High-temperature wear-resistant high-entropy alloy with cross-submicron-micron composite in-situ precipitation reinforced phase and preparation method of high-temperature wear-resistant high-entropy alloy

Abstract

The invention provides a high-temperature wear-resistant high-entropy alloy with a cross-submicron-micron composite in-situ precipitation reinforced phase and a preparation method of the high-temperature wear-resistant high-entropy alloy, and relates to the technical field of alloy materials. According to the atomic ratio, the high-temperature wear-resistant high-entropy alloy is composed of 50-95% of M and 5-50% of R, M is 0.2% of Al, 1.5% of Co, 1.5% of CrFeNi, 0.5% of Ti or 0.4% of Al, 1.8% of Co, and 0.01% of CrFeNiY; r is 0.05 to 0.50 percent of Si, 0.35 to 0.85 percent of B, 10 to 0.60 percent of M, 0.20 to 0.80 percent of B or 10 to 0.60 percent of M, 0.10 to 0.60 percent of M, 0.20 to 0.80 percent of B, and M1 and M2 are Nb, W, Zr, V or Mo. According to the invention, dissimilar nonmetal or metal-nonmetal is introduced into the face-centered cubic high-entropy alloy, a cross-submicron-micron composite in-situ precipitation reinforced phase is constructed, and the high-temperature wear-resistant high-entropy alloy with outstanding mechanical and high-temperature wear resistance is obtained.

Description

Technical Field

[0001] This invention relates to the field of alloy materials technology, and in particular to a high-temperature wear-resistant high-entropy alloy with a trans-submicron-micron composite in-situ precipitated reinforcing phase and its preparation method. Background Technology

[0002] High-temperature wear is a major cause of failure in high-temperature moving and load-bearing components such as spherical bearings, seals, reactor control rod drive mechanisms, and high-temperature valves. Furthermore, with the development of science and technology, the requirements for service life, stability, and energy efficiency of moving / transmission components in mechanical systems are increasingly stringent in the aerospace, nuclear energy, and marine industries. Conventional high-temperature wear-resistant metal materials, such as iron-based alloys (e.g., hot-work die steel, high-speed steel, and heat-resistant and wear-resistant steel) and nickel-based alloys, are insufficient to meet the demands of high-end equipment such as aero-engines, gas turbines, and nuclear reactor systems for high-temperature wear-resistant moving components due to the mismatch between their strength / ductility and high-temperature wear resistance. Therefore, the development of new high-temperature wear-resistant metal materials is urgently needed. Summary of the Invention

[0003] In view of this, the purpose of this invention is to provide a high-temperature wear-resistant high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase and a method for preparing the same. The high-temperature wear-resistant high-entropy alloy provided by this invention possesses both good strength and plasticity and excellent high-temperature wear resistance.

[0004] To achieve the above-mentioned objectives, the present invention provides the following technical solution: This invention provides a high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase. The chemical composition of this high-temperature wear-resistant, high-entropy alloy, based on atomic ratio, is M. 50~95 R 5~50 Where M is Al 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 Or Al 0.4 Co 1.8 CrFeNiY 0.01 R is Si with non-equiatomic ratio 0.05~0.50 B 0.35~0.85 M1 0.10~0.60 B 0.20~0.80 Or M1 0.10~0.60 M2 0.10~0.60 B 0.20~0.80 M1 and M2 are Nb, W, Zr, V or Mo, and M1 and M2 are not the same.

[0005] Preferably, R is Si 0.1 B 0.75 、Nb 0.33 B 0.67 Mo 0.2W 0.1 B 0.5 or Zr 0.2 V 0.55 B 0.3 .

[0006] Preferably, the in-situ precipitated phase of the high-temperature wear-resistant high-entropy alloy includes submicron grains with a size of 100 nm to 1 μm and micron-sized grains with a size of 1 to 300 μm.

[0007] This invention provides a method for preparing the high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase as described in the above technical solution, comprising the following steps: According to the chemical composition of the high-temperature wear-resistant high-entropy alloy with the cross-submicron-micron composite in-situ precipitated reinforcing phase, the raw materials corresponding to each element are vacuum arc melted to obtain the high-temperature wear-resistant high-entropy alloy with the cross-submicron-micron composite in-situ precipitated reinforcing phase. The vacuum arc melting process is repeated 8 to 15 times. After each melting, the resulting high-entropy alloy melt is cooled and solidified in a water-cooled copper crucible. Except for the last melting, when the cooling water flow rate is 2.4 to 3.5 L / min and the temperature is 30 to 40°C, the cooling water flow rate is 16 to 24 L / min and the temperature is 12 to 15°C.

[0008] Preferably, the purity of each raw material is ≥99.9wt%.

[0009] Preferably, after the ingredients are mixed, the raw materials are placed in a water-cooled copper crucible in the order of non-refractory metal raw materials, non-metallic raw materials, and refractory metal raw materials from bottom to top, and then vacuum arc melting is carried out.

[0010] Preferably, the vacuum arc melting is carried out in an argon atmosphere at 0.06 MPa.

[0011] Preferably, the voltage of the vacuum arc melting is 20~80 V and the current is 500~850 A.

[0012] Preferably, the melting time for a single melting session is 3 to 5 minutes.

[0013] Preferably, during the vacuum arc melting process, the first two meltings are carried out without stirring, and the subsequent meltings are carried out under electromagnetic stirring conditions; after each melting is completed, the cooled and solidified ingot is flipped over before the next melting is carried out.

[0014] This invention provides a high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase. The chemical composition of this high-temperature wear-resistant, high-entropy alloy, based on atomic ratio, is M.50~95 R 5~50 Where M is Al 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 Or Al 0.4 Co 1.8 CrFeNiY 0.01 R is Si with non-equiatomic ratio 0.05~0.50 B 0.35~0.85 M1 0.10~0.60 B 0.20~0.80 Or M1 0.10~0.60 M2 0.10~0.60 B 0.20~0.80 M1 and M2 are Nb, W, Zr, V, or Mo, and M1 and M2 are not the same. Compared with the prior art, the present invention has the following beneficial effects: In this invention, M represents the matrix phase. By adjusting the elemental ratio, this invention achieves Al with high mixing entropy, low mixing enthalpy, large atomic radius difference, and predominantly FCC phase, exhibiting non-equiatomic ratios. 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 Or Al 0.4 Co 1.8 CrFeNiY 0.01 High-entropy alloy matrix has good high-temperature stability in structure and high plasticity and toughness in performance; In this invention, R refers to the component that promotes the formation of in-situ precipitated reinforcing phases across submicron-micron composites. This invention introduces an in-situ precipitated reinforcing phase nucleation system Si into a face-centered cubic high-entropy alloy matrix. 0.05~0.50 B 0.35~0.85 M1 0.10~ 0.60 B 0.20~0.80 Or M1 0.10~0.60 M2 0.10~0.60 B 0.20~0.80 (M1 and M2 are Nb, W, Zr, V or Mo), which induces active metal elements and non-metal elements in the high-entropy alloy to form a trans-submicron-micron composite in-situ precipitation reinforcement phase structure through in-situ chemical reaction during the liquid phase diffusion process, improves high-temperature wear resistance, and obtains a high-temperature wear-resistant high-entropy alloy with a good balance of strength, plasticity and high-temperature wear resistance. The B element introduced into the alloy in this invention also has the effect of stabilizing and cleaning grain boundaries, reducing residual stress at the interface, improving the bonding strength between the in-situ precipitated reinforcing phase and the high-entropy alloy matrix, inhibiting the pull-out and shedding of the in-situ precipitated phase during friction, and enhancing the high-temperature resistance to abrasive wear.

[0015] This invention provides a method for preparing high-temperature wear-resistant high-entropy alloys with submicron-micron composite in-situ precipitated reinforcing phases as described in the above technical solutions. By utilizing the in-situ chemical reactions of each raw material and coordinating the control of cooling and solidification rates, the nucleation sequence and growth rate of the in-situ precipitated reinforcing phases are controlled, achieving controllable construction of the composite in-situ precipitated reinforcing phase structure across the submicron-micron scale in the high-entropy alloy. Furthermore, the preparation method provided by this invention is simple, has high production efficiency, and offers precise and controllable composition.

[0016] The results of the examples show that the high-entropy alloy with in-situ precipitated reinforcing phases across submicron and micron composites provided by the present invention possesses both strong plasticity and high-temperature wear resistance. Its compressive yield strength at 25℃ is ≥1600 MPa, its compressive strength at 25℃ is ≥2000 MPa, and its engineering strain at 25℃ is ≥10%; its hardness at 25℃ is ≥700 HV, and its hardness at 800℃ is ≥500 HV; the wear rate at 25~600℃ remains at 10%. -5 mm 3 ·N -1 ·m -1 The wear rate at 800℃ is 10. -7 ~10 -6 mm 3 ·N -1 ·m -1 . Attached Figure Description

[0017] Figure 1 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 XRD diffraction pattern of a high-entropy alloy; Figure 2 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 Electron backscattering diagrams and elemental surface distribution diagrams of the microstructure of high-entropy alloys. Figure 2 In the diagram, (a) and (b) correspond to electron backscattering patterns, and (c) corresponds to the elemental surface distribution pattern. Figure 3 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 )50 (Si 0.1 B 0.75 ) 50 EBSD phase distribution diagram of high-entropy alloys; Figure 4 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 Typical compressive stress-strain curves of high-entropy alloys; Figure 5 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 Vickers hardness of high-entropy alloys at 25~800℃; Figure 6 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 Average wear rate of high-entropy alloys at 25~800℃; Figure 7 (Al) prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 XRD diffraction pattern of a high-entropy alloy; Figure 8 (Al) prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 Electron backscattering diagram and elemental surface distribution diagram of the microstructure of high-entropy alloys; Figure 8 In the diagram, (a) and (b) correspond to electron backscattering patterns, and (c) corresponds to the elemental surface distribution pattern. Figure 9 (Al) prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 Typical compressive stress-strain curves of high-entropy alloys; Figure 10 (Al) prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 Vickers hardness of high-entropy alloys at 25~800℃; Figure 11 (Al) prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 Average wear rate of high-entropy alloys at 25~800℃. Detailed Implementation

[0018] This invention provides a high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase. The chemical composition of the high-temperature wear-resistant, high-entropy alloy, based on atomic ratio, is M. 50~95 R 5~50 Where M is Al 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 Or Al 0.4 Co 1.8 CrFeNiY 0.01 R is Si with non-equiatomic ratio 0.05~0.50 B 0.35~0.85 M1 0.10~0.60 B 0.20~0.80 Or M1 0.10~0.60 M2 0.10~0.60 B 0.20~0.80 M1 and M2 are Nb, W, Zr, V or Mo, and M1 and M2 are not the same.

[0019] In this invention, the M 50~95 R 5~50 M is preferred 50~82 R 18~50It can be M 50 R 50 M 58 R 42 M 64 R 36 Or M 82 R 18 .

[0020] In this invention, M is the matrix phase, which is a non-equiatomic high-entropy alloy dominated by the FCC phase.

[0021] In this invention, R is a component that promotes the formation of a trans-submicron-micron composite in-situ precipitated reinforcing phase. In this invention, Si... 0.05~0.50 B 0.35~0.85 It can be Si 0.1~0.50 B 0.55~0.75 Specifically, it can be Si 0.1 B 0.75 The M1 0.10~0.60 B 0.20~0.80 It can be M1 0.30~0.50 B 0.50~0.70 Specifically, it can be M1 0.33 B 0.67 Furthermore, it can be used for Nb 0.33 B 0.67 In this invention, M1 0.10~0.60 M2 0.10~0.60 B 0.20~0.80 (All B elements above are boron) can be M1 0.20~0.30 M2 0.10~0.55 B 0.30~0.50 Specifically, it can be M1 0.20 M2 0.10 B 0.50 Or M1 0.20 M2 0.55 B 0.3 Furthermore, it can be used for Mo 0.2 W 0.1 B 0.5 or Zr 0.2 V 0.55 B 0.3 .

[0022] In this embodiment of the invention, the chemical composition of the high-temperature wear-resistant high-entropy alloy is (Al 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 、(Al 0.2 Co 1.5 CrFeNi 1.5Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 、(Al 0.4 Co 1.8 CrFeNiY 0.01 ) 58 (Mo 0.2 W 0.1 B 0.5 ) 42 or (Al) 0.4 Co 1.8 CrFeNiY 0.01 ) 64 (Zr 0.2 V 0.55 B 0.3 ) 36 .

[0023] In this invention, the in-situ precipitated phase of the high-temperature wear-resistant high-entropy alloy includes submicron grains with a size of 100 nm to 1 μm and micron-sized grains with a size of 1 to 300 μm.

[0024] Compared to conventional metallic materials, face-centered cubic (FCC) high-entropy alloys exhibit unique high-entropy effects, lattice distortion effects, and hysteresis diffusion effects, making them prone to forming simple solid solution structures rather than conventional intermetallic compounds. This results in excellent high-temperature stability, mechanical properties, oxidation resistance, and wear resistance. Furthermore, by controlling the composition and preparation process of high-entropy alloys, constructing multi-scale structures can effectively address the mismatch between the strength and ductility and high-temperature wear resistance of conventional metallic wear-resistant materials. Currently, through chemical composition design, thermomechanical treatment, and laser remelting techniques, various multi-scale structures have been designed in FCC high-entropy alloys: medium / short-range ordered structures, multi-scale grain structures, multi-scale precipitate structures, and multi-scale grain / precipitate composite structures. Among them, the cross-scale precipitate structure is an effective mechanism to improve the high-temperature wear resistance of alloys. The cross-scale precipitate structure effectively hinders dislocation movement, thereby greatly improving the high-temperature strength, high-temperature hardness and high-temperature wear resistance of the alloy. At the same time, the deformation mechanism of twinning and stacking faults generated in the FCC matrix enhances the work hardening ability of the alloy and reduces high-temperature abrasive wear. In addition, there is a large back stress between adjacent precipitate structures of different scales, which can induce hardening on the wear surface and subsurface, thereby further increasing the work hardening rate of the alloy wear surface and thus obtaining high wear resistance.

[0025] This invention is based on the design concept of improving high-temperature wear resistance through a cross-submicron-micron composite in-situ precipitated reinforcing phase structure. By introducing dissimilar nonmetals or metal-nonmetal elements into a face-centered cubic high-entropy alloy and utilizing in-situ chemical reactions, a cross-submicron-micron composite in-situ precipitated reinforcing phase structure is constructed. This results in a high-temperature wear-resistant high-entropy alloy with a cross-submicron-micron composite in-situ precipitated reinforcing phase structure that matches both strength and high-temperature wear resistance. The in-situ precipitated phase consists of submicron grains with a size of 100 nm to 1 μm and micron-sized grains with a size of 1 to 300 μm. The size and type of the cross-scale in-situ precipitated phase exhibit a random distribution, thereby obtaining a dense high-entropy alloy with uniform overall structure and performance and free from metallurgical defects such as shrinkage porosity, shrinkage cavities, and microcracks. The high-entropy alloy with in-situ precipitated reinforcing phases across submicron and micron composites provided by this invention achieves a balance between strong plasticity and high-temperature wear resistance. Its mechanical and high-temperature wear resistance properties are outstanding, and it has broad application prospects in components such as spherical bearings, sealing rings, reactor control rod drive mechanisms, and high-temperature valves that involve high-temperature load bearing and high-temperature wear in the fields of aviation, nuclear energy, and shipbuilding.

[0026] This invention provides a method for preparing the high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase as described in the above technical solution, comprising the following steps: According to the chemical composition of the high-temperature wear-resistant high-entropy alloy with the cross-submicron-micron composite in-situ precipitated reinforcing phase, the raw materials corresponding to each element are vacuum arc melted to obtain the high-temperature wear-resistant high-entropy alloy with the cross-submicron-micron composite in-situ precipitated reinforcing phase.

[0027] Unless otherwise specified, all raw materials involved in this invention are commercially available products well known in the art.

[0028] In this invention, the raw materials corresponding to each element include metallic raw materials (Al, Co, Cr, Fe, Ni, Ti, Y, Nb, W, Zr, V, and Mo) and non-metallic raw materials (B and Si); the metallic and non-metallic raw materials can be cylindrical or irregularly shaped particles, wherein the size of the cylindrical particles can be [missing information]. 0.5~10 mm × 3~10 mm; In this embodiment of the invention, the metal raw material is The raw materials are 3 mm × 5 mm cylinders, and the non-metallic particles are irregular particles with a size of 3-5 mm. In this invention, the purity of each raw material is preferably ≥99.9 wt%, more preferably ≥99.95 wt%. In this invention, the ingredients are prepared according to the chemical composition of the high-temperature wear-resistant high-entropy alloy with a trans-submicron-micron composite in-situ precipitated reinforcing phase, converting the atomic ratios therein into mass ratios, and then weighing the required amounts of each raw material sequentially using an electronic analytical balance, the accuracy of which is preferably ≥0.001 g.

[0029] In this invention, each raw material is preferably removed from its impurities before use. The preferred method for removing impurities is as follows: the surface of the raw material is polished with 400-1000 grit sandpaper to remove the surface oxide scale; then the polished raw material is ultrasonically cleaned with acetone to remove surface oil; and then the cleaned raw material is dried in an oven at 35-40°C to obtain a clean and dry raw material.

[0030] In this invention, after the ingredients are prepared, the raw materials are placed in a water-cooled copper crucible in the following order from bottom to top: non-refractory metal raw materials, non-metallic raw materials, and refractory metal raw materials (the metal raw materials are placed in order of increasing melting point and from bottom to top). This process is called material placement, followed by vacuum arc melting. In this invention, the melting points of the raw materials from low to high are: Al→Ni→Co→Y→Fe→Si→B→Ti→Zr→Cr→V→Nb→Mo→W. Placing the refractory metal elements at the top of the crucible ensures complete melting of the metal; placing the non-metallic elements in the middle allows the molten metal to encapsulate them, preventing splashing during alloy melting, reducing material loss, and improving the accuracy of the alloy composition.

[0031] In this invention, the vacuum arc melting is preferably carried out in an argon atmosphere (i.e., melting atmosphere) of 0.06 MPa. Specifically, the melting atmosphere is controlled by repeatedly performing vacuuming and argon purging. Specifically: the first vacuuming is performed to bring the vacuum level of the arc melting furnace to below 10 Pa (e.g., 3.0, 7.5, 8, or 9 Pa); then, high-purity argon is first purged to maintain the vacuum level at 0.03~0.08 MPa; subsequently, a second vacuuming is performed to bring the vacuum level to 1×10⁻⁶ MPa. -3 Pa below (e.g., 5.5 × 10) -4 7×10 -4 Or 9×10 -4 The vacuum arc melting process is then repeated, with a second filling of high-purity argon gas to obtain an argon atmosphere melting environment of 0.06 MPa. In this invention, the voltage for vacuum arc melting is preferably 20-80 V, which can be 50, 52, 60, 68, or 80 V, and the current is preferably 500-850 A, which can be 570, 660, 720, or 850 A. In this invention, the number of vacuum arc melting cycles is 8-15, which can be 9, 10, 12, or 15 cycles, and the time for each melting cycle is preferably 3-5 min, which can be 3.5, 3.8, 4, or 4.5 min. During vacuum arc melting, the first two melting cycles are preferably carried out without stirring (mainly to melt the metal particles into ingots and encapsulate non-metallic elements), and subsequent melting cycles are preferably carried out under stirring conditions. Specifically, a single-winding spiral electromagnetic stirring device can be used to electromagnetically stir the high-entropy alloy melt.

[0032] In this invention, after each melting process, the resulting high-entropy alloy melt is cooled and solidified by water cooling (the ingot is cooled in a water-cooled copper crucible). Except for the cooling and solidification process after the last melting process, where the flow rate of the cooling water is 2.4~3.5 L / min (which can be 2.4, 2.8, 3.0 or 3.5 L / min) and the temperature is 30~40℃ (which can be 30, 35.5, 36.0 or 40℃), the cooling and solidification process after other melting processes uses a flow rate of 16~24 L / min (which can be 16, 18.5, 22 or 24 L / min) and a temperature of 12~15℃ (which can be 12, 13, 13.5 or 15℃). This invention controls the cooling water conditions used for cooling and solidification after each melting stage (except the final melting stage) at a flow rate of 16-24 L / min and a temperature of 12-15°C, which improves the cooling rate and melting efficiency during the melting process. For the final melting stage, the cooling water conditions are controlled at a flow rate of 2.4-3.5 L / min and a temperature of 30-40°C, providing relatively mild cooling conditions that allow sufficient time for grain crystallization and growth, resulting in the formation of submicron-micron composite in-situ precipitated reinforcing phases. This determines the final grain morphology, distribution, size, and type of reinforcing phase in the alloy. By adjusting the cooling water flow rate and temperature, this invention controls the cooling rate, solidification rate, undercooling, and internal temperature gradient of the ingot, thereby achieving regulation of the type, distribution, and size of in-situ precipitated phases within the ingot.

[0033] In this invention, after each melting process, the cooled and solidified ingot is flipped over for the next melting process to promote element diffusion and ensure uniform composition of the ingot.

[0034] This invention provides a novel development strategy for high-temperature wear-resistant high-entropy alloys with high production efficiency and stable, reliable service performance. The strategy uses a face-centered cubic high-entropy alloy with good plasticity and toughness as the matrix. By introducing dissimilar nonmetals or metal-nonmetal elements into the high-entropy alloy, and utilizing the in-situ chemical reactions between active metal and nonmetal elements, two or more composite in-situ precipitated reinforcing phases are formed. By controlling the cooling and solidification rate of the alloy, the size of different in-situ precipitated phases can be controlled, ultimately obtaining a high-temperature wear-resistant high-entropy alloy with composite in-situ precipitated reinforcing phases spanning submicron to micron levels. This invention is of great significance for expanding the application range of high-entropy alloys and improving their application potential in extreme wear environments such as high temperature, heavy load, and high speed.

[0035] To further illustrate the present invention, the following detailed description, in conjunction with examples, of the high-temperature wear-resistant high-entropy alloy with trans-submicron to micron composite in-situ precipitated reinforcing phases and its preparation method provided by the present invention, shall not be construed as limiting the scope of protection of the present invention.

[0036] Example 1 A high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase, according to its atomic ratio and composition (Al) 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 The various elemental compositions of the alloy, converted to mass percentages, are shown in Table 1.

[0037] Table 1 (Al) 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 Mass percentage (wt.%) of each element in high-entropy alloys

[0038] Preparation method of high temperature wear-resistant high entropy alloy: (1) Impurity Removal: The surfaces of raw materials Al, Co, Cr, Fe, Ni, Ti, Si, and B are successively polished with 400-mesh, 600-mesh, and 800-mesh sandpaper to remove surface oxide scale. Then, the polished raw materials are ultrasonically cleaned with acetone to remove surface oil. Finally, all cleaned raw materials are dried in a 35°C oven to obtain clean and dry raw materials. The above-mentioned metal raw materials are... A 3 mm × 5 mm cylinder, with Si and B being irregular particles of 3~5 mm.

[0039] (2) Placement: Place the weighed raw materials in the water-cooled copper crucible in the following order from bottom to top: Al→Ni→Co→Fe→Si→B→Ti→Cr.

[0040] (3) Smelting: Smelting includes two parts: smelting atmosphere control and electric arc smelting.

[0041] Melting atmosphere control: The first vacuuming was performed to achieve a vacuum level of 7.5 Pa in the electric arc melting furnace. Then, high-purity argon was introduced for the first time to maintain the vacuum level at 0.07 MPa. The second vacuuming was performed to achieve a vacuum level of 7 × 10⁻⁶ MPa. -4 Pa, and then high-purity argon gas is introduced a second time to obtain an argon atmosphere melting environment of 0.06 MPa.

[0042] Arc melting parameters: The melting voltage is 52 V, the melting current is 570 A, the melting time is 4.0 min per melting, and the number of melting cycles is 12. The first two melting cycles are without magnetic stirring. The third to 12th melting cycles use a single-winding spiral electromagnetic stirring device to electromagnetically stir the high-entropy alloy melt. After each melting cycle, the ingot is flipped over before the next melting cycle.

[0043] (4) Cooling and solidification: The ingot is cooled in the water-cooled copper crucible. The cooling water flow rate for cooling and solidification after the first to 11th melting is 24 L / min and the cooling water temperature is 12.0℃. The cooling water flow rate for cooling and solidification after the 12th melting is 3.5 L / min and the cooling water temperature is 30.0℃.

[0044] After cooling, an in-situ precipitated reinforcement phase with submicron-micron composite was obtained (Al). 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 High-temperature wear-resistant high-entropy alloy.

[0045] Figure 1 The (Al) composite in-situ precipitated reinforcement phase with submicron-micron composite structure prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 XRD pattern of high-temperature wear-resistant high-entropy alloy. XRD analysis shows that the main component of this high-entropy alloy is the FCC phase. During the arc melting process, two reinforcing phases, silicides and borides, are formed through in-situ chemical reactions, and L12 in-situ precipitates are also formed.

[0046] Figure 2 (Al) prepared in Example 1 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 Electron backscattering patterns and elemental distribution maps of high-entropy alloys. Figure 2 In the diagram, (a) and (b) correspond to electron backscattering patterns, and (c) corresponds to the elemental surface distribution pattern. Figure 3 (Al) prepared in Example 10.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 EBSD phase distribution diagram of high-entropy alloys. Figure 2 In (a) and (b), the microstructure of this high-entropy alloy is a composite structure composed of dendrites, eutectic phases, and in-situ precipitated phases. Figure 2 (c) element surface distribution Figure 1 XRD and Figure 3 The EBSD phase distribution diagram shows that the light gray dendrites are enriched in Al, Co, Cr, Fe, and Ni, and their main components are a mixture of FCC and L12 phases. The eutectic structure consists of a eutectic structure with alternating light gray (average lamellar width 475 nm) and gray (average lamellar width 298 nm) lamellar phases. The gray regions contain a relatively large amount of Ti and Si, which are concentrated areas of in-situ titanium silicide. In addition to the titanium silicide in the eutectic structure, there are also randomly distributed blocky titanium silicide precipitates with a size of less than 2.0 μm in this high-entropy alloy. Furthermore, there are Cr-rich in-situ precipitates with lengths of 0.3–180 μm in this high-entropy alloy. Combined with XRD and EBSD, it can be seen that the main component of this structure is chromium boride. Due to the small atomic mass of boron (B), it is difficult to detect accurately by EDS, so the elemental surface distribution of B is not accurate. Therefore, based on grain size, the in-situ precipitates of this high-entropy alloy mainly consist of three types: a submicron-micron-scale in-situ chromium boride reinforcing phase (grain size 0.3~180 μm), a micron-scale bulk titanium silicide in-situ phase (grain size <2 μm), and a submicron-scale eutectic structure (average lamellar width 298 nm). Based on the above analysis, it is demonstrated that this invention has successfully prepared a (Al) alloy with a submicron-micron-scale composite in-situ precipitated reinforcing phase. 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 High-temperature wear-resistant high-entropy alloy.

[0047] Based on the national standard GB / T 7314-2005 "Metallic Materials - Room Temperature Compression Test Method", the compressive mechanical properties of high-entropy alloys were tested. For example... Figure 4As shown, at 25℃, the high-entropy alloy exhibits a compressive yield strength of 1728 MPa, a compressive strength of 2002 MPa, and a fracture strain of 13.2%. Furthermore, based on GB / T 4340.1-2024 "Metallic Materials - Vickers Hardness Testing - Part 1: Test Methods", the Vickers hardness of this high-entropy alloy at different temperatures was analyzed. Figure 5 The high-entropy alloy exhibits a hardness of 531-807 HV at temperatures ranging from 25 to 800°C, with the hardness decreasing as temperature increases; specifically, the hardness at 25°C and 800°C is 807 HV and 531 HV, respectively. This demonstrates that the (Al) alloy developed in this invention... 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50 High-temperature wear-resistant high-entropy alloys possess both good strength and plasticity.

[0048] The wear resistance of this high-entropy alloy in the range of 25℃ to 800℃ was evaluated using a high-temperature tribological testing machine. The friction load was 10 N, the friction speed was 0.2 m / s, the friction time was 45 min, and the friction pair consisted of Si3N4 balls. Figure 6 As shown, the average wear rate of this high-entropy alloy at 25℃, 200℃, 400℃, 600℃ and 800℃ is 2.38×10⁻⁶. -5 mm 3 ·N -1 ·m -1 4.85×10 -5 mm 3 ·N -1 ·m -1 5.56×10 -5 mm 3 ·N -1 ·m -1 0.565×10 -5 mm 3 ·N -1 ·m -1 and 0.237×10 - 5 mm 3 ·N -1 ·m -1 This demonstrates that the (Al) developed in this invention... 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 50 (Si 0.1 B 0.75 ) 50High-entropy alloys exhibit good wear resistance at temperatures ranging from 25℃ to 800℃, especially excellent high-temperature wear resistance.

[0049] Example 2 A high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase, its composition according to atomic ratio is (Al 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 The various elemental compositions of the alloy, converted to mass percentages, are shown in Table 2.

[0050] Table 2 (Al) 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 Mass percentage (wt.%) of each element in high-entropy alloys

[0051] Preparation method of high temperature wear-resistant high entropy alloy: (1) Impurity Removal: The surfaces of raw materials Al, Co, Cr, Fe, Ni, Ti, Nb, and B are successively polished with 400-mesh, 800-mesh, and 1000-mesh sandpaper to remove surface oxide scale. Then, the polished raw materials are ultrasonically cleaned with acetone to remove surface oil. Finally, the cleaned raw materials are dried in a 35°C oven to obtain clean and dry raw materials. The above-mentioned metal raw materials are... A cylinder of 3 mm × 5 mm, and B consists of irregular particles of 3~5 mm.

[0052] (2) Material placement: Place the weighed raw materials in the water-cooled copper crucible in the following order from bottom to top: Al→Ni→Co→Fe→B→Ti→Cr→Nb.

[0053] (3) Smelting: Smelting includes two parts: smelting atmosphere control and electric arc smelting.

[0054] Melting atmosphere control: The first vacuuming was performed to achieve a vacuum level of 8 Pa in the electric arc melting furnace, followed by the first introduction of high-purity argon gas to maintain the vacuum level at 0.08 MPa; the second vacuuming was performed to achieve a vacuum level of 9 × 10⁻⁶ MPa. -4 Pa, and then high-purity argon gas is introduced a second time to obtain an argon atmosphere melting environment of 0.06 MPa.

[0055] Arc melting parameters: The melting voltage is 60 V, the melting current is 660 A, the melting time is 3.5 min per melting, and the number of melting cycles is 9. The first two melting cycles are without magnetic stirring. The third to ninth melting cycles use a single-winding spiral electromagnetic stirring device to electromagnetically stir the high-entropy alloy melt. After each melting cycle is completed, the ingot is flipped over before the next melting cycle.

[0056] (4) Cooling and solidification: The ingot is cooled in the furnace in a water-cooled copper crucible. The cooling water flow rate for cooling and solidification after the first to eighth melting is 22 L / min and the cooling water temperature is 13.0℃. The cooling water flow rate for cooling and solidification after the ninth melting is 3.0 L / min and the cooling water temperature is 35.5℃.

[0057] After cooling, an in-situ precipitated reinforcement phase with submicron-micron composite was obtained (Al). 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 High-temperature wear-resistant high-entropy alloy.

[0058] Figure 7 The (Al) composite in-situ precipitated reinforcement phase with submicron-micron composite structure prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 XRD pattern of high-temperature wear-resistant high-entropy alloy. XRD analysis shows that, after vacuum arc melting, a boride reinforcing phase was formed in situ in the FCC matrix through chemical reaction.

[0059] Figure 8 (Al) prepared in Example 2 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 Electron backscattering diagram and elemental surface distribution diagram of the microstructure of high-temperature wear-resistant high-entropy alloy. Figure 8 In the diagram, (a) and (b) correspond to electron backscattering patterns, and (c) corresponds to the elemental surface distribution pattern. For example... Figure 8In (a), the in-situ precipitated boride reinforcing phase is randomly distributed in the FCC phase matrix, and the size of the boride is clearly divided into three levels. Calculated by volume fraction, 58.2% of the boride precipitates are micron-sized coarse rod-shaped grains with a size of 20–80 μm; 26.9% of the boride precipitates are candy-like grains with a size of 1–20 μm (e.g.,...). Figure 8 (b)); and 14.9% of the elongated in-situ borates are submicron in size, with a size of less than 1 μm. Figure 8 The elemental distribution in the (c) plane indicates that the FCC matrix phase is mainly composed of Al, Co, Cr, Fe, and Ni; while the in-situ precipitated phase is enriched with Nb and Ti; the B element, due to its small atomic number, is difficult to analyze accurately using EDS technology; this suggests that the in-situ precipitated reinforcing phase is mainly composed of Nb-B and Ti-B compounds. Combined with the analysis results of XRD and SEM-EDS, it can be concluded that this invention has successfully prepared an in-situ precipitated reinforcing phase with a submicron-micron composite structure (Al... 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 High-temperature wear-resistant high-entropy alloy.

[0060] Based on the national standard GB / T 7314-2005 "Metallic Materials - Room Temperature Compression Test Method", the compressive mechanical properties of high-entropy alloys were tested. For example... Figure 9 As shown, at 25℃, the high-entropy alloy exhibits a compressive yield strength of 1859 MPa, a compressive strength of 2301 MPa, and a fracture strain of 14.9%. Based on these parameters, the Vickers hardness of the high-entropy alloy at different temperatures was analyzed according to GB / T 4340.1-2024 "Metallic Materials - Vickers Hardness Testing - Part 1: Test Methods". Figure 10 The high-entropy alloy exhibits a hardness of 502-761 HV at temperatures ranging from 25 to 800°C, with the hardness decreasing as temperature increases; specifically, the hardness at 25°C and 800°C is 761 HV and 502 HV, respectively. This demonstrates that the (Al) alloy developed in this invention... 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 High-temperature wear-resistant high-entropy alloys possess both good strength and toughness.

[0061] The tribological properties of this high-entropy alloy in the range of 25℃ to 800℃ were evaluated using a high-temperature tribological testing machine. The friction load was 10 N, the friction speed was 0.2 m / s, the friction time was 45 min, and the friction pair consisted of Si3N4 balls. Figure 11 As shown, the average wear rate of this high-entropy alloy at 25℃, 200℃, 400℃, 600℃ and 800℃ is 4.07×10⁻⁶. -5 mm 3 ·N -1 ·m -1 3.22×10 -5 mm 3 ·N -1 ·m -1 2.93×10 -5 mm 3 ·N -1 ·m -1 0.571×10 -5 mm 3 ·N -1 ·m -1 and 0.0982×10 -5 mm 3 ·N -1 ·m -1 This demonstrates that the (Al) developed in this invention... 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 ) 82 (Nb 0.33 B 0.67 ) 18 High-entropy alloys exhibit good wear resistance at temperatures ranging from 25℃ to 800℃, especially excellent high-temperature wear resistance.

[0062] Example 3 A high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase, its composition according to atomic ratio is (Al 0.4 Co 1.8 CrFeNiY 0.01 ) 58 (Mo 0.2 W 0.1 B 0.5 ) 42 The various elemental compositions of the alloy, converted to mass percentages, are shown in Table 3.

[0063] Table 3 (Al) 0.4 Co 1.8 CrFeNiY 0.01 ) 58 (Mo 0.2 W 0.1 B0.5 ) 42 Mass percentage (wt.%) of each element in high-entropy alloys

[0064] Preparation method of high temperature wear-resistant high entropy alloy: (1) Impurity Removal: The surfaces of raw materials Al, Co, Cr, Fe, Ni, Y, Mo, W, and B are successively polished with 400-mesh, 600-mesh, and 1000-mesh sandpaper to remove surface oxide scale. Then, the polished raw materials are ultrasonically cleaned with acetone to remove surface oil. Finally, the cleaned raw materials are dried in a 35°C oven to obtain clean and dry metal raw materials. The above-mentioned metal raw materials are... A cylinder of 3 mm × 5 mm, and particles B are irregular particles of 3~5 mm.

[0065] (2) Placement: Place the weighed raw materials in the water-cooled copper crucible in the following order from bottom to top: Al→Ni→Co→Y→Fe→B→Cr→Mo→W.

[0066] (3) Smelting: Smelting includes two parts: smelting atmosphere control and electric arc smelting.

[0067] Melting atmosphere control: The first vacuum evacuation was performed to achieve a vacuum level of 3.0 Pa in the electric arc melting furnace. Then, high-purity argon gas was introduced for the first time to maintain the vacuum level at 0.03 MPa. The second vacuum evacuation was performed to achieve a vacuum level of 5.5 × 10⁻⁶ Pa. -4 Pa, and then high-purity argon gas is introduced a second time to obtain an argon atmosphere melting environment of 0.06 MPa.

[0068] Arc melting parameters: The melting voltage is 80 V, the melting current is 850 A, the melting time is 4.5 min per melting, and the number of melting cycles is 15. The first two melting cycles are without magnetic stirring. The third to fifteenth melting cycles use a single-winding spiral electromagnetic stirring device to electromagnetically stir the high-entropy alloy melt. After each melting cycle, the ingot is flipped over before the next melting cycle.

[0069] (4) Cooling and solidification: The ingot is cooled in the furnace in a water-cooled copper crucible. The cooling water flow rate for cooling and solidification after the first to 14th melting is 16 L / min and the cooling water temperature is 15℃. The cooling water flow rate for cooling and solidification after the 15th melting is 2.4 L / min and the cooling water temperature is 40.0℃.

[0070] After cooling, an in-situ precipitated reinforcement phase with submicron-micron composite was obtained (Al). 0.4 Co 1.8 CrFeNiY 0.01 ) 58 (Mo 0.2W 0.1 B 0.5 ) 42 High-temperature wear-resistant high-entropy alloy.

[0071] The tribological properties of the high-entropy alloy in the range of 25℃ to 800℃ were evaluated using a high-temperature tribological testing machine. The friction load was 10 N, the friction velocity was 0.2 m / s, the friction time was 45 min, and the friction pair consisted of Si3N4 balls. The average wear rate of the high-entropy alloy at 25℃, 200℃, 400℃, 600℃, and 800℃ was 6.27 × 10⁻⁶. -5 mm 3 ·N -1 ·m -1 6.81×10 - 5 mm 3 ·N -1 ·m -1 7.25×10 -5 mm 3 ·N -1 ·m -1 2.08×10 -5 mm 3 ·N -1 ·m -1 and 0.512×10 -5 mm 3 ·N -1 ·m -1 This shows (Al) 0.4 Co 1.8 CrFeNiY 0.01 ) 58 (Mo 0.2 W 0.1 B 0.5 ) 42 High-entropy alloys exhibit good wear resistance at temperatures ranging from 25℃ to 800℃, especially excellent high-temperature wear resistance.

[0072] Example 4 A high-temperature wear-resistant, high-entropy alloy with a trans-submicron to micron composite in-situ precipitated reinforcing phase, its composition according to atomic ratio is (Al 0.4 Co 1.8 CrFeNiY 0.01 ) 64 (Zr 0.2 V 0.55 B 0.3 ) 36 The various elemental compositions of the alloy, converted to mass percentages, are shown in Table 4.

[0073] Table 4 (Al) 0.4 Co 1.8CrFeNiY 0.01 ) 64 (Zr 0.2 V 0.55 B 0.3 ) 36 Mass percentage (wt.%) of each element in high-entropy alloys

[0074] Preparation method of high temperature wear-resistant high entropy alloy: (1) Impurity Removal: The surfaces of raw materials Al, Co, Cr, Fe, Ni, Y, Zr, V, and B are successively polished with 600-mesh, 800-mesh, and 1000-mesh sandpaper to remove surface oxide scale. Then, the polished raw materials are ultrasonically cleaned with acetone to remove surface oil. Finally, the cleaned raw materials are dried in a 35°C oven to obtain clean and dry raw materials. The above-mentioned metal raw materials are... A cylinder of 3 mm × 5 mm, and particles B are irregular particles of 3~5 mm.

[0075] (2) Placement: Place the weighed raw materials in a water-cooled copper crucible in the following order from bottom to top: Al→Ni→Co→Y→Fe→B→Zr→Cr→V.

[0076] (3) Smelting: Smelting includes two parts: smelting atmosphere control and electric arc smelting.

[0077] Melting atmosphere control: The first vacuuming was performed to achieve a vacuum level of 9 Pa in the electric arc melting furnace. Then, high-purity argon was introduced for the first time to maintain the vacuum level at 0.07 MPa. The second vacuuming was performed to achieve a vacuum level of 2.7 × 10⁻⁶ MPa. -4 Pa, and then high-purity argon gas is introduced a second time to obtain an argon atmosphere melting environment of 0.06 MPa.

[0078] Arc melting parameters: The melting voltage is 68 V, the melting current is 720 A, the melting time is 3.8 min per melting, and the number of melting cycles is 10. The first two melting cycles are without magnetic stirring. The third to tenth melting cycles use a single-winding spiral electromagnetic stirring device to electromagnetically stir the high-entropy alloy melt. After each melting cycle, the ingot is flipped over before the next melting cycle.

[0079] (4) Cooling and solidification: The ingot is cooled in the furnace in a water-cooled copper crucible. The cooling water flow rate for cooling and solidification after the first to ninth melting is 18.5 L / min and the cooling water temperature is 13.5℃. The cooling water flow rate for cooling and solidification after the tenth melting is 2.8 L / min and the cooling water temperature is 36.0℃.

[0080] After cooling, an in-situ precipitated reinforcement phase with submicron-micron composite was obtained (Al). 0.4Co 1.8 CrFeNiY 0.01 ) 64 (Zr 0.2 V 0.55 B 0.3 ) 36 High-temperature wear-resistant high-entropy alloy.

[0081] The tribological properties of the high-entropy alloy in the range of 25℃ to 800℃ were evaluated using a high-temperature tribological testing machine. The friction load was 10 N, the friction velocity was 0.2 m / s, the friction time was 45 min, and the friction pair consisted of Si3N4 balls. The average wear rate of the high-entropy alloy at 25℃, 200℃, 400℃, 600℃, and 800℃ was 3.69 × 10⁻⁶. -5 mm 3 ·N -1 ·m -1 2.91×10 - 5 mm 3 ·N -1 ·m -1 3.07×10 -5 mm 3 ·N -1 ·m -1 1.14×10 -5 mm 3 ·N -1 ·m -1 and 0.42×10 -5 mm 3 ·N -1 ·m -1 This shows (Al) 0.4 Co 1.8 CrFeNiY 0.01 ) 64 (Zr 0.2 V 0.55 B 0.3 ) 36 High-entropy alloys exhibit good wear resistance at temperatures ranging from 25℃ to 800℃, especially excellent high-temperature wear resistance.

[0082] The above description is merely a preferred embodiment of the present invention and is not intended to limit the present invention in any way. It should be noted that those skilled in the art can make various improvements and modifications without departing from the principles of the present invention, and these improvements and modifications should also be considered within the scope of protection of the present invention.

Claims

1. A high-temperature wear-resistant, high-entropy alloy with a trans-submicron-micron composite in-situ precipitated reinforcing phase, characterized in that, Based on atomic ratio, the chemical composition of the high-temperature wear-resistant high-entropy alloy is M. 50~95 R 5~50 Where M is Al 0.2 Co 1.5 CrFeNi 1.5 Ti 0.5 Or Al 0.4 Co 1.8 CrFeNiY 0.01 R is Si with non-equiatomic ratio 0.05~0.50 B 0.35~0.85 M1 0.10~0.60 B 0.20~0.80 Or M1 0.10~ 0.60 M2 0.10~0.60 B 0.20~0.80 M1 and M2 are Nb, W, Zr, V or Mo, and M1 and M2 are not the same.

2. The high-temperature wear-resistant high-entropy alloy according to claim 1, characterized in that, R is Si 0.1 B 0.75 、Nb 0.33 B 0.67 Mo 0.2 W 0.1 B 0.5 or Zr 0.2 V 0.55 B 0.3 .

3. The high-temperature wear-resistant high-entropy alloy according to claim 1 or 2, characterized in that, The in-situ precipitated phases of the high-temperature wear-resistant high-entropy alloy include submicron grains with a size of 100 nm to 1 μm and micron-sized grains with a size of 1 to 300 μm.

4. The method for preparing the high-temperature wear-resistant high-entropy alloy with a trans-submicron-micron composite in-situ precipitated reinforcing phase as described in any one of claims 1 to 3, characterized in that, Includes the following steps: According to the chemical composition of the high-temperature wear-resistant high-entropy alloy with the cross-submicron-micron composite in-situ precipitated reinforcing phase, the raw materials corresponding to each element are vacuum arc melted to obtain the high-temperature wear-resistant high-entropy alloy with the cross-submicron-micron composite in-situ precipitated reinforcing phase. The vacuum arc melting process is repeated 8 to 15 times. After each melting, the resulting high-entropy alloy melt is cooled and solidified in a water-cooled copper crucible. Except for the last melting, when the cooling water flow rate is 2.4 to 3.5 L / min and the temperature is 30 to 40°C, the cooling water flow rate is 16 to 24 L / min and the temperature is 12 to 15°C.

5. The preparation method according to claim 4, characterized in that, The purity of each raw material is ≥99.9wt%.

6. The preparation method according to claim 4, characterized in that, After the ingredients are mixed, the raw materials are placed in a water-cooled copper crucible in the order of non-refractory metal raw materials, non-metallic raw materials, and refractory metal raw materials from bottom to top, and then vacuum arc melting is carried out.

7. The preparation method according to claim 4, characterized in that, The vacuum arc melting was carried out in an argon atmosphere of 0.06 MPa.

8. The preparation method according to claim 4 or 7, characterized in that, The voltage of the vacuum arc melting is 20~80V, and the current is 500~850A.

9. The preparation method according to claim 4, characterized in that, The time for a single melting is 3 to 5 minutes.

10. The preparation method according to claim 4 or 9, characterized in that, During the vacuum arc melting process, the first two meltings are carried out without stirring, while subsequent meltings are carried out under electromagnetic stirring conditions. After each melting is completed, the cooled and solidified ingot is flipped over before the next melting is carried out.

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