High-temperature wear-resistant and corrosion-resistant AlCrCuMoNi high-entropy alloy powder with good heat conductivity, coating and preparation method of AlCrCuMoNi high-entropy alloy powder

Abstract

The invention relates to the technical field of metal material surface modification, in particular to AlCrCuMoNi high-entropy alloy powder with high temperature, wear resistance, corrosion resistance and good heat conduction, a coating and a preparation method thereof.The high-entropy alloy powder with the particle size being 15-45 microns and suitable for thermal spraying is prepared through a mechanical alloying method, and then the high-entropy alloy powder is prepared through an oxygen-kerosene supersonic flame spraying technology; the preparation method comprises the following steps: spraying high-entropy alloy powder on the surface of a key part matrix by taking high-entropy alloy as a matrix, oxygen as a combustion improver, kerosene as a fuel, high-purity nitrogen as a powder feeding carrier gas and air as a cooling medium to prepare an AlCrCuMoNi HEA coating; al, Cr, Cu, Mo and Ni elementary substance powder is subjected to ball milling according to the required molar ratio through a mechanical alloying method, AlCrCuMoNi HEA powder is obtained, the coating is prepared through the hypersonic flame spraying technology, the method is suitable for improving the high-temperature abrasion resistance and hot corrosion resistance of the surfaces of key parts in the industries of energy, metallurgy, chemical engineering and the like, and the service life of boiler pipes is prolonged.

Description

Technical Field

[0001] This invention relates to the field of surface modification technology for metallic materials, specifically to a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder, coating, and preparation method thereof. Background Technology

[0002] With the development of industries such as energy, metallurgy, and chemicals, the service environment of equipment under harsh conditions such as high temperature, corrosion, and wear is becoming increasingly stringent. Typical examples include the "four tubes" of coal-fired boilers, hot-end components of gas turbines, and heat transfer pipelines in chemical equipment, which are exposed to high-temperature environments of 600-800 ℃ for extended periods. They not only endure the scouring of high-temperature airflow and particle abrasion but also suffer from the corrosion of molten salts containing sulfates and chlorides. These factors often synergistically exacerbate material degradation, leading to wear failure, corrosion perforation, and thermal fatigue cracking, thus seriously threatening the safe operation and service life of equipment. Therefore, it is essential to improve the wear resistance and heat corrosion resistance of key components. Utilizing surface modification technology to improve the high-temperature wear and corrosion resistance of key components is the most common method. High-velocity vapor deposition (HVOF) spraying is one of the widely used thermal spraying technologies. Due to its high spraying speed and dense coating, HVOF technology has become one of the main technologies for preparing alloy coatings.

[0003] The design concept of high-entropy alloys (HEAs) expands the design space of alloy materials, extending the alloy composition design space to the central region of the multi-element phase diagram. Their thermodynamic high-entropy effect, structural lattice distortion effect, kinetic hysteresis diffusion effect, and cocktail effect endow high-entropy alloys with excellent wear resistance, corrosion resistance, and high-temperature oxidation resistance. This has made them a research hotspot in recent years, distinct from traditional alloy materials. By adjusting the types and proportions of high-entropy alloying elements and selecting appropriate manufacturing methods and heat treatment processes, the wear resistance and corrosion resistance of HEAs can be improved.

[0004] While HVOF technology can produce HEA coatings, the key challenge in producing high-quality HEA coatings lies in first preparing HEA powder suitable for spraying. Currently, commonly used methods for manufacturing HEA powder include gas atomization, spray granulation, and mechanical alloying. However, powders prepared by spray granulation are brittle and have low density. Mechanical alloying (MA) is a solid-state non-equilibrium processing technique that can produce alloy powders with good uniformity. Therefore, MA opens a new avenue for preparing thermal spray powders.

[0005] In view of the above-mentioned defects, the inventors of this invention have finally obtained this invention after a long period of research and practice. Summary of the Invention

[0006] The purpose of this invention is to solve the problem of high-temperature wear and thermal corrosion on the surface of key components in industries such as energy, metallurgy and chemical engineering, and to provide a high-temperature wear-resistant, corrosion-resistant AlCrCuMoNi high-entropy alloy powder, coating and preparation method thereof.

[0007] To achieve the above preparation method, this invention discloses a method for preparing high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder, comprising the following steps:

[0008] S1, mix Al, Cr, Cu, Mo and Ni elemental powders;

[0009] S2, put the mixed powder obtained in step S1 into a ball mill jar, evacuate the jar and then introduce argon gas;

[0010] S3. The mixed powder obtained in step S2 is ball-milled and sieved to obtain AlCrCuMoNi high-entropy alloy powder. The sieved high-entropy alloy powder is then subjected to vacuum annealing at 800 °C for 2 h.

[0011] In step S1, the molar ratio of Al, Cr, Cu, Mo, and Ni elemental powders is: Al 25%, Cr 25%, Cu 6.25-18.75%, Mo 6.25-18.75%, and Ni 25%.

[0012] In step S1, a premixer is used for mixing. The speed of the premixer is 60 r / min and the mixing time is 2 h.

[0013] In step S2, the vacuum pump pressure is set to 10 Pa and the vacuuming time is 10 min; high-purity argon gas is passed through at a pressure of 0.5 Pa for 3 min.

[0014] In step S3, the grinding balls used in the ball milling are ZrO2 grinding balls with diameters of 15mm, 10mm, 6mm and 5mm mixed in a ratio of 1:4:2:1, the mass ratio of grinding balls to powder is 10:1, the ball milling speed is 220 rpm, and the ball milling time is 45 h.

[0015] This invention also discloses a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder prepared by the above method, wherein the AlCrCuMoNi high-entropy alloy powder is AlCrCu 1-x Mo x Ni high-entropy alloy powder, wherein x = 0.25, 0.5 or 0.75.

[0016] This invention also discloses a method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy coating, comprising the following steps:

[0017] (1) Before spraying, the surface of the metal substrate is degreased and cleaned, then the surface is roughened by sandblasting, and the roughened substrate is preheated.

[0018] (2) Using oxygen-kerosene supersonic flame spraying technology, oxygen is used as a combustion aid, kerosene is used as fuel, high-purity nitrogen is used as a powder carrier gas, and air is used as a cooling medium to spray AlCrCuMoNi high-entropy alloy powder onto the surface of a metal substrate to form an AlCrCuMoNi high-entropy alloy coating.

[0019] In step (1), the sandblasting material is 60-mesh brown corundum sand, the sandblasting pressure is 3~5MPa, the surface roughness of the substrate after sandblasting reaches 2.5~3 μm, and the substrate preheating temperature reaches 80~120 ℃.

[0020] In step (2), the process of supersonic flame spraying technology is as follows: oxygen flow rate is 900 L / min, kerosene flow rate is 28 L / h, spraying distance is 380 mm, spraying step is 4 mm, spraying speed is 800 mm / s, powder feeding voltage is 3.3 V, and powder feeding rate is 32 g / min.

[0021] The present invention also discloses a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy coating prepared by the above preparation method, wherein the thickness of the AlCrCuMoNi high-entropy alloy coating is 200~300 μm.

[0022] The performance of the AlCrCuMoNi high-entropy alloy coating stems from its unique microstructure and multi-element synergistic mechanism. First, the multiple principal elements in the coating collectively form a high-entropy solid solution structure. The lattice distortion effect inhibits atomic diffusion and high-temperature grain growth, ensuring the stability of the microstructure and phase structure during high-temperature service. Second, during the spraying process, molten or semi-molten particles impact the substrate at high speed, forming a dense layered structure. The dispersed high-entropy solid solution phase and fine oxide phase particles within this structure hinder dislocation movement, thereby endowing the coating with high hardness and wear resistance.

[0023] Compared with the prior art, the beneficial effects of the present invention are as follows:

[0024] 1. This invention prepares high-entropy alloy powder through mechanical alloying technology, which enables each component to be uniformly distributed in the powder particles, avoiding the element segregation problem that may occur in traditional smelting processes, thereby ensuring the compositional uniformity and performance stability of the high-entropy alloy coating.

[0025] 2. This invention effectively controls the particle size and morphology of high-entropy alloy powder by optimizing ball milling process parameters, such as rotation speed, time, and ball-to-powder ratio, thereby affecting the microstructure and performance of the coating. For example, appropriate ball milling time can promote the refinement of powder particles and improve the degree of alloying, while a reasonable ball-to-powder ratio helps to improve ball milling efficiency and powder uniformity.

[0026] 3. This invention employs supersonic flame spraying technology, enabling high-entropy alloy powder to be sprayed onto the substrate surface at high speed and high energy, forming a dense coating with high bonding strength. During wear at 700 ℃, the synergistic lubrication effect of the generated Al2O3, Cr2O3 and MoO3 significantly improves the wear resistance of the coating. During hot corrosion, the addition of a small amount of Mo promotes the formation of the Al2O3 and Cr2O3 double oxide film, thereby improving the corrosion resistance of the HEA coating. The presence of Cu improves the thermal conductivity of the HEA coating.

[0027] 4. By controlling spraying parameters, such as spraying distance, kerosene flow rate and powder feeding rate, this invention can further optimize the performance of the coating, such as hardness, density and bonding strength, thereby improving the wear resistance and corrosion resistance of the coating. Attached Figure Description

[0028] Figure 1 Surface and cross-sectional morphology of HEA powder prepared by the mechanical alloying process: (a)(d)AlCrCu 0.75 Mo 0.25 Ni, (b)(e)AlCrCu 0.5 Mo 0.5 Ni, (c)(f) AlCrCu 0.25 Mo 0.75 Ni;

[0029] Figure 2 The surface morphology of the HEA coating prepared by the supersonic flame spraying process in this invention: (a) AlCrCu 0.75 Mo 0.25 Ni, (b)AlCrCu 0.5 Mo 0.5 Ni, (c)AlCrCu 0.25 Mo 0.75 Ni;

[0030] Figure 3 The cross-sectional morphology of the HEA coating prepared by the supersonic flame spraying process in this invention: (a)(d)AlCrCu 0.75 Mo 0.25 Ni, (b)(e)AlCrCu 0.5 Mo 0.5Ni, (c)(f) AlCrCu 0.25 Mo 0.75 Ni;

[0031] Figure 4 AlCrCu prepared by the stepwise mechanical alloying process 0.75 Mo 0.25 Ni HEA, AlCrCu 0.5 Mo 0.5 NiHEA and AlCrCu 0.25 Mo 0.75 Vickers hardness comparison chart of Ni HEA coatings;

[0032] Figure 5 AlCrCu prepared by the supersonic flame spraying process 0.75 Mo 0.25 Ni HEA, AlCrCu 0.5 Mo 0.5 NiHEA and AlCrCu 0.25 Mo 0.75 Comparison of high-temperature friction coefficient and wear rate of Ni HEA coating: (a) friction coefficient, (b) wear rate;

[0033] Figure 6 Cross-sectional morphology of EPMA after 700 °C hot corrosion for 100 h for the HEA coating prepared by the supersonic flame spraying process: (a) AlCrCu 0.75 Mo 0.25 Ni, (b)AlCrCu 0.5 Mo 0.5 Ni, (c) AlCrCu 0.25 Mo 0.75 Ni;

[0034] Figure 7 AlCrCu prepared by the supersonic flame spraying process 0.75 Mo 0.25 Ni HEA, AlCrCu 0.5 Mo 0.5 NiHEA and AlCrCu 0.25 Mo 0.75 The relationship between the thermal conductivity of the Ni HEA coating and temperature. Detailed Implementation

[0035] The above-mentioned and other technical features and advantages of the present invention will be described in more detail below with reference to the accompanying drawings.

[0036] Example 1

[0037] Weigh out Al, Cr, Cu, Mo, and Ni elemental powders with a molar ratio of 1:1:0.75:0.25:1 according to the required total weight, place them in a premixer and mix for 2 hours. After mixing, remove the powder and pour it into a ceramic-lined ball mill jar. Then, add grinding balls of different diameters at a grinding ball to powder mass ratio of 10:1, with a grinding ball ratio of 15 mm:10 mm:6 mm:5 mm = 1:4:2:1. Subsequently, perform vacuum treatment and purging with argon gas protective atmosphere, and use dry grinding method. Set the rotation speed to 220 rpm, rotate forward for 10 minutes and stop for 1 minute, rotate backward for 10 minutes and stop for 1 minute, and repeat the ball milling for 45 hours.

[0038] After ball milling, the HEA powder and grinding balls were separated. The resulting HEA powder was then sieved using metal sieves with mesh sizes of 15 μm and 45 μm. When using smaller mesh sieves, an ultrasonic vibrator was added to the edge of the sieve frame to assist in sieving. The ultrasonic vibrator frequency was a 3 Hz pulse frequency. After sieving through different mesh sieves, AlCrCu particles with a particle size distribution of 15–45 μm were obtained. 0.75 Mo 0.25 Ni HEA powder.

[0039] The AlCrCu metal surface high-temperature protection 0.75 Mo 0.25 The main steps in preparing a Ni HEA coating are:

[0040] S1: Before spraying, the surface of the 12CrMoV substrate is cleaned and degreased using detergent, alcohol, and acetone. Then, the surface after degreasing is roughened by sandblasting. The sandblasting material is 60-mesh brown corundum alumina (Al2O3), and the air valve is adjusted to achieve a sandblasting pressure of 3 MPa. After sandblasting, the surface roughness Ra of the substrate reaches 2.5 μm.

[0041] S2: Turn on the power, gas circuit switch and cooling water switch of the spraying equipment. Use oxygen as the combustion aid, kerosene as fuel, high-purity nitrogen as the powder carrier gas and air as the cooling medium. Fix the sample on the worktable and modify the robotic arm operation program to make the spraying distance reach 380 mm, the spraying speed 800 mm / s, and the spraying step distance 4 mm.

[0042] S3: Open the kerosene, oxygen, and liquid oxygen flow valves, adjusting the oxygen flow rate to 900 L / min, the kerosene flow rate to 28 L / h, and the liquid oxygen flow rate to 350 L / min. Ignite the kerosene flame to preheat the substrate surface, raising the surface temperature to 80~120 ℃. Turn on the powder feeder switch and adjust the powder feeding voltage to 3.3 V, maintaining the powder feeding rate at 32 g / min. After every 8 coats, use an air gun to blow and cool the coating surface, and use a micrometer to measure the coating thickness. When the coating temperature drops to approximately 70 ℃, restart the spraying equipment and continue spraying. Repeat this process until the coating thickness reaches approximately 250 μm.

[0043] Example 2

[0044] In this embodiment, the experimental conditions are the same as in Example 1. Al, Cr, Cu, Mo, and Ni elemental powders with a molar ratio of 1:1:0.5:0.5:1 are weighed according to the required total weight and placed in a premixer for 2 hours. After mixing, the powder is poured into a ceramic-lined ball mill jar. Then, grinding balls of different diameters are added at a mass ratio of 10:1 (grind balls to powder), with a grinding ball ratio of 15 mm:10 mm:6 mm:5 mm = 1:4:2:1. Subsequently, vacuum treatment and argon protective atmosphere are applied. Dry grinding is used with a rotation speed of 220 rpm. The rotation is repeated for 10 minutes forward and 1 minute pause, then 10 minutes reverse and 1 minute pause, for a total of 45 hours.

[0045] After ball milling, the composite powder and grinding balls were removed and separated. The resulting HEA powder was then sieved using metal sieves with mesh sizes of 15 μm and 45 μm. When using smaller mesh sieves, an ultrasonic vibrator was added to the edge of the sieve frame to assist in sieving. The ultrasonic vibrator frequency was a 3 Hz pulse frequency. After sieving through different mesh sieves, AlCrCu particles with a particle size distribution of 15–45 μm were obtained. 0.5 Mo 0.5 Ni HEA powder.

[0046] Preparation of AlCrCu using supersonic flame spraying 0.5 Mo 0.5 Ni HEA coating, the specific steps are the AlCrCu in Example 1. 0.75 Mo 0.25 Steps S1, S2, and S3 of the Ni HEA coating preparation method.

[0047] Example 3

[0048] In this embodiment, the experimental conditions are the same as in Example 1. Al, Cr, Cu, Mo, and Ni elemental powders with a molar ratio of 1:1:0.25:0.75:1 were weighed according to the required total weight and placed in a premixer for 2 hours. After mixing, the powder was poured into a ceramic-lined ball mill jar. Then, grinding balls of different diameters were added at a mass ratio of 10:1 (grind balls to powder), with a grinding ball ratio of 15 mm:10 mm:6 mm:5 mm = 1:4:2:1. Subsequently, vacuum treatment and argon gas protection atmosphere were applied, and dry grinding was performed. The rotation speed was set to 220 rpm, rotating forward for 10 minutes and stopping for 1 minute, then rotating backward for 10 minutes and stopping for 1 minute, and repeating the ball milling for 45 hours.

[0049] After ball milling, the composite powder and grinding balls were removed and separated. The resulting HEA powder was then sieved using metal sieves with mesh sizes of 15 μm and 45 μm. When using smaller mesh sieves, an ultrasonic vibrator was added to the edge of the sieve frame to assist in sieving. The ultrasonic vibrator frequency was a 3 Hz pulse frequency. After sieving through different mesh sieves, AlCrCu particles with a particle size distribution of 15–45 μm were obtained. 0.25 Mo 0.75 Ni HEA powder.

[0050] Preparation of AlCrCu using supersonic flame spraying 0.25 Mo 0.75 Ni HEA coating, the specific steps are the AlCrCu in Example 1. 0.75 Mo 0.25 Steps S1, S2, and S3 of the Ni HEA coating preparation method.

[0051] AlCrCu prepared in Examples 1, 2, and 3 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75 Ni HEA coating performance test:

[0052] The microhardness of the coatings was tested using a small-load Vickers hardness tester with a load of 2.94 N and a loading time of 15 s. Ten points were tested for each coating, and the average value was taken as the microhardness value of the coating. The test results are shown in Table 1.

[0053] Table 1. AlCrCu prepared in Examples 1, 2, and 3 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5Ni HEA coating and AlCrCu 0.25 Mo 0.75 Microhardness of Ni HEA coating

[0054]

[0055] (1) The test method for high-temperature wear performance of coating is as follows:

[0056] AlCrCu 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75 The high-temperature wear performance of the Ni HEA coating was tested in an HT-1000 high-temperature tribometer. The wear load was 10 N, the wear temperature was 700 ℃, the friction radius was 4 mm, and the wear time was 60 min. Al2O3 ceramic balls with a diameter of 6.35 mm were used as the grinding balls. The coefficient of friction of the coating was recorded using a computer connected to the tribometer. The wear volume of the coating was calculated using a KLA P7 probe profilometer, and the wear rate was calculated according to the wear rate formula.

[0057] The wear rate formula is: V(mm) 3 V is the wear volume, V = A × π × D, where A is the cross-sectional area of ​​the wear track, calculated by integrating the fitted data using Origin software, P (N) is the load, L (m) is the friction distance, and D is the wear track diameter.

[0058] Test and calculation results are as follows Figure 5 As shown, with AlCrCu 0.75 Mo 0.25 Ni HEA coating and AlCrCu 0.5 Mo 0.5 Compared to the Ni HEA coating, the test results show that the AlCrCu prepared in Example 3... 0.25 Mo 0.75 The Ni HEA coating exhibits the lowest wear rate at 700 ℃, giving it better wear resistance.

[0059] (2) The test method for the hot corrosion performance of the coating is as follows:

[0060] AlCrCu 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75The hot corrosion performance of the Ni HEA coating was tested in a high-temperature tube furnace at 700 °C for 100 h. After the test, the coating was removed and air-cooled. The corrosion weight gain of the three coatings was then measured using an electronic balance. The cross-sectional morphology of the three coatings was observed using a scanning electron microscope, and the cross-sectional elements of the coatings were analyzed using an EDS (Energy Dispersive X-ray Diode) instrument. The test results are as follows: Figure 6 As shown. With AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75 Compared to the Ni HEA coating, the AlCrCu prepared in Example 1 0.75 Mo 0.25 During the hot corrosion process, the Ni HEA coating forms a double oxide film with an inner layer of Al2O3 and an outer layer of Cr2O3. The continuous and dense oxide film can effectively improve the coating's resistance to hot corrosion.

[0061] (3) The test method for the thermal conductivity of the coating is as follows:

[0062] AlCrCu 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75 The thermal corrosion performance of the Ni HEA coating was tested using a laser thermal conductivity meter, with experimental temperatures ranging from room temperature (25℃) to 700℃. The test results are as follows: Figure 7 As shown. AlCrCu 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75 The room temperature thermal conductivity of the Ni HEA coating is 8.81, 7.35, and 7.00 W / (m·K), respectively. The thermal conductivity of AlCrCu at 700 ℃ is... 0.75 Mo 0.25 Ni HEA coating, AlCrCu 0.5 Mo 0.5 Ni HEA coating and AlCrCu 0.25 Mo 0.75 The thermal conductivity of the Ni HEA coatings were 18.65, 14.71, and 14.64 W / (m·K), respectively. The thermal conductivity of the substrate at 700 °C was 22.61 W / (m·K). Compared with AlCrCu... 0.5 Mo 0.5 Ni HEA coating and AlCrCu0.25 Mo 0.75 Compared to the Ni HEA coating, the AlCrCu prepared in Example 1 0.75 Mo 0.25 The Ni HEA coating has the highest thermal conductivity, reaching over 80% of that of the substrate at 700 ℃.

[0063] In summary, the AlCrCu alloy prepared by this invention provides high-temperature protection for the surface of key components. 0.75 Mo 0.25 Ni HEA coatings meet the requirements of high-temperature wear resistance, high-temperature corrosion resistance, and high thermal conductivity for metal surfaces. Optimal powder and coating preparation processes were obtained through improved methods and procedures. An AlCrCu alloy with a molar ratio of Al:Cr:Cu:Mo:Ni = 1:1:0.75:0.25:1 was prepared using a mechanical alloying process. 0.75 Mo 0.25 Ni HEA powder was used. The spraying process parameters were as follows: kerosene flow rate of 28 L / h, oxygen flow rate of 900 L / min, liquid oxygen flow rate of 350 L / min, spraying distance of 380 mm, spraying step size of 4 mm, spraying speed of 800 mm / s, powder feeding voltage of 3.3 V, and powder feeding rate of 32 g / min. The HEA coating prepared under these parameters has good high-temperature wear resistance and excellent heat corrosion resistance.

[0064] The above description is merely a preferred embodiment of the present invention and is illustrative rather than restrictive. Those skilled in the art will understand that many changes, modifications, and even equivalents can be made within the spirit and scope defined by the claims of the present invention, all of which will fall within the protection scope of the present invention.

Claims

1. A method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder, characterized in that, Includes the following steps: S1, mix Al, Cr, Cu, Mo and Ni elemental powders; S2, put the mixed powder obtained in step S1 into a ball mill jar, evacuate the jar and then introduce argon gas; S3. The mixed powder obtained in step S2 is ball-milled and sieved to obtain AlCrCuMoNi high-entropy alloy powder. The sieved high-entropy alloy powder is then subjected to vacuum annealing treatment at 800 °C for 2 h in a vacuum heat treatment furnace.

2. The method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder as described in claim 1, characterized in that, In step S1, the molar ratio of Al, Cr, Cu, Mo, and Ni elemental powders is: Al 25%, Cr 25%, Cu 6.25-18.75%, Mo 6.25-18.75%, and Ni 25%.

3. The method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder as described in claim 1, characterized in that, In step S1, a premixer is used for mixing. The speed of the premixer is 60 r / min and the mixing time is 2 h.

4. The method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder as described in claim 1, characterized in that, In step S2, the vacuum pump pressure is set to 10 Pa and the vacuuming time is 10 min during the evacuation process; high-purity argon gas is passed through at a pressure of 0.5 Pa for 3 min.

5. The method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder as described in claim 1, characterized in that, In step S3, the grinding balls used in the ball milling are ZrO2 grinding balls with diameters of 15mm, 10mm, 6mm and 5mm mixed in a ratio of 1:4:2:1, the mass ratio of grinding balls to powder is 10:1, the ball milling speed is 220 rpm, and the ball milling time is 45 h.

6. A high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy powder prepared by the preparation method according to any one of claims 1 to 5, characterized in that, The AlCrCuMoNi high-entropy alloy powder is AlCrCu 1-x Mo x Ni high-entropy alloy powder, wherein x = 0.25, 0.5 or 0.

75.

7. A method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy coating, characterized in that, Includes the following steps: (1) Before spraying, the surface of the metal substrate is degreased and cleaned, then the surface is roughened by sandblasting, and the roughened substrate is preheated. (2) Using oxygen-kerosene supersonic flame spraying technology, oxygen is used as a combustion aid, kerosene is used as fuel, high-purity nitrogen is used as a powder carrier gas, and air is used as a cooling medium to spray AlCrCuMoNi high-entropy alloy powder onto the surface of a metal substrate to form an AlCrCuMoNi high-entropy alloy coating.

8. The method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy coating as described in claim 7, characterized in that, In step (1), the sandblasting material is 60-mesh brown corundum sand, the sandblasting pressure is 3~5MPa, the surface roughness of the substrate after sandblasting reaches 2.5~3 μm, and the substrate preheating temperature reaches 80~120 ℃.

9. The method for preparing a high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy coating as described in claim 7, characterized in that, In step (2), the process of supersonic flame spraying technology is as follows: oxygen flow rate is 900 L / min, kerosene flow rate is 28 L / h, spraying distance is 380 mm, spraying step is 4 mm, spraying speed is 800 mm / s, powder feeding voltage is 3.3 V, and powder feeding rate is 32 g / min.

10. A high-temperature wear-resistant, corrosion-resistant, and thermally conductive AlCrCuMoNi high-entropy alloy coating prepared by the preparation method according to any one of claims 7 to 9, characterized in that, The AlCrCuMoNi high-entropy alloy coating has a thickness of 200~300 μm.

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