CN117230336B - Method for preparing high-entropy alloy - Google Patents
Method for preparing high-entropy alloy Download PDFInfo
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention discloses a method for preparing high-entropy alloy, and belongs to the technical field of high-entropy alloy preparation. The invention takes high-entropy alloy powder as a raw material, adopts a direct laser deposition process to prepare the high-entropy alloy, and the chemical composition of the high-entropy alloy is (FeCoNi) 86Al7Ti7. Printing parameters were determined by laser melting (FeCoNi) 86Al7Ti7 high-entropy alloy powder and adopting an orthogonal test mode, and a (FeCoNi) 86Al7Ti7 high-entropy alloy block with high density was successfully prepared. The block molding piece has the characteristics of higher dimensional accuracy, more flexible structural design, high density, one-step molding and the like.
Description
Technical Field
The invention belongs to the technical field of high-entropy alloy preparation, and particularly relates to a method for preparing high-entropy alloy.
Background
The metal material is an important material foundation for human survival and development, and plays an extremely important role in promoting the development and progress of human society. At present, the traditional metal material designed based on the single main element alloy design concept is difficult to obtain further breakthrough in performance due to the limitation of the design concept, and cannot meet the requirements of modern industrial production and further development of human society. Therefore, how to develop and design a novel metal material with excellent properties has become an important research point for researchers in recent years. She Junwei et al break through the constraint of the traditional metal material single principal element alloy design concept, propose a brand new multi principal element alloy design concept for the first time, and design a brand new metal alloy material of high-entropy alloy. The high-entropy alloy is used as a novel metal alloy material consisting of five or more principal elements, has high entropy effect, delayed diffusion effect, lattice distortion effect and cocktail effect due to the unique design concept of multi-principal element alloy, can obtain simple and random solid solution phase, and shows excellent mechanical properties. Compared with the traditional metal materials, the high-entropy alloy has unique performance combination, mainly comprises high strength, high hardness, good corrosion resistance, oxidation resistance, high thermal stability, strong fatigue resistance and the like, and has great application potential in the fields of aerospace, energy power, automobile manufacturing, biomedical treatment and the like. At present, the high-entropy alloy is mainly prepared by conventional methods such as vacuum arc melting, powder metallurgy, casting and the like, and the high-entropy alloy prepared by the method has metallurgical defects such as pores, inclusions and the like, and meanwhile, complicated thermo-mechanical processing is required in the follow-up process due to the limitations of the preparation technology, so that the application of the high-entropy alloy in daily life and industrial production is greatly limited. Therefore, the development of advanced high-entropy alloy forming techniques is of great importance.
Disclosure of Invention
The present invention provides a method for preparing a high-entropy alloy, aiming at the problems existing in the prior art.
In order to achieve the above purpose, the present invention provides the following technical solutions:
A method for preparing high-entropy alloy mainly prepares raw material (FeCoNi) 86Al7Ti7 powder into high-entropy alloy material by controlling parameters in a direct laser deposition technology. The structure of the high-entropy alloy material can be changed by adjusting parameters, and the mechanical property is improved.
Compared with the conventional preparation method, the Direct Laser Deposition (DLD) is an emerging rapid prototyping technology, has the advantages of net prototyping manufacture, high material utilization rate, high design freedom, short processing period and the like, can directly prepare target parts with high geometric complexity, and effectively overcomes the defects of the conventional method in preparing parts with high geometric complexity due to the limitations of the technology. Meanwhile, the DLD technology can also effectively avoid the problems of coarse grains and the like of the high-entropy alloy prepared by adopting a vacuum arc melting method. The invention breaks the limit of (FeCoNi) 86Al7Ti7 high-entropy alloy in the aspects of realizing modern industrial production and commercial application by adopting a DLD technology.
The method for preparing the high-entropy alloy specifically comprises the following steps:
Step 1, preparing prealloy powder from raw materials (FeCoNi) 86Al7Ti7 by adopting an air atomization method, and drying;
Step 2, designing a three-dimensional model of the part by utilizing Magics three-dimensional modeling software on a computer, and performing slicing treatment and laser scanning path, scanning strategy and process parameter setting on the three-dimensional model of the part designed by the Magics software by using BLT-BP software so as to obtain profile data of each section;
And 3, adjusting the position of the substrate in the forming bin, and installing and fixing the substrate on a forming platform of the forming bin.
Step 4, placing the dried prealloyed powder in a powder storage tank of 3D printing equipment;
Step 5, starting a BLT-C400 type metal 3D printer and related auxiliary equipment, and introducing high-purity argon into the forming bin for gas washing so that the oxygen concentration in the forming bin is lower than 500ppm;
and 6, after the program setting work is completed, outputting the processed NC file format, importing the processed NC file format into BLT-MCS equipment execution software of a BLT-C400 type metal 3D printer, calling slice contour information by using BLT-MCS software of the C400 equipment, controlling a laser beam movement track through triaxial movement of a machine tool, adjusting the powder discharge amount, coaxially feeding powder to melt prealloyed powder, and accumulating the prealloyed powder layer by layer into a three-dimensional entity identical with the model.
Further, in the step 1, the pre-alloy powder is dried in a vacuum drying oven at 80 ℃ for 4 hours, so that the powder has good fluidity. The prealloyed powder is spherical in shape, and the particle size of the powder ranges from 53 mu m to 150 mu m.
Further, the thickness of the slice in step 2 is 0.35mm.
Further, the process parameters in step 2 are set as follows: the laser power is 350-550W, the laser scanning speed is 220-380mm/min, the scanning interval is 0.6-0.8mm, and the laser spot diameter is 1mm.
Further, the maximum output power of the laser apparatus in step 6 is 1000W.
Further, when the powder output amount is adjusted in the step 6, the motor speed is 2%, and the powder carrying gas speed is 5L/min.
Further, the step further comprises subjecting the obtained high-entropy alloy to heat treatment, wherein the heat treatment is that at 780 ℃ for 4 hours.
The invention also provides the high-entropy alloy prepared by the method.
Compared with the prior art, the invention has the following advantages and technical effects:
1. The invention adopts the direct laser deposition technology to successfully prepare the (FeCoNi) 86Al7Ti7 high-entropy alloy block sample with smooth surface and no obvious defects, and has high density and good dimensional accuracy.
2. The sample structure prepared by the invention is improved, and the part can obtain an ultrafine grain structure due to higher melting and solidification rate, and the formed part is found to consist of an FCC phase and an L2 1 phase after XRD test.
3. The molded part prepared by the invention has good mechanical properties: the room temperature tensile yield strength is 733.14MPa, the tensile strength is 1066.81MPa, and the breaking elongation is 25.49%.
4. The sample prepared by the method has the advantages of net forming manufacture, high material utilization rate, high design freedom, short processing period and the like, and effectively overcomes the defect of the conventional method in preparing parts with high geometric complexity due to the limitation of the technology.
Drawings
The accompanying drawings, which are included to provide a further understanding of the application and are incorporated in and constitute a part of this specification, illustrate embodiments of the application and together with the description serve to explain the application. In the drawings:
FIG. 1 is a surface morphology diagram of (FeCoNi) 86Al7Ti7 high-entropy alloy powder prepared in example 1 of the present invention;
FIG. 2 is a graph of the macroscopic topography of the upper surface of the (FeCoNi) 86Al7Ti7 high-entropy alloy block prepared in example 1 of the present invention;
FIG. 3 is an optical electron micrograph of a longitudinal section of a (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in example 1 of the present invention;
FIG. 4 is an optical electron micrograph of the (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in example 1 of the present invention after corrosion of the longitudinal section;
FIG. 5 is an XRD analysis of the (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in example 2 of the present invention;
FIG. 6 is a stress-strain curve of the (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in example 2 of the present invention;
FIG. 7 is an XRD analysis of the (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in comparative example 2 of the present invention after heat treatment;
FIG. 8 is a stress-strain curve of the (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in example 3 of the present invention;
FIG. 9 is an optical electron micrograph of a longitudinal section of a (FeCoNi) 86Al7Ti7 high-entropy alloy prepared in example 4 of the present invention.
Detailed Description
Various exemplary embodiments of the invention will now be described in detail, which should not be considered as limiting the invention, but rather as more detailed descriptions of certain aspects, features and embodiments of the invention.
It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. In addition, for numerical ranges in this disclosure, it is understood that each intermediate value between the upper and lower limits of the ranges is also specifically disclosed. Every smaller range between any stated value or stated range, and any other stated value or intermediate value within the stated range, is also encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention. All documents mentioned in this specification are incorporated by reference for the purpose of disclosing and describing the methods and/or materials associated with the documents. In case of conflict with any incorporated document, the present specification will control.
It will be apparent to those skilled in the art that various modifications and variations can be made in the specific embodiments of the application described herein without departing from the scope or spirit of the application. Other embodiments will be apparent to those skilled in the art from consideration of the specification of the present application. The specification and examples of the present application are exemplary only.
As used herein, the terms "comprising," "including," "having," "containing," and the like are intended to be inclusive and mean an inclusion, but not limited to.
The "room temperature" as used herein is calculated as 25.+ -. 2 ℃ unless otherwise indicated.
The printing parameters are determined by laser melting (FeCoNi) 86Al7Ti7 high-entropy alloy powder and adopting an orthogonal test mode, so that the (FeCoNi) 86Al7Ti7 high-entropy alloy block with high density is successfully prepared. The formed part prepared by the direct laser deposition technology provided by the invention has the characteristics of higher dimensional accuracy, more flexible structural design, high density, one-step forming and the like. Because of the high cooling rate, the formed part can obtain microstructure such as superfine crystal structure and supersaturated solid solution, and the like, so that the high-entropy alloy component with excellent structure and mechanical property can be obtained.
A method of preparing a high entropy alloy comprising the steps of:
Step 1, preparing prealloy powder from raw materials (FeCoNi) 86Al7Ti7 by adopting an air atomization method, and drying;
Step 2, designing a three-dimensional model of the part by utilizing Magics three-dimensional modeling software on a computer, and performing slicing treatment and laser scanning path, scanning strategy and process parameter setting on the three-dimensional model of the part designed by the Magics software by using BLT-BP software so as to obtain profile data of each section;
And 3, adjusting the position of the substrate in the forming bin, and installing and fixing the substrate on a forming platform of the forming bin.
Step 4, placing the dried prealloyed powder in a powder storage tank of 3D printing equipment;
Step 5, starting a BLT-C400 type metal 3D printer and related auxiliary equipment, and introducing high-purity argon into the forming bin for gas washing so that the oxygen concentration in the forming bin is lower than 500ppm;
and 6, after the program setting work is completed, outputting the processed NC file format, importing the processed NC file format into BLT-MCS equipment execution software of a BLT-C400 type metal 3D printer, calling slice contour information by using BLT-MCS software of the C400 equipment, controlling a laser beam movement track through triaxial movement of a machine tool, adjusting the powder discharge amount, coaxially feeding powder to melt prealloyed powder, and accumulating the prealloyed powder layer by layer into a three-dimensional entity identical with the model.
In some preferred embodiments of the invention, step 1, the drying is performed by drying the prealloyed powder in a vacuum oven at 80 ℃ for 4 hours, ensuring good flowability of the powder. The prealloyed powder is spherical in shape, and the particle size of the powder ranges from 53 mu m to 150 mu m.
In some preferred embodiments of the invention, step 2, the thickness of the slice is 0.35mm. The technological parameters are as follows: the laser power is 350-550W, preferably 450-500W, more preferably 450W and 500W; the laser scanning speed is 220-380mm/min, preferably 340-380mm/min, more preferably 340mm/min and 380mm/min; the scanning interval is 0.6-0.8mm, preferably 0.8mm; the scanning angle is 45 degrees, and the laser spot diameter is 1mm.
The maximum output power of the laser device in step 6 is 1000W in some preferred embodiments of the invention. When the powder discharge amount is regulated, the motor speed is 2%, and the powder carrying gas speed is 5L/min.
In some preferred embodiments of the invention, the step further comprises subjecting the obtained high entropy alloy to a heat treatment, which is a heat treatment at 780 ℃ for 4 hours.
The invention also provides the high-entropy alloy prepared by the method.
The raw material (FeCoNi) 86Al7Ti7 used in the following examples of the present invention was purchased from Ningbo, new Material technology Co.
The prealloyed powder in the following examples of the invention has an average particle size of 53 to 150. Mu.m.
The following examples serve as further illustrations of the technical solutions of the invention. It is common knowledge in the art and conventional methods to know and not explicitly described, and the difference in the means to be taken does not affect the product performance.
Example 1
1) Raw material preparation: the raw material (FeCoNi) 86Al7Ti7 is placed into an air atomization device, and high-speed inert gas high-purity argon is adopted to impact and prealloy the (FeCoNi) 86Al7Ti7 high-entropy alloy in a molten flow state. Under the action of high-speed argon gas flow, breaking and decomposing into metal liquid drops, and cooling and solidifying to obtain spherical or nearly spherical (FeCoNi) 86Al7Ti7 high-entropy alloy powder. And (3) placing (FeCoNi) 86Al7Ti7 high-entropy alloy powder into a vacuum drying oven for drying, wherein the drying temperature is set to 80 ℃, the drying time is 4 hours, and a vibrating screen is adopted to separate prealloy powder with the particle size of 53-150 mu m as a raw material for DLD (digital versatile disc) forming.
2) And designing a three-dimensional model of the part on a computer by utilizing Magics three-dimensional modeling software, and outputting the model into a file in an STL format, wherein the size of the part is a block body of 15mm multiplied by 5 mm. Slicing a three-dimensional model of a part designed by Magics software through BLT-BP software, setting a laser scanning path, a scanning strategy and technological parameters, obtaining profile data of each section, converting the profile data into NC format files, and introducing the NC format files into BLT-MCS equipment executing software of a BLT-C400 type metal 3D printer, wherein the technological parameters are as follows: the laser power is 450W, the laser scanning speed is 340mm/min, the printing layer thickness is 0.35mm, the scanning path interval is 0.8mm, the scanning angle is 45 degrees, and the spot diameter is 1mm.
3) And (3) adjusting the position of the substrate in the forming bin, installing and fixing the substrate on a forming platform of the forming bin, and placing the screened prealloyed powder in a powder storage tank.
4) And starting the BLT-C400 type metal 3D printer and related auxiliary equipment, closing the forming bin, then opening the argon bottle, and introducing high-purity argon into the forming bin for gas washing so as to maintain the oxygen concentration in the forming bin at about 500 ppm.
5) After the gas washing is completed, the BLT-MCS software of the C400 equipment is used for adjusting slice contour information, the motion track of the laser beam is controlled through the triaxial motion of the machine tool, the powder output amount is adjusted (at the moment, the motor speed is 2%, the powder carrying gas speed is 5L/min), and the metal powder is melted through coaxial powder feeding and is stacked layer by layer to form the same three-dimensional entity as the model. Finally, a high-entropy alloy block sample with the size of 15mm multiplied by 5mm is obtained.
FIG. 1 is a surface morphology diagram of (FeCoNi) 86Al7Ti7 high-entropy alloy powder prepared in example 1 of the present invention.
The macro morphology of the block sample obtained in the embodiment is shown in fig. 2, and as can be seen from fig. 2, the surface morphology of the sample is smooth, and the sample has good formability.
The block samples prepared in this example were polished as follows: firstly, embedding a high-entropy alloy block sample into a cylindrical metallographic sample by adopting a cold embedding method; then, sequentially polishing the surfaces of the SiC abrasive paper with different meshes from low to high to make the surfaces smooth; and finally, polishing the surface to be observed by adopting a semi-automatic polishing machine, wherein in the polishing process, diamond grinding pastes with different particle sizes are respectively adopted as polishing auxiliary reagents until the surface to be observed is polished to a mirror surface state without scratches. And carrying out ultrasonic cleaning on the high-entropy alloy block sample after finishing polishing treatment to remove the residual polishing paste and greasy dirt on the surface, wherein the adopted cleaning solution is absolute ethyl alcohol. The polished sample was then etched as follows: and (3) adopting diluted aqua regia as an etching reagent to respectively etch the transverse and longitudinal sections of the high-entropy alloy block sample subjected to polishing treatment, wherein the etching time is 3-5s. And immediately flushing with a large amount of clear water to remove aqua regia on the surface of the block sample after the surface of the block sample is slightly darkened, and repeating the step of cleaning the surface by using absolute ethyl alcohol.
The polished and corroded morphology of the block sample obtained in this embodiment is shown in fig. 3 and fig. 4, and it can be seen from fig. 3 that the sample has no pores basically, and the density is good, and that the equiaxed grains are uniformly distributed in fig. 4.
Example 2
1) Raw material preparation: the raw material (FeCoNi) 86Al7Ti7 is placed into an air atomization device, and high-speed inert gas high-purity argon is adopted to impact and prealloy the (FeCoNi) 86Al7Ti7 high-entropy alloy in a molten flow state. Under the action of high-speed argon gas flow, breaking and decomposing into metal liquid drops, and cooling and solidifying to obtain spherical or nearly spherical (FeCoNi) 86Al7Ti7 high-entropy alloy powder. And (3) placing (FeCoNi) 86Al7Ti7 high-entropy alloy powder into a vacuum drying oven for drying, wherein the drying temperature is set to 80 ℃, the drying time is 4 hours, and a vibrating screen is adopted to separate prealloy powder with the particle size of 53-150 mu m as a raw material for DLD (digital versatile disc) forming.
2) And designing a three-dimensional model of the part on a computer by utilizing Magics three-dimensional modeling software, and outputting the model into a file in an STL format, wherein the size of the part is a block body of 15mm multiplied by 5 mm. Slicing a three-dimensional model of a part designed by Magics software through BLT-BP software, setting a laser scanning path, a scanning strategy and technological parameters, obtaining profile data of each section, converting the profile data into NC format files, and introducing the NC format files into BLT-MCS equipment executing software of a BLT-C400 type metal 3D printer, wherein the technological parameters are as follows: the laser power is 500W, the laser scanning speed is 380mm/min, the printing layer thickness is 0.35mm, the scanning path interval is 0.8mm, the scanning angle is 45 degrees, and the spot diameter is 1mm.
3) And (3) adjusting the position of the substrate in the forming bin, installing and fixing the substrate on a forming platform of the forming bin, and placing the screened prealloyed powder in a powder storage tank.
4) And starting the BLT-C400 type metal 3D printer and related auxiliary equipment, closing the forming bin, then opening the argon bottle, and introducing high-purity argon into the forming bin for gas washing so as to maintain the oxygen concentration in the forming bin at about 500 ppm.
5) After the gas washing is completed, the BLT-MCS software of the C400 equipment is used for adjusting slice contour information, the motion track of the laser beam is controlled through the triaxial motion of the machine tool, the powder output amount is adjusted (at the moment, the motor speed is 2%, the powder carrying gas speed is 5L/min), and the metal powder is melted through coaxial powder feeding and is stacked layer by layer to form the same three-dimensional entity as the model. Finally, high-entropy alloy block samples with the dimensions of 30mm multiplied by 50mm multiplied by 10mm are obtained.
XRD analysis of the bulk sample obtained in this example is shown in fig. 5, and it can be seen from fig. 5 that the DLD state sample consists of FCC phase and L2 1 phase.
Example 3
The high-entropy alloy block sample prepared in the example 2 is subjected to heat treatment for 4 hours at 780 ℃, and then is subjected to water quenching (putting into water) to obtain the heat-treated high-entropy alloy.
The DLD-state high-entropy alloy obtained in example 2 and the heat-treated high-entropy alloy obtained in example 3 were subjected to room temperature tensile test, with a tensile machine of a CMT-5205 microcomputer controlled electronic tester, at a tensile test rate of 0.84mm/min. FIG. 6 is a stress strain curve for a DLD state (FeCoNi) 86Al7Ti7 high-entropy alloy, with a room temperature tensile yield strength of 733.14MPa, a tensile strength of 1066.81MPa, and an elongation at break of 25.49%. The DLD alloy has high strength and good plasticity, and can be matched with the DLD alloy well in strength and plasticity. Fig. 7 shows XRD curves of the heat-treated (FeCoNi) 86Al7Ti7 high-entropy alloy, and it can be seen by XRD analysis that the heat-treated (FeCoNi) 86Al7Ti7 high-entropy alloy consists of FCC phase, L1 2 phase, and L2 1 phase. Compared to the high entropy alloy bulk sample in the printed state, the bulk sample after 4h of heat treatment at 780 ℃ produced a new L1 2 phase inside. According to the related literature, the L1 2 phase intermetallic compound particles can play an important role in improving the mechanical properties of the metal alloy material.
FIG. 8 is a stress strain curve of (FeCoNi) 86Al7Ti7 high-entropy alloy after heat treatment at 780℃for 4 hours, and it can be seen that the room temperature tensile yield strength of the heat-treated alloy at 780℃is 1076.63MPa, the tensile strength is 1510.09MPa, and the elongation at break is 10.74%. Compared with the printing state high-entropy alloy, the strength is greatly improved, the plasticity is reduced, and the mechanical property is remarkably improved. The reason why the high-entropy alloy can obtain excellent mechanical properties after being subjected to heat treatment for 4 hours at 780 ℃ is mainly caused by high-density evenly-distributed near-spherical L1 2 -phase intermetallic compound particles generated in the alloy after heat treatment.
Example 4
The difference from example 2 is that in step 2), the process parameters are: the laser power is 300W, the laser scanning speed is 340mm/min, the printing layer thickness is 0.35mm, the scanning path spacing is 0.8mm, and the scanning angle is 45 degrees.
The density of the high-entropy alloy block prepared by the method is only 89.16% as measured by an Archimedes drainage method, and the high-entropy alloy block is low in laser power and short in residence time because the laser beam provided by the combination of the low laser power and the high laser scanning speed is low in energy and cannot sufficiently melt high-entropy alloy powder particles, so that a large number of fusion defects are generated. In fig. 9, a large number of under-fusion defects can be seen, with more coarse pores, resulting in poor mechanical properties of the sample.
The present application is not limited to the above-mentioned embodiments, and any changes or substitutions that can be easily understood by those skilled in the art within the technical scope of the present application are intended to be included in the scope of the present application. Therefore, the protection scope of the present application should be subject to the protection scope of the claims.
Claims (6)
1. A method of preparing a high entropy alloy comprising the steps of:
Step 1, preparing a raw material (FeCoNi) 86Al7Ti7 into prealloyed powder by adopting an air atomization method, and drying;
Step 2, designing a three-dimensional model of the part on a computer, and regulating and controlling laser parameters as follows: the power is 500W, the scanning speed is 380mm/min, the scanning interval is 0.8mm, the scanning angle is 45 degrees, and the spot diameter is 1mm, so that the profile data of each section is obtained;
And 3, controlling the movement track and the powder discharge amount of the laser beam according to the profile data of each section by adopting a 3D printing technology, and accumulating the dried prealloyed powder layer by layer to obtain the high-entropy alloy.
2. The method for producing a high-entropy alloy according to claim 1, wherein the prealloyed powder is spherical and has a particle size of 53 to 150 μm.
3. The method for preparing high-entropy alloy according to claim 1, wherein during the controlling of the powder yield, the motor rate is 2% and the powder carrying gas rate is 5L/min.
4. The method for preparing high-entropy alloy according to claim 1, wherein before 3D printing, pure argon is introduced into a forming bin in the apparatus, and the oxygen concentration is controlled to be lower than 500ppm.
5. The method for producing a high-entropy alloy according to any one of claims 1 to 4, further comprising a step of heat treatment after the high-entropy alloy is obtained.
6. The method for preparing a high-entropy alloy according to claim 5, wherein the heat treatment is a heat treatment at 780 ℃ for 4 hours.
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