-2800℃) for 40-50 minutes, the powder can be shaped into spherical or pebble-like forms. This spherical or pebble-like powder exhibits better flowability and uniformity during the cladding process, allowing TiC to be more evenly distributed within the wear-resistant layer and effectively preventing TiC from floating to the surface.

[0048] In another preferred embodiment, the transition bonding layer powder is mixed using a planetary ball mill with a ball-to-powder ratio of 8-10:1 and a mixing speed of 250-280 rpm for 6-8 h under argon protection; subsequently, it is spheroidized for 40-50 min using an airflow vortex ball mill at a compressed air pressure of 0.20-0.30 MPa and a temperature of 2000-2800℃, resulting in a powder that is spherical or pebble-shaped.

[0049] In this embodiment, step S2 involves sandblasting the steel substrate to a surface roughness Ra of 6.3-12.5 μm, followed by ultrasonic cleaning with acetone at 40-50°C for 15-20 minutes. This step removes impurities, oil, and scale from the steel substrate surface, improving its cleanliness and roughness. A suitable surface roughness (Ra 6.3-12.5 μm) increases the mechanical interlocking between the cladding layer and the substrate, enhancing the bonding strength. Acetone ultrasonic cleaning utilizes the cavitation effect of ultrasound to more thoroughly remove minute impurities and oil from the substrate surface. Cleaning at 40-50°C for 15-20 minutes achieves optimal cleaning results. The cleaner steel substrate surface facilitates the subsequent cladding of the transition bonding layer and the surface wear-resistant layer, ensuring a strong metallurgical bond between the cladding layer and the substrate.

[0050] In this embodiment, plasma cladding includes steps such as substrate preheating, transition layer cladding, and wear-resistant layer cladding. The steel substrate is preheated to 280-320°C before the transition layer cladding. The transition layer cladding is performed using a plasma arc (transfer arc mode) under a protective atmosphere of Ar gas and 2-4% N2. The plasma cladding current is 320-430 A, the voltage is 28-32 V, the scanning speed is 3.5-4.0 mm / s, and the powder feed rate is 25-30 g / min.

[0051] Furthermore, the surface wear-resistant layer is clad after the interlayer temperature of the transition bonding layer has cooled to 150-180°C to prevent overheating and delamination. The surface wear-resistant layer is clad in a plasma arc non-transfer arc mode under a pure Ar atmosphere with a current of 340-360 A, a voltage of 25-28 V, a scanning speed of 5.0-6.0 mm / s, and a powder feed rate of 20-25 g / min.

[0052] This step is a crucial stage in the preparation of wear-resistant plates. Precise control of the cladding parameters ensures the quality of both the transition bonding layer and the surface wear-resistant layer. Preheating the steel substrate before cladding the transition bonding layer effectively reduces thermal stress during the cladding process and prevents cracking. The preheating temperature is controlled between 280-320℃, ensuring sufficient temperature for good bonding between the cladding layer and the substrate without causing a degradation in substrate performance due to excessive temperature. Plasma arc (transfer arc mode) cladding is used in the transition layer, conducted under the protective gas Ar and an atmosphere of 2-4% N2. Ar, as an inert gas, prevents metal oxidation during cladding, while an appropriate amount of N2 reacts with the metal elements, further improving the hardness and wear resistance of the transition bonding layer.

[0053] In this embodiment, the micro-pit construction in step S4 involves shot peening the surface wear-resistant layer with ceramic pellets of 0.2-0.6 mm in diameter. The ceramic pellets have a hardness higher than the surface hardness of the wear-resistant layer, such as silicon carbide or zirconia ceramic pellets. The shot peening pressure is 0.4-0.6 MPa; the peening angle is 70°-90°; and the coverage is ≥150%, ensuring that uniformly distributed micro-pits are formed on the surface. Ultimately, micro-pits with a depth of 10-30 μm and a random distribution are formed on the surface (serving as lubricant storage pools), while simultaneously introducing residual compressive stress into the surface layer.

[0054] The solid lubricant is a composite lubricant composed of 5% graphene and 95% molybdenum disulfide. The solid lubricant is dispersed in a volatile organic solvent (such as anhydrous ethanol or acetone) to prepare a suspension with a concentration of 1-5 wt%, and ultrasonically dispersed for 30 minutes to prevent agglomeration. The wear-resistant plate, treated with S4, is completely immersed in the suspension and subjected to ultrasonic vibration (power 400-600 W, frequency 20-40 kHz) for 20-40 minutes. Utilizing the cavitation effect and micro-jets of the ultrasound, the lubricant particles are forcibly pushed into the depths of the micro-pits formed by shot peening. The workpiece is then removed and sintered at 80-120℃ for 1-1.5 hours to allow the solvent to evaporate, and the lubricant to firmly adhere to the micro-pits, forming a self-lubricating surface.

[0055] A composite lubricant composed of 5% graphene and 95% molybdenum disulfide is used, fully leveraging the advantages of both materials. Graphene possesses excellent lubrication properties and high chemical stability, forming a lubricating film on the friction surface and reducing the coefficient of friction; molybdenum disulfide exhibits superior friction-reducing and anti-wear properties, maintaining good lubrication even under high temperature and pressure. The combined use of these two materials provides stable lubrication performance under various working conditions. This self-lubricating surface allows the wear-resistant plate to automatically replenish lubricant during operation, reducing the need for external lubrication and improving the efficiency and reliability of the wear-resistant plate.

[0056] A third aspect of this application provides the application of the aforementioned wear-resistant plate in concrete pump truck spectacle plates, cutting rings, crushers, and shredders.

[0057] In practical applications, this wear-resistant plate performs exceptionally well in spectacle plates and cutting rings of concrete pump trucks. During operation, spectacle plates and cutting rings in concrete pump trucks must withstand high-pressure, high-wear environments. This wear-resistant plate, with its superior wear and corrosion resistance, effectively reduces wear and corrosion, extends service life, and lowers equipment maintenance costs and replacement frequency. Furthermore, due to its relatively low cost, it can save companies significant production costs while ensuring performance, thereby improving economic efficiency.

[0058] Example The following examples describe the disclosure of this invention in more detail. These examples are merely illustrative, as various modifications and variations will be apparent to those skilled in the art within the scope of this disclosure. Unless otherwise stated, all parts, percentages, and ratios reported in the following examples are based on weight. Unless otherwise stated, all reagents used in the examples are available commercially or synthesized using conventional methods and are ready for use without further processing. Unless otherwise stated, all instruments used in the examples are available commercially.

[0059] Example 1 A type of wear-resistant plate, see Figure 1 The material includes a steel substrate and a wear-resistant surface layer clad on the substrate. The powder raw material of the wear-resistant surface layer contains, by mass percentage: TiC 60%, Cr 6%, Ni 8%, Mo 0.8%, Mn 0.05%, Si 0.6%, B 0.8%, with the balance being Fe. The powder raw material is spherical with a particle size of 50 μm.

[0060] The method for preparing the wear-resistant plate includes the following steps: S1: The surface wear-resistant layer powder is mixed at a speed of 260 rpm for 6 hours under argon protection; then, it is spheroidized for 45 minutes using an airflow vortex spheroidizer at a compressed air pressure of 0.25 MPa and a temperature of 2500℃, and the resulting powder is spherical or pebble-shaped. S2: The steel substrate is pretreated by sandblasting to a surface roughness Ra of 9.5μm, followed by ultrasonic cleaning with acetone at 40℃ for 15 min. S3: Preheat the steel substrate to 300℃; in plasma arc non-transfer arc mode, under pure Ar atmosphere, with a current of 350 A, a voltage of 25V, a scanning speed of 5.0 mm / s, and a powder feed rate of 20 g / min, clad the wear-resistant layer on the surface.

[0061] S4: The surface wear-resistant layer is shot-peened with ceramic pellets with a diameter of 0.4 mm at a pressure of 0.5 MPa and a blasting angle of 80°. The coverage is ≥150%, ensuring that the surface forms uniformly distributed micro-pits. A composite lubricant consisting of 5% graphene and 95% molybdenum disulfide is used for filling, and the surface is sintered at 120°C for 1 hour to form a self-lubricating surface.

[0062] Example 2 A wear-resistant plate includes a steel substrate and a transition bonding layer and a surface wear-resistant layer clad on the substrate. The powder raw material of the surface wear-resistant layer comprises, by mass percentage: TiC 60%, Cr 6%, Ni 8%, Mo 0.8%, Mn 0.05%, Si 0.6%, B 0.8%, with the balance being Fe. The powder raw material of the transition bonding layer comprises, by mass percentage: Cr 7%, Ni 12%, Mo 1.5%, B 0.7%, with the balance being Fe. The powder raw material is spherical with a particle size of 50 μm.

[0063] The method for preparing the wear-resistant plate includes the following steps: S1: The transition bonding layer and the surface wear-resistant layer powders were mixed separately at a speed of 260 rpm for 6 hours under argon protection; then, an airflow vortex spheroidizer was used to spheroidize the powders for 45 minutes at a compressed air pressure of 0.25 MPa and a temperature of 2500℃, resulting in spheroid-shaped or pebble-shaped powders. S2: The steel substrate is pretreated by sandblasting to a surface roughness Ra of 9.5μm, followed by ultrasonic cleaning with acetone at 40℃ for 15min. S3: Preheat the steel substrate to 300℃; use plasma arc (transfer arc mode) in a protective atmosphere of Ar and 3% N2; plasma cladding current is 380 A, voltage is 30 V, scanning speed is 3.5 mm / s, and powder feed rate is 25 g / min to clad the transition bonding layer; use plasma arc non-transfer arc mode in a pure Ar atmosphere, with current of 350 A, voltage of 25 V, scanning speed of 5.0 mm / s, and powder feed rate of 20 g / min to clad the surface wear-resistant layer. S4: The surface wear-resistant layer is shot-peened with ceramic pellets with a diameter of 0.3 mm at a pressure of 0.5 MPa and a blasting angle of 80°. The coverage is ≥150% to ensure that the surface forms uniformly distributed micro-pits. A composite lubricant consisting of 5% graphene and 95% molybdenum disulfide is used for filling, and the surface is sintered at 120°C for 1 hour to form a self-lubricating surface.

[0064] Example 3 This embodiment is basically the same as Embodiment 2, except that: the powder raw material of the surface wear-resistant layer contains, by mass percentage: TiC 65%, Cr 5%, Ni 6%, Mo 0.5%, Mn 0.15%, Si 0.4%, B 0.6%, with the balance being Fe; the powder raw material of the transition bonding layer contains, by mass percentage: Cr 6%, Ni 15%, Mo 1.8%, B 1.0%, with the balance being Fe.

[0065] Example 4 This embodiment is basically the same as embodiment 2, except that: in step S3, the steel substrate is preheated to 280°C; a plasma arc (transfer arc mode) is used, and the process is carried out in a protective atmosphere of Ar and 2% N2; the plasma cladding current is 320-430A, the voltage is 32V, the scanning speed is 4.0 mm / s, and the powder feeding rate is 28 g / min for cladding the transition bonding layer.

[0066] Example 5 This embodiment is basically the same as embodiment 2, except that: step S3 adopts the plasma arc non-transfer arc mode, and the wear-resistant layer on the surface is clad under a pure Ar atmosphere with a current of 350 A, a voltage of 28 V, a scanning speed of 6.0 mm / s, and a powder feeding rate of 22 g / min.

[0067] Comparative Example 1 This comparative example is basically the same as Example 2, except that the protective atmosphere does not contain N2 when cladding the transition bonding layer in step S3.

[0068] Comparative Example 2 This comparative example is basically the same as Example 2, except that: the surface wear-resistant layer contains 0.02% Si and 0.06% B.

[0069] Comparative Example 3 This comparative example is basically the same as Example 2, except that the particle size of the powder fragmentation layer of the transition bonding layer and the surface wear-resistant layer is 50μm and does not have a spherical structure.

[0070] Experimental Case The wear-resistant plates of Examples 1-5 and Comparative Examples 1-3 were subjected to performance tests, and the results are shown in Table 1.

[0071]

[0072] As shown in Table 1, Example 2 exhibits superior performance across various indicators. Its transition bonding layer hardness reaches 83.9 HRA, the surface wear-resistant layer hardness is as high as 86.1 HRA, and the bonding strength is 3320 MPa. This indicates that the use of a double-layer cladding structure (transition bonding layer and surface wear-resistant layer), along with reasonable powder raw material ratios and precise control of cladding parameters, can significantly improve the overall performance of the wear-resistant plate during its preparation. Compared to Example 2, Example 1 is a single-layer cladding, with a surface wear-resistant layer hardness of 81.3 HRA and a bonding strength of 2350 MPa, showing relatively weaker performance. This demonstrates the crucial role of the double-layer cladding structure in improving the performance of the wear-resistant plate. This may be because the presence of the transition bonding layer enhances the bonding force between the surface wear-resistant layer and the substrate, allowing for a more uniform stress distribution, reducing crack generation and propagation, and thus improving the overall performance of the wear-resistant plate. Furthermore, the nitride hard phase in the transition bonding layer further enhances hardness and wear resistance, providing better support and protection for the surface wear-resistant layer.

[0073] In Comparative Example 1, the protective atmosphere lacked N2 during the cladding of the transition bonding layer, resulting in the failure to form a Ti(C,N) hard phase. Consequently, the hardness of the transition bonding layer was only 80.1 HRA, and the bonding strength was significantly reduced. This demonstrates that an appropriate amount of N2 plays a crucial role in forming a hard phase and improving the performance of the transition bonding layer. In Comparative Example 2, the insufficient Si and B content in the surface wear-resistant layer and the insufficient melt viscosity exacerbated TiC flotation, leading to a significant 40% decrease in wear resistance. This highlights the importance of Si and B in regulating melt properties and stabilizing TiC distribution to ensure wear resistance. In Comparative Example 3, the powder in the transition bonding layer and surface wear-resistant layer was not spherical, resulting in irregular powder with poor flowability, high cladding porosity, and decreased hardness. This indicates that the spherical structure of the powder is crucial for improving flowability, reducing porosity, and enhancing hardness and performance.

[0074] The friction and wear coefficients in the table above show that the wear-resistant plates of each embodiment and comparative example exhibit different wear resistance under different conditions. The friction and wear coefficient of Example 2 is 0.35, the lowest among all tested samples, which again demonstrates the advantages brought by its double-layer cladding structure, reasonable powder raw material ratio, and precise control of cladding parameters. These factors work together to enable the wear-resistant plate to better resist wear and reduce energy loss during friction. The friction and wear coefficients of Examples 1, 3, 4, and 5 are between 0.36 and 0.37, slightly higher than Example 2, but still showing better wear resistance compared to the comparative example. In contrast, in Comparative Example 1, because the protective atmosphere during the cladding transition layer did not contain N2, the Ti(C,N) hard phase could not be formed, leading to a decrease in the performance of the transition layer and an increase in the friction and wear coefficient to 0.39. In Comparative Example 2, the insufficient Si and B content in the surface wear-resistant layer intensified the TiC flotation, reducing wear resistance and resulting in a friction and wear coefficient of 0.38. Comparative Example 3 has the worst wear resistance because the transition bonding layer and surface wear-resistant layer powder do not have a spherical structure, have poor flowability and high cladding porosity, resulting in decreased hardness and a friction wear coefficient as high as 0.40, which is the highest among all samples.

[0075] In summary, by optimizing the structural design of the wear-resistant plate, adopting a double-layer cladding structure, precisely controlling the proportion of powder raw materials and cladding process parameters, and ensuring the spherical structure of the powder, the overall performance of the wear-resistant plate, such as hardness, bonding strength, and wear resistance, can be significantly improved. This makes it more suitable for harsh working conditions such as spectacle plates for concrete pump trucks and cutting rings, extending equipment service life, reducing costs, and improving economic efficiency.

[0076] It should be noted that this application is not limited to the above-described embodiments. The above embodiments are merely examples, and any embodiments with the same structure and effect as the technical concept within the scope of this application are included in the technical scope of this application. Furthermore, various modifications that can be conceived by those skilled in the art to the embodiments, and other ways of constructing by combining some of the constituent elements of the embodiments, without departing from the spirit of this application, are also included in the scope of this application.

Claims

1. A wear-resistant plate, characterized in that, It includes a steel substrate and a surface wear-resistant layer clad on the substrate. The powder raw materials of the surface wear-resistant layer contain, by mass percentage: TiC 30-72%, Cr 4-10%, Ni 5-25%, Mo 0.3-5%, Mn 0.01-1%, Si 0.1-1.0%, B 0.3-1.0%, with the balance being Fe. The powder raw material is spherical with a particle size of 42-150 μm.

2. The wear-resistant plate according to claim 1, characterized in that, It also includes a transition bonding layer, which is clad between the substrate and the surface wear-resistant layer. The transition bonding layer contains, by mass percentage: Cr 6-9%, Ni 10-15%, Mo 1.0-1.8%, B 0.3-1.0%, with the balance being Fe.

3. The wear-resistant plate according to claim 2, characterized in that, The thickness ratio of the transition bonding layer to the surface wear-resistant layer is 1:1.5-2.

5.

4. A method for preparing a wear-resistant plate according to any one of claims 1-3, characterized in that, Includes the following steps: S1: Mix the powders of the transition bonding layer and the surface wear-resistant layer separately; S2: Surface pretreatment of the steel substrate; S3: The steel substrate is sequentially coated with a transition bonding layer and a surface wear-resistant layer; S4: After the cladding is completed and cooled, micro-pits are constructed on the surface wear-resistant layer, and solid lubricant is filled in and sintered.

5. The method for preparing the wear-resistant plate according to claim 4, characterized in that, After mixing for 6-8 hours in step S1, the powder is spheroidized for 40-50 minutes at a compressed air pressure of 0.20-0.30 MPa and a temperature of 2000-2800℃ to obtain spheroidal powder.

6. The method for preparing the wear-resistant plate according to claim 4, characterized in that, Step S2 involves sandblasting the steel substrate to a surface roughness Ra of 6.3-12.5 μm and then ultrasonically cleaning it.

7. The method for preparing the wear-resistant plate according to claim 4, characterized in that, Step S3 involves preheating the steel substrate to 280-320°C during the cladding of the transition bonding layer, and performing the process under a protective atmosphere of Ar and 2-4% N2; and / or The plasma cladding uses a current of 320-430 A and / or a voltage of 28-32 V and / or a scanning speed of 3.5-4.0 mm / s.

8. The method for preparing the wear-resistant plate according to claim 7, characterized in that, Step S3, surface wear-resistant layer cladding, involves cladding the surface wear-resistant layer in a pure Ar atmosphere after the interlayer temperature of the transition bonding layer has cooled to 150-180°C, using a current of 340-360 A and / or a voltage of 25-28 V and / or a scanning speed of 5.0-6.0 mm / s.

9. The method for preparing the wear-resistant plate according to claim 4, characterized in that, The micro-pit construction in step S4 involves shot peening the surface wear-resistant layer with shot at a pressure of 0.4-0.6 MPa; and / or the solid lubricant is graphene and / or molybdenum disulfide.

10. The application of a wear-resistant plate as described in any one of claims 1-3 in a concrete pump truck spectacle plate, a cutting ring, a crusher, or a shredder.

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