A B-containing high-performance multi-principal-element high-entropy alloy with eutectic structure and a preparation method thereof

Abstract

The application provides a B-containing high-performance multi-principal-element high-entropy alloy with eutectic structure and a preparation method thereof. 15 Cr 15 Fe a Ni b B c , wherein 45 < a < 55, 10 < b < 20, 0 < c < 9, and a + b + c = 70, preferably 0.92 < b / 15 < 1.33, a, b and c are the molar ratios of the corresponding elements respectively. The application determines the high-entropy alloy composition through simple thermodynamic phase diagram calculation. The B-containing high-performance multi-principal-element high-entropy alloy with eutectic structure contains FCC phase, BCC phase and boride phase at room temperature, can exert multiple strengthening effects of high-entropy alloy, has good room temperature strength and plastic deformation capacity. Compared with most traditional high-entropy alloys, the application has good comprehensive mechanical properties and potential application value. Meanwhile, with the increase of the B content, the high-entropy alloy system in the application has a microstructure transformation of hypoeutectic-eutectic-hypereutectic, which promotes the design of eutectic high-entropy alloys with high plasticity.

Description

Technical Field

[0001] This invention relates to the field of alloy materials, and in particular to a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B and its preparation method. Background Technology

[0002] High-entropy alloys, with their multi-principal element composition, break away from the traditional alloy design concept of using one or two main elements. Composed of five or more alloying elements, they exhibit excellent wear resistance, corrosion resistance, mechanical properties, and potential application prospects under the combined effects of high-entropy, lattice distortion, atomic hysteresis diffusion, and cocktail effects. Existing research on high-entropy alloys has found that single-phase FCC structure high-entropy alloys have excellent elongation but low strength; single-phase BCC structure high-entropy alloys have high strength but poor plasticity. Furthermore, current research on high-entropy alloy systems mainly focuses on transition metals such as Co, Cr, Fe, Ni, and Mn, and some high-melting-point metals such as Nb, Ta, Mo, and W. These alloys typically have high density, generally around 8.0 g / cm³. 3 The above factors contribute to the high density of the prepared high-entropy alloys. Furthermore, the relatively expensive alloying elements such as Co, Ta, Mo, and Nb also increase the cost of the prepared high-entropy alloys. Currently, materials are increasingly trending towards lightweight and low-cost designs; excessively high density and cost reduce the engineering application value of these high-entropy alloys. Therefore, obtaining high-entropy alloys with lower density, lower cost, and good ductility and toughness is urgently needed.

[0003] The crystallization of eutectic alloys occurs at an isothermal temperature, progressing layer by layer from the surface towards the center. Because the inner surface of the solidified layer is relatively smooth, it offers less resistance to the flow of the undried liquid alloy, facilitating the alloy's filling of the mold cavity. Furthermore, at the same casting temperature, eutectic alloys have the lowest solidification temperature, resulting in a relatively high superheat of the liquid alloy, which delays solidification and thus provides the best fluidity. Based on this, Lu Yiping et al. from Dalian University of Technology combined the advantages of high-entropy alloys and eutectic alloys in 2014 to design an AlCoCrFeNi alloy with a pearlitic lamellar microstructure. 2.1 The eutectic high-entropy alloy exhibits a uniform and fine lamellar eutectic structure, composed of two phases, FCC and BCC, and displays high tensile strength and good ductility and toughness. The tensile strength at room temperature reaches 1.2 GPa, with a strain value of 22.8%. This provides a new approach for designing and developing high-entropy alloys that combine good strength and ductility.

[0004] Regarding the high-entropy alloys containing eutectic composition that have been reported so far, the existing designs of high-entropy alloys containing eutectic composition mainly focus on adding metallic elements to the matrix, which have characteristics such as large atomic radii and extremely negative mixing enthalpy (e.g., Al, Ta, Hf, Nb, Zr, Ti, Mo, etc.). However, high-entropy alloys containing interstitial atoms and having eutectic composition have been rarely reported. The atomic size of element B is small and can exist as an interstitial atom. The design concept of adding interstitial atoms to traditional alloy systems (such as Cu, Fe, etc.) has long been widely used in the field of engineering structures. For example, Cu-B alloy is one of the important intermediate alloys for deoxidizing copper alloys, improving corrosion resistance and strength. It is also a highly efficient boron additive for copper processing. Trace amounts of boron (0.005% to 0.05% wt) can significantly improve the strength and corrosion resistance of copper materials and are widely used in the field of engineering structures. (Wang Jihui, Jiang Xiaoxia, Li Shizhuo. The Influence of Boron on the Microstructure and Properties of Copper Alloys. Journal of Materials Research, 1997.11(4):381-386).

[0005] In conclusion, the design of high-performance multi-principal-element high-entropy alloys with eutectic structure has promising prospects for engineering applications. Summary of the Invention

[0006] To address the issues of high-entropy alloys, such as the inability to simultaneously achieve both strength and plasticity, poor fluidity, and severe compositional segregation, a design concept and preparation method for a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B are proposed. This high-entropy alloy with a eutectic structure exhibits a lamellar eutectic morphology in the as-cast state, with a phase structure composed of FCC, BCC, and borides. The high-entropy alloy system in this invention also exhibits a microstructural transformation from hypoeutectic to eutectic to hypereutectic, which promotes the design of eutectic high-entropy alloys that balance strength and plasticity.

[0007] This invention provides a compositional design approach for a high-performance multi-component high-entropy alloy with a eutectic structure containing type B elements. Research has shown that Co, Fe, and Ni are all FCC stabilizers, and Co and Ni have similar atomic sizes and chemical properties. Therefore, by rationally controlling the content of Fe and Ni in the alloy system, Co can be substituted. Based on these considerations, to reduce costs, Fe is used to completely replace expensive Co and part of Ni, resulting in the design of an AlCrFe2Ni2 high-entropy alloy. This alloy, along with AlCoCrFeNi... 2.1The alloy exhibits the same FCC+BCC phase structure. In the as-cast state, it displays an ultimate tensile strength of 1437 MPa and an elongation of 15.7%, which is superior to most high-entropy alloys and even comparable to Ti-based ultrafine-grained alloys. Could the cost of this AlCrFe2Ni2 high-entropy alloy be further reduced by replacing some of the relatively expensive Ni with cheaper Fe? For this purpose, since Ni-Al has a very negative entropy of mixing, reaching -22 KJ / mol, while Fe-Cr has a mixing entropy near 0, this indicates that Ni and Al are more likely to combine to form intermetallic compounds. Assuming that the NiAl phase (ordered BCC phase) can reach the eutectic temperature, this can be determined based on the Ni-Al binary phase diagram (e.g., ...). Figure 1 As shown in the diagram, when the molar ratio of Ni to Al is close to 1:1, a NiAl phase (ordered BCC phase) will form. To obtain this toughening phase that greatly improves strength, the molar ratio of Ni to Al should be kept as close as possible. The reduced portion of Ni is then replaced by Fe, thus achieving low cost. Theoretically, using the above method, iron-based high-entropy alloys containing both FCC and BCC phases can be designed. However, whether the high-entropy alloys designed using this method will have good fluidity and castability remains uncertain.

[0008] Alloys containing eutectic components are currently the most widely used casting alloys. They have good fluidity and a relatively uniform microstructure after solidification, generally consisting of two or more phases. By changing the phase composition, alloys with both sufficient strength and good plasticity can be obtained. If the above manufacturing method is modified and the AlCrFe2Ni2 high-entropy alloy is further designed, the problems of poor fluidity and castability of high-entropy alloys can be solved by introducing an element that can undergo a eutectic reaction with most of the matrix elements (Al, Cr, Fe, Ni). While keeping the Al and Cr content essentially unchanged, the relatively expensive Ni element is partially replaced by the cheaper Fe element and the introduced element, aiming to reduce costs. Since B-Cr, B-Fe, and B-Ni can undergo eutectic reactions, and their enthalpies of mixing are -31 KJ / mol, -26 KJ / mol, and -24 KJ / mol, respectively, introducing a small amount of B element into the matrix is ​​a good solution. It is important to note that when introducing B element, the molar ratio of Ni to Al must be kept close, while the content of other elements remains essentially unchanged. The reduced Ni element should be replaced by Fe element and a small amount of B element. Therefore, this invention proposes a high-performance multi-component high-entropy alloy with a eutectic structure containing type B components.

[0009] Technical solution of the present invention:

[0010] A high-performance multi-principal-element high-entropy alloy with a eutectic structure, wherein the molar ratio of each element in the multi-principal-element high-entropy alloy is Al:Cr:Fe:Ni:B = 15:15:a:b:c, wherein 45 < a < 55, 10 < b < 20, 0 < c < 9, and a + b + c = 70; preferably, 0.92 < b / 15 < 1.33.

[0011] A method for preparing a high-performance multi-principal-element high-entropy alloy with a eutectic structure, comprising the following steps:

[0012] Step 1, Grinding: Grind the surfaces of Al, Cr, Fe and Ni raw materials with a purity greater than 99.9% (mass fraction) to remove the oxide scale and impurities on the surface;

[0013] Step 2, Cleaning: Place the polished elemental metals Al, Cr, Fe and Ni into separate containers, pour in ethanol, and perform ultrasonic cleaning. After they are fully dried, place them into sealed bags for later use.

[0014] Step 3, Ingredient Preparation: Prepare the required raw materials Al, Cr, Fe, Ni, and B according to the molar ratio of each element.

[0015] Step 4, Feeding: Place the raw materials Al, Cr, Fe, Ni and B prepared in step 3 into a water-cooled copper crucible, and place the pure titanium used for oxygen measurement and oxygen absorption into another copper crucible.

[0016] Step 5, Initial Vacuuming: The vacuum arc furnace is used for initial vacuuming; then, argon gas is introduced as a protective gas.

[0017] Step 6, Secondary Vacuuming: The vacuum arc furnace is subjected to a secondary vacuuming process and filled with argon gas; before the melting begins, the pure titanium is melted for 5-6 minutes.

[0018] Step 7: Start melting: Adjust the welding torch to a suitable position to successfully ignite the arc; after the alloy is completely liquefied, stabilize the melting and turn off the arc; after the alloy cools, flip it over and repeat the above operation six times to obtain a high-performance multi-principal-element high-entropy alloy with uniform composition and eutectic structure containing type B.

[0019] Preferably, in step 2, during ultrasonic cleaning, the metallic raw material is cleaned 3 to 5 times, with each cleaning cycle lasting 8 to 10 minutes.

[0020] Preferably, in step 5: initial vacuuming: the vacuum arc furnace is subjected to initial vacuuming to achieve a vacuum level of 0.75-0.8 Pa; then, protective argon gas is introduced to a pressure of 0.04-0.07 MPa.

[0021] Preferably, in step 6, the second vacuuming involves the vacuum arc furnace undergoing a second vacuuming process to bring the cavity to a temperature of 10°C. -3 ~10 -5 Vacuum degree, purged with argon gas to 0.04-0.07 MPa.

[0022] Preferably, in step 7, starting the melting process: the welding torch is adjusted to a suitable position to successfully ignite the arc; the current is increased from 18-22A to 290-310A, and the position of the welding torch is adjusted to stabilize the flame; after the alloy is completely liquefied, the melting process is stabilized for 4.5-5.5 minutes, and then the arc is turned off.

[0023] The high-entropy alloy containing type B with a eutectic structure of the present invention has the following advantages compared with the prior art:

[0024] 1. This invention designs a novel high-performance multi-principal-element high-entropy alloy with a eutectic structure by rationally selecting elements and adjusting the composition. The addition of interstitial atoms (B) with small atomic radii and good diffusion properties effectively regulates the alloy's microstructure and morphology, improving its mechanical properties. The B-type high-entropy alloy with a eutectic structure exhibits a typical lamellar eutectic microstructure in the as-cast state, with the phase structure composed of soft FCC solid solution, hard BCC solid solution, and borides.

[0025] 2. Since Al, Cr, and Fe are inexpensive, the atomic percentages of Al, Cr, and Fe in the high-entropy alloy of this invention are 15%, 15%, and 45% to 55%, respectively, which is a high proportion and keeps the cost of the high-entropy alloy at a low level.

[0026] 3. The high-entropy alloy of this invention incorporates Al and B elements, effectively reducing the content of high-density elements such as Cr, Fe, and Ni, resulting in an alloy density of 6.35 g / cm³ in the embodiments. 3 -6.80g / cm 3 It remained at a low level (well below 8.0 g / cm³). 3 Meanwhile, the addition of Al and B elements also improves the alloy's wear resistance, oxidation resistance, and corrosion resistance.

[0027] 4. The high-entropy alloy of the present invention exhibits good strength, hardness, and plasticity in the as-cast state. The high-entropy alloy of Example 1 of the present invention has excellent plasticity and cannot be broken under pressure, and its hardness can reach 484.71 HV. The high-entropy alloys of Examples 2-5 have compressive strengths ranging from 2070.3 MPa to 2564 MPa, strains between 16.2% and 41.5%, and hardnesses between 491.76 HV and 574.78 HV. In summary, the high-entropy alloy of the present invention has excellent mechanical properties, characterized by high strength, high plasticity, and high hardness.

[0028] 5. The high-entropy alloy provided by this invention has the characteristics of low melting point and good fluidity, and can be used to cast complex structural parts. Attached Figure Description

[0029] Figure 1 This is the Ni-Al binary phase diagram referenced in the design concept of this invention.

[0030] Figure 2 This is an experimental flowchart of a specific embodiment of the present invention.

[0031] Figure 3 This is an X-ray diffraction pattern of a high-entropy alloy in a specific embodiment of the present invention.

[0032] Figure 4 This is a metallographic diagram of the high-entropy alloy in a specific embodiment of the present invention.

[0033] Figure 5 This is a room temperature compressive stress-strain curve of a high-entropy alloy in a specific embodiment of the present invention.

[0034] Figure 6 This is a microscopic Vickers hardness variation diagram of the high-entropy alloy in a specific embodiment of the present invention. Detailed Implementation

[0035] To facilitate understanding of the present invention, the invention will be described more fully below in conjunction with specific embodiments, accompanying drawings, and preferred embodiments. It should be emphasized that the scope of protection of the present invention is not limited to the following specific embodiments.

[0036] All technical terms used in this document have the same meaning as commonly understood by those skilled in the art.

[0037] All the raw materials, reagents, instruments and equipment used in this invention can be purchased on the market.

[0038] Example 1:

[0039] This embodiment discloses a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B elements, wherein the molar ratio of each element is Al:Cr:Fe:Ni:B = 15:15:50:18:2. The specific preparation method is as follows:

[0040] Step 1, Grinding: Use different grades (240#, 400#, 600# and 800#) of SiC sandpaper to grind the surface of Al, Cr, Fe and Ni metal raw materials with a purity greater than 99.9% (mass fraction) to remove the oxide scale and impurities on the surface. Select B as high-purity powdered boron powder with a purity greater than 99.9% (mass fraction) and do not perform the above grinding process.

[0041] Step 2, Cleaning: Place the polished elemental metals Al, Cr, Fe, and Ni into separate containers, pour in ethanol, and perform ultrasonic cleaning. During ultrasonic cleaning, the elemental metals are cleaned four times, with each cleaning cycle lasting 9 minutes. After thorough drying, place them in sealed bags for later use. Element B is not involved in the above cleaning process and is directly placed in a sealed bag for later use.

[0042] Step 3, Batching: Calculate the molar percentage of a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B. Based on a total mass of 40g per alloy ingot, weigh the required elemental raw materials of Al, Cr, Fe, Ni, and B using an electronic balance, with a weighing error of ±0.001g.

[0043] Step 4, Feeding: Powdered boron is placed at the bottom of the copper crucible in the electric arc melting furnace, while other elemental metals are sequentially placed on top of B in order of increasing melting point, namely Al, Ni, Fe, and Cr. Pure titanium, used for oxygen measurement and absorption, is placed in another copper crucible.

[0044] Step 5, Initial Vacuuming: The vacuum arc furnace is initially evacuated to achieve a vacuum level of 0.78 Pa; then, argon gas is introduced to provide a protective gas pressure of 0.06 MPa.

[0045] Step 6, Secondary Vacuuming: The vacuum arc furnace undergoes a secondary vacuuming process to bring the cavity to a temperature of 10°C. -3 Vacuum degree of Pa, purged with argon to 0.06 MPa; before the melting begins, pure titanium is melted for 5.5 minutes to eliminate residual oxygen in the cavity and prevent the alloy from oxidizing during the melting process;

[0046] Step 7: Start melting: Adjust the welding torch to a suitable position to successfully ignite the arc; slowly increase the current from about 20A to 300A, and adjust the position of the welding torch to stabilize the flame; after the alloy is completely liquefied, stabilize the melting for about 5 minutes, and then turn off the arc; after the alloy cools, flip it over and repeat the above operation six times to obtain a high-performance multi-principal-element high-entropy alloy with uniform composition and eutectic structure containing type B.

[0047] Example 2

[0048] This embodiment discloses a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B elements, wherein the molar ratio of each element is Al:Cr:Fe:Ni:B = 15:15:50:16:4. The specific preparation method is as follows.

[0049] The preparation method of the high-entropy alloy in this embodiment is the same as that in Example 1.

[0050] Example 3

[0051] This embodiment discloses a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B elements, wherein the molar ratio of each element is Al:Cr:Fe:Ni:B = 15:15:50:15:5. The specific preparation method is as follows.

[0052] The preparation method of the high-entropy alloy in this embodiment is the same as that in Example 1.

[0053] Example 4

[0054] This embodiment discloses a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B elements, wherein the molar ratio of each element is Al:Cr:Fe:Ni:B = 15:15:50:14:6. The specific preparation method is as follows.

[0055] The preparation method of the high-entropy alloy in this embodiment is the same as that in Example 1.

[0056] Example 5

[0057] This embodiment discloses a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B elements, wherein the molar ratio of each element is Al:Cr:Fe:Ni:B = 15:15:50:12:8. The specific preparation method is as follows.

[0058] The preparation method of the high-entropy alloy in this embodiment is the same as that in Example 1.

[0059] Comparative Example 1

[0060] This comparative example discloses a type B high-entropy alloy without a eutectic structure, wherein the molar ratio of each element is Al:Cr:Fe:Ni = 15:15:50:20. The specific preparation method is as follows:

[0061] The preparation method of the high-entropy alloy in this comparative example is the same as that in Example 1.

[0062] Performance testing methods for high-entropy alloys:

[0063] 1. XRD (X-ray diffraction experiment)

[0064] Cylindrical samples of Φ5mm×6mm were taken from the ingot using wire electrical discharge machining (EDM). The samples were polished with 240-grit, 400-grit, 800-grit, and 1200-grit sandpaper until the surface had a silvery-white luster before XRD testing.

[0065] like Figure 3 As shown by the XRD results, the comparative example and Example 1 consist of the FCC+BCC phase, while Examples 2-5 consist of the FCC+BCC+boride phase. The absence of the boride phase in Example 1 is due to the low amount of boron added, resulting in weaker diffraction peaks that are difficult to reflect in the XRD pattern.

[0066] 2. Metallographic microscopic observation

[0067] Cylindrical samples of Φ5mm×6mm were taken from the ingot using wire electrical discharge machining (EDM). After mounting, the samples were polished with 240-grit, 400-grit, 800-grit, 1200-grit, and 2000-grit sandpaper, and then polished. After observing no scratches under an optical microscope, the samples were etched with aqua regia in a 1:3 volume ratio of concentrated nitric acid and concentrated hydrochloric acid until a clear microstructure was visible under an optical microscope.

[0068] Figure 4 The images show the metallographic microstructure of Examples 1-5 and the comparative examples. Examples 1-5 show that the alloy exhibits a typical dendritic morphology and forms a distinct lamellar eutectic structure. Simultaneously, combined with... Figure 3 XRD analysis revealed that the microstructure of alloys in Examples 1-3 was a hypoeutectic microstructure consisting of FCC phase, BCC phase, and irregular lamellar boride phase; the microstructure of alloy in Example 4 was a fully eutectic microstructure consisting of FCC phase, BCC phase, and irregular lamellar boride phase; and the microstructure of alloy in Example 5 was a hypereutectic microstructure consisting of FCC phase, BCC phase, and irregular lamellar boride phase. Figure 4 It can also be seen that without the addition of boron, the comparative alloy exhibits significant compositional segregation within its grains, and the grains are coarse. Furthermore, with the addition of boron, a noticeable refinement of the alloy's grains can be observed.

[0069] 3. Room temperature compression test

[0070] A cylindrical sample of Φ5mm×6mm was taken from the ingot using wire electrical discharge machining (EDM) for compression testing at a compression rate of 0.36mm / min.

[0071] Table 1. Compressive strength and compressibility of high-entropy alloys in Examples 1-5, Comparative Examples, and some prior art.

[0072]

[0073] Figure 5 This is a room temperature compressive stress-strain curve of the high-entropy alloy described in this invention. (Combined with...) Figure 5 As shown in Table 1, the embodiments exhibit high compressive strength and excellent plasticity, achieving a balance between plasticity and strength, which is a significant advantage compared to the comparative examples and existing high-entropy alloys. Among them, Example 3 demonstrates the best compressive strength, reaching 2595 MPa, while also exhibiting good plasticity with a compression ratio of up to 30.9%.

[0074] 4. Microhardness test and density test

[0075] To reduce experimental error, each alloy was measured at least 10 times in different regions. The highest and lowest values ​​were discarded, and the average value was taken as the microhardness value of the microstructure or constituent phase. The density was tested using the Archimedes displacement method.

[0076] Table 2 shows the micro Vickers hardness and density of comparative examples, Examples 1-5, and some prior art high-entropy alloys.

[0077] Group Hardness (HV) <![CDATA[Density (g / cm 3 )]]> Example 1 484.71 6.80 Example 2 491.76 6.61 Example 3 574.78 6.50 Example 4 536.77 6.42 Example 5 497.52 6.35 Comparative Example 433.02 6.91 <![CDATA[CoCrFeNiMnB 0.15 ]]> 195.27 7.91 <![CDATA[Al 0.25 CrFeNi 1.75 Nb 0.3 ]]> 395.55 7.76 <![CDATA[Fe2NiCrNb 0.2 ]]> 242 7.98 <![CDATA[Fe2NiCrNb 0.5 ]]> 417 8.04

[0078] Figure 6 This is a Vickers hardness variation diagram of the high-entropy alloy described in this invention, from... Figure 6 As shown in Table 2, the hardness of the examples is higher than that of the comparative examples and most prior art alloys. Table 2 also shows that the density of the examples is lower than that of the comparative examples and prior art alloys, and even lower than 8.0 g / cm³. 3 .

[0079] Based on the above data, all the embodiments exhibit good mechanical properties, with Embodiment 3 showing the best mechanical properties. This alloy has a compressive strength of 2595 MPa, a compression ratio of 30.9%, a Vickers hardness of 574.78 HV, and a density of 6.50 g / cm³. 3 .

[0080] This invention, through reasonable element selection and composition adjustment, enables a high-performance multi-principal-element high-entropy alloy with a eutectic structure containing type B to possess comprehensive properties of high strength, high plasticity, and low density while ensuring cost control. This enriches the research results of high-entropy alloys with a eutectic structure containing type B and expands the application range of the alloy.

[0081] The above description is merely a preferred embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any equivalent substitutions or modifications made by those skilled in the art within the technical scope disclosed in the present invention, based on the technical solution and inventive concept of the present invention, should be covered within the scope of protection of the present invention.

Claims

1. A high-performance multi-principal-element high-entropy alloy with a eutectic structure, characterized in that, In the multi-principal high-entropy alloy, the molar ratio of each element is Al:Cr:Fe:Ni:B = 15:15:a:b:c, where 45 < a < 55, 10 < b < 20, 0 < c < 9, and a + b + c = 70.

2. The high-performance multi-principal-element high-entropy alloy with a eutectic structure of type B according to claim 1, characterized in that, 0.92＜b / 15＜1.33。 3. A method for preparing a high-performance multi-principal-element high-entropy alloy with a eutectic structure as described in any one of claims 1-2: characterized in that, Includes the following steps: Step 1, Grinding: Grind the surfaces of Al, Cr, Fe and Ni raw materials with a purity greater than 99.9% (mass fraction) to remove the oxide scale and impurities on the surface; Step 2, Cleaning: Place the polished elemental metals Al, Cr, Fe and Ni into separate containers, pour in ethanol, and perform ultrasonic cleaning. After they are fully dried, place them into sealed bags for later use. Step 3, Ingredient Preparation: Prepare the required raw materials Al, Cr, Fe, Ni, and B according to the molar ratio of each element. Step 4, Feeding: Place the raw materials Al, Cr, Fe, Ni and B prepared in step 3 into a water-cooled copper crucible, and place the pure titanium used for oxygen measurement and oxygen absorption into another copper crucible. Step 5, Initial Vacuuming: The vacuum arc furnace is used for initial vacuuming; then, argon gas is introduced as a protective gas. Step 6, Secondary Vacuuming: The vacuum arc furnace is subjected to a secondary vacuuming process and filled with argon gas; before the melting begins, the pure titanium is melted for 5-6 minutes. Step 7, Start Melting: Adjust the welding torch to the appropriate position to successfully ignite the arc; After the alloy is completely liquefied, it is smelted stably and the electric arc is turned off. After the alloy cools, it is flipped over and the above operation is repeated six times to obtain a high-performance multi-principal-element high-entropy alloy with uniform composition and eutectic structure containing type B.

4. The method for preparing a high-performance multi-principal-element high-entropy alloy with a eutectic structure of type B according to claim 3, characterized in that, In step 2: During ultrasonic cleaning, the metallic raw materials are cleaned 3 to 5 times, with each cleaning cycle lasting 8 to 10 minutes.

5. The method for preparing a high-performance multi-principal-element high-entropy alloy with a eutectic structure of type B according to claim 3, characterized in that, In step 5: Initial vacuuming: The vacuum arc furnace is initially evacuated to achieve a vacuum level of 0.75–0.8 Pa; then, argon gas is introduced to provide a protective gas pressure of 0.04–0.07 MPa.

6. The method for preparing a high-performance multi-principal-element high-entropy alloy with a eutectic structure of type B according to claim 3, characterized in that, In step 6: Secondary vacuuming: The vacuum arc furnace undergoes a secondary vacuuming process to bring the cavity to a temperature of 10°C. -3 ~10 -5 Vacuum degree, purged with argon gas to 0.04-0.07 MPa.

7. The method for preparing a high-performance multi-principal-element high-entropy alloy with a eutectic structure of type B according to claim 3, characterized in that, In step 7: Start melting: Adjust the welding torch to a suitable position to successfully ignite the arc; increase the current from 18-22A to 290-310A, and adjust the position of the welding torch to stabilize the flame; after the alloy is completely liquefied, stabilize the melting for 4.5-5.5 minutes, and then turn off the arc.

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