A eutectic high-entropy alloy material with high compression deformation capacity and high temperature oxidation resistance performance and a preparation method thereof

Abstract

This invention discloses a eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance, and its preparation method, belonging to the field of high-entropy alloy material preparation and processing technology. The alloy, by atomic percentage, has the following composition: Fe 38%, Co 22%, Ni 15%, Nb 3%-10%, Al 5%-12%, Cr 5%-7%, and Ta 3%-5%. The alloy prepared by this invention exhibits excellent heat-free properties, spontaneously forming a eutectic layer structure composed of Laves and FCC phases in the as-cast state. This microstructure endows the material with excellent comprehensive properties: high room-temperature compressibility and compressive stress resistance without heat treatment, and excellent high-temperature oxidation resistance. It overcomes the dependence of traditional high-performance eutectic high-entropy alloys on complex heat treatment processes, effectively shortening the production cycle and reducing manufacturing costs, and has good engineering application prospects.

Description

Technical Field

[0001] This invention relates to the field of high-entropy alloy material preparation and processing technology, specifically to a eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance, and its preparation method. Background Technology

[0002] High entropy alloys (HEAs) have shown great application potential in aerospace, nuclear industry, and high-temperature structural materials due to their unique compositional design and excellent mechanical properties. Among them, eutectic high entropy alloys (EHEAs), through their alternating lamellar structure of soft and hard phases, achieve a good balance between strength and compressive deformation capacity, and have become a research hotspot in recent years.

[0003] In recent years, traditional FeCoNi-based high-entropy alloys have attracted widespread attention. However, existing technologies for this type of alloy still face significant performance and process bottlenecks in practical engineering applications. Existing FeCoNi-based high-entropy alloys often rely heavily on complex high-temperature heat treatment processes to improve their brittleness. For example, a published article (Obrabotka metallov, 2025, 27(3): 137-150) reports that typical AlCoCrFeNiNb alloys have poor room-temperature compressive deformation capacity in the as-cast state and must undergo long-term high-temperature heat treatment at temperatures as high as 1000℃ or even 1100℃ to increase their compressive strain to about 10%~16%. This reliance on subsequent high-temperature heat treatment processes not only increases manufacturing costs, energy consumption, and process cycle time, but also limits the integrated molding and engineering application of complex shapes or large-sized components.

[0004] On the other hand, existing high-entropy alloys often face the challenge of balancing oxidation resistance and compressive strength in their composition design. For example, existing literature (such as Chinese patent application publication number CN118241097A) reports a Fe-Co-Ni-Nb-Al-Ta-Cr eutectic high-entropy alloy. This system adopts a design strategy of maintaining a low aluminum content to improve oxidation resistance at around 900℃. While this design improves the alloy's mid-to-high temperature oxidation resistance to some extent, it is accompanied by a significant loss of plasticity—its room temperature compressive strength is only about 8%-10%, exhibiting a clear tendency for brittle fracture and failing to fully utilize the ductility and toughness advantages that eutectic high-entropy alloys should possess. Therefore, there is an urgent need to develop a novel FeCoNi eutectic high-entropy alloy material that can be directly used in its as-cast state without undergoing complex heat treatment processes, and that simultaneously possesses high room temperature compressive strength and high temperature oxidation resistance, along with a simple preparation method. Summary of the Invention

[0005] To address the aforementioned technical problems, the present invention aims to provide a eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance, and its preparation method, thereby solving the problems of limited oxidation resistance and difficulty in achieving room-temperature compressive strength and plasticity in existing eutectic high-entropy alloys under high-temperature service conditions.

[0006] The technical solution of the present invention to solve the above-mentioned technical problems is as follows: In a first aspect, the present invention provides a eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance, which has the following composition by atomic percentage: Fe 38%, Co 22%, Ni 15%, Nb 3%-10%, Al 5%-12%, Cr 5%-7% and Ta 3%-5%.

[0007] The beneficial effects of this invention are as follows: This invention provides a eutectic high-entropy alloy material. Based on FeCoNi-based eutectic high-entropy alloy materials, a specific content of Al element is introduced. This Al element works synergistically with components such as Nb, Ta, and Cr, not only achieving a significant increase in fracture strength with increasing Al content, but more importantly, through precise control of the preparation process and composition, strong lattice distortion is induced, causing the alloy to spontaneously form a eutectic crystalline structure composed of Laves and FCC phases in the as-cast state. This achieves both good microstructural stability and stable high-temperature oxidation resistance and significant room-temperature compressive deformation capability in the as-cast state without heat treatment, demonstrating promising engineering application prospects.

[0008] Furthermore, the microstructure of the eutectic high-entropy alloy material in the as-cast state is a eutectic layer structure composed of the Laves phase and the FCC phase. The beneficial effects of adopting the above-mentioned further technical solutions are as follows: The eutectic high-entropy alloy material provided by the present invention can spontaneously form a stable eutectic wafer microstructure in the as-cast state. This unique microstructure endows the material with a high room-temperature compressibility (up to 32%) and compressive stress resistance (withstanding compressive stress exceeding 2000 MPa without brittle fracture) without any subsequent heat treatment. Furthermore, unlike traditional alloys that rely on high-temperature heat treatment to improve performance, the eutectic high-entropy alloy provided by the present invention exhibits a decline in yield strength and oxidation resistance if subjected to high-temperature annealing. This characteristic breaks the dependence of high-performance eutectic high-entropy alloys on complex heat treatment processes, solving the technical bottlenecks of long process cycles, low energy efficiency, and performance degradation caused by microstructure coarsening after high-temperature service in traditional alloys. This greatly improves the reliability and production efficiency of the material in complex engineering applications.

[0009] A second aspect of the present invention provides a method for preparing the above-mentioned eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance, comprising the following steps: According to the design ratio, each metal raw material is prepared and repeatedly smelted under a protective atmosphere to obtain a eutectic high-entropy alloy material. The smelting process adopts a stepped current smelting process: the first smelting is carried out with a low current intensity, and then the current intensity is gradually increased for the second to N-1 smeltings. Finally, the Nth smelting is carried out with a reduced current intensity based on the N-1 smelting and is held at a certain temperature.

[0010] The beneficial effects of this invention are as follows: the preparation process of this invention is simple and efficient, and suitable for large-scale industrial production. By adopting a stepped current melting method, the constituent elements are fully diffused and dissolved, which increases the influence of Al and other atoms on lattice distortion, while reducing the overheating and volatilization of low-melting-point elements during the melting process, thus ensuring the accuracy of the composition.

[0011] Furthermore, the current intensity for the first melting is 180-250 A, the current intensity for each subsequent melting is 100-150 A, the current intensity for the (N-1)th melting is 550-750 A, and the current intensity for each subsequent melting is 50-100 A; N is 5-6 times.

[0012] Furthermore, the melting process is maintained at a high current intensity of 550-750 A for 2-3 minutes.

[0013] The beneficial effects of adopting the above-mentioned further technical solution are as follows: The present invention adopts a stepped current melting process. In the first melting, a low current intensity of 180-250 A is used for arc initiation and preheating, so that the low melting point components are initially melted to form a molten pool and encapsulate refractory particles. Subsequently, the current intensity is increased by 100-150 A for the second to N-1 meltings, so that the current intensity is finally increased to 550-750 A and maintained. The strong arc hydrodynamics promotes the full melting and homogenization of refractory metals Ta and Nb, and finally achieves full diffusion and solid solution of each component element. It increases the influence of Al and other atoms on lattice distortion, reduces the overheating and volatilization of low melting point elements during the melting process, and ensures the accuracy of the composition.

[0014] Furthermore, the heat preservation time is 5-10 minutes.

[0015] Furthermore, intermittent electromagnetic stirring is employed during the smelting process.

[0016] The beneficial effects of adopting the above-mentioned further technical solutions are as follows: the present invention uses intermittent electromagnetic stirring to assist in stepped current melting, which breaks dendrite growth, promotes the uniform distribution of solute elements, ensures the uniformity of lattice distortion effect, and thus further improves the high-temperature oxidation resistance of the alloy.

[0017] Furthermore, the alloy sample is flipped before each melting process.

[0018] The beneficial effect of adopting the above-mentioned further technical solution is that the uniformity of the composition is ensured by repeatedly turning and melting.

[0019] Furthermore, the metal raw materials are pretreated. The pretreatment process involves first polishing with sandpaper, then mechanically polishing with diamond polishing agent until the surface is free of scratches, and finally ultrasonically cleaning with anhydrous ethanol for 5-10 minutes.

[0020] Furthermore, the metal raw materials are pure Fe, pure Co, pure Ni, pure Nb, pure Al, pure Cr and pure Ta with a purity ≥ 99.9 wt%.

[0021] Furthermore, during the loading process, Al is first placed at the bottom of the crucible, then Fe, Co, Ni and Cr are placed on top of Al as a transition layer, and finally the high-melting-point metals Ta and Nb are placed on top.

[0022] The beneficial effect of adopting the above-mentioned further technical solution is that the above-mentioned charging method prevents Al elements from melting and volatilizing prematurely during the smelting process.

[0023] Further, after loading, the crucible is placed inside the furnace chamber of the vacuum arc melting furnace, and a vacuum is first drawn to 5×10⁻⁶. -3 The pressure is below Pa, and then high-purity argon is introduced as a protective atmosphere.

[0024] The present invention has the following beneficial effects: 1. This invention introduces 3%~5% Ta element, utilizing the synergistic effect of Ta and Al to enhance crystal lattice distortion, enabling the alloy to spontaneously form a eutectic layer structure in the as-cast state within the range of 5%~12% Al. This allows the alloy to achieve a room temperature compressibility of 32% without heat treatment, thus improving its plasticity.

[0025] 2. This invention relies on the spontaneous eutectic layer structure in the as-cast state. When the alloy is oxidized in air at 1000℃ for 96 hours, the oxidation rate is as low as 0.1006 mg / (cm³). 2 ·h), exhibiting extremely high service life and reliability.

[0026] 3. The eutectic high-entropy alloy obtained by this invention is a heat-free alloy. It can achieve high performance indicators simply by controlling the microstructure in the as-cast state, eliminating the need for complex graded heat treatment processes, shortening the production cycle and reducing manufacturing costs. Attached Figure Description

[0027] Figure 1 The XRD patterns of the as-cast eutectic high-entropy alloys obtained in Examples 1 and 2 of this invention are shown below. Figure 2These are SEM images of the microstructures of Examples 1 and 2 of the present invention; wherein, (a) is Example 1 and (b) is Example 2; Figure 3 This is a comparison chart of the room temperature compression stress-strain curves of the alloys prepared in Examples 1, 2 and Comparative Example 1 of the present invention; Figure 4 The high-temperature oxidation kinetics curves of the alloys prepared in Examples 1, 2 and Comparative Example 1 of this invention are shown in the air environment at 1000°C. Detailed Implementation

[0028] The principles and features of the present invention are described below with reference to the accompanying drawings. The examples given are for illustrative purposes only and are not intended to limit the scope of the invention. Unless otherwise specified in the examples, conventional conditions or conditions recommended by the manufacturer should be followed. Reagents or instruments whose manufacturers are not specified are all commercially available products.

[0029] The metal raw materials used in the following examples and comparative examples are pure Fe, pure Co, pure Ni, pure Nb, pure Al, pure Cr and pure Ta with a purity ≥99.9 wt%.

[0030] Example 1: A Fe with high compressive strength and high-temperature oxidation resistance 38 Co 22 Ni 15 Nb 10 The preparation method of Al5Cr5Ta5 eutectic high-entropy alloy material includes the following steps: S1. Raw material preparation and pretreatment Based on atomic percentage, the composition of the eutectic high-entropy alloy material in this embodiment is: Fe 38 at.%, Co 22 at.%, Ni 15 at.%, Nb 10 at.%, Al 5 at.%, Cr 5 at.%, and Ta 5 at.%. According to the atomic weights and target atomic ratios of each element, each component is converted to a mass percentage, and the elemental metals Fe, Co, Ni, Nb, Al, Cr, and Ta are accurately weighed based on a total mass of 100g for a single melting operation.

[0031] Metal surface pretreatment: Surface treatment is performed on the metal raw materials Fe, Co, Ni, Nb, Al, Cr, and Ta. A physical grinding method is used, sequentially grinding away the surface oxide scale and attached impurities with SiC sandpaper of a gradient from 80# to 1000# until the substrate reveals a fresh metallic luster. Subsequently, the ground metal raw materials are placed in anhydrous ethanol solvent and treated with an ultrasonic cleaner for 8 minutes to thoroughly remove residual powder and oil stains from the surface. After removal, they are dried with cold air or by baking for later use.

[0032] The pretreated raw materials were placed in a water-cooled copper crucible in a non-consumable vacuum arc melting furnace. During loading, Al was first placed at the bottom of the crucible, followed by Fe, Co, Ni, and Cr above Al as a transition layer. Finally, the high-melting-point Ta and Nb were placed on top to ensure priority contact with the high temperature of the arc. To ensure alloy purity, the melting chamber was pre-evacuated to a vacuum level of 2 × 10⁻⁶. -2 Pa, then high-purity argon gas with a purity of not less than 99.99% is introduced as a protective atmosphere to maintain the furnace pressure at around 0.05 MPa.

[0033] S2, Smelting Before formal melting, a high-purity titanium (Ti) getter pre-placed at the edge of the crucible was first ignited for 45 seconds to further reduce the residual oxygen content in the furnace. The arc was then moved to the alloy raw material. Given the large single-melting volume and the presence of refractory metals Ta and Nb, a stepped current melting strategy was adopted: first, a 225 A current was used for arc ignition and preheating; then, before each melting, the alloy sample was flipped, and the current intensity was increased by 150 A for the second to fourth meltings, reaching 675 A for the fourth melting; finally, the fifth melting was performed with a current intensity reduced by 75 A from the fourth melting, and held at that temperature for 5 minutes. After melting, the alloy ingot was cooled to below 200°C under vacuum, ultimately obtaining a uniformly composed, cast eutectic high-entropy alloy ingot.

[0034] Example 2: A Fe with high compressive strength and high-temperature oxidation resistance 38 Co 22 Ni 15 Nb3Al 12 The preparation method of Cr7Ta3 eutectic high-entropy alloy material includes the following steps: S1. Raw material preparation and pretreatment Based on atomic percentage, the composition of the eutectic high-entropy alloy material in this embodiment is: Fe 38 at.%, Co 22 at.%, Ni 15 at.%, Nb 3 at.%, Al 12 at.%, Cr 7 at.%, and Ta 3 at.%. According to the atomic weights and target atomic ratios of each element, each component is converted to a mass percentage, and the elemental metals Fe, Co, Ni, Nb, Al, Cr, and Ta are accurately weighed based on a total mass of 100g for a single melting operation.

[0035] Metal surface pretreatment: Surface treatment is performed on the metal raw materials Fe, Co, Ni, Nb, Al, Cr, and Ta. A physical grinding method is used, sequentially grinding away the surface oxide scale and attached impurities with SiC sandpaper of a gradient from 80# to 1000# until the substrate reveals a fresh metallic luster. Subsequently, the ground metal raw materials are placed in anhydrous ethanol solvent and treated with an ultrasonic cleaner for 8 minutes to thoroughly remove residual powder and oil stains from the surface. After removal, they are dried with cold air or by baking for later use.

[0036] The pretreated raw materials were placed in a water-cooled copper crucible in a non-consumable vacuum arc melting furnace. During loading, Al was placed at the bottom of the crucible first, followed by Fe, Co, Ni, and Cr above Al as a transition layer. Finally, the high-melting-point Ta and Nb were placed on top to ensure priority contact with the high temperature of the arc. To ensure alloy purity, the melting chamber was pre-evacuated to 2 × 10⁻⁶ ppm. -2 Pa, then high-purity argon gas with a purity of not less than 99.99% is introduced as a protective atmosphere to maintain the furnace pressure at around 0.05 MPa.

[0037] S2, Smelting Before formal melting, a high-purity titanium (Ti) getter pre-placed at the edge of the crucible was first ignited for 45 seconds to further reduce the residual oxygen content in the furnace. The arc was then moved to the alloy raw material. Given the high Al content of this system, a stepped current melting strategy was adopted, supplemented by intermittent electromagnetic stirring during the melting process. A total of six melting operations were performed: the first melting used a low current intensity of 200 A for arc ignition and preheating; subsequently, before each melting operation, the alloy sample was flipped, and the current intensity was increased by 100 A for the second to fifth melting operations, reaching 600 A for the fifth melting operation; finally, the sixth melting operation was performed with a current intensity reduced by 50 A from the fifth operation, and held at that temperature for 8 minutes. After melting, the alloy ingot was cooled to below 200℃, ultimately obtaining a segregated, as-cast high-entropy alloy ingot.

[0038] Comparative Example 1: Fe homogenized at 1200℃ 38 Co 22 Ni 15 Nb 10 The preparation method of Al5Cr5Ta5 high-entropy alloy includes the following steps: S1. Prepare as-cast Fe using the same preparation process as in Example 1. 38 Co 22 Ni 15 Nb 10 Al5Cr5Ta5 high-entropy alloy ingot.

[0039] S2, Heat Treatment The sample to be heat-treated was cut from the above ingot using a wire EDM machine. After grinding and cleaning, it was placed in a quartz glass tube, and the tube was evacuated to 5×10⁻⁶ using a vacuum sealing system. -3 Pa, and under dynamic vacuum, the quartz tube and the stopper were fused together using an oxyhydrogen flame to seal the tube, thus creating a vacuum-sealed quartz tube to isolate it from external oxygen. Subsequently, the sealed quartz tube was placed in a high-temperature oxidation furnace, heated to 1200℃ and held for 12 h to drive the full diffusion of alloying elements and homogenization of the microstructure. After cooling to room temperature with the furnace, the sample was removed, and then the quartz tube was broken to extract the sample, thus obtaining a high-entropy alloy that had undergone high-temperature homogenization at 1200℃.

[0040] Comparative Example 2: A high-performance high-entropy alloy AlCoCrFeNiNb 0.25 The preparation method refers to the existing technical literature: Obrabotkametallov, 2025, 27(3):137-150. In order to improve its extremely poor as-cast plasticity, the alloy was subjected to air cooling heat treatment at 1100℃ for 1 h.

[0041] Experimental example: I. Experimental Methods (1) Phase and microstructure analysis methods A 5×5×5 mm sample was cut from the center of the alloy ingot using an electrical discharge wire cutting machine. 3 Metallographic samples were prepared. After being progressively polished to a mirror finish using 80#~1400# SiC sandpaper, the samples were analyzed as follows: XRD was used to scan the phase composition of the polished samples, with a scanning range of 2θ of 10-90° and a scanning speed of 5° / min. Subsequently, the microstructure of each sample was observed using a scanning electron microscope (SEM) equipped with an energy dispersive spectroscopy (EDS) instrument in backscattered electron (BSE) mode, and the chemical composition distribution of each phase region was analyzed.

[0042] (2) Test method for room temperature compressive mechanical properties Cylindrical compression specimens with dimensions of Ø4 mm × 8 mm were processed from Examples 1, 2, and Comparative Example 1 using a wire EDM machine. Uniaxial compression tests were then conducted at room temperature using a universal testing machine, with the strain rate uniformly set to 1 × 10⁻⁶. -3 s -1 Record the load and displacement data during the test, and calculate the engineering stress-engineering strain curve.

[0043] (3) High-temperature antioxidant performance test method Using an electrical discharge wire cutting machine, 5×5×5mm pieces were cut from the alloys of Example 1, Example 2, and Comparative Example 1. 2Cubic oxidation samples were prepared. All six surfaces of the samples were ground and polished, cleaned and dried, and the surface area was accurately measured and weighed. The samples were placed in a high-temperature oxidation furnace at 1000℃ for static oxidation experiments: a discontinuous weighing method was used, and the samples were taken out, cooled and weighed at preset time points. The weight gain per unit area was calculated, and the high-temperature oxidation kinetic curves of Example 1, Example 2 and Comparative Example 1 at 1000℃ were plotted.

[0044] II. Experimental Results and Analysis (1) Results of phase and microstructure analysis XRD pattern as follows Figure 1 As shown, Figure 1 In the diagram, FCC exhibits a face-centered cubic structure, while Laves represents the Lafferse phase. A comparison of the microstructures is shown below. Figure 2 As shown, Figure 2 In the image, (a) shows the Fe prepared in Example 1. 38 Co 22 Ni 15 Nb 10 (a) Al5Cr5Ta5 as-cast high-entropy alloy; (b) Fe prepared in Example 2 38 Co 22 Ni 15 Nb3Al 12 Cr7Ta3 as-cast high-entropy alloy.

[0045] Depend on Figure 1 and Figure 2 It can be seen that both Examples 1 and 2 spontaneously formed a fine and continuous network eutectic structure in the as-cast state, and both were composed of an FCC matrix and a Laves phase, indicating that the system of the present invention has good phase structure stability. Furthermore, with the increase of Al content, the diffraction peak of Example 2 shifted significantly to a lower angle, which confirms that the large atomic radius Al solid solution caused strong lattice distortion, and this distortion effect provides the alloy with significant solid solution strengthening effect.

[0046] (2) Results of room temperature compression mechanical properties test Depend on Figure 3 The compression curves show that both Examples 1 and 2, in their as-cast state without any heat treatment, can withstand compressive stress exceeding 2000 MPa without brittle fracture, and their room temperature compressive deformation rate reaches approximately 32%. In contrast, Comparative Example 1, after undergoing complex heat treatment at 1200℃, exhibits a decrease in compressive strength, and even after undergoing complex heat treatment at 1100℃, the residual strain of Comparative Example 2 in the prior art can only barely increase to 16.4%. The results demonstrate that the alloy of this invention, through its unique compositional design and strong lattice distortion effect, overcomes the dependence of traditional high-performance eutectic high-entropy alloys on complex high-temperature heat treatment, achieving a good match between as-cast strength and plasticity.

[0047] (3) Results of high-temperature antioxidant performance test Depend on Figure 4 The high-temperature oxidation kinetics curves show that the alloy of this invention exhibits stable oxidation resistance under an extreme high-temperature oxidation environment of 1000℃ for 96 hours. Example 1 shows an extremely low oxidation rate constant, while Example 2, with its high aluminum content, exhibits a nearly flat, ultra-low weight gain curve. In contrast, the oxidation resistance of Comparative Example 1, after heat treatment, significantly deteriorates. This is attributed to the high homogeneity of composition and microstructure ensured by the preparation process of this invention, allowing anti-oxidation elements such as Al and Cr in the alloy to preferentially migrate and accumulate to the surface under high-temperature conditions, spontaneously establishing an extremely dense composite anti-oxidation barrier on the alloy surface. This barrier effectively blocks further diffusion of oxygen from the environment into the interior, thereby significantly improving the high-temperature service reliability of the alloy.

[0048] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance, characterized in that, The eutectic high-entropy alloy material, by atomic percentage, has the following composition: Fe 38%, Co 22%, Ni 15%, Nb 3%-10%, Al 5%-12%, Cr 5%-7%, and Ta 3%-5%; the eutectic high-entropy alloy material is a cast alloy, and its microstructure in the cast state is a eutectic layer structure composed of Laves phase and FCC phase.

2. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance as described in claim 1, characterized in that, Includes the following steps: According to the design ratio, each metal raw material is prepared and repeatedly smelted under a protective atmosphere to obtain a eutectic high-entropy alloy material. The smelting process adopts a stepped current smelting process: the first smelting is carried out with a low current intensity, and then the current intensity is gradually increased for the second to N-1 smeltings. Finally, the Nth smelting is carried out with a reduced current intensity based on the N-1 smelting and is held at a certain temperature. The current intensity for the first melting is 180-250 A, the current intensity for each subsequent melting is 100-150 A, the current intensity for the (N-1)th melting is 550-750 A, and the current intensity for each subsequent melting is 50-100 A; N is 5-6 times.

3. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance according to claim 2, characterized in that, The heat preservation time is 5-10 minutes.

4. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance according to claim 2, characterized in that, Intermittent electromagnetic stirring is used during the smelting process, and the alloy sample is flipped before each smelting operation.

5. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance according to claim 2, characterized in that, The metal raw material is pretreated by first polishing with sandpaper, then mechanically polishing with diamond polishing agent until the surface is free of scratches, and then ultrasonically cleaning with anhydrous ethanol for 5-10 minutes.

6. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance according to claim 2 or 5, characterized in that, The metal raw materials are pure Fe, pure Co, pure Ni, pure Nb, pure Al, pure Cr and pure Ta with a purity ≥ 99.9 wt%.

7. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance according to claim 2, characterized in that, When loading the crucible, first place Al at the bottom, then place Fe, Co, Ni and Cr on top of Al as a transition layer, and finally place the high melting point metals Ta and Nb on top.

8. The method for preparing the eutectic high-entropy alloy material with high compressive deformation capacity and high-temperature oxidation resistance according to claim 7, characterized in that, After loading, place the crucible inside the vacuum arc melting furnace, and first evacuate to 5×10⁻⁶ ℃. -3 The pressure is below Pa, and then high-purity argon is introduced as a protective atmosphere.

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