A high-strength, high-toughness, low-activation refractory multi-component alloy, its preparation method and application

Abstract

This invention discloses a high-strength, high-toughness, low-activation refractory multi-component alloy, its preparation method, and its applications. The alloy is composed of three low-activation refractory elements: W, Cr, and Zr, as well as O introduced through contact with the environment during preparation. By atomic percentage, it consists of 75.0–91.5% W, 7.0–16.5% Cr, 1.0–5.5% Zr, and 0.5–3.0% O; wherein the atomic fraction ratio of Cr to Zr is 1.5–5.5, and the atomic fraction ratio of Zr to O is 0.5–2. This multi-component alloy retains many advantages of pure W while significantly improving room-temperature strength and toughness. It also possesses excellent properties such as high density, high strength and toughness, low activation, and high-temperature resistance, making it suitable as a high-performance heavy alloy for applications in aerospace, defense industry, nuclear energy, and many other fields.

Description

Technical Field

[0001] This invention belongs to the field of metallic materials and their preparation technology, specifically relating to a high-strength, high-toughness, high-density, low-activation, refractory multi-component alloy, its preparation method, and its application. Background Technology

[0002] Tungsten alloys, with their high thermal conductivity, high melting point, low activation, low tritium retention, excellent sputtering resistance, and high-temperature stability, have shown broad application prospects in aerospace, defense, and nuclear energy industries. However, they exhibit significant brittleness at room temperature, and their strength and toughness are limited at both high and low temperatures, restricting their application as key structural materials. Although alternatives exist, such as heavy tungsten alloys (W-Ni-Fe / Cu), their density is significantly reduced, and the Ni and Fe elements they contain are easily activated under irradiation. Cu, on the other hand, is limited by its inherent low melting point, making it difficult to meet the stringent requirements of high density, refractory properties, and low activation in extreme service environments. Notably, the search for tungsten-based alloys that combine high strength and toughness, high density, and a body-centered cubic (BCC) structure also faces significant challenges. For example, binary W-Re alloys, ternary W-Cr-V alloys, and W-Ta-Nb-Mo-V tungsten-based refractory high-entropy alloys all exhibit significant brittleness at room temperature, and this brittleness intensifies with increasing density. Therefore, designing and preparing novel alloys that combine high strength and toughness, high density, low activation, and refractory properties has become a key challenge and research hotspot in this field. Summary of the Invention

[0003] The purpose of this section is to outline some aspects of embodiments of the present invention and to briefly describe some preferred embodiments. Simplifications or omissions may be made in this section, as well as in the abstract and title of this application, to avoid obscuring the purpose of these documents; however, such simplifications or omissions should not be construed as limiting the scope of the invention.

[0004] In view of the problems existing in the above and / or prior art, the present invention is proposed.

[0005] One objective of this invention is to provide a high-strength, high-toughness, low-activation refractory multi-component alloy. This alloy uses low-activation refractory elements W, Cr, and Zr, as well as O introduced from the environment during the preparation process. By optimizing the ball milling and sintering process parameters, the size of the matrix grains and the size and distribution of the second-phase particles are precisely controlled, thereby achieving a good toughness match while ensuring high strength and high density, so as to meet its application requirements in aerospace, defense industry, nuclear energy and other fields.

[0006] To solve the above-mentioned technical problems, the present invention provides the following technical solution: a high-strength, high-toughness, low-activation, refractory multi-component alloy, wherein the alloy matrix is ​​a solid solution with a BCC structure and contains a small amount of in-situ self-generated and dispersed tetragonal or monoclinic nano-ceramic particles. The alloy, by atomic percentage, consists of 75.0–91.5% W, 7.0–16.5% Cr, 1.0–5.5% Zr, and O (atomic fraction 0.5–3.0%) absorbed from the environment during the preparation process; wherein the atomic fraction ratio of Cr to Zr is 1.5–5.5, and the atomic fraction ratio of Zr to O is 0.5–2.

[0007] As a preferred embodiment of the high-strength, high-toughness, high-density, low-activation refractory multi-component alloy of the present invention, it is composed of W 87.0~90.5%, Cr 8.0%, Zr 1.5~5.0% and O 0.5~3.0% by atomic percentage.

[0008] This invention utilizes a multi-component alloy design approach, using high-purity W, Cr, and Zr powders as raw materials and taking advantage of oxygen in the environment to obtain a low-activation refractory alloy with high strength, high density, and good deformability.

[0009] W, as the base metal, ensures the alloy's high strength, high density, low activation, and refractory properties. Cr, as the main solid solution element, has low activation and high solid solubility with W; its appropriate addition can strengthen the alloy through solid solution. Furthermore, due to its inherent properties, Cr also improves the alloy's corrosion resistance. Zr, as a small additive element, forms ZrO2 in situ during sintering, which plays a crucial role in refining grains, purifying grain boundaries, pinning dislocations, and improving brittleness.

[0010] As a preferred embodiment of the high-strength, high-toughness, high-density, low-activation, refractory multi-component alloy of the present invention, the alloy has the following characteristics:

[0011] (i) Second-phase nanoparticles with tetragonal and monoclinic structures are dispersed in a BCC disordered solid solution matrix;

[0012] (ii) Mass density is 16.0–18.0 g / cm³ 3 ;

[0013] (iii) The compressive yield strength at room temperature is 2050–2500 MPa;

[0014] (iv) The ultimate compressive strength at room temperature is 2500–3850 MPa;

[0015] (v) The compressive strain value at room temperature is 5–25%;

[0016] (vi) Vickers hardness HV30 is 600-950.

[0017] Another object of the present invention is to provide a method for preparing a high-strength, high-toughness, high-density, low-activation, refractory multi-component alloy as described above, comprising: taking each component raw material according to the atomic percentage of the alloy, ball milling under vacuum or inert gas protection, sieving the powder and sintering under vacuum or inert gas protection to obtain the alloy material.

[0018] In a preferred embodiment of the preparation method described in this invention, the ball milling uses cemented carbide balls, the ball milling speed is 200-500 rpm, and the total ball milling time is 5-50 h.

[0019] As a preferred embodiment of the preparation method described in this invention, the sintering can be performed using methods such as spark plasma sintering, rapid hot pressing sintering, or gas pressure sintering.

[0020] In a preferred embodiment of the preparation method described in this invention, the alloy is sintered under vacuum or inert gas protection conditions, maintaining the furnace pressure at 10–10 ppm. 5 Pa.

[0021] In a preferred embodiment of the preparation method described in this invention, the mass ratio of the cemented carbide ball to all powders of each alloy component is 5:1 to 10:1.

[0022] In a preferred embodiment of the preparation method described in this invention, the sintering heating rate is 10–100 °C / min, and the sintering temperature is 1400–1800 °C.

[0023] As a preferred embodiment of the preparation method described in this invention, the sintering holding time is 3 to 20 minutes, and the holding pressure during sintering is 10 to 50 MPa.

[0024] As a preferred embodiment of the high-strength, high-toughness, low-activation, refractory multi-component alloy of the present invention, wherein: the raw materials of each component are pure metal powders with a purity higher than 98 wt.%.

[0025] Compared with the prior art, the present invention has the following beneficial effects:

[0026] The alloy prepared by this invention uses refractory and low-activation elements. By optimizing the Cr / Zr ratio, it maintains the BCC structure while possessing high strength, high density and excellent room temperature toughness. It effectively overcomes the problem of significant room temperature brittleness in existing tungsten-based high-density refractory alloys and shows broad application prospects in aerospace, defense industry and nuclear energy fields. Attached Figure Description

[0027] To more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the description of the embodiments will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort. Wherein:

[0028] Figure 1 These are scanning electron microscope (SEM) images and particle size distribution curves of the alloy ball-milled powders in Examples 1, 2, 3, 4, 5, 6, and 7 of this invention.

[0029] Figure 2 These are the XRD patterns of the ball-milled alloy powders from Examples 1, 2, 3, 4, 5, 6, and 7 of this invention, after 0-25 hours.

[0030] Figure 3 This is a real-time change curve of temperature and pressure head displacement during the alloy sintering process of Embodiment 1 of the present invention.

[0031] Figure 4 This is the XRD pattern of the alloy bulk material in Example 1 of the present invention.

[0032] Figure 5 This is a scanning electron microscope image of the alloy bulk material in Embodiment 1 of the present invention.

[0033] Figure 6 This is a Vickers hardness indentation morphology image of the alloy block material in Embodiment 1 of the present invention;

[0034] Figure 7 This is a room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 1 of the present invention.

[0035] Figure 8 This is a fracture morphology diagram of the alloy block material in Embodiment 1 of the present invention.

[0036] Figure 9 This is a real-time change curve of temperature and pressure head displacement during the alloy sintering process of Embodiment 2 of the present invention.

[0037] Figure 10 This is the XRD pattern of the alloy bulk material in Example 2 of the present invention.

[0038] Figure 11 This is a scanning electron microscope image of the alloy bulk material in Embodiment 2 of the present invention.

[0039] Figure 12 This is a Vickers hardness indentation morphology image of the alloy block material in Embodiment 2 of the present invention;

[0040] Figure 13 This is the room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 2 of the present invention.

[0041] Figure 14 This is a real-time change curve of temperature and pressure head displacement during the alloy sintering process of Embodiment 3 of the present invention.

[0042] Figure 15 This is the XRD pattern of the alloy bulk material in Example 3 of the present invention.

[0043] Figure 16 These are scanning electron microscope images and elemental distribution diagrams of the alloy bulk material in Embodiment 3 of the present invention.

[0044] Figure 17 This is a Vickers hardness indentation morphology image of the alloy block material in Embodiment 3 of the present invention;

[0045] Figure 18 This is the room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 3 of the present invention.

[0046] Figure 19 This is a scanning electron microscope image of the alloy bulk material in Embodiment 4 of the present invention.

[0047] Figure 20 This is a Vickers hardness indentation morphology image of the alloy block material in Example 4 of the present invention;

[0048] Figure 21 This is the room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 4 of the present invention.

[0049] Figure 22 This is a scanning electron microscope (SEM) image of the alloy bulk material in Embodiment 5 of the present invention.

[0050] Figure 23 This is a Vickers hardness indentation morphology image of the alloy block material in Embodiment 5 of the present invention;

[0051] Figure 24 This is the room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 5 of the present invention.

[0052] Figure 25 This is a scanning electron microscope (SEM) image of the alloy bulk material in Embodiment 6 of the present invention.

[0053] Figure 26 This is a Vickers hardness indentation morphology image of the alloy block material in Embodiment 6 of the present invention;

[0054] Figure 27 This is the room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 6 of the present invention.

[0055] Figure 28 This is a scanning electron microscope image of the alloy bulk material in Embodiment 7 of the present invention.

[0056] Figure 29 This is a Vickers hardness indentation morphology image of the alloy block material in Embodiment 7 of the present invention;

[0057] Figure 30 This is the room temperature compression engineering stress-engineering strain curve of the alloy block material in Embodiment 7 of the present invention.

[0058] Figure 31 This is the room temperature compressive stress-strain curve of the high-strength, high-density multi-component alloy of Comparative Example 1. Detailed Implementation

[0059] To make the above-mentioned objects, features and advantages of the present invention more apparent and understandable, the specific embodiments of the present invention will be described in detail below with reference to the examples in the specification.

[0060] Many specific details are set forth in the following description in order to provide a full understanding of the invention. However, the invention may also be practiced in other ways different from those described herein, and those skilled in the art can make similar extensions without departing from the spirit of the invention. Therefore, the invention is not limited to the specific embodiments disclosed below.

[0061] Secondly, the term "one embodiment" or "embodiment" as used herein refers to a specific feature, structure, or characteristic that may be included in at least one implementation of the present invention. The phrase "in one embodiment" appearing in different places in this specification does not necessarily refer to the same embodiment, nor is it a single or selective embodiment that is mutually exclusive with other embodiments.

[0062] Unless otherwise specified, all raw materials used in the examples are commercially available. Example 1

[0063] According to the chemical formula W 90.5 Cr 8.0 Zr 1.5 The raw materials were prepared using metal powders corresponding to each pure element, with a purity of 99.9% and a particle size of 1-3 μm. Under argon protection, the metal powder was placed into a ball mill jar containing cemented carbide balls and sealed tightly. The ball-to-powder ratio was 5:1. The ball mill jar was then loaded into a ball mill and run for 25 hours (to reduce temperature rise during milling, the mill was stopped for 5 minutes of cooling after 25 minutes of forward and 25 minutes of reverse rotation). Every 5 hours of milling, the ball mill jar was transferred to a glove box for powder crushing, after which milling continued. The milling speed was 225 rpm. After milling, the jar was allowed to cool completely at room temperature.

[0064] Open the ball mill jar under argon protection, pass the ball-milled powder through a 200-mesh standard sieve, and then pack the powder into a mold or store it under an inert gas for later use.

[0065] The pre-alloyed powder, after ball milling and sieving, was loaded into a graphite mold protected and lubricated with graphite paper and pre-pressed at 30 MPa. Subsequently, it was sintered under vacuum by discharge plasma (vacuum degree 10~100 Pa) at a temperature of 1700 ℃, a heating rate of 20~50 ℃ / min, a holding time of 7 min, and a holding pressure of 50 MPa. After sintering, the furnace door was opened below 100 ℃, and the alloy sample was demolded and removed.

[0066] Depend on Figures 1-8 It can be seen that with the extension of ball milling time, the grain size decreases, and the alloying of the powder tends to be complete. After ball milling for 25 h, the D... v (50) is 0.54 μm. After SPS sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure with an average grain size of about 1.23 μm. The matrix contains tetragonal and monoclinic ZrO2 structures generated in situ during sintering.

[0067] Chemical composition analysis revealed that the alloy's chemical composition is W. 88.1 Cr 7.8 Zr 1.5 O 2.6 (Oxygen is mainly introduced through contact with the environment during ball milling and sintering.) The alloy has a mass density of 17.9 g / cm³. 3 The Vickers hardness (HV30) is 658, the room temperature compressive yield strength is about 2250 MPa, the compressive strength is about 3121 MPa, the compressive strain value after correction of the theoretical elastic modulus is about 17.1%, and the fracture morphology shows a mixed fracture mode of intergranular fracture and transgranular fracture, exhibiting excellent mechanical properties. Example 2

[0068] The difference from Example 1 is that the sintering temperature of SPS is 1800 °C.

[0069] Depend on Figures 1-2 and Figures 9-13 It can be seen that with the extension of ball milling time, the grain size decreases, and the alloying of the powder tends to be complete. After ball milling for 25 h, the D... v (50) is 0.54 μm. After SPS sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure with an average grain size of about 0.86 μm. The matrix contains tetragonal and monoclinic ZrO2 structures generated in situ during sintering.

[0070] Chemical composition analysis revealed that the alloy's chemical composition is W. 88.2 Cr 7.8 Zr 1.5 O 2.5(Oxygen is mainly introduced through contact with the environment during ball milling and sintering.) The alloy has a mass density of 17.9 g / cm³. 3 It has a Vickers hardness (HV30) of 669, a room temperature compressive yield strength of approximately 2300 MPa, a compressive strength of approximately 2672 MPa, and a compressive strain value of approximately 10.9% after correction for the theoretical elastic modulus, exhibiting excellent mechanical properties. Example 3

[0071] The difference from Example 1 is that the sintering temperature of SPS is 1600 °C.

[0072] Depend on Figures 1-2 and Figures 14-18 It can be seen that with the extension of ball milling time, the grain size decreases, and the alloying of the powder tends to be complete. After ball milling for 25 h, the D... v (50) is 0.54 μm. After SPS sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure with an average grain size of about 0.35 μm. The matrix contains tetragonal and monoclinic ZrO2 structures generated in situ during sintering.

[0073] Chemical composition analysis revealed that the alloy's chemical composition is W. 88.6 Cr 7.8 Zr 1.5 O 2.1 (Oxygen is mainly introduced through contact with the environment during ball milling and sintering.) The alloy has a mass density of 17.8 g / cm³. 3 It has a Vickers hardness (HV30) of 787, a room temperature compressive strength of approximately 3196 MPa, and a compressive strain value of approximately 3.3% after correction for the theoretical elastic modulus, exhibiting excellent mechanical properties. Example 4

[0074] The difference from Example 1 is that the sintering method is rapid hot pressing sintering, and the sintering temperature is 1400 ℃.

[0075] Depend on Figures 1-2 and Figures 19-21 It can be seen that with the extension of ball milling time, the grain size decreases and the alloying of the powder tends to be complete. The Dv(50) of the powder is 0.54 μm after ball milling for 25 h. After rapid hot pressing sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure with an average grain size of about 0.22 μm. The matrix contains tetragonal and monoclinic ZrO2 structures generated in situ during sintering.

[0076] Theoretical calculations show that the atomic ratio of Zr to O in this alloy is between 0.5 and 2; meanwhile, its theoretical density is not less than 16 g / cm³. 3The alloy has a Vickers hardness (HV30) of 901, a room temperature compressive strength of approximately 3742 MPa, and a compressive strain value of approximately 3.2% after correction for the theoretical elastic modulus, exhibiting excellent mechanical properties. Example 5

[0077] The difference from Example 4 is that this alloy is made according to the chemical formula W 89.0 Cr 8.0 Zr 3.0 Ingredients are prepared according to (atomic percentage).

[0078] Depend on Figures 1-2 and Figures 22-24 It can be seen that with the extension of ball milling time, the grain size decreases and the alloying of the powder tends to be complete. The Dv(50) of the powder is 0.54 μm after ball milling for 25 h. After rapid hot pressing sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure, and the tetragonal and monoclinic ZrO2 structures generated in situ during sintering are dispersed in the matrix.

[0079] Theoretical calculations show that the atomic ratio of Zr to O in this alloy is between 0.5 and 2; meanwhile, its theoretical density is not less than 16 g / cm³. 3 The alloy has a Vickers hardness (HV15) of 899, a room temperature compressive strength of approximately 3012 MPa, and a compressive strain value of approximately 0.9% after correction for the theoretical elastic modulus, exhibiting excellent mechanical properties. Example 6

[0080] The difference from Example 4 is that this alloy is made according to the chemical formula W 87.0 Cr 8.0 Zr 5.0 Ingredients are prepared according to (atomic percentage).

[0081] Depend on Figures 1-2 and Figures 25-27 It can be seen that with the extension of ball milling time, the grain size decreases and the alloying of the powder tends to be complete. The Dv(50) of the powder is 0.54 μm after ball milling for 25 h. After rapid hot pressing sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure with an average grain size of about 0.23 μm. The matrix contains tetragonal and monoclinic ZrO2 structures generated in situ during sintering.

[0082] Theoretical calculations show that the atomic ratio of Zr to O in this alloy is between 0.5 and 2; meanwhile, its theoretical density is not less than 16 g / cm³. 3 The alloy has a Vickers hardness (HV30) of 864, a room temperature compressive strength of approximately 3159 MPa, and a compressive strain value of approximately 0.9% after correction for the theoretical elastic modulus, exhibiting excellent mechanical properties. Example 7

[0083] The difference from Example 4 is that this alloy is made according to the chemical formula W 81.0 Cr 16.0 Zr 3.0 Ingredients are prepared according to (atomic percentage).

[0084] Depend on Figures 1-2 and Figures 28-30 It can be seen that with the extension of ball milling time, the grain size decreases and the alloying of the powder tends to be complete. The Dv(50) of the powder is 0.54 μm after ball milling for 25 h. After rapid hot pressing sintering, the alloy matrix is ​​a W and Cr rich BCC solid solution structure, and the tetragonal and monoclinic ZrO2 structures generated in situ during sintering are dispersed in the matrix.

[0085] Theoretical calculations show that the atomic ratio of Zr to O in this alloy is between 0.5 and 2; meanwhile, its theoretical density is not less than 16 g / cm³. 3 The alloy has a Vickers hardness (HV15) of 668, a room temperature compressive strength of approximately 2360 MPa, and a compressive strain value corrected for the theoretical elastic modulus of approximately 3.3%. Comparative Example 1

[0086] According to the literature HU X, LIU X, YAN D, et al. A high-density non-equiatomic WTaMoNbV high-entropy alloy: Alloying behavior, microstructure and mechanical properties [J]. Journal of Alloys and Compounds, 2022, 894:162505. This literature reports a non-equiatomic W... 35 Ta 35 Mo 10 Nb 10 V 10 The (at.%) alloy system was prepared by spark plasma sintering (1600~1800 ℃, 1~10 min) after ball milling for 55 h. Figure 31 As shown, the sample sintered at 1700 ℃ exhibited the best performance, with a density of 14.7 g / cm³, a room temperature compressive strength of approximately 2500 MPa, and no macroscopic plastic deformation was observed.

[0087] Comparing Example 5 and Example 7, it can be seen that excessive addition of Cr will lead to a decrease in the strength of the alloy. Therefore, the amount of Cr element should be appropriate.

[0088] Comparing Examples 1, 2, 3, 4, 5, and 6 with Comparative Example 1, it can be seen that the high-density, high-strength alloys outside the composition range of the present invention, under the same or similar sintering processes, have lower overall performance than the high-strength, high-toughness, high-density multi-component alloys of the present invention.

[0089] Pure tungsten and tungsten-based materials have broad application prospects in aerospace, defense, and nuclear energy fields due to their high melting point, excellent sputter resistance, outstanding high-temperature stability, low activation, and low tritium retention. However, their significant room-temperature brittleness severely limits their application range. This invention successfully prepares a high-strength, high-toughness, and high-density multi-component alloy by introducing refractory and low-activation elements Cr and Zr into a pure tungsten matrix, precisely controlling the Cr / Zr ratio, and utilizing in-situ oxygen in the environment to generate a strengthening phase. This alloy significantly improves room-temperature toughness while fully retaining the excellent properties of pure tungsten.

[0090] It should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention and are not intended to limit it. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions can be made to the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, and all such modifications or substitutions should be covered within the scope of the claims of the present invention.

Claims

1. A high-strength, high-toughness, low-activation, refractory multi-component alloy, characterized in that: The alloy is composed of three low-activation refractory elements, W, Cr, and Zr, as well as O introduced through contact with the environment during the preparation process; by atomic percentage, it consists of 75.0~91.5% W, 7.0~16.5% Cr, 1.0~5.5% Zr, and 0.5~3.0% O; wherein the atomic fraction ratio of Cr to Zr is 1.5~5.5, and the atomic fraction ratio of Zr to O is 0.5~2; The high-strength, high-toughness, high-density, low-activation, refractory multi-component alloy has the following characteristics: (i) Second-phase nanoparticles with tetragonal and monoclinic structures are dispersed in a BCC disordered solid solution matrix; (ii) Mass density is 16.0~18.0 g / cm³ 3 ; (iii) The compressive yield strength at room temperature is 2050~2500 MPa; (iv) The ultimate compressive strength at room temperature is 2500~3850 MPa; (v) Compressive strain at room temperature: 5-25%; (vi) Vickers hardness HV30 is 600~950.

2. The high-strength, high-toughness, high-density, low-activation, refractory multi-component alloy as described in claim 1, characterized in that: It consists of 87.0-90.5% W, 8.0% Cr, 1.5-5.0% Zr and 0.5-3.0% O by atomic percentage.

3. The method for preparing a high-strength, high-toughness, low-activation, refractory multi-component alloy as described in claim 1 or 2, characterized in that: The process includes preparing powdered raw materials of each component according to the atomic percentage of the alloy, ball milling them under vacuum or inert gas protection, sieving the powders, loading them into a mold, and sintering them under vacuum or inert gas protection to obtain the alloy material.

4. The method for preparing the multi-component alloy as described in claim 3, characterized in that: The ball mill uses cemented carbide balls, the ball milling speed is 200~500 rpm, and the total ball milling time is 5~50 h.

5. The method for preparing a multi-component alloy as described in claim 4, characterized in that: The mass ratio of the cemented carbide ball to all powders of each component of the alloy is 5:1 to 10:

1.

6. The method for preparing the multi-component alloy as described in claim 3, characterized in that: The alloy is sintered under vacuum or inert gas protection conditions, maintaining the furnace pressure at 10~10. 5 Pa.

7. The method for preparing a multi-component alloy as described in claim 3, characterized in that: The sintering process is either spark plasma sintering, rapid hot pressing sintering, or gas pressure sintering.

8. The method for preparing the multi-component alloy as described in claim 7, characterized in that: The sintering pressure is 10~50 MPa, the sintering heating rate is 10~100 ℃ / min, the sintering temperature is 1400~1800 ℃, and the holding time is 3~20 min.

9. The method for preparing the multi-component alloy as described in claim 3, characterized in that: The raw materials for each component are pure metal powders with a purity higher than 98 wt.%.

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