CN114653944A - Preparation method of NiCoCr medium-entropy alloy particle reinforced titanium-based composite material - Google Patents
Preparation method of NiCoCr medium-entropy alloy particle reinforced titanium-based composite material Download PDFInfo
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- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 64
- 239000002131 composite material Substances 0.000 title claims abstract description 57
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- 238000002360 preparation method Methods 0.000 title claims abstract description 11
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- 238000000034 method Methods 0.000 claims abstract description 30
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- 238000002490 spark plasma sintering Methods 0.000 claims description 7
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- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
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- MRELNEQAGSRDBK-UHFFFAOYSA-N lanthanum oxide Inorganic materials [O-2].[O-2].[O-2].[La+3].[La+3] MRELNEQAGSRDBK-UHFFFAOYSA-N 0.000 description 1
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- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
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- B22—CASTING; POWDER METALLURGY
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
- B22F2003/1051—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding by electric discharge
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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Abstract
The invention discloses a preparation method of NiCoCr particle reinforced titanium-based composite material, which comprises the steps of carrying out mechanical alloying on Ni, Co and Cr element powder to obtain fine NiCoCr prealloyed powder particles, screening alloy powder particles with proper particle size, then adding the alloy powder particles into pure titanium powder to mix, and carrying out discharge plasma sintering molding to obtain the NiCoCr particle reinforced titanium-based composite material. The method realizes the alloying of Ni, Co and Cr powder by high-energy ball milling, realizes the densification of the composite material by a discharge plasma sintering technology and controls the interface diffusion between NiCoCr particles and a titanium matrix so as to obtain the NiCoCr particles which are well combined with the interface between the titanium matrix and reduce the generation of brittle compounds as far as possible, and the NiCoCr particles reinforced titanium matrix composite material can obviously enhance the strength of the material and obtain better plasticity and has better application prospect in the field of high-strength titanium matrix composite materials for aerospace.
Description
Technical Field
The invention belongs to the technical field of metal material processing, and particularly relates to a preparation method of a NiCoCr medium entropy alloy particle reinforced titanium-based composite material.
Background
The particle reinforced titanium-based composite material has the advantages of isotropy, good machinability, easy preparation, low cost and the like, has higher material strength and dimensional stability, is light in weight and high-temperature resistant, can meet the structural requirements of high-performance spacecrafts, realizes the purposes of reducing oil consumption and prolonging flight time, and is successfully applied to the aviation industry fields of missile shells, aircraft engines and the like. Common particle reinforcements include carbides, oxides, nitrides, borides and the like, and reinforcements of different types and properties have different strengthening effects. Generally speaking, the size of the reinforcing body particles is 10-30 μm, and the volume fraction of the reinforcing body particles in the composite material is 15-20%. The carbide and the boride have the advantages of high melting point, high hardness, high modulus, good chemical stability and the like, and are favorable for improving the mechanical property of the material when being used as a reinforcement of the titanium-based composite material. TiB and TiC particles become mainstream reinforcement materials in current research due to the advantages of high hardness and modulus, good compatibility with a titanium matrix, similar density, Poisson's ratio and thermal expansion coefficient with the titanium or titanium alloy matrix and the like. The oxide reinforcing particles can be classified as metal oxides, such as Al2O3、La2O3、ZrO2Etc. and non-metal oxides, e.g. SiO2. Nitride reinforcing particles also play an important role in the reinforcement of titanium alloys. For example, TiN not only has the properties of high hardness, high temperature resistance, wear resistance, corrosion resistance and the like, but also can effectively slow down the wear of materials when being used for preparing TiN particle reinforced titanium-based composite materials. However, the combination of these particles with titanium substrates presents problems, leading to a drastic reduction in plasticity, such as La by Luxian et al2O3And TiC is added into a pure titanium matrix as a reinforcing particle phase, so that the strength is greatly improved, but the plasticity is only one seventh of that of the pure titanium.
In addition, the metal particles can also be used as reinforcing particles for the titanium-based composite material. Compared with the traditional metal particles, the high-entropy alloy has higher strength; compared with amorphous alloy, the high-entropy alloy has good stability, so that the components and characteristics of the strengthening phase are easier to store in the processing process. The thermal expansion coefficient of the high-entropy alloy is very close to that of the metal matrix, and the high-entropy alloy is cooledNo phase change occurs in the process. Thus, high entropy alloy particles exhibit great potential as a new strengthening phase. Meanwhile, in the high-entropy alloy particle reinforced aluminum matrix composite, the high-entropy alloy shows good binding capacity with a matrix and stable interface compatibility. Selecting CoNiFeAl0.4Ti0.6Cr0.5The 7075 aluminum alloy is enhanced by the high-entropy alloy particles, and the tensile strength and the plasticity of the 7075 aluminum alloy are obviously superior to those of SiC prepared by the same processpThe/7075 composite material. AlFeCoCrNi/Mg composite material is prepared by selecting AlFeCoCrNi high-entropy alloy particles, the interface combination of the particles and a matrix is good, and the compressive yield strength and the compressive strength of the composite material can be respectively improved by 68.8 percent and 45.02 percent relative to the matrix. The article that the CoCrFeMnNi particles reinforce pure Ti is rare, which is probably related to that Ti is easy to react with other elements at high temperature to generate intermetallic compounds and deteriorates the performance. Therefore, the high-entropy alloy is selected as the reinforcement, so that the combination of the reinforced particles and the metal matrix interface is facilitated, and the comprehensive mechanical property of the composite material can be improved. And how to select proper element powder and components to avoid generating hard and brittle intermetallic compounds and better realize one of the important factors of the particle reinforced titanium-based composite material.
The powder metallurgy method can realize the regulation and control of the granularity and the volume fraction of the reinforcing phase by regulating the grain diameter and the proportion of the powder, thereby obtaining the composite material with uniform tissue and excellent stability, and being an ideal process means. The high-energy ball milling method is an important means for realizing the uniformity of the particle size of the element powder, the element powder with proper particle size distribution is obtained through ball milling and screening, and meanwhile, mechanical alloying is realized between the element powder through collision and crushing in the high-energy ball milling process, so that the pre-alloying of the element powder is realized, the element powder is more stable in the subsequent sintering process, and the expected diffusion effect is achieved. Spark Plasma Sintering (SPS) sintering is one of typical powder metallurgy methods, and titanium alloy powder and reinforcement powder are mixed and then put into a mold, so that the mixed powder is subjected to rapid heating densification and in-situ reaction in the processes of electrification and pressurization, and uniform and fine tissues are obtained. At present, researchers have combined computer control technology with SPS to achieve precise control of sintering temperature and time, making it possible to rapidly prepare high-performance titanium-based composite materials.
However, there are also some potential problems with high entropy alloy particle reinforced titanium based alloys that need to be considered and solved:
1. the structure and performance of the composite material are deteriorated due to the hard and brittle intermetallic compounds generated by the multi-component in the high-entropy alloy and the matrix alloy, the deterioration influence is amplified due to the severe application environment of the aeronautical part, and a hardened particle material component which has good wettability with the titanium base and cannot form the hard and brittle intermetallic compounds needs to be searched.
2. How to obtain and select the reinforcing phase particles with proper particle size distribution is an important factor influencing the reinforcing effect of the particle reinforcing phase in the matrix.
3. How to realize good combination and uniform distribution of the reinforcing phase particles in the titanium matrix is also an important factor influencing the performance of the particle reinforced titanium matrix composite, and a proper mass fraction ratio of the reinforcing phase to the matrix is selected.
4. The rapid heating and cooling of the spark plasma sintering process can obtain the composite material with uniform and fine tissue, and meanwhile, proper sintering temperature and sintering time are selected to avoid overburning.
Disclosure of Invention
The invention aims to provide a preparation method of a NiCoCr entropy alloy particle reinforced titanium-based composite material, which aims to solve the problems in the background technology.
Aiming at the problems that the existing high-entropy alloy particle reinforced pure titanium matrix has blank components, the hard and brittle intermetallic compounds generated by a particle reinforced phase and a titanium matrix are avoided, the particle size distribution of particles is selected, the good combination and uniform distribution of the particles of the reinforced phase in the titanium matrix are improved, the proper sintering process avoids overburning and the like, the invention aims to provide the component proportion of the medium-entropy alloy particle reinforced pure titanium matrix, the medium-entropy alloy particle reinforced titanium matrix composite material and the preparation method thereof, the method adopts NiCoCr medium-entropy alloy particles with fewer components and good chemical stability to avoid the hard and brittle intermetallic compounds generated by the reinforced phase and the titanium matrix, the particle surface is mechanically alloyed by high-energy ball milling to achieve the prealloying state, and the uniform particle size is screened to achieve the proper particle size distribution, thereby realizing the good combination and uniform distribution of the reinforced phase and the matrix to achieve the good reinforcing effect, sintering densification is realized by combining a spark plasma sintering process with proper parameters, and the diffusion degree of reinforcing phase particles in a pure titanium matrix is regulated and controlled, so that uniform and fine tissues are obtained, and the particle reinforcement of the titanium-based composite material is realized.
In order to achieve the purpose, the invention provides the following technical scheme: a preparation method of a NiCoCr intermediate entropy alloy particle reinforced titanium-based composite material is characterized by comprising the following steps: the method comprises the following steps:
s1: selecting Ni, Co and Cr element powder, and proportioning according to the atomic percentage of 33.33%;
s2: mechanically alloying the element powder by planetary ball milling to obtain NiCoCr prealloyed powder;
s3: vibrating and screening the pre-alloyed powder to obtain NiCoCr alloy powder particles with proper particle size;
s4: mixing NiCoCr alloy particles with pure titanium powder to obtain mixed powder;
s5: sintering and molding the mixed powder through spark plasma sintering to obtain the compact NiCoCr particle reinforced titanium-based composite material.
In a preferred scheme, the main element powder selected in the medium entropy alloy particle reinforced titanium-based composite material is Ni, Co and Cr, and the atomic ratio of the main element powder to the main element powder is 1: 1: 1.
in the preferred scheme, the alloying means of the medium-entropy alloy element powder is to prealloy Ni, Co and Cr element powder by high-energy ball milling, and the ball milling parameters are as follows: the ball milling rotation speed is 200-500 r/min, the ball material ratio is 10:1, the ball milling tank and the milling balls are made of hard alloy materials, and the ball milling time is 4-12 hours.
In a preferable scheme, the particle size distribution of the medium-entropy alloy particles obtained through screening is 20-53 um.
In a preferable scheme, the mass fraction of NiCoCr element powder in the NiCoCr particle reinforced titanium-based composite material is 2-10%. In a more preferable scheme, the NiCoCr element powder in the NiCoCr particle reinforced titanium-based composite material is 2-8% by weight. Under the preferable NiCoCr particle mass fraction, a small amount of particles are added to realize the remarkable enhancement effect of the titanium matrix, and simultaneously, a large amount of plasticity is not lost, so that the toughness of the titanium matrix composite material is well balanced. Higher mass fraction increases the difficulty of good bonding of the particles to the matrix on the one hand, and on the other hand brings about a great increase in strength while drastically reducing plasticity.
Preferably, the discharge plasma sintering conditions are as follows: the temperature is 800-1100 ℃, and the time is 5-30 min. More preferably, the discharge plasma sintering conditions are as follows: the temperature is 850-1000 ℃, and the time is 5-10 min. Under the preferred sintering process conditions, the NiCoCr particles and the matrix realize good combination through a certain degree of diffusion, and meanwhile, the complete diffusion does not occur to lose the particle reinforcing effect. The NiCoCr particles can be completely diffused in the sintering process due to the excessively high sintering temperature, so that the aim of obtaining a local alpha + beta double-phase structure by microalloying is achieved, and the particle reinforcing effect is lost.
The key point of the technical scheme is that the appropriate main element powder Ni, Co and Cr of the medium entropy alloy is selected to realize pre-alloying through high-energy ball milling to obtain medium entropy alloy particles, the medium entropy particles of NiCoCr are used as a titanium-based reinforcing phase to further improve the combination of the reinforcing phase and a matrix, the particle size distribution, the mass fraction and the mixing ratio of the reinforcing phase particles are regulated and controlled to play the maximum effect of particle reinforcement, the toughness balance of the titanium-based composite material is kept, the diffusion condition in the particle sintering process is regulated and controlled by a discharge plasma sintering process to realize the toughening regulation and control of the titanium-based composite material, and finally the NiCoCr particle reinforced titanium-based composite material with the toughening balance is obtained.
The invention has the technical effects and advantages that: 1. the method selects Ni, Co and Cr element powder, and obtains medium-entropy alloy reinforced particles with certain particle size distribution by high-energy ball milling;
2. the NiCoCr entropy particles with high strength and good chemical stability are used as a titanium-based alloy reinforcing phase, so that the performance deterioration caused by the generation of hard and brittle intermetallic compounds between the reinforcing phase and a matrix is effectively avoided;
3. according to the invention, the effect of the particle reinforced phase in the loading process of the titanium-based composite material can be effectively regulated and controlled by regulating and controlling the particle size distribution and the mass fraction of the reinforced phase, so that the strengthening and toughening balance is obtained;
4. the discharge plasma sintering process regulation and control of the invention can effectively regulate and control the existence form and the diffusion degree of the particle reinforced phase in the matrix, realize the maximum strengthening and toughening of the reinforced relative matrix and further realize the purpose of regulating and controlling the mechanical property of the NiCoCr particle reinforced titanium-based composite material.
Drawings
FIG. 1 is a structural morphology of a NiCoCr particle-reinforced titanium matrix composite prepared in example 1 of the present invention;
FIG. 2 is a graph showing mechanical properties of a NiCoCr particle-reinforced titanium matrix composite prepared in example 1 of the present invention;
FIG. 3 is a structural morphology of a NiCoCr particle-reinforced titanium matrix composite prepared in example 2 of the present invention;
FIG. 4 shows the mechanical properties of NiCoCr particle-reinforced Ti-based composite material prepared in example 2 of the present invention.
Detailed Description
The following further describes embodiments of the present invention with reference to the drawings. It should be noted that the description of the embodiments is provided to help understanding of the present invention, but the present invention is not limited thereto. In addition, the technical features involved in the embodiments of the present invention described below may be combined with each other as long as they do not conflict with each other.
In the description of the present invention, it is to be understood that the terms "central," "longitudinal," "lateral," "length," "width," "thickness," "upper," "lower," "front," "rear," "left," "right," "vertical," "horizontal," "top," "bottom," "inner," "outer," "clockwise," "counterclockwise," "axial," "radial," "circumferential," and the like are used in the orientations and positional relationships indicated in the drawings for convenience in describing the invention and to simplify the description, and are not intended to indicate or imply that the referenced devices or elements must have a particular orientation, be constructed and operated in a particular orientation, and are therefore not to be considered limiting of the invention.
Furthermore, the terms "first", "second" and "first" are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implicitly indicating the number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include at least one of the feature.
Example 1
The preparation method of the NiCoCr particle reinforced titanium-based composite material comprises the following steps:
s1: mixing the raw materials in a ratio of 1: 1: 1, putting Ni, Co and Cr element powder into a planetary ball mill for high-energy ball milling at an atomic ratio to realize mechanical alloying, wherein the parameters are 300r/min, and the ball milling time is 8 hours;
s2: screening the ball-milled NiCoCr intermediate entropy alloy particles, and selecting NiCoCr intermediate entropy alloy particles with the particle size distribution of 30-45 mu m;
s3: mixing the entropy alloy particles in the NiCoCr in the step (2) with pure Ti powder according to the mass fraction Ti-5% NiCoCr, and fully mixing at the rotating speed of 150r/min for 5 h;
s4: and (4) placing the mixed powder in the step (3) in a discharge plasma sintering furnace at 1000 ℃ for sintering for 5 min.
The product of this example was tested by texture observation, and the texture of the NiCoCr particle-reinforced titanium matrix composite obtained after sintering in this example is shown in fig. 1, in this example, the NiCoCr particles retain part of the morphology of the particles in the titanium matrix, and form a continuous diffusion interface layer with the matrix, and the titanium matrix is α + β biphase. As can be seen from FIG. 2, the NiCoCr particle-reinforced titanium-based composite material of the present invention is excellent in strength and has a tensile strength of about 1280 MPa.
Example 2
The preparation method of the NiCoCr particle reinforced titanium-based composite material comprises the following steps:
s1: mixing the raw materials in a ratio of 1: 1: 1, putting Ni, Co and Cr element powder into a planetary ball mill for high-energy ball milling at an atomic ratio to realize mechanical alloying, wherein the parameters are 320r/min, and the ball milling time is 6 hours;
s2: screening the ball-milled NiCoCr intermediate entropy alloy particles, and selecting the NiCoCr intermediate entropy alloy particles with the particle size distribution of 35-53 mu m;
s3: mixing the entropy alloy particles in the NiCoCr in the step (2) with pure Ti powder according to the mass fraction Ti-8.3% NiCoCr, and fully mixing at the rotating speed of 200r/min for 5 h;
s4: and (4) placing the mixed powder in the step (3) into a discharge plasma sintering furnace at 850 ℃ for sintering for 5 min.
Tests show that the structure of the NiCoCr particle-reinforced titanium matrix composite obtained after sintering in the embodiment is shown in FIG. 3, and in the embodiment, the NiCoCr particles retain the particle morphology in the titanium matrix and are well connected with the interface of the pure titanium matrix. As can be seen from figure 4, the NiCoCr particle reinforced titanium-based composite material has good comprehensive performance, and the detection shows that the tensile strength of the material is 920MPa, and the elongation is about 16%.
Although embodiments of the present invention have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present invention, and that variations, modifications, substitutions and alterations can be made to the above embodiments by those of ordinary skill in the art within the scope of the present invention.
Claims (6)
1. A preparation method of a NiCoCr intermediate entropy alloy particle reinforced titanium-based composite material is characterized by comprising the following steps: the method comprises the following steps:
s1: selecting Ni, Co and Cr element powder, and proportioning according to the atomic percentage of 33.33%;
s2: mechanically alloying the element powder by planetary ball milling to obtain NiCoCr prealloyed powder;
s3: vibrating and screening the pre-alloyed powder to obtain NiCoCr alloy powder particles with proper particle size;
s4: mixing NiCoCr alloy particles with pure titanium powder to obtain mixed powder;
s5: and sintering and molding the mixed powder through spark plasma sintering to obtain the compact NiCoCr particle reinforced titanium-based composite material.
2. The method of claim 1, wherein said NiCoCr entropy alloy particle reinforced Ti-based composite material comprises: in step S1, the atomic ratio of the Ni, Co, Cr elemental powders is 1: 1: 1, and the impurity content of each element powder is less than 1000 ppm.
3. The method of claim 1, wherein said NiCoCr entropy alloy particle reinforced Ti-based composite material comprises: in step S2, the ball milling conditions are: the ball milling rotation speed is 200-500 r/min, the ball material ratio is 10:1, the ball milling tank and the milling balls are made of hard alloy materials, and the ball milling time is 4-12 hours.
4. The method of claim 1, wherein said NiCoCr entropy alloy particle reinforced Ti-based composite material comprises: the particle size of NiCoCr enhanced particles in the NiCoCr particle enhanced titanium-based composite material is 20-53 um.
5. The method of claim 1, wherein said NiCoCr entropy alloy particle reinforced Ti-based composite material comprises: the mass fraction of the reinforced particles in the NiCoCr particle reinforced titanium-based composite material is 2-10%, the material mixing parameters are set to be 75-200 r/min of rotation speed, and the time is 4-8 h.
6. The method of claim 1, wherein said NiCoCr entropy alloy particle reinforced Ti-based composite material comprises: in step S5, the sintering parameters in the spark plasma sintering process are 800-1100 ℃, and the heat preservation time is 5-30 min.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108531776A (en) * | 2018-05-28 | 2018-09-14 | 中南大学 | A kind of high-strength titanium matrix composite of brake system of car powder metallurgy and preparation method thereof |
| CN111705252A (en) * | 2020-06-18 | 2020-09-25 | 西北工业大学 | Al (aluminum)2O3Nano-particle reinforced CrCoNi intermediate entropy alloy-based composite material and preparation method thereof |
| CN112548089A (en) * | 2020-11-04 | 2021-03-26 | 华南理工大学 | Application of discharge plasma modification method in treatment of spherical/quasi-spherical metal powder prepared by atomization method |
| CN113403493A (en) * | 2020-10-29 | 2021-09-17 | 暨南大学 | High-toughness medium-entropy CrCoNi particle reinforced Cu-based composite material and preparation method thereof |
| CN113414384A (en) * | 2021-07-02 | 2021-09-21 | 宜宾上交大新材料研究中心 | Medium-entropy alloy composite material and preparation method and application thereof |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108531776A (en) * | 2018-05-28 | 2018-09-14 | 中南大学 | A kind of high-strength titanium matrix composite of brake system of car powder metallurgy and preparation method thereof |
| CN111705252A (en) * | 2020-06-18 | 2020-09-25 | 西北工业大学 | Al (aluminum)2O3Nano-particle reinforced CrCoNi intermediate entropy alloy-based composite material and preparation method thereof |
| CN113403493A (en) * | 2020-10-29 | 2021-09-17 | 暨南大学 | High-toughness medium-entropy CrCoNi particle reinforced Cu-based composite material and preparation method thereof |
| CN112548089A (en) * | 2020-11-04 | 2021-03-26 | 华南理工大学 | Application of discharge plasma modification method in treatment of spherical/quasi-spherical metal powder prepared by atomization method |
| CN113414384A (en) * | 2021-07-02 | 2021-09-21 | 宜宾上交大新材料研究中心 | Medium-entropy alloy composite material and preparation method and application thereof |
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