Refractory multi-component main alloy as well as preparation method and application thereof

Abstract

The invention belongs to the technical field of alloy materials, and particularly relates to a refractory multi-element main alloy and a preparation method and application thereof. The refractory multi-element main alloy provided by the invention comprises Ti, Zr, Ta and Ni, wherein the atomic percentage content of Ni in the refractory multi-element main alloy is 0-25%; the atomic ratio of Ti to Zr is (0.8-1.2): (0.8-1.2), and the atomic ratio of Ti to Ta is (0.8-1.2): (0.8-1.2). Ti, Zr and Ta are all high-melting-point metals, a BCC solid solution phase with a high entropy value can be formed, and excellent high-temperature stability and softening resistance are achieved; and meanwhile, by introducing 0-25 at.% of adjustable Ni element, a dispersed Laves phase is formed in a solid solution matrix, the precipitation strengthening effect is achieved, and the hardness and high-temperature strength of the alloy are remarkably improved. The refractory multi-element main alloy provided by the invention shows the characteristic of low wear rate in the range of 25-600 DEG C.

Description

Technical Field

[0001] This invention belongs to the field of alloy materials technology, specifically relating to a refractory multi-component main alloy, its preparation method, and its application. Background Technology

[0002] With the rapid development of aerospace, nuclear energy and high-end equipment technologies, key moving parts (such as high-temperature bearings, valve seats, sealing rings, etc.) are facing increasingly harsh service environments, requiring materials to maintain excellent wear resistance and oxidation resistance under high temperature (600℃), heavy load and unlubricated dry friction conditions.

[0003] Traditional wear-resistant materials mainly consist of tool steel, hot work die steel, cobalt-based alloys, or nickel-based alloys. These materials exhibit high strength and wear resistance at room temperature, but their wear resistance decreases at high temperatures due to softening or oxidation. Research has shown that applying a ceramic coating to the surface of wear-resistant materials can improve their temperature resistance. Although ceramic coatings possess excellent high-temperature hardness and chemical stability, their fracture toughness is low, making them sensitive to thermal shock and mechanical vibration. Under complex dynamic friction conditions, they are prone to brittle spalling or even catastrophic fracture, severely limiting their application in critical moving parts.

[0004] Therefore, developing high-temperature wear-resistant materials is an urgent technical problem that needs to be solved. Summary of the Invention

[0005] In view of this, the present invention provides a refractory multi-component main alloy, its preparation method and application. The refractory multi-component main alloy provided by the present invention has good high-temperature wear resistance and solves the problems of easy softening and wear and short service life of existing wear-resistant materials under high-temperature friction conditions.

[0006] To address the aforementioned technical problems, this invention provides a refractory multi-component main alloy comprising Ti, Zr, Ta, and Ni, wherein the atomic percentage of Ni in the refractory multi-component main alloy is 0-25%. The atomic ratio of Ti to Zr is 0.8~1.2:0.8~1.2, and the atomic ratio of Ti to Ta is 0.8~1.2:0.8~1.2.

[0007] Preferably, the atomic ratio of Ti, Zr and Ta is 1:1:0.997~1, and the atomic percentage of Ni is 0, 14.3% or 25%.

[0008] Preferably, the microstructure of the refractory multi-component master alloy includes a body-centered cubic crystal structure, and when the atomic percentage of Ni is 0, it also includes a B2 phase, and when the atomic percentage of Ni is greater than 0, it also includes a Laves phase. The relative density of the refractory multi-component main alloy is above 98%.

[0009] This invention also provides a method for preparing the refractory multi-component main alloy described above, comprising the following steps: The raw materials are mixed according to the element ratio and then mechanically alloyed to obtain alloyed powder. The alloyed powder is subjected to discharge plasma sintering to obtain the refractory multi-component main alloy.

[0010] Preferably, the mechanical alloying is carried out under ball milling conditions, the ball milling speed is 200~300 r / min, the ball milling time is 10~50 h, and the ball-to-material ratio is 3~10:1.

[0011] Preferably, the ball mill is an intermittent ball mill, which includes continuous ball milling in a cycle and shutdown cooling. The continuous ball milling time is 10-30 minutes, and the shutdown cooling time is 5-15 minutes.

[0012] Preferably, the vacuum degree of the discharge plasma sintering is below 20 Pa, the temperature of the discharge plasma sintering is 1200~1600℃, the holding time of the discharge plasma sintering is 3~15 min, and the pressure of the discharge plasma sintering is 20~60 MPa. The heating rate to the temperature required for the discharge plasma sintering is 50~200℃ / min.

[0013] Preferably, the raw material is a metal powder of the corresponding element, the average particle size of the metal powder is 5~80μm, and the purity of the metal powder is ≥99.0%.

[0014] The present invention also provides the application of the refractory multi-component main alloy described in the above technical solution or the refractory multi-component main alloy prepared by the preparation method described in the above technical solution in the preparation of high-temperature wear-resistant parts.

[0015] Preferably, the high-temperature wear-resistant parts include hot forging dies, die-casting dies, aero-engine components, gas turbine components, or nuclear reactor components.

[0016] This invention provides a refractory multi-element main alloy comprising Ti, Zr, Ta, and Ni, wherein the atomic percentage of Ni in the refractory multi-element main alloy is 0-25%; the atomic ratio of Ti to Zr is 0.8-1.2:0.8-1.2, and the atomic ratio of Ti to Ta is 0.8-1.2:0.8-1.2. In this invention, Ti, Zr, and Ta are all high-melting-point metals that can form a BCC solid solution phase with high entropy, exhibiting excellent high-temperature stability and resistance to softening. Simultaneously, by introducing 0-25 at.% of Ni, this invention achieves the formation of a dispersed Laves phase in the solid solution matrix, resulting in precipitation strengthening and significantly improving the alloy's hardness and high-temperature strength. The refractory multi-element main alloy provided by this invention exhibits low wear rate characteristics in the temperature range of 25-600℃. Under dry sliding friction conditions, the coefficient of friction is approximately 0.4-0.6 at 600℃, and the wear rate is ≤6.3×10⁻⁶. -5 mm 3 N / m, significantly better than traditional hot work die steel.

[0017] This invention also provides a method for preparing the refractory multi-component main alloy described in the above technical solution, comprising the following steps: mixing raw materials according to the element ratio and then mechanically alloying them to obtain alloyed powder; subjecting the alloyed powder to discharge plasma sintering to obtain the refractory multi-component main alloy. This invention promotes fine grain strengthening and uniform grain distribution through mechanical alloying (powder metallurgy process), maintaining structural stability even at a high temperature of 600℃. This invention employs a powder metallurgy route combining mechanical alloying and discharge plasma sintering, achieving thorough and uniform mixing of elements in the solid state, avoiding the element segregation problem of smelting methods, and facilitating industrial production. Attached Figure Description

[0018] Figure 1 The XRD pattern of the alloyed powder prepared in Example 1; Figure 2 The images show the SEM image and EDS elemental distribution diagram of the alloyed powder prepared in Example 1. Figure 3 The XRD patterns of the refractory multi-component main alloys prepared in Examples 1-3 are shown below. Figure 4 The backscattered electron diagram and EDS elemental distribution diagram of the refractory multi-component master alloy prepared in Example 1 are shown below. Figure 5 The chart shows a comparison of the wear rates of the alloys prepared in Examples 1-3 at different temperatures. Figure 6 The graph shows a comparison of the friction coefficients of the alloys prepared in Examples 1-3 at different temperatures. Figure 7The image shows the wear track profile of the TiZrTa block prepared in Example 1 at 600°C. Figure 8 The XRD patterns of the alloyed powders prepared in Comparative Example 1 and Comparative Example 2 are shown. Detailed Implementation

[0019] The present invention provides a refractory multi-component main alloy comprising Ti, Zr, Ta and Ni; wherein the atomic percentage of Ni in the refractory multi-component main alloy is 0 to 25%, specifically 0, 3%, 5%, 10%, 14.3%, 20% or 25%.

[0020] In this invention, the atomic ratio of Ti to Zr is 0.8~1.2:0.8~1.2, which can be 1:1; the atomic ratio of Ti to Ta is 0.8~1.2:0.8~1.2, which can be 1:0.997~1. In this invention, the atomic ratio of Ti, Zr, and Ta can be 1:1:0.997~1.

[0021] In this invention, the microstructure of the refractory multi-component master alloy includes a body-centered cubic (BCC) crystal structure. When the atomic percentage of Ni is 0, it also includes the B2 phase. When the atomic percentage of Ni is greater than 0, it also includes the Laves phase. In this invention, as the atomic percentage of Ni increases, the Laves phase will precipitate in the refractory multi-component master alloy. In this invention, the relative density of the refractory multi-component main alloy is above 98%, specifically 99%.

[0022] The refractory multi-component master alloy provided by this invention possesses a high-density, multi-scale heterogeneous structure, specifically characterized by a micron-scale body-centered cubic (BCC) solid solution as the matrix, with nano-scale Laves precipitates dispersed within it. Benefiting from the synergistic regulatory effect of the multi-scale structure on oxygen diffusion and interfacial reactions, the refractory multi-component master alloy can generate a dense and firmly bonded oxide glaze layer in situ on its surface under dry friction conditions at 600℃. The growth rate of this glaze layer can compensate for or even exceed the wear of the substrate, stabilizing the macroscopic wear rate at 10%. -5 mm 3 The wear rate is on the order of N / m, exhibiting near-zero wear or "negative wear" characteristics under certain operating conditions. The refractory multi-component main alloy provided by this invention is suitable for aerospace moving parts with extremely high requirements for dimensional accuracy and service life.

[0023] This invention also provides a method for preparing the refractory multi-component main alloy described above, comprising the following steps: The raw materials are mixed according to the element ratio and then mechanically alloyed to obtain alloyed powder. The alloyed powder is subjected to discharge plasma sintering to obtain the refractory multi-component main alloy.

[0024] This invention involves mixing raw materials according to elemental ratios and then mechanically alloying them to obtain alloyed powder. In this invention, the raw materials can be metal powders of corresponding elements, specifically Ti powder, Zr powder, Ta powder, and Ni powder; the average particle size of the metal powder can be 5~80 μm, or 8.5~50 μm, specifically 10 μm, 20 μm, 30 μm, or 48 μm; the purity of the metal powder can be ≥99.0%, specifically 99.5% or 99.9%.

[0025] In this invention, the mixing can be carried out in a protective atmosphere, which may include nitrogen or argon.

[0026] In this invention, the mechanical alloying can be carried out under ball milling conditions. The ball milling speed can be 200~300 r / min, specifically 250 r / min or 300 r / min; the ball milling time can be 10~50 h, specifically 20 h, 30 h or 40 h; the grinding balls used for ball milling can be made of an alloy, specifically YG6 tungsten steel, and the diameter of the grinding balls can be 10 mm; the ball-to-material ratio of the ball milling can be 3~10:1, specifically 5:1, 6:1 or 8:1. This invention uses ball milling for mechanical alloying, which enables the solid solution to achieve fine-grained strengthening and uniform distribution, thereby improving the high-temperature resistance of the alloy.

[0027] In this invention, the ball milling can be carried out in a protective atmosphere, which may include nitrogen or argon.

[0028] In this invention, the ball milling can be intermittent ball milling, which can include continuous ball milling in a cycle and shutdown cooling. The continuous ball milling time can be 10-30 minutes, specifically 15 minutes, 20 minutes, or 25 minutes; the shutdown cooling time can be 5-15 minutes, specifically 8 minutes, 10 minutes, or 13 minutes. This invention, through intermittent ball milling, avoids incomplete alloying and powder contamination caused by excessive energy.

[0029] In this invention, the process after ball milling may further include: sieving the ball-milled product, taking the undersize material, and obtaining the alloy powder; the mesh size of the sieve used for sieving may be 200 mesh.

[0030] After obtaining the alloyed powder, the present invention performs discharge plasma sintering on the alloyed powder to obtain the refractory multi-component main alloy. In the present invention, the vacuum degree of the discharge plasma sintering can be below 20 Pa, and can be 2~20 Pa, specifically 2 Pa, 5 Pa, 10 Pa or 15 Pa; the temperature of the discharge plasma sintering can be 1200~1600℃, specifically 1300℃, 1400℃ or 1500℃; the heating rate to the temperature required for discharge plasma sintering can be 50~200℃ / min, specifically 80℃ / min, 100℃ / min or 150℃ / min; the holding time of the discharge plasma sintering can be 3~15 min, specifically 5 min, 10 min or 13 min; the pressure of the discharge plasma sintering can be 20~60 MPa, specifically 30 MPa, 40 MPa or 50 MPa.

[0031] In this invention, the discharge plasma sintering can transfer the alloyed powder to a mold and then place it in a discharge plasma sintering (SPS) device; the mold can be made of graphite, and the shape and size of the mold can be designed according to actual needs.

[0032] In this invention, the process after discharge plasma sintering may further include: cooling the product after discharge plasma sintering to room temperature; the room temperature may be 20~35℃ or 25~30℃; the cooling method may be furnace cooling.

[0033] This invention also provides the application of the refractory multi-component main alloy described in the above-described technical solutions or the refractory multi-component main alloy prepared by the preparation method described in the above-described technical solutions in the preparation of high-temperature wear-resistant parts. In this invention, the high-temperature wear-resistant parts may include hot forging dies, die-casting dies, aero-engine components, gas turbine components, or nuclear reactor components.

[0034] This invention provides a TiZrTaNi multi-component alloy based on cross-scale heterostructure and localized chemically ordered strengthening. A cross-scale structure of micron-sized matrix, nano-precipitates, and atomically ordered localized chemical structure was successfully constructed in the TiZrTaNi alloy system. Through the synergistic effect of multi-level strengthening mechanisms, the technical challenges of high room-temperature brittleness and insufficient high-temperature wear resistance in traditional refractory alloys are effectively solved.

[0035] To further illustrate the present invention, the technical solutions provided by the present invention will be described in detail below with reference to the embodiments, but they should not be construed as limiting the scope of protection of the present invention.

[0036] Example 1 (1) Raw material preparation: Weigh out Ti powder (average particle size 48 μm, atomic percentage 33.33%), Zr powder (average particle size 48 μm, atomic percentage 33.33%), and Ta powder (average particle size 48 μm, atomic percentage 33.33%) with a purity ≥99.5% respectively, with a total powder mass of 100g; to prevent oxidation, the entire weighing process is carried out in an argon gas environment in a glove box.

[0037] (2) Mechanical alloying ball milling: The raw material was poured into a vacuum ball mill jar, and a number of ø10 mm YG6 tungsten steel balls were added, controlling the ball-to-material mass ratio to be 8:1. After argon protection, the ball mill was intermittently milled at 300 r / min for 30 h, with a 10 min stop every 30 min to dissipate heat. During the ball milling process, the powder gradually changed from the initial metallic luster to dark gray. After 30 h, the powder was taken out and passed through a 200 mesh sieve. The material passing through the sieve was collected to obtain the alloyed powder.

[0038] (3) Plasma sintering: The obtained alloyed powder was loaded into a ø26 mm graphite mold and heated to 1600℃ in an SPS device at a heating rate of 100℃ / min under a vacuum of 5Pa. The temperature was held for 5 minutes under an axial pressure of 30MPa. After sintering, the sample was cooled to room temperature in the furnace and removed to obtain a refractory multi-element main alloy, denoted as TiZrTa block.

[0039] Example 2 (1) Raw material preparation: Weigh out Ti powder (average particle size 48 μm, atomic percentage 28.6%), Zr powder (average particle size 48 μm, atomic percentage 28.6%), Ta powder (average particle size 48 μm, atomic percentage 28.5%) and Ni powder (average particle size 48 μm, atomic percentage 14.3%) with a purity ≥99.5%, with a total powder mass of 100g; to prevent oxidation, the entire weighing process is carried out in an argon gas environment in a glove box.

[0040] (2) Mechanical alloying ball milling: The raw materials are mechanically alloyed according to the method in Example 1 to obtain alloyed powder.

[0041] (3) Plasma sintering: The alloy powder was plasma sintered according to the method in Example 1 to obtain a refractory multi-component main alloy, denoted as TiZrTaNi0.5 bulk.

[0042] Example 3 (1) Raw material preparation: Weigh out Ti powder (average particle size 48μm, atomic percentage 25%), Zr powder (average particle size 48μm, atomic percentage 25%), Ta powder (average particle size 48μm, atomic percentage 25%) and Ni powder (average particle size 48μm, atomic percentage 25%) with a purity ≥99.5%, with a total powder mass of 100g; to prevent oxidation, the entire weighing process is carried out in an argon gas environment in a glove box.

[0043] (2) Mechanical alloying ball milling: The raw materials are mechanically alloyed according to the method in Example 1 to obtain alloyed powder.

[0044] (3) Plasma sintering: The alloy powder was plasma sintered according to the method in Example 1 to obtain a refractory multi-component main alloy, denoted as TiZrTaNi bulk.

[0045] Comparative Example 1 Weigh the raw material metal powder according to step (1) of Example 1; The raw material weighed in step (1) is poured into a vacuum ball mill jar and intermittently ball-milled according to step (2) of Example 1. The difference is that the ball milling speed is 350 r / min to obtain alloyed powder. The alloyed powder was subjected to discharge plasma sintering according to step (2) of Example 1 to obtain an alloy block.

[0046] Figure 8 The XRD pattern of the alloyed powder prepared in Comparative Example 1 is shown below. Figure 8 It can be seen that elemental Ti and Zr are still present in the alloyed powder, indicating that the rotation speed affects the degree of alloying. The reason is that the ball milling of the comparative example at a higher rotation speed generates higher energy, which causes sticking to the can and leads to a poorer alloying effect.

[0047] Comparative Example 2 Weigh the raw material metal powder according to step (1) of Example 1; The raw material weighed in step (1) is poured into a vacuum ball mill jar and intermittently ball-milled according to step (2) of Example 1. The difference is that the ball-to-material ratio of the ball mill is 2:1, and alloyed powder is obtained. The alloyed powder was subjected to discharge plasma sintering according to step (3) of Example 1 to obtain an alloy block.

[0048] Figure 8 The XRD pattern of the alloyed powder prepared in Comparative Example 2 is shown below. Figure 8 It can be seen that the alloyed powder contains elemental Ti and Zr, indicating that the ball-to-powder ratio affects the degree of alloying. The reason for this is that in Comparative Example 2, ball milling at a lower ball-to-powder ratio would reduce energy, resulting in incomplete alloying.

[0049] The alloyed powder prepared in Example 1 was subjected to XRD analysis, and the XRD pattern was obtained, as shown below. Figure 1 As shown. By Figure 1 It can be seen that only the diffraction peaks of a single BCC phase exist in the alloy powder, and no other phases were detected.

[0050] The alloyed powder prepared in Example 1 was subjected to SEM and EDS elemental analysis to obtain SEM images and EDS elemental distribution maps, as shown below. Figure 2 As shown. By Figure 2 It can be seen that the three elements Ti, Zr and Ta in the alloyed powder are uniformly distributed without segregation.

[0051] XRD analysis was performed on the refractory multi-component main alloys prepared in Examples 1-3, and the obtained XRD spectra are shown below. Figure 3 As shown. By Figure 3 It can be seen that the introduction of Ni (with its strong negative enthalpy of mixing with other elements) into the alloy induces the appearance of the Laves phase. The peak intensity of the Laves phase in the alloy increases significantly with increasing Ni content, demonstrating that high Ni content promotes the precipitation of a large amount of ordered Laves phase. These results indicate that when the atomic percentage of Ni reaches 25%, a significant proportion of Laves intermetallic compound phases coexist in the alloy, in addition to the BCC solid solution matrix, forming a multiphase structure.

[0052] The refractory multi-component main alloy prepared in Example 1 was subjected to SEM detection and EDS elemental analysis. The backscattered electron pattern and EDS elemental distribution map obtained are as follows: Figure 4 As shown. By Figure 4 It can be seen that the microstructure of the TiZrTa alloy forms a multi-scale structure, with the matrix composed of micron-sized large grains, and nanoscale precipitates existing within the large grains. The corresponding EDS shows that Ta-rich grain boundary precipitation occurs at the interface.

[0053] The relative densities of the alloy blocks prepared in Examples 1-3 were measured using a fully automated true density analyzer, and the results are listed in Table 1.

[0054] Friction tests were conducted on the samples prepared in Examples 1-3 and Comparative Examples 1-2 according to the following method. The friction coefficient and wear rate results are listed in Table 1: The samples were subjected to friction and wear tests at 25℃, 400℃ and 600℃ respectively; a pin-disc friction tester was used, the sample surface was polished to Ra<0.1µm, the dual ball was Si3N4 ceramic, the load was 5N, the rotation speed was 200r / min, the friction radius was 5mm, and the steady-state data were collected for 30 minutes at each temperature.

[0055] Table 1. Properties of the alloys prepared in Examples 1-3 and Comparative Examples 1-2

[0056] As can be seen from Table 1, the TiZrTa bulk material prepared in Example 1 has extremely high wear resistance and exhibits negative wear phenomenon. The reason for the negative wear is friction catalysis. The local flash temperature and ambient heat generated during the friction process promote further oxidation of the wear track to generate metal oxides, and lead to local expansion to form a stable friction glaze layer.

[0057] As can be seen from the test results of Examples 2 and 3 in Table 1, the addition of an appropriate amount of Ni has a significant positive effect on reducing the friction coefficient of the alloy. This is attributed to the fact that the addition of Ni enhances the lubrication and protection of the oxide film, thereby reducing the friction coefficient.

[0058] Based on Table 1, a bar chart comparing the wear rates of the alloys prepared in Examples 1-3 at different temperatures was plotted. Figure 5 As shown. (Combined with Table 1 and...) Figure 5 It can be seen that due to the inherent brittleness of the BCC structure in the refractory multi-component main alloy, the wear rate is high at room temperature, but different results appear at 400℃. This is due to the trade-off between the formation and stability of the tribooxide layer. The poor stability of the tribooxide layer and the softening of the structure of TiZrTa at 400℃ increase the wear rate. With the addition of Ni, the wear rate of TiZrTaNi0.5 bulk and TiZrTaNi bulk at 400℃ is reduced, which means that Ni stabilizes the tribooxide glaze layer. At higher temperatures, the wear rates of the alloys prepared in Examples 1-3 are all reduced, which is due to the more stable formation of the tribooxide layer. For example, higher ambient heat accelerates tribooxide oxidation and element diffusion, and promotes the sintering and densification / bonding (even local viscoplastic flow) of oxide debris under load and shear to form a continuous load-bearing film. Cracks can be filled by "self-healing" and re-oxidation. At the same time, interfacial interdiffusion enhances adhesion and reduces the direct contact between the metal and the friction pair, so the glaze layer is less likely to be repeatedly broken and peeled off.

[0059] Based on Table 1, a bar chart comparing the friction coefficients of the alloys prepared in Examples 1-3 at different temperatures was plotted, as shown below. Figure 6 As shown. (Combined with Table 1 and...) Figure 6It can be seen that the decrease in the friction coefficient of refractory multi-component main alloys with increasing temperature can be attributed to material softening. The slight increase in the friction coefficient at 600℃ is due to the high melting point, high hardness, and large lattice shear resistance of oxides such as TiO2, ZrO2, and Ta2O5; higher temperatures lead to faster oxidation, making it easier for the interface to transform into an "oxide-oxide / oxide-dual" bearing contact, resulting in increased interfacial shear strength and consequently, a higher COF. Furthermore, increased temperature reduces the yield strength of the alloy matrix, making plastic flow more likely to occur subsurface; simultaneously, the mismatch in thermal expansion coefficients between the film and the matrix exacerbates interfacial damage, leading to repeated film breakage and regeneration, increasing roughness and debris supply, and further increasing COF.

[0060] Figure 7 The image shows the wear track profile morphology of the TiZrTa bulk material prepared in Example 1 at 600°C. Figure 7 The two-dimensional interface diagram of the wear track clearly reveals an anomaly during the friction process: friction causes the depth of the sliding track to exceed the baseline, resulting in negative wear behavior. The oxide / glaze layer forms rapidly and is not easily removed, leading to an increase in net mass.

[0061] The test results of the above examples fully demonstrate that the microstructure and properties of the TiZrTaNix (where x is any value from 0 to 1) multi-component alloy prepared by mechanical alloying and spark plasma sintering can be adjusted by controlling the Ni content. When the Ni content is 0, the BCC and B2 phases coexist in the refractory multi-principal alloy, exhibiting excellent high-temperature wear resistance. When Ni is added, the refractory multi-principal alloy still exhibits excellent low friction and high wear resistance at 600℃. Therefore, the TiZrTaNix alloy provided by this invention has good high-temperature wear resistance.

[0062] Although the above embodiments have provided a detailed description of the present invention, they are only some embodiments of the present invention, and not all embodiments. People can obtain other embodiments based on these embodiments without creative effort, and these embodiments all fall within the protection scope of the present invention.

Claims

1. A refractory multi-component main alloy, characterized in that, The alloy comprises Ti, Zr, Ta, and Ni, wherein the atomic percentage of Ni in the refractory multi-component alloy is 0-25%. The atomic ratio of Ti to Zr is 0.8~1.2:0.8~1.2, and the atomic ratio of Ti to Ta is 0.8~1.2:0.8~1.

2.

2. The refractory master alloy of claim 1, wherein The atomic ratio of Ti, Zr and Ta is 1:1:0.997~1, and the atomic percentage of Ni is 0, 14.3% or 25%.

3. The refractory master alloy of claim 1, wherein The microstructure of the refractory multi-component master alloy includes a body-centered cubic crystal structure. When the atomic percentage of Ni is 0, it also includes the B2 phase, and when the atomic percentage of Ni is greater than 0, it also includes the Laves phase. The relative density of the refractory multi-component main alloy is above 98%.

4. A method of producing the refractory master alloy according to any one of claims 1 to 3, characterized in that Includes the following steps: The raw materials are mixed according to the element ratio and then mechanically alloyed to obtain alloyed powder. The alloyed powder is subjected to discharge plasma sintering to obtain the refractory multi-component main alloy.

5. The preparation method according to claim 4, characterized in that, The mechanical alloying is carried out under ball milling conditions, the ball milling speed is 200~300 r / min, the ball milling time is 10~50 h, and the ball-to-material ratio is 3~10:

1.

6. The preparation method according to claim 4 or 5, characterized in that, The ball mill is an intermittent ball mill, which includes continuous ball milling in a cycle and shutdown cooling. The continuous ball milling time is 10~30min, and the shutdown cooling time is 5~15min.

7. The preparation method according to claim 4, characterized in that, The vacuum degree of the discharge plasma sintering is below 20 Pa, the temperature of the discharge plasma sintering is 1200~1600℃, the holding time of the discharge plasma sintering is 3~15 min, and the pressure of the discharge plasma sintering is 20~60 MPa. The heating rate to the temperature required for the discharge plasma sintering is 50~200℃ / min.

8. The preparation method according to claim 4, characterized in that, The raw material is a metal powder of the corresponding element, the average particle size of the metal powder is 5~80μm, and the purity of the metal powder is ≥99.0%.

9. The application of the refractory multi-component main alloy according to any one of claims 1 to 3 or the refractory multi-component main alloy prepared by the preparation method according to any one of claims 4 to 8 in the preparation of high-temperature wear-resistant parts.

10. Use according to claim 9, characterized in that, The high-temperature wear-resistant parts include hot forging dies, die-casting dies, aero-engine components, gas turbine components, or nuclear reactor components.

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