CN111334698A

CN111334698A - Wear-resistant high-entropy alloy containing modulation and demodulation decomposition structure and capable of generating hard phase and preparation method of wear-resistant high-entropy alloy

Info

Publication number: CN111334698A
Application number: CN202010178745.2A
Authority: CN
Inventors: 张楠楠; 金冰倩; 郝德喜; 马永亮; 于惠舒; 张悦; 李德元
Original assignee: Shenyang University of Technology
Current assignee: Shenyang University of Technology
Priority date: 2020-03-15
Filing date: 2020-03-15
Publication date: 2020-06-26
Anticipated expiration: 2040-03-15
Also published as: CN111334698B

Abstract

The invention relates to the technical field of alloy preparation, in particular to a wear-resistant high-entropy alloy containing a hard phase generated by regulating and controlling an amplitude modulation decomposition structure, wherein a V element is doped into a matrix of the AlCoCrFeNi high-entropy alloy to obtain AlCoCrFeNiV_X(x is 0.2, 0.4, 0.6, 0.8, 1.0, and x is a molar ratio), the hardness is 643.46HV, the friction coefficient is 0.335 ± 0.005, and the weight loss is 0.007 g. According to the invention, V element is added into the FCC and BCC biphase AlCoCrFeNi multi-principal element alloy, and an amplitude modulation decomposition structure (Ni-Al phase) and a hard phase (Cr-V phase) are formed in the process, so that the effects of grain boundary strengthening, fine grain strengthening and second phase strengthening are achieved on the basis of the original high-entropy alloy. In addition, the increase of the V content is helpful for forming more body-centered cubic structures, and the improvement of the wear resistance is realized due to the transformation of the structure and the phase.

Description

Wear-resistant high-entropy alloy containing modulation and demodulation decomposition structure and capable of generating hard phase and preparation method of wear-resistant high-entropy alloy

Technical Field

The invention relates to the technical field of alloy preparation, in particular to a wear-resistant high-entropy alloy containing a regulated amplitude modulation decomposition structure and a generated hard phase and a preparation method thereof.

Background

Different from the design concept of the traditional alloy, the design concept of the high-entropy alloy breaks through the design concept of one or two basic elements, and the high-entropy alloy has unique and excellent performances such as higher strength and hardness, excellent wear resistance, heat resistance, good high-temperature oxidation performance and the like due to four major effects, so that the high-entropy alloy has a good application prospect, and therefore the high-entropy alloy draws attention of people.

The high-entropy alloy has characteristics which are not possessed by other alloys because the high-entropy alloy contains more elements and each element exists as a principal element. Researchers summarize basic rules and characteristics of some high-entropy alloys through a large amount of research, and the basic rules and characteristics are called as four major effects of the high-entropy alloys. The thermodynamic high entropy effect makes the high mixing entropy result in that the free energy of the whole alloy system is very low, and atoms are difficult to move, so that various intermediate phases and intermetallic compounds are difficult to form, and a simple solid solution structure is prone to form. The lattice distortion effect on the structure can be used as solute or solvent atoms, and the difference of atomic radius is large, so that serious lattice distortion is generated, and the performance of the alloy is greatly enhanced. The slow diffusion effect on kinetics can produce spinodal decomposition structures as well as nanoparticles. The 'cocktail effect' in performance enables people to purposefully add alloy elements according to the alloy performance desired by people. For example, elements such as chromium, titanium, or nickel, which are relatively corrosion-resistant, may be added to improve the corrosion resistance of the alloy, and cobalt may be added to obtain an alloy having a high-temperature performance.

The high-entropy alloy is greatly concerned due to the excellent performance, but due to the numerous systems, some aspects are still less researched, and the alloying process mechanism of the novel alloy and the problems involved therein need to be deeply explored for further researching the solidified structure and performance of the novel alloy. Therefore, the vanadium element is added into the AlCoCrFeNi system to prepare the high-entropy alloy, and the influence of the vanadium element on the organization structure, the phase formation and the performance in a new alloy system is researched by controlling the content of the vanadium.

Disclosure of Invention

In order to overcome the technical problems, the invention provides the wear-resistant high-entropy alloy containing the regulated amplitude modulation decomposition structure and generating the hard phase, the V element is introduced into the high-entropy alloy AlCoCrFeNi system, and the lattice distortion effect of the high-entropy alloy is more obvious because the atomic radius of the V element is larger; in addition, with the addition of the element V, a reticular spinodal decomposition structure (Ni-Al phase) is gradually increased and refined, and meanwhile, a hard phase (Cr-V phase) with a hexagonal structure is generated at a grain boundary position in the high-entropy alloy, so that the obvious grain boundary strengthening effect is achieved, and the hardness and the wear resistance of the alloy are further improved.

The technical scheme for solving the technical problems is as follows:

a wear-resistant high-entropy alloy containing hard phase generated by regulating and controlling spinodal decomposition structure is prepared by doping V element into substrate of AlCoCrFeNi high-entropy alloy to obtain AlCoCrFeNiV_X(x is 0.2, 0.4, 0.6, 0.8 and 1.0, and x is a molar ratio) high-entropy alloy, wherein the regulation and control spinodal decomposition structure is a Ni-Al phase, and the generated hard phase is a Cr-V phase; the hardness of the high-entropy alloy is 643.46HV, the friction coefficient is 0.335 +/-0.005, and the weight loss is 0.007 g.

Another object of the invention is to produce wear resistant multi-principal element alloys by vacuum arc melting. By adding elements and forming two different phase structures, the performance is improved, and the alloy with good wear resistance is obtained.

The method comprises the following specific steps:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: al, Co, Cr, Fe, Ni and V with the purity higher than 99.9 percent are mixed according to the alloy components AlCoCrFeNiV_x(x is 0.2, 0.4, 0.6, 0.8, 1.0, and x is a molar ratio),cleaning each metal raw material, removing oil stains and impurities on the surface of each metal raw material, washing with alcohol, and drying for later use; before the step of cleaning each metal raw material, removing oxide scales on the surfaces of the metal raw materials in advance; the cleaning step is performed in an ultrasonic cleaner.

2) Cleaning a hearth of the vacuum arc furnace: the inner wall of the electric arc furnace is wiped by dipping the gauze with absolute ethyl alcohol, and the tungsten electrode is polished by fine abrasive paper until the tip of the tungsten electrode has metallic luster, so that the concentrated heat is facilitated, the efficiency is improved, and the waste heat caused by electric arc emission is prevented. Placing each spare metal raw material into a sample tank in a hearth of an electric arc furnace, and placing a titanium ingot into the rest sample tanks for oxygen absorption, further eliminating oxygen in the furnace and preventing the alloy from being oxidized in the smelting process; the method comprises the following steps of placing all metal raw materials in a sample tank in a hearth of an electric arc furnace, and arranging the metal raw materials from the bottom layer to the top layer of the sample tank of the electric arc furnace in sequence from low to high in melting point, so that the metal with low melting point is ensured to be on the lower layer, and the metal with high melting point is ensured to be on the upper layer, and the burning loss of the metal with low melting point is prevented.

3) Smelting, namely putting all metal raw materials into an electric arc furnace, vacuumizing until the pressure in the furnace is reduced to 5 × 10^-3Pa, then introducing high-purity argon to 1atm, starting electric arc at the position of a titanium ingot, keeping the arc starting current at 100A, continuously melting the titanium ingot for 1min, moving a tungsten electrode above each metal raw material, regulating the current to 250A and 300A respectively after each metal raw material is melted into the ingot, keeping the current for 1min respectively, turning off a power supply after the smelting is finished, turning over the alloy ingot after the alloy ingot is cooled on a water-cooling copper die, smelting again, repeating the steps for 5 times to ensure the uniformity of alloy components, and cooling to obtain the high-entropy alloy.

The invention has the beneficial effects that:

the invention provides a wear-resistant high-entropy alloy containing a regulated amplitude modulation decomposition structure and generating a hard phase and a preparation method thereof, the wear-resistant high-entropy alloy has a novel alloy component proportion, and is smelted for 5 times by using a vacuum arc furnace so as to ensure the uniformity of the alloy and prevent the alloy from being oxidized. AlCoCrFeNiV obtained by the invention_xThe surface metal luster of the multi-principal-element alloy is obvious, and the structure is relatively uniform. The main phase is BCC phase, and with the addition of V element, the alloyThe structure is obviously refined, a reticular amplitude modulation decomposition structure (Ni-Al phase) and a strip-shaped hard phase (Cr-V) phase appear, the hardness of the alloy is obviously improved, and the initial hardness value is 507.92HV when V is not added, and V_0.2The hardness value of the high-entropy alloy is 536.74HV, and then when the V content is continuously increased to 1.0, the alloy hardness reaches 643.46HV, which is increased by 143HV compared with the high-entropy alloy without the V element. When the V element is not added, the coefficient of friction of the alloy is large, the fluctuation is large, the abrasion condition of the alloy surface is not stable, the average friction coefficients of the alloy with the components are respectively 0.419, 0.396, 0.391, 0.372, 0.362 and 0.335 along with the addition of the V element, the alloy friction coefficient is obviously reduced, and the V element is added_1.0The friction coefficient of the high-entropy alloy is the lowest and reaches 0.335. In addition, the abrasion condition of the alloy is gradually improved, the depth and the width of the furrows on the surface are gradually reduced, and the flaking phenomenon is gradually reduced, which indicates that the frictional abrasion performance of the alloy is gradually improved. Although the wear surface without V element has no deeper furrow, a large amount of stripping can be obviously seen and is intermittently paved on the alloy surface, which also causes unstable wear condition and large friction coefficient fluctuation. V_0.2The alloy surface still has some flaking, but the flaking is obviously reduced, and the surface has deeper furrows, and the abrasion mechanism is abrasive abrasion. As the V content continues to increase, the wear condition is obviously improved, the surface spalling condition is gradually reduced, and the furrows are shallower. When the V content was increased to 1.0, the surface flaking was very small, there was essentially no deeper furrows and the wear surface was smoother. With the increase of the V content, the lattice distortion of the alloy is more and more serious, so that the alloy has higher and higher hardness, the friction coefficient is smaller and more stable, and the corresponding abrasion weight loss is smaller and smaller. And the abrasion weight loss of the components is small on the whole, the phase structure of alloy BCC plays a certain role, and the grain refinement and the lattice distortion generated after the V element is added play a certain role, so that the frictional abrasion performance of the alloy is improved.

The invention adds V element into FCC and BCC biphase AlCoCrFeNi multi-principal element alloy to form novel high-entropy alloy AlCoCrFeNiV_X(x is 0.2, 0.4, 0.6, 0.8, 1.0, and x is a molar ratio). In thatIn the process, an amplitude-modulated decomposition structure is formed and the wear-resistant high-entropy alloy of a hard phase is generated, and the hard phase (Cr-V) of a reticular amplitude-modulated decomposition structure (Ni-Al) phase plays roles in grain boundary strengthening, fine grain strengthening and second phase strengthening on the basis of the original high-entropy alloy. In addition, increasing the V content contributes to the formation of more body-centered cubic structures, and the improvement of wear resistance is achieved due to the transformation of the structure and phase.

Drawings

The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.

FIG. 1 shows AlCoCrFeNiV of comparative example 1 and examples 1 to 5 of the present invention_x(x ═ 0.2, 0.4, 0.6, 0.8, 1.0, and x is the molar ratio) XRD diffractogram;

FIG. 2 shows the microstructure of the alloy of comparative example 1 and examples 1 to 5 under a thermal field scanning electron microscope; wherein a is AlCoCrFeNi, and b is AlCoCrFeNiV_0.2C is AlCoCrFeNiV_0.4D is AlCoCrFeNiV_0.6E is AlCoCrFeNiV_0.8F is AlCoCrFeNiV;

FIG. 3 shows AlCoCrFeNiV of comparative example 1 and examples 1 to 5 of the present invention_xThe morphology of the intercrystalline structure of the multi-principal-element alloy; wherein a is X ═ 0, b is X ═ 0.2, c is X ═ 0.4, d is X ═ 0.6, e is X ═ 0.8, and f is X ═ 1.0;

FIG. 4 shows AlCoCrFeNiV of comparative example 1 and examples 1 to 5 of the present invention_xA multi-principal element alloy hardness diagram;

FIG. 5 shows AlCoCrFeNiV of comparative example 1 and examples 1 to 5 of the present invention_xA friction and wear coefficient diagram of the multi-principal element alloy;

FIG. 6 shows AlCoCrFeNiV of comparative example 1 and examples 1 to 5 of the present invention_xLoss of weight of the multi-principal element alloy after abrasion.

FIG. 7 shows AlCoCrFeNiV of comparative example 1 and examples 1 to 5 of the present invention_xAnd (5) a surface topography map of the multi-principal-element alloy after friction and wear.

Detailed Description

Example 1:

a preparation method of wear-resistant high-entropy alloy containing a regulated amplitude modulation decomposition structure and generating a hard phase comprises the following specific steps:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: al, Co, Cr, Fe, Ni and V elementary metals with the purity higher than 99.9 percent are mixed according to the molar ratio of alloy components AlCoCrFeNiV_0.2Calculating the mass ratio, respectively preparing, cleaning each metal raw material, removing oil stains and impurities on the surface of each metal raw material, washing with alcohol, and drying for later use; before the cleaning step of each metal raw material, removing oxide scales on the surfaces of the metal raw materials such as Al, Co, V and the like in advance; the cleaning step is carried out in an ultrasonic cleaning machine, the metal raw materials are placed into a beaker, then absolute ethyl alcohol is poured into the beaker, the absolute ethyl alcohol completely submerges the metal raw materials, then the beaker is placed into the ultrasonic cleaning machine, alcohol is also poured into the ultrasonic cleaning machine, and then the cleaning is carried out for 5 min.

3) Smelting, namely putting all metal raw materials into an electric arc furnace, vacuumizing until the pressure in the furnace is reduced to 5 × 10^-3Pa, then introducing high-purity argon to 1atm, starting electric arc at the position of a titanium ingot with the arc starting current of 100A, continuously melting the titanium ingot for 1min, moving a tungsten electrode above each metal raw material, adjusting the current to 250A and 300A respectively after each metal raw material is melted into the ingot, keeping for 1min respectively, closing a power supply after the melting is finished, turning over the alloy ingot after the alloy ingot is cooled on a water-cooled copper mold, melting again, repeating the steps for 5 times to ensure the uniformity of alloy components, and cooling to obtain the alloy ingotHigh entropy alloy. The hardness of the high-entropy alloy obtained in the embodiment is 643.46HV, the friction coefficient is 0.335 +/-0.005, and the weight loss is 0.007 g.

Example 2:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: al, Co, Cr, Fe, Ni and V elementary metals with the purity higher than 99.9 percent are mixed according to the molar ratio of alloy components AlCoCrFeNiV_0.4The mass ratios were calculated and prepared separately, and the procedure was the same as in example 1. The hardness of the high-entropy alloy obtained in the embodiment is 643.46HV, the friction coefficient is 0.335 +/-0.005, and the weight loss is 0.007 g.

Example 3:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: al, Co, Cr, Fe, Ni and V elementary metals with the purity higher than 99.9 percent are mixed according to the molar ratio of alloy components AlCoCrFeNiV_0.6The mass ratios were calculated and prepared separately, and the procedure was the same as in example 1.

Example 4:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: al, Co, Cr, Fe, Ni and V elementary metals with the purity higher than 99.9 percent are mixed according to the molar ratio of alloy components AlCoCrFeNiV_0.8The mass ratios were calculated and prepared separately, and the procedure was the same as in example 1.

Example 5:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: the Al, Co, Cr, Fe, Ni and V elementary metals with the purity higher than 99.9 percent are respectively prepared according to the mass ratio calculated by the molar ratio of the alloy components AlCoCrFeNiV, and the subsequent steps are the same as the example 1.

Comparative example 1:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: the Al, Co, Cr, Fe, Ni and V elementary metals with the purity higher than 99.9 percent are respectively prepared according to the calculated mass ratio of the molar ratio of the alloy components AlCoCrFeNi, and the subsequent steps are the same as the example 1.

The following table 1 shows the surface element component contents of the high-entropy alloys of examples 1 to 5 of the present invention and comparative example 1 after frictional wear.

TABLE 1

	Alloy (I)	Al	Co	Cr	Fe	Ni	V	O
									Example 1	AlCoCrFeNiV_0.2	14.15	16.60	16.73	16.17	16.07	3.53	16.75
Example 2	AlCoCrFeNiV_0.4	15.50	16.40	16.49	16.50	15.97	7.27	11.87
									Example 3	AlCoCrFeNiV_0.6	14.34	15.33	15.84	14.70	14.88	8.99	15.91
Example 4	AlCoCrFeNiV_0.8	12.51	14.50	14.91	13.86	14.31	10.31	19.59
									Example 5	AlCoCrFeNiV	12.87	14.81	15.10	13.94	15.65	13.49	15.13
Comparative example 1	AlCoCrFeNi	14.57	16.61	16.78	16.42	16.43	0.00	19.19

FIGS. 1 to 7 show the respective experiments of AlCoCrFeNiV of comparative example 1 and examples 1 to 5_x(x is 0, 0.2, 0.4, 0.6, 0.8, 1.0, x is a molar ratio) of:

the detection of the alloy phase structure was carried out by XRD (Shimadzu 7000, Kyoto, Japan) diffraction; observing the microstructure morphology of the alloy under a thermal field scanning electron microscope (SU8010, Hitachi, Japan) including the morphology of a reticular amplitude modulation decomposition tissue (Ni-Al phase) and a hard phase (Cr-V phase) among dendrites; detecting the frictional wear performance in a multifunctional surface tester (MFT-4000, China) and obtaining a friction coefficient diagram; observing the surface morphology of the alloy after friction and wear by using a thermal field scanning electron microscope (SU8010, Hitachi, Japan); and (4) carrying out weight loss test on the alloy by using an electronic balance and obtaining a weight loss chart.

As can be seen from FIG. 1, the alloy generally exhibits a single-phase BCC structure, with a small amount of B2 phase, which is a Ni-Al phase, appearing in the samples having V contents of 0.8 and 1.0, and the Ni-Al phase peak being weak in the sample having V content of 0, while the Ni-Al phase diffraction peak being relatively strong in the sample having V content of 1.0, and containing much Ni-Al phase, but the bulk of the sample still has a BCC structure.

As can be seen from fig. 2, the alloy generally exhibits typical as-cast Dendrites (DR) and interdendritic structures (ID), and when no V element is added, the alloy has a columnar equiaxed structure with larger grains and interdendritic structures as Cr-rich phases; when the vanadium content is gradually increased to 0.4, the alloy structure is still equiaxed crystal, but the structure is obviously refined and has a tendency of transforming from equiaxed crystal to dendrite, the interdendritic structure in the alloy is mainly Cr-V phase, the Cr-V phase is connected into pieces around the equiaxed crystal, when the V content is 0.6mol, the alloy structure presents dendrite structure, when the V content is increased to 1.0mol, the alloy structure is transformed into typical dendrite structure, the dendrite orientation is obvious, the crystal grains are also obviously refined compared with V0.6, and some Cr-V phase is still distributed among dendrites.

As is clear from fig. 3, when the V element is not added, no particular phase appears in the interdendritic region, some Cr-rich particles are distributed in the vicinity of the interdendritic region, and a reticular spinodal decomposition structure (Ni — Al phase), which is denoted by SD in the drawing, is distributed around the Cr-rich particles. The samples with the V content of 0.2mol have Cr-V phases in interdendritic regions, the Cr-V phases are slowly connected and distributed among interdendritic regions along with the increase of the V content, and the samples with the V content of 1.0 have lath-shaped Cr-V phases. Although there are network Ni-Al phases in the vicinity of the dendrite boundaries, XRD has no significant diffraction peaks in the samples of V0.2, V0.4 and V0.6 because of its small content. The B2 phase in the alloy is clearly seen from the (g) and (h) graphs, and the microstructure of the sample V1.0 is clearly thinner than that of the sample V0.

As can be seen from FIG. 4, when the V element is not added, the initial hardness value of the alloy is 507.92HV, the hardness value of a sample with V0.2 is 536.74HV, and then the V content is continuously increased to 1.0, the alloy hardness reaches 643.46HV, which is increased by 143HV compared with the sample without the V element, and in addition, the increase range of the alloy hardness value is smaller and smaller with the addition of the V element, which indicates that the increase of the V element on the alloy hardness is smaller and smaller. The lattice distortion generated by the alloy after the V element is added is the main reason for improving the hardness of the alloy, the atomic radii of Al, Co, Cr, Fe, Ni and other elements in the alloy are respectively 0.143, 0.125, 0.128, 0.126 and 0.124pm, the atomic radius of the V element is 0.134pm, the atomic radius is next to that of the Al element, the alloy can generate serious lattice distortion after the V element is added, but the lattice distortion effect does not linearly increase along with the V content along with the increase of the V content, so the subsequent hardness value increase range is smaller and smaller. In addition, the alloy structure is obviously refined after the V element is added, and the mechanical property of the alloy is also improved by refining the crystal grains.

As can be seen from FIG. 5, when the V element is not added, the coefficient of friction of the alloy is large, the fluctuation is large, which indicates that the abrasion of the alloy surface is not stable, and the average friction coefficients of the alloys of the components are respectively 0.419, 0.396, 0.391, 0.372, 0.362 and 0.335 with the addition of the V element, so that the coefficient of friction of the alloy is obviously reduced, the coefficient of friction of the sample of V1.0 is the lowest and reaches 0.335, and the curve fluctuation is small, which indicates that the abrasion of the alloy is stable.

As can be seen from fig. 6, the frictional wear performance of the alloy is in direct proportion to the hardness of the alloy, and as the V content increases, the lattice distortion of the alloy becomes more and more severe, so that the hardness of the alloy becomes higher and higher, the friction coefficient becomes smaller and is stable, and the corresponding wear weight loss becomes smaller and smaller. And the abrasion weight loss of the components is small on the whole, the phase structure of alloy BCC plays a certain role, and the grain refinement and the lattice distortion generated after the V element is added play a certain role, so that the frictional abrasion performance of the alloy is improved.

As can be seen from FIG. 7, with the addition of element V, the wear of the alloy gradually improved, the depth and width of furrows on the surface gradually decreased, and the flaking phenomenon gradually decreased, indicating that the frictional wear performance of the alloy gradually improved. Although the wear surface without V element has no deeper furrow, a large amount of stripping can be obviously seen and is intermittently paved on the alloy surface, which also causes unstable wear condition and large friction coefficient fluctuation. The surface of the test specimen with V0.2 still has some flaking, but the flaking is obviously reduced, and deeper furrows appear on the surface, and the abrasion mechanism is abrasive abrasion. As the V content continues to increase, the wear condition is obviously improved, the surface spalling condition is gradually reduced, and the furrows are shallower. When the V content was increased to 1.0, the surface flaking was very small, there was essentially no deeper furrows and the wear surface was smoother.

The invention adds V element into FCC and BCC biphase AlCoCrFeNi multi-principal element alloy to form novel high-entropy alloy AlCoCrFeNiV_x(x is 0.2, 0.4, 0.6, 0.8, 1.0, and x is a molar ratio). In the process, an amplitude-modulated decomposition structure and a wear-resistant high-entropy alloy of a hard phase are formed, and the hard phase (Cr-V phase) of a reticular amplitude-modulated decomposition structure (Ni-Al phase) plays roles in grain boundary strengthening, fine grain strengthening and second phase strengthening on the basis of the original high-entropy alloy. In addition, increasing the V content contributes to the formation of more body-centered cubic structures, and the improvement of wear resistance is achieved due to the transformation of the structure and phase.

The above description is only a preferred embodiment of the present invention, and is not intended to limit the present invention in any way, and all simple modifications and equivalent variations of the above embodiment according to the present invention are within the scope of the present invention.

Claims

1. The wear-resistant high-entropy alloy containing the controlled spinodal decomposition structure and capable of generating the hard phase is characterized in that the high-entropy alloy is obtained by doping a V element into a matrix of the AlCoCrFeNi high-entropy alloy to obtain the AlCoCrFeNiV_X(x is 0.2, 0.4, 0.6, 0.8 and 1.0, and x is a molar ratio) high-entropy alloy, wherein the regulation and control spinodal decomposition structure is a Ni-Al phase, and the generated hard phase is a Cr-V phase; the hardness of the high-entropy alloy is 643.46HV, the friction coefficient is 0.335 +/-0.005, and the weight loss is 0.007 g.

2. The method for preparing the wear-resistant high-entropy alloy containing the regulated spinodal decomposition structure and generating the hard phase according to claim 1, is characterized by comprising the following steps of:

1) accurately weighing all metal raw materials required by the alloy ingot casting by using an electronic balance: al, Co, Cr, Fe, Ni and V with the purity higher than 99.9 percent are mixed according to the alloy components AlCoCrFeNiV_x(x is 0.2, 0.4, 0.6, 0.8 and 1.0, and x is a molar ratio) respectively, cleaning each metal raw material, removing oil stains and impurities on the surface of each metal raw material, washing with alcohol, and drying for later use;

2) cleaning a hearth of the vacuum arc furnace: dipping absolute ethyl alcohol by using gauze to wipe the inner wall of the electric arc furnace, polishing a tungsten electrode by using fine abrasive paper, placing each spare metal raw material into a sample groove in a hearth of the electric arc furnace, and placing a titanium ingot into the rest sample grooves for absorbing oxygen and further eliminating oxygen in the furnace;

3. The method for preparing the wear-resistant high-entropy alloy containing the controlled spinodal decomposition structure and generating the hard phase according to claim 2, wherein before the step of cleaning each metal raw material in the step 1), the surface of each metal raw material is subjected to scale removal treatment in advance; the cleaning step is performed in an ultrasonic cleaner.

4. The method for preparing the wear-resistant high-entropy alloy containing the regulated spinodal decomposition structure and generating the hard phase according to claim 2, wherein the tungsten electrode is polished in the step 2) until the tip of the tungsten electrode has metallic luster.

5. The method for preparing the wear-resistant high-entropy alloy containing the controlled spinodal decomposition structure and generating the hard phase according to claim 2, wherein the standby metal raw materials in the step 2) are placed in a sample tank in a hearth of an electric arc furnace and are sequentially arranged from the bottom layer to the top layer of the sample tank of the electric arc furnace according to the sequence that the melting points of the metal raw materials are from low to high.