A lightweight refractory high-entropy alloy with strong-ductility matching, its preparation method and application

Abstract

This invention relates to the field of high-entropy superalloys, specifically to a lightweight refractory high-entropy alloy with a strong-ductility balance, its preparation method, and its applications. The general formula of this lightweight refractory high-entropy alloy is (TiNbAlMoV). x Zr y Among them, 14 at.% ≤ y ≤ 18 at.%, and x + y = 100 at.%, the lightweight refractory high-entropy alloy has a multiphase structure of BCC1 + BCC2 + AlZr phases, and the melting point of the alloy is not lower than 1500℃; the density is 6.35-6.50 g / cm³. 3 The alloy was prepared using a vacuum non-consumable arc furnace. By controlling the atomic ratio of Zr, a series of refractory multi-principal element alloys were obtained, which exhibited dendritic morphology in the as-cast state. The as-cast alloy had a compressive yield strength of up to 1545 MPa at room temperature and also exhibited excellent mechanical properties at high temperatures. The alloy density was significantly reduced, which holds promise for the engineering application of refractory high-entropy high-temperature alloys.

Description

Technical Field

[0001] This invention relates to the field of high-entropy alloys, specifically to a lightweight refractory high-entropy alloy with a strong-plasticity balance, its preparation method, and its applications. Background Technology

[0002] With industrial development and humanity's further exploration of the unknown, especially the rapid development of my country's aviation industry in recent years, the demand for alloys with superior high-temperature performance has increased dramatically. This has placed higher demands on the high-temperature resistance of aerospace hot-end components, requiring structural materials with low density and excellent comprehensive performance at high temperatures. Currently, nickel-based superalloys are the main materials for hot-end components (such as turbine disks, turbine blades, and casings). However, as service temperatures continue to rise, their alloying degree and γ′ phase content are approaching design limits. At the same time, the difficulty of controlling their melting and hot working is also increasing, resulting in extremely limited room for increasing the service temperature of nickel-based superalloy aerospace hot-end components. Therefore, it is urgent to find alternative alloy systems.

[0003] High-entropy alloys (HEAs), as a novel alloy design concept, have received extensive research and rapid development in recent years. Unlike traditional alloys, which are designed primarily with matrix elements and supplemented by trace amounts of other elements, HEAs utilize the interrelationships between various alloys to uniformly occupy lattice points, forming an alloy system with a simple structure that effectively suppresses the formation of intermetallic compounds. Compared to traditional alloys, high-entropy alloys exhibit superior properties, such as high high-temperature strength, high toughness, thermal stability, resistance to high-temperature oxidation, high corrosion resistance, and resistance to high-temperature softening.

[0004] Refractory high-entropy alloys, through the addition of refractory elements, possess excellent high-temperature strength and properties, making them promising candidates to overcome the shortcomings of traditional nickel-based high-temperature alloys that have reached their theoretical operating temperature limits. They hold immense development potential and offer a new option for the research and development of novel high-temperature resistant materials for high-performance aerospace hot-end components. However, currently, few refractory high-entropy alloys meet the requirements of practical engineering applications, mainly due to problems such as excessive density, low plasticity, and unstable high-temperature performance in most refractory high-entropy alloys. Therefore, there is an urgent need to design a refractory high-entropy alloy with low density, high yield strength, and good deformation plasticity. Summary of the Invention

[0005] The purpose of this invention is to provide a lightweight refractory high-entropy alloy with a strong-plasticity balance, its preparation method, and its application. The aim is to solve the problems of high density and poor room temperature plasticity of existing refractory high-entropy alloys, and to develop a non-equimolar refractory high-entropy alloy that combines low density, high yield strength, room temperature plasticity, and good high-temperature performance.

[0006] To achieve the above objectives, the technical solution provided by this invention is: a lightweight refractory high-entropy alloy with a strong-ductility matching in the as-cast state, wherein the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). x Zr y Where 14at.% ≤ y ≤ 18at.%, and x + y = 100at.%.

[0007] Furthermore, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). x Zr y Where 15at.% ≤ y ≤ 17at.%, and x + y = 100at.%.

[0008] Furthermore, the lightweight refractory high-entropy alloy has a multiphase structure of BCC1+BCC2+AlZr phases, and the alloy's melting point is not lower than 1500℃; its density is 6.35-6.50 g / cm³. 3 .

[0009] Furthermore, the lightweight refractory high-entropy alloy has a compressive yield strength of not less than 1400 MPa and a maximum compressive strength of not less than 1470 MPa in the as-cast state at room temperature; a yield strength of not less than 938 MPa and a compressive strength of not less than 967 MPa at 800℃; a yield strength of not less than 202 MPa and a compressive strength of not less than 212 MPa at 1000℃; a fracture strain of not less than 10.00%; and an average Vickers microhardness of 482.19.

[0010] Furthermore, when x = 84.27 at.% and y = 15.73 at.%, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). 84.27 Zr 15.73 The density of the alloy is 6.42 g / cm³. 3 At room temperature, the compressive yield strength is 1401 MPa, the fracture strain is 11.65%, the compressive strength is 1470 MPa, and the average Vickers microhardness is 482.19; at 800℃, the yield strength is 938 MPa, the compressive strength is 967 MPa, and at 1000℃, the yield strength is 202 MPa, the compressive strength is 212 MPa.

[0011] Furthermore, when x = 83.39 at.% and y = 16.61 at.%, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). 83.39 Zr 16.61 The density of the alloy is 6.39 g / cm³. 3At room temperature, the compressive yield strength is 1450 MPa, the fracture strain is 10.72%, the compressive strength is 1531 MPa, and the average Vickers microhardness is 485.26; at 800℃, the yield strength is 872 MPa, the compressive strength is 893 MPa, and at 1000℃, the yield strength is 178 MPa, the compressive strength is 205 MPa.

[0012] Furthermore, when x = 82.36 at.% and y = 17.64 at.%, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). 82.36 Zr 17.64 The alloy density is 6.43 g / cm³. 3 At room temperature, the compressive yield strength is 1545 MPa, the fracture strain is 12.10%, the compressive strength is 1587 MPa, and the average Vickers microhardness is 488.54; at 800℃, the yield strength is 884 MPa, the compressive strength is 925 MPa, and at 1000℃, the yield strength is 183 MPa, the compressive strength is 208 MPa.

[0013] Another object of the present invention is to provide a method for preparing the above-mentioned lightweight refractory high-entropy alloy with strong-ductility matching, the method specifically including the following preparation steps:

[0014] S1) Convert the atomic percentage of each alloy component into a mass ratio and weigh the required mass of each element;

[0015] S2) Remove impurities and oxide scale from the surface of the selected raw material block, place it in anhydrous ethanol for ultrasonic vibration cleaning to remove surface impurities, and then dry it.

[0016] S3) Weigh the raw material blocks after processing S2) according to the mass of each raw material calculated by S1). Place the weighed raw materials and titanium ingots into the copper crucible of the non-consumable vacuum arc furnace in order of their melting points from low to high.

[0017] S4) First, the furnace cavity is evacuated, then a protective atmosphere is introduced into the furnace cavity, and multiple melting processes are carried out under a certain current to obtain a lightweight refractory high-entropy alloy.

[0018] Furthermore, the specific process parameters in S4) are: vacuuming to 5×10 -3 Below Pa, the protective atmosphere is high-purity argon gas at a pressure of 0.02 MPa; each melting time is 2 to 3 minutes, and the mixture needs to be turned over after each melting.

[0019] An application of the aforementioned lightweight refractory high-entropy alloy in the field of high-temperature structural materials.

[0020] Compared with the prior art, the present invention has the following beneficial effects:

[0021] The present invention prepares a lightweight refractory high-entropy alloy with strong and ductile properties in the as-cast state. By replacing Ta with V, the density of the refractory high-entropy alloy system is greatly reduced, while the manufacturing cost of the alloy is also reduced, and its strength and ductility are greatly improved.

[0022] This alloy, through optimization of its composition and the content of each component, is a refractory high-entropy alloy dominated by the BCC phase and containing trace amounts of Zr-rich phase. It has a melting point greater than 1500℃ and exhibits high room-temperature compressive mechanical properties. Its as-cast room-temperature compressive yield strength can reach up to 1510 MPa, and its compressive strength can reach up to 1587 MPa. Furthermore, it demonstrates excellent structural and mechanical stability at high temperatures of 800℃ and 1000℃. At 800℃, its yield strength reaches 938 MPa, and its compressive strength reaches 967 MPa; at 1000℃, its yield strength reaches 202 MPa, and its compressive strength reaches 212 MPa. The average Vickers microhardness reaches 482.19, which can effectively meet the stringent requirements of advanced aerospace and space nuclear reactor systems for high-performance high-temperature structural materials.

[0023] The high-entropy alloys involved in this invention can all be melted in a non-consumable vacuum arc furnace to obtain alloy ingots. The preparation method is simple to operate and easy to implement, the preparation process is pollution-free and has low energy consumption and cost, and can realize large-scale industrial production. Attached Figure Description

[0024] Figure 1 The X-ray diffraction (XRD) pattern of the refractory high-entropy alloy prepared in Example 1.

[0025] Figure 2 The image shows the as-cast microstructure of the refractory high-entropy alloy prepared in Example 1. (a) is 100x and (b) is 500x.

[0026] Figure 3 The results of EDS energy dispersive spectroscopy analysis are shown for the refractory high-entropy alloy prepared in Example 1.

[0027] Figure 4 The stress-strain curves of the as-cast room temperature compression test of the refractory high-entropy alloys prepared in Examples 1-3 are shown.

[0028] Figure 5 The stress-strain curves of the refractory high-entropy alloy prepared in Example 1 are obtained from the high-temperature compression test. Detailed Implementation

[0029] The present invention will be further described below with reference to specific embodiments. Unless otherwise specified, the methods described are conventional methods, and the raw materials described are obtainable from publicly available commercial sources.

[0030] In the following embodiments:

[0031] The purity (mass percentage, wt%) of the elemental forms corresponding to Ti, Nb, Al, Mo, V and Zr is greater than 99.9%;

[0032] Phase analysis: The high-entropy alloy was analyzed using a Rigaku Smartlab X-ray diffractometer manufactured by Rigaku Corporation, Japan. A Cu-Kα (λ=0.1542nm) X-ray source was used with a working voltage of 40kV and a working current of 200mA. Block samples with dimensions of 5×6×10mm were cut from the initial master alloy ingot using an EDM wire cutter. Before testing, the surface of the sample was polished smooth and flat using 60#, 400#, 800# and 2000# sandpaper in sequence. The sample was then mechanically polished with diamond polishing paste on a metallographic polishing machine. After that, it was ultrasonically cleaned with anhydrous ethanol. After the sample was dried, the test was performed. The test angle range was 10~90° and the scanning speed was 5° / min.

[0033] Microstructure characterization: The microstructure of the prepared as-cast high-entropy alloy was observed using a Supra 55 field emission scanning electron microscope manufactured by Zeiss, Germany. Block samples with dimensions of 5×6×10mm were cut using wire electrical discharge machining. The surface of the sample was polished smooth and flat with 60#, 400#, 800# and 2000# sandpaper in sequence. The sample was mechanically polished with diamond polishing paste on a metallographic polishing machine. Electrolytic polishing was performed with an electrolyte of 6% perchloric acid + 30% n-butanol + 64% methanol (volume fraction). The sample was then ultrasonically cleaned in anhydrous ethanol. After the sample was fully dried, it was observed under an electron microscope.

[0034] Compression performance testing: Compression performance tests were conducted at room temperature (298K) and high temperatures (1073K, 1273K) using an MTS 370 electronic universal testing machine from MTS Industrial Systems (China) Co., Ltd., with the strain rate maintained at 1×10⁻⁶. -3 s -1 For room temperature compression performance testing, a Φ3×6mm sample was selected for the test, with a loading rate of 0.5mm / min. For high temperature compression performance testing, a Φ6×9mm cylinder was selected for high-temperature compression tests at 800℃ and 1000℃, with a loading rate of 0.5mm / min, a holding time of 5min, and a compression amount of 50%. The compression test was only conducted after ensuring uniform heating of all parts of the alloy.

[0035] Density test: The density of the prepared refractory high-entropy alloy is tested using the Archimedes displacement method; in order to reduce measurement error, the average value is usually obtained by taking multiple measurements.

[0036] Phase diagram calculation: Thermo-Calc software was used to perform phase diagram calculations to analyze the phase composition of the alloy. The TCHEA4 high-entropy alloy thermodynamic database was used in the calculations.

[0037] The lightweight refractory high-entropy alloy prepared by the method has a simple body-centered cubic structure and a density of 6.35-6.50 g / cm³. 3 It has a room temperature compressive strength of 1.2–1.6 GPa, an elongation at break of more than 10%, and good high-temperature mechanical properties.

[0038] Example 1

[0039] A lightweight, refractory, high-entropy alloy with a strong-ductility matching structure, its chemical formula being (TiNbAlMoV). 84.27 Zr 15.73 The alloy density is 6.42 g / cm³. 3 .

[0040] The specific preparation steps of the refractory high-entropy alloy are as follows:

[0041] Raw material preparation: Calculate and take a certain amount of Ti, Nb, Al, Mo, V and Zr raw material blocks, use sandpaper to polish off the impurities and oxide scale generated by cutting on the surface of the raw materials, then accurately weigh the required raw material mass on a balance, then place all the weighed raw materials in anhydrous ethanol for ultrasonic vibration cleaning in order to further remove surface impurities, and finally dry them.

[0042] Melting and preparation: The raw materials are placed in a small vacuum arc furnace for melting to obtain a new type of refractory high-entropy alloy. The current required during melting is 380A-400A. Before melting, the vacuum degree of the vacuum arc furnace needs to be evacuated to 5×10⁻⁶. -3 The melting time is below Pa. Each melting session takes 2 to 3 minutes. The alloy must be flipped after each melting session and the melting process is repeated at least 8 times to obtain the alloy ingot.

[0043] Table 1. Alloy density test results for Example 1:

[0044]

[0045] Figure 1 The X-ray diffraction (XRD) pattern of the refractory high-entropy alloy prepared in Example 1 shows that the alloy consists of a BCC matrix phase and an AlZr compound phase.

[0046] Figure 2 The image shows a backscattered electron image of the as-cast microstructure of the refractory high-entropy alloy prepared in Example 1. It shows two regions with different contrasts, exhibiting a dendritic morphology. The dendrite trunks are enriched with metal elements with larger atomic numbers, while the interdendritic spaces are enriched with elements with smaller atomic numbers.

[0047] Table 2. EDS analysis results (at%) of alloy in Example 1

[0048]

[0049]

[0050] Figure 3 The following are the EDS energy dispersive spectroscopy (EDS) results of the refractory high-entropy alloy prepared in Example 1. The dendrite trunks are rich in Nb and Mo, corresponding to the bright areas in the backscattered image; the interdendritic spaces are rich in Al and Zr, corresponding to the dark areas in the backscattered image; and the distribution of Ti and V is relatively uniform.

[0051] Table 3. Vickers hardness test results of alloy in Example 1 (HV1.0):

[0052]

[0053] Figure 4 The stress-strain curves of the as-cast compression test of the refractory high-entropy alloys prepared in Examples 1 to 3 are shown. The as-cast room temperature compression strength is 1.2 to 1.6 GPa, and the elongation at break is greater than 10%.

[0054] Figure 5 The stress-strain curves of the high-temperature compression test of the refractory high-entropy alloy prepared in Example 1 are shown. The as-cast alloy has excellent mechanical properties at high temperatures of 800℃ and 1000℃. At 800℃, the yield strength can reach 938MPa and the compressive strength can reach 967MPa. At 1000℃, the yield strength can reach 202MPa and the compressive strength can reach 212MPa.

[0055] Example 2

[0056] A lightweight, refractory, high-entropy alloy with a strong-ductility matching structure, its chemical formula being (TiNbAlMoV). 83.39 Zr 16.61 The alloy density is 6.39 g / cm³. 3 .

[0057] The specific preparation steps of the refractory high-entropy alloy are as follows:

[0058] Raw material preparation: Calculate and take a certain amount of Ti, Nb, Al, Mo, V and Zr raw material blocks, use sandpaper to polish off the impurities and oxide scale generated by cutting on the surface of the raw materials, then accurately weigh the required raw material mass on a balance, then place all the weighed raw materials in anhydrous ethanol for ultrasonic vibration cleaning in order to further remove surface impurities, and finally dry them.

[0059] Melting and preparation: The raw materials are placed in a small vacuum arc furnace for melting to obtain a new type of refractory high-entropy alloy. The current required during melting is 380A-400A. Before melting, the vacuum degree of the vacuum arc furnace needs to be evacuated to 5×10⁻⁶. -3 The density is below Pa. Each melting cycle takes 2-3 minutes, and the alloy must be flipped after each melting cycle. This melting process is repeated at least 8 times to obtain the alloy ingot. The density of the lightweight refractory high-entropy alloy is 6.39 g / cm³. 3 At room temperature, the compressive yield strength is 1450 MPa, the fracture strain is 10.72%, the compressive strength is 1531 MPa, and the average Vickers microhardness is 485.26; at 800℃, the yield strength is 872 MPa, the compressive strength is 893 MPa, and at 1000℃, the yield strength is 178 MPa, the compressive strength is 205 MPa.

[0060] Example 3

[0061] A lightweight, refractory, high-entropy alloy with a strong-ductility matching structure, having the general formula (TiNbAlMoV). 82.36 Zr 17.64 The alloy density is 6.43 g / cm³. 3 .

[0062] The specific preparation steps of the refractory high-entropy alloy are as follows:

[0063] Raw material preparation: Calculate and take a certain amount of Ti, Nb, Al, Mo, V and Zr raw material blocks, use sandpaper to polish off the impurities and oxide scale generated by cutting on the surface of the raw materials, then accurately weigh the required raw material mass on a balance, then place all the weighed raw materials in anhydrous ethanol for ultrasonic vibration cleaning in order to further remove surface impurities, and finally dry them.

[0064] Melting and preparation: The raw materials are placed in a small vacuum arc furnace for melting to obtain a new type of refractory high-entropy alloy. The current required during melting is 380A-400A. Before melting, the vacuum degree of the vacuum arc furnace needs to be evacuated to 5×10⁻⁶. -3 The density is below Pa. Each melting cycle takes 2-3 minutes, and the alloy must be flipped after each melting cycle. This melting process is repeated at least 8 times to obtain the alloy ingot. The density of the lightweight refractory high-entropy alloy is 6.43 g / cm³. 3 At room temperature, the compressive yield strength is 1545 MPa, the fracture strain is 12.10%, the compressive strength is 1587 MPa, and the average Vickers microhardness is 488.54; at 800℃, the yield strength is 884 MPa, the compressive strength is 925 MPa, and at 1000℃, the yield strength is 183 MPa, the compressive strength is 208 MPa.

[0065] The foregoing has provided a detailed description of a lightweight, refractory, high-entropy alloy with a strong-plasticity match, its preparation method, and its application, as provided in the embodiments of this application. The descriptions of the embodiments above are merely for the purpose of helping to understand the method and core ideas of this application; furthermore, those skilled in the art will recognize that, based on the ideas of this application, there will be changes in the specific implementation methods and application scope. Therefore, the content of this specification should not be construed as a limitation of this application.

[0066] Certain terms are used in the specification and claims to refer to specific components. Those skilled in the art will understand that hardware manufacturers may use different names to refer to the same component. This specification and claims do not distinguish components based on differences in name, but rather on differences in function. The terms "comprising" and "including" used throughout the specification and claims are open-ended and should be interpreted as "comprising / including but not limited to". "Approximately" means that within an acceptable margin of error, those skilled in the art can solve the technical problem and substantially achieve the technical effect within a certain margin of error. The following descriptions in the specification are preferred embodiments for carrying out this application; however, these descriptions are for the purpose of illustrating the general principles of this application and are not intended to limit the scope of this application. The scope of protection of this application shall be determined by the appended claims.

[0067] It should also be noted that the terms "comprising," "including," or any other variations thereof are intended to cover non-exclusive inclusion, such that a product or system comprising a list of elements includes not only those elements but also other elements not expressly listed, or elements inherent to such a product or system. Without further limitation, an element defined by the phrase "comprising one..." does not exclude the presence of other identical elements in the product or system that includes said element.

[0068] It should be understood that the term "and / or" used in this article is merely a description of the relationship between related objects, indicating that three relationships can exist. For example, A and / or B can represent: A existing alone, A and B existing simultaneously, and B existing alone. Additionally, the character " / " in this article generally indicates that the preceding and following related objects have an "or" relationship.

[0069] The foregoing description illustrates and describes several preferred embodiments of this application. However, as previously stated, it should be understood that this application is not limited to the forms disclosed herein and should not be construed as excluding other embodiments. It can be used in various other combinations, modifications, and environments, and can be altered within the scope of the application concept described herein through the foregoing teachings or techniques or knowledge in related fields. Any modifications and variations made by those skilled in the art that do not depart from the spirit and scope of this application should be within the protection scope of the appended claims.

Claims

1. A lightweight, refractory, high-entropy alloy with a strong-ductility matching structure, characterized in that, The general formula for the lightweight refractory high-entropy alloy is (TiNbAlMoV). x Zr y Where 14at.% ≤ y ≤ 18at.%, and x + y = 100at.%. The lightweight refractory high-entropy alloy has a multiphase structure of BCC1+BCC2+AlZr phases, and its melting point is not lower than 1500℃; its density is 6.35-6.50 g / cm³. 3 ; The lightweight refractory high-entropy alloy has a compressive yield strength of not less than 1400 MPa and a maximum compressive strength of not less than 1470 MPa in the as-cast state at room temperature; a yield strength of not less than 938 MPa and a compressive strength of not less than 967 MPa at 800℃; a yield strength of not less than 202 MPa and a compressive strength of not less than 212 MPa at 1000℃; a fracture strain of not less than 10.00%; and an average Vickers microhardness of 482.

19.

2. The lightweight refractory high-entropy alloy according to claim 1, characterized in that, The general formula for the lightweight refractory high-entropy alloy is (TiNbAlMoV). x Zr y Where 15at.% ≤ y ≤ 17at.%, and x + y = 100at.%.

3. The lightweight refractory high-entropy alloy according to claim 1, characterized in that, When x = 84.27 at.% and y = 15.73 at.%, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). 84.27 Zr 15.73 The density of the alloy is 6.42 g / cm³. 3 At room temperature, the compressive yield strength is 1401 MPa, the fracture strain is 11.65%, the compressive strength is 1470 MPa, and the average Vickers microhardness is 482.

19.

4. The lightweight, refractory, high-entropy alloy with a strong-ductility matching according to claim 2, characterized in that, When x = 83.39 at.% and y = 16.61 at.%, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). 83.39 Zr 16.61 The density of the alloy is 6.39 g / cm³. 3 At room temperature, the compressive yield strength is 1450 MPa, the fracture strain is 10.72%, the compressive strength is 1531 MPa, and the average Vickers microhardness is 485.

26.

5. The lightweight, refractory, high-entropy alloy with a strong-ductility matching according to claim 1, characterized in that, When x = 82.36 at.% and y = 17.64 at.%, the general formula of the lightweight refractory high-entropy alloy is (TiNbAlMoV). 82.36 Zr 17.64 The density of the alloy is 6.43 g / cm³. 3 At room temperature, the compressive yield strength is 1545 MPa, the fracture strain is 12.10%, the compressive strength is 1587 MPa, and the average Vickers microhardness is 488.

54.

6. A method for preparing a lightweight, refractory, high-entropy alloy with a strength-ductility balance as described in any one of claims 1-5, characterized in that: The method specifically includes the following preparation steps: S1) Convert the atomic percentage of each alloy component into a mass ratio and weigh the required mass of each element; S2) Remove impurities and oxide scale from the surface of the selected raw material block, place it in anhydrous ethanol for ultrasonic vibration cleaning to remove surface impurities, and then dry it. S3) Weigh the raw material blocks after processing S2) according to the mass of each raw material calculated by S1). Place the weighed raw materials and titanium ingots into the copper crucible of the non-consumable vacuum arc furnace in order of their melting points from low to high. S4) First, the furnace cavity is evacuated, then a protective atmosphere is introduced into the furnace cavity, and multiple melting processes are carried out under a certain current to obtain a lightweight refractory high-entropy alloy.

7. The method according to claim 6, characterized in that, The specific process parameters in S4) are: vacuuming to 5×10 -3 Below Pa, the protective atmosphere is high-purity argon gas at a pressure of 0.02 MPa; each melting time is 2 to 3 minutes, and the mixture needs to be turned over after each melting.

8. The application of a lightweight refractory high-entropy alloy as described in any one of claims 1-5 in the field of high-temperature structural materials.

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