TWI729899B - Method for processing high-entropy alloy - Google Patents

Abstract

The present invention discloses a method for processing high-entropy superalloy so as to make the high-entropy superalloy be formed with hierarchical-precipitation microstructure therein. When the proposed method is executed, a first thermal process and a first cooling process are sequentially applied to a high-entropy superalloy (HESA), thereby leading a solid solution of a strengthening phase to be generated in a base phase of the HESA. Subsequently, a second thermal process and a second cooling process are sequentially applied to the HESA, so as to make a base-phase microstructure grow and precipitate in the strengthening phase. After the proposed method is completed, there is a hierarchical-precipitation microstructure formed in the HESA, such that the HESA not only has the advantages of lightweight and low manufacturing cost, but also exhibits outstanding high-temperature mechanical properties. As a result, after being applied with the proposed method of the present invention, product applications of HESA is hence expanded.

Description

Processing method of high-entropy superalloy

The present invention relates to the related technical field of high-entropy superalloys, and particularly refers to a method for processing high-entropy superalloys, which makes the high-entropy superalloys have a layered precipitation microstructure after a series of processing steps.

Superalloy (superalloy) has excellent high-temperature mechanical strength and is a very economical high-temperature application material. In addition to the characteristics that can be used for a long time at high temperatures above 650℃, different high-temperature application materials will also have resistance to (acid and alkali) corrosion, high temperature creep resistance, high thermal fatigue strength, wear resistance, and high temperature oxidation resistance. And other properties. Therefore, high-temperature application materials have been widely used in various industries, including: aerospace industry, energy industry, electronics industry, general industry, etc. It is known that super alloys are divided into iron-nickel base (Iron-Ni base), cobalt base (Co base) and nickel base (Ni base).

On the other hand, unlike traditional alloys that usually include a main element in their composition, the new concept of high-entropy alloys (HEA) is proposed in Reference 1. Here, reference file one refers to: Yeh et.al, "Nanostructured High-entropy Alloys with Multi-Principal Elements-Novel Alloy Design Concepts and Outcomes", Advanced Engineering Materials, 6(5)(2004), pp.299 -303.

Further, in Reference Document 2, the manufacturing technology of high-entropy alloys is introduced into the production of superalloys, so as to obtain the so-called high-entropy superalloy (HESA). Here, the second reference document is Taiwan Patent No. I595098. According to the disclosure of Taiwan Patent No. I595098, the high-entropy superalloy mainly includes at least one main element, multiple base phase elements, and at least one strengthening element. Wherein, the main element system and the base phase element together form a high-entropy base phase structure, and the strengthening element system and the base phase element together form an ordered precipitation phase structure. Wherein, the main element has a first element content of at least 35 at%, each of the base phase elements has a second element content of at least 5 at%, and each of the strengthening elements has a third element content of at least 0.1 at% . Moreover, a mixing entropy of the high-entropy superalloy is greater than or equal to 1.5R.

Compared with traditional superalloys, high-entropy superalloys not only have the advantages of light weight and low cost, but also show excellent high temperature mechanical properties such as corrosion resistance, high temperature oxidation resistance, and high temperature creep resistance. However, practical experience shows, gamma] high entropy superalloy 'phase (ordered precipitation phase) of the solution temperature (solvus temperature) will increase the mixing entropy is lowered, but reduces the high entropy degree of high-temperature superalloys is not conducive The high-temperature application of the high-entropy superalloy. Thus, Taiwan Patent No. I670377 further discloses a strengthened high entropy superalloy precipitated, which through super alloy of high entropy gamma] phase (base phase) and γ 'phase (ordered precipitation phase) administering a segregation regulation, in order to obtain so-called precipitation strengthening Type high-entropy super alloy. For example, the following table (1) lists the composition of a sample A high-entropy superalloy and a sample B high-entropy superalloy. Comparing sample B and sample A, it can be found that the element content of precipitated element Ti in sample B is increased by 2at%, while the element content of the main alloying element Ni is reduced by 2at% by the same amount. Simply put, the sample B high-entropy superalloy is obtained by performing the element segregation control on the sample A high-entropy superalloy.

Experimental data shows that element segregation control does help to improve the high-temperature mechanical properties of high-entropy superalloys. However, the difficulty in implementing element segregation control lies in the choice of "segregated elements". In more detail, Table (1) shows that the Ni and Ti elements in the composition of sample A are selected to perform the element segregation control, thereby transforming into sample B with excellent mechanical properties. It should be understood that if the mechanical properties of another sample C high-entropy superalloy need to be further strengthened, it is necessary to repeat the experiment several times to be able to select from the composition of the sample C at least suitable for performing the element segregation control Two elements.

It can be seen from the above description that the conventional technical solutions for improving the mechanical properties of high-entropy superalloys still need to be improved. In view of this, the inventor of this case tried his best to research and invent, and finally developed and completed the processing method of a high-entropy superalloy of the present invention.

The main purpose of the present invention is to provide a high-entropy superalloy processing method for performing a first heat treatment and a first cold treatment on an existing high-entropy superalloy including a base phase and a precipitation strengthening phase in sequence, so as to promote the precipitation strengthening The phase is dissolved in the base phase. Further, a second heat treatment and a second cold treatment are sequentially performed on the high-entropy superalloy to promote the growth of a base phase microstructure and precipitate in the precipitation strengthening phase, so that the high-entropy superalloy contains a layered precipitation microstructure. In particular, the method of the present invention can not only be applied to significantly improve the mechanical properties of any high-entropy superalloy, but also The advantages of low cost and light weight of the high-entropy superalloy can also be maintained, thereby expanding the application range of the high-entropy superalloy.

Therefore, in order to achieve the above object, the present invention proposes an embodiment of the processing method of the high-entropy superalloy, which includes the following steps: (1) taking a high-entropy superalloy including a base phase and a precipitation strengthening phase; (2) The high-entropy superalloy performs a first heat treatment to promote the precipitation strengthening phase to dissolve in the base phase; wherein, a process temperature of the first heat treatment is between 1000°C and 1350°C, and the first heat treatment A process time is between 2 hours and 45 hours; (3) Perform a first cold treatment on the high-entropy superalloy until the temperature of the high-entropy superalloy drops to room temperature, so that the precipitation strengthening phase and the base phase are supersaturated The medium stable state; wherein a cooling rate of the first cold treatment is between 0.01°C/sec and 350°C/sec; (4) performing a second heat treatment on the high-entropy superalloy to promote the growth of a base phase microstructure And precipitated out of the precipitation strengthening phase, so that the high-entropy superalloy contains a layered precipitation microstructure; wherein, a process temperature of the second heat treatment is between 650°C and 850°C, and the temperature of the second heat treatment is between 650°C and 850°C. A process time is between 10 hours and 200 hours; and (5) performing a second cold treatment on the high-entropy superalloy until the temperature of the high-entropy superalloy drops to room temperature to maintain the layered precipitation microstructure; wherein, A cooling rate of the second cold treatment is greater than 1°C/sec.

In one embodiment, the aforementioned base phase microstructure precipitated in the precipitation strengthening phase includes a plurality of microstructure grains, and the microstructure grains are any one of the following: single crystal microstructure grains, directional crystal grains Microstructure grains, or polycrystalline microstructure grains.

In one embodiment, the high-entropy superalloy includes: at least one main element; a plurality of base phase elements to form the base phase together with the main element; and at least one strengthening element to combine with the main element and The base phase elements together constitute the precipitation strengthening phase; wherein the main element has a first element content of at least 35 at%, each of the base phase elements has a second element content of at least 5 at%, and the strengthening element It has a third element content of at least 0.1at%.

In one embodiment, the high-entropy superalloy has a mixing entropy, and the mixing entropy is greater than or equal to 1.5R.

In one embodiment, the high-entropy superalloy is produced by any of the following processes: atmospheric melting method, vacuum arc melting method, vacuum induction melting method, electric heating method, induction heating method, rapid solidification method, mechanical alloy ball milling method , Powder metallurgy, or multilayer manufacturing.

In one embodiment, the main element is a ferrophilic element, and the ferrophilic element is any one of the following: nickel (Ni), cobalt (Co), iron (Fe), copper (Cu), titanium (Ti) , Vanadium (V), Chromium (Cr), Manganese (Mn), or platinum group elements.

In an embodiment, both the base phase element and the strengthening element can be any of the following: aluminum (Al), titanium (Ti), tantalum (Ta), niobium (Nb), chromium (Cr), manganese (Mn) ), vanadium (V), zirconium (Zr), a combination of any two of the above, or a combination of any two or more of the above.

In a feasible embodiment, the high-entropy superalloy further includes at least one noble metal element, and the noble metal element has an element weight percentage less than 15 wt%. And, the precious metal element is any one of the following: tantalum (Ta), molybdenum (Mo), tungsten (W), rhenium (Re), ruthenium (Ru), silver (Ag), gold (Au), any two of the above , Or a combination of any two or more of the above.

In another feasible embodiment, the high-entropy superalloy may further include at least one grain boundary strengthening element, and the grain boundary strengthening element has an element weight percentage less than 15 wt%. And, the grain boundary strengthening element is any one of the following: carbon (C), silicon (Si), boron (B), beryllium (Be), magnesium (Mg), calcium (Ca), hafnium (Hf), rare earth elements , A combination of any two of the above, or a combination of any two or more of the above.

<The present invention>

S1-S5: steps

Figure 1 shows the flow chart of a high-entropy superalloy processing method of the present invention; Figure 2 shows the phase diagram of the high-entropy superalloy produced by the thermodynamic simulation software JMatPro; Figure 3 shows the thermal differential analysis curve diagram of the high-entropy superalloy; Figure 4 shows the high-entropy superalloy Scanning electron microscope images; Figure 5 shows scanning electron microscope images of four experimental examples of high-entropy superalloys; Figure 6 shows scanning electron microscope images of five comparative examples of high-entropy superalloys; FIG. 7 shows the statistical bar graphs of the yield strength of Example 1, Comparative Example 5 and Comparative Example 6; and FIG. 8 shows the statistical bar graphs of the yield strength of Example 1, Comparative Example 5 and Comparative Example 6.

In order to more clearly describe the processing method of a high-entropy superalloy proposed by the present invention, the preferred embodiments of the present invention will be described in detail below in conjunction with the drawings.

Please refer to FIG. 1, which shows a flow chart of a processing method of a high-entropy superalloy of the present invention. The present invention provides a high-entropy superalloy processing method for post-processing any high-entropy superalloy, so as to achieve the positive effect of significantly improving the mechanical properties of the high-entropy superalloy without changing the basic element composition of the high-entropy superalloy. As shown in FIG. 1, the method flow first executes step S1: a high-entropy superalloy including a base phase and a precipitation strengthening phase is taken.

Materials engineers familiar with the design and production of high-entropy superalloys must know that high-entropy superalloys can be made by any of the following processes: atmospheric melting method, vacuum arc melting method, vacuum induction melting method, electric wire heating method, induction heating method, fast Solidification method, mechanical alloy ball milling method, powder metallurgy method, or multilayer manufacturing method. In terms of composition, high-entropy superalloys usually include: at least one main element, a multi-base phase element, and at least one strengthening element. Wherein, the plurality of base phase elements are used to form a base phase together with the main element, and the strengthening element is used to form a precipitation strengthening phase together with the main element and the base phase element. In addition, the main element has a first element content of at least 35 at%, and each of the base phase elements has a second element of at least 5 at% Content, and the strengthening element has a third element content of at least 0.1at%, so that the high-entropy superalloy has a mixing entropy greater than or equal to 1.5R.

In order to facilitate the understanding of the element composition of high-entropy superalloys, the following table (2) records exemplary materials of main elements, base phase elements and strengthening elements.

It must be particularly noted that the exemplary materials listed in Table (2) are not used to limit the main elements, base-phase elements, and strengthening elements. The important point is that the main elements, base phase elements, and strengthening elements compose the high-entropy superalloy according to the mixed entropy formula listed in the following formula (1).

△S _mix =-R(X _A ln(X _A )+X _B ln(X _B )+‧‧‧)................(1)

In the formula (1), XA represents the mole percentage of the A element, XB represents the mole percentage of the B element, and ln() is the natural logarithm. Further, the high-entropy superalloy can also include at least one noble metal element and/or at least one grain boundary strengthening element at the same time. Among them, the noble metal element and the grain boundary strengthening element both have small It is an element weight percentage of 15wt%, and its exemplary materials are organized in the following table (3).

In order to help explain how the manufacturing method of the present invention performs post-processing on a high-entropy superalloy to improve the mechanical properties of the high-entropy superalloy, the following table (4) lists the composition of a sample 1 high-entropy superalloy.

As shown in FIG. 1, the method flow then executes step S2: performing a first heat treatment on the high-entropy superalloy to promote the precipitation strengthening phase to dissolve in the base phase. It is worth noting that a process temperature of the first heat treatment must be between the solid solution temperature of the primary precipitate and the melting point temperature. This temperature range can be achieved by using thermodynamic simulation software (Such as: Thermo-Calc, PANDAT or JMatPro) and thermal analysis experiment to assist in the decision.

FIG. 2 shows the phase diagram of the high-entropy superalloy generated by the thermodynamic simulation software JMatPro, FIG. 3 shows the thermal differential analysis curve diagram of the high-entropy superalloy, and FIG. 4 shows the scanning electron microscope (SEM) image of the high-entropy superalloy. From the SEM images (a) of Fig. 2, Fig. 3 and Fig. 4, it can be found that if the process temperature of the first heat treatment is lower than 1000°C, the primary phase of strengthening precipitates (Primary phase of strengthening precipitates) cannot be completely dissolved in the center of the face. In the base phase of the face-centered cubic (FCC) structure, the formation of the subsequent hierarchical-precipitation microstructure (Hierarchical-precipitation microstructure) is affected, and the mechanical strength of the high-entropy superalloy cannot be smoothly improved. From the SEM images (b) of Fig. 2, Fig. 3 and Fig. 4, it can be found that, on the contrary, if the process temperature of the first heat treatment is higher than 1350℃, the phenomenon of incipient melting will be caused, which will seriously reduce the strength of the high-entropy superalloy. And malleability. Therefore, as shown in the SEM images (c) of FIG. 2, FIG. 3, and FIG. 4, the process temperature suitable for the first heat treatment of the high-entropy superalloy is between 1000°C and 1350°C.

It is supplemented that the process time of the first heat treatment is exemplarily 20 hours. However, in a feasible embodiment, the process time of the first heat treatment should be a range rather than a fixed value. When applying the present invention to post-treatment of high-entropy superalloys of different compositions, the process time of the first heat treatment is selected to be between 2 hours and 45 hours, for example: 5 hours, 10 hours, or 20 hours, as long as the precipitation strengthening can be promoted The phase can be dissolved in the base phase.

As shown in Fig. 1, the method flow then proceeds to step S3: performing a first cold treatment on the high-entropy superalloy to promote the precipitation strengthening phase and the base phase to be in a supersaturated medium stable state. After completing multiple sets of experiments, it can be seen that one of the cooling rates of the first cold treatment is between 0.01° C./sec and 350° C./sec. Next, perform step S4: perform a second heat treatment on the high-entropy superalloy to promote the growth of a base phase microstructure and precipitate out of the precipitation strengthening phase, so that the high-entropy superalloy contains a layered precipitation microstructure; wherein, the The base phase microstructure includes a plurality of microstructure grains, and the microstructure grains are any one of the following: single crystal microstructure grains, directional crystal microstructure grains, or polycrystalline microstructure grains. Moreover, after completing multiple sets of experiments, it can be known that a process temperature of the second heat treatment is between 650°C and 850°C. Finally, the method flow is to perform step S5: perform a second cold treatment on the high-entropy superalloy until the temperature of the high-entropy superalloy drops to room temperature to maintain the layered precipitation microstructure; wherein, one of the second cold treatments has a cooling rate that is More than 1°C/sec.

FIG. 5 shows scanning electron microscope (SEM) images of four experimental examples of the high-entropy superalloy, and FIG. 6 shows scanning electron microscope (SEM) images of five comparative examples of the high-entropy superalloy. In addition, the following table (5) and table (6) summarize the process conditions of four experimental examples and four comparative examples.

It can be seen from the above table (5) and the above table (6) that the difference between the experimental example 1 and the comparative example 1 lies in the method of the first cold treatment used. Moreover, after comparing the SEM image (A) of FIG. 5 with the SEM image (A) of FIG. 6, it can be ascertained that the high-entropy superalloy of Experimental Example 1 has been subjected to the post-processing method of the present invention, which contains Hierarchical-precipitation microstructures. ). However, the high-entropy superalloy of Comparative Example 1 does not contain the layered precipitation microstructure. Similarly, the difference between Experimental Example 2 and Comparative Example 2 is that the process method of the first cold treatment and the process time of the second heat treatment used are different, and the second heat treatment time of both is within the allowable range. Moreover, after comparing the SEM image (B) of FIG. 5 with the SEM image (B) of FIG. 6, it can be ascertained that the high-entropy superalloy of Experimental Example 2 has been subjected to the post-processing method of the present invention, which contains hierarchical-precipitation microstructures. ). However, the high-entropy superalloy of Comparative Example 2 does not contain the layered precipitation microstructure.

In more detail, the difference between Experimental Example 3 and Comparative Example 3 lies in the process conditions of the second heat treatment used. Moreover, after comparing the SEM image (C) of FIG. 5 with the SEM image (C) of FIG. 6, it can be ascertained that the high-entropy superalloy of Experimental Example 3 has undergone the processing (ie, post-processing) method of the present invention, which contains layered precipitation microstructures. structure. However, the high-entropy superalloy of Comparative Example 3 does not contain the layered precipitation microstructure. The main reason is that when the process temperature of the second heat treatment is lower than 650°C, the diffusion rate will be too low and it is difficult to form a gradient structure. Similarly, the difference between Experimental Example 4 and Comparative Example 4 lies in the process conditions of the second heat treatment and the process method of the second cold treatment used. Moreover, after comparing the SEM image (D) of FIG. 5 with the SEM image (D) of FIG. 6, it can be ascertained that the high-entropy superalloy of Experimental Example 4 has been subjected to the post-processing method of the present invention, and it contains a layered precipitation microstructure. However, the comparative example 4 The high-entropy superalloy does not contain the layered precipitation microstructure. The main reason is that when the process temperature of the second heat treatment is higher than 850°C, the phase equilibrium state will be changed and the gradient structure cannot be formed.

It is added that when the experimental verification is performed, the conventional high-entropy superalloy system is used as Comparative Example 5, and the SEM image (E) of FIG. 6 shows the microstructure of Comparative Example 5. Obviously, without applying the manufacturing method of the present invention, the conventional high-entropy superalloy does not have the so-called hierarchical precipitation microstructure. Furthermore, the high-entropy superalloy system disclosed in Reference Document 3 is taken as Comparative Example 6. The disclosed high-entropy superalloy also does not have the so-called gradation precipitation microstructure. Here, the reference file three refers to: Tsao et al., The High Temperature Tensile and Creep Behaviors of High Entropy Superalloy, Scientific Report 7, 12658 (2017); DOI: 10.1038/s41598-017-13026-7.

Furthermore, FIG. 7 shows a statistical bar graph of the yield strength of Example 1, Comparative Example 5, and Comparative Example 6. Among them, the data in Figure 7 was measured at room temperature. It can be seen from the data in FIG. 7 that after applying the processing method of the high-entropy superalloy of the present invention, the room temperature yield strength of the high-entropy superalloy of Experimental Example 1 is 993MPa, which is significantly higher than that of Comparative Example 5 without the manufacturing method of the present invention. Yield strength of high-entropy superalloy at room temperature (880MPa). At the same time, the room temperature yield strength of the high-entropy superalloy of Experimental Example 1 is also significantly higher than the room temperature yield strength (840 MPa) of the high-entropy superalloy of Comparative Example 6 disclosed in Reference Document 3.

On the other hand, FIG. 8 shows a statistical bar graph of the yield strength of Example 1, Comparative Example 5, and Comparative Example 6. Among them, the data in Figure 8 was measured at 750°C. It can be seen from the data in FIG. 8 that after applying the manufacturing method of the present invention, the room temperature yield strength of the high-entropy superalloy of Experimental Example 1 is 1023 MPa, which is significantly higher than the processing method of the high-entropy superalloy without applying the present invention. The room temperature yield strength (954MPa) of the high-entropy superalloy of Comparative Example 5 of the method. At the same time, the room temperature yield strength of the high-entropy superalloy of Experimental Example 1 is also significantly higher than the room temperature yield strength (855 MPa) of the high-entropy superalloy of Comparative Example 6 disclosed in Reference Document 3.

In this way, the above system has completely and clearly explained the processing method of a high-entropy superalloy disclosed in the present invention. From the above, it can be known that the present invention has the following advantages:

(1) The present invention provides a high-entropy superalloy processing method for performing a first heat treatment and a first cold treatment on a high-entropy superalloy including a base phase and a precipitation strengthening phase in sequence, so as to promote the precipitation strengthening phase to solid-dissolve In the base phase. Further, a second heat treatment and a second cold treatment are sequentially performed on the high-entropy superalloy to promote the growth of a base phase microstructure and precipitate in the precipitation strengthening phase, so that the high-entropy superalloy contains a layered precipitation microstructure. In particular, the method of the present invention can not only be applied to significantly improve the mechanical properties of any high-entropy superalloy, but also can maintain the advantages of low-cost and lightweight of the high-entropy superalloy, thereby expanding the application range of the high-entropy superalloy.

It must be emphasized that the above detailed description is a specific description of possible embodiments of the present invention, but this embodiment is not intended to limit the patent scope of the present invention. Any equivalent implementation or modification that does not deviate from the technical spirit of the present invention, All should be included in the patent scope of this case.

S1-S5: steps

Claims (11)

A processing method of a high-entropy superalloy includes the following steps: (1) taking a high-entropy superalloy containing a base phase and a precipitation strengthening phase; (2) performing a first heat treatment on the high-entropy superalloy to promote the precipitation strengthening phase to solid-dissolve In the base phase; wherein, a process temperature of the first heat treatment is between 1000°C and 1350°C, and a process time of the first heat treatment is between 2 hours and 45 hours; (3) Perform a first cold treatment on the high-entropy superalloy until the temperature of the high-entropy superalloy drops to room temperature, so that the precipitation strengthening phase and the base phase are in a supersaturated medium stable state; wherein, a cooling rate of the first cold treatment is a medium Between 0.01°C/sec and 350°C/sec; (4) Perform a second heat treatment on the high-entropy superalloy to promote the growth of a base phase microstructure and precipitate out of the precipitation strengthening phase, so that the high-entropy superalloy contains A layered precipitation microstructure; wherein a process temperature of the second heat treatment is between 650° C. and 850° C., and a process time of the second heat treatment is between 10 hours and 200 hours; and (5 ) Perform a second cold treatment on the high-entropy superalloy until the temperature of the high-entropy superalloy drops to room temperature to maintain the layered precipitation microstructure; wherein a cooling rate of the second cold treatment is greater than 1° C./sec. The method for processing a high-entropy superalloy according to claim 1, wherein the base phase microstructure includes a plurality of microstructure grains, and the microstructure grains are any one of the following: single crystal microstructure grains, directional crystal grains Structural grains, or polycrystalline microstructure grains. The method for processing a high-entropy superalloy according to claim 1, wherein the high-entropy superalloy includes: at least one main element; a plurality of base phase elements for forming the base phase together with the main element; and at least one strengthening element , Used to form the precipitation strengthening phase together with the main element and the base phase element; wherein the main element has a first element content of at least 35 at%, and each of the base phase elements has a content of at least 5 at% The second element content, and the strengthening element has a third element content of at least 0.1 at%. The method for processing a high-entropy superalloy according to claim 3, wherein the high-entropy superalloy has a mixing entropy, and the mixing entropy is greater than or equal to 1.5R. The method for processing a high-entropy superalloy as described in claim 3, wherein the high-entropy superalloy is produced by any of the following processes: atmospheric melting method, vacuum arc melting method, vacuum induction melting method, electric wire heating method, induction heating method , Rapid solidification method, mechanical alloy ball milling method, powder metallurgy method, or layered manufacturing method. The method for processing a high-entropy superalloy according to claim 3, wherein the main element is an iron-philic element, and the iron-philic element is any one of the following: nickel (Ni), cobalt (Co), iron (Fe), Copper (Cu), titanium (Ti), vanadium (V), chromium (Cr), manganese (Mn), or platinum group elements. The method for processing a high-entropy superalloy according to claim 3, wherein the base phase element and the strengthening element can be any of the following: aluminum (Al), titanium (Ti), tantalum (Ta), niobium (Nb) , Chromium (Cr), manganese (Mn), vanadium (V), zirconium (Zr), a combination of any two of the above, or a combination of any two or more of the above. The method for processing a high-entropy superalloy according to claim 3, wherein the high-entropy superalloy further includes at least one noble metal element, and the noble metal element has an element weight percentage less than 15wt%. The method for processing a high-entropy superalloy according to claim 8, wherein the precious metal element is any one of the following: tantalum (Ta), molybdenum (Mo), tungsten (W), rhenium (Re), ruthenium (Ru), silver (Ag), gold (Au), a combination of any two of the above, or a combination of any two or more of the above. The method for processing a high-entropy superalloy according to claim 3, wherein the high-entropy superalloy further includes at least one grain boundary strengthening element, and the grain boundary strengthening element has an element weight percentage less than 15 wt%. The method for processing a high-entropy superalloy according to claim 10, wherein the grain boundary strengthening element is any one of the following: carbon (C), silicon (Si), boron (B), beryllium (Be), magnesium (Mg) , Calcium (Ca), Hafnium (Hf), rare earth elements, a combination of any two of the above, or a combination of any two or more of the above.

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