CN111893362B - Three-dimensional network structure high-entropy alloy and preparation method thereof - Google Patents
Three-dimensional network structure high-entropy alloy and preparation method thereof Download PDFInfo
- Publication number
- CN111893362B CN111893362B CN202010721605.5A CN202010721605A CN111893362B CN 111893362 B CN111893362 B CN 111893362B CN 202010721605 A CN202010721605 A CN 202010721605A CN 111893362 B CN111893362 B CN 111893362B
- Authority
- CN
- China
- Prior art keywords
- entropy alloy
- ball milling
- grains
- dimensional network
- ball
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses a high-entropy alloy with a three-dimensional network structure and a preparation method thereof, and the high-strength, high-toughness and high-entropy alloy with a special three-dimensional network structure is successfully prepared by adopting mechanical ball milling and spark plasma sintering. The high-entropy alloy obtained by the technical scheme of the invention has yield strength of 600-960MPa, tensile strength of 960-1230MPa, uniform elongation of more than or equal to 11%, excellent high-strength and high-toughness matching property, isotropic mechanical property and is expected to be used for near-net forming of various small metal components with complex structures.
Description
Technical Field
The invention belongs to the technical field of high-entropy alloy preparation, and particularly relates to a three-dimensional network structure high-entropy alloy and a preparation method thereof.
Background
The high-entropy alloy is a novel metal material emerging in recent years and generally consists of 4 or more main elements with approximate equimolar ratio. The high-entropy alloy is easy to form a solid solution with simple face-centered cubic, body-centered cubic and close-packed hexagonal crystal structures, has unique advantages in the aspects of physical, chemical and thermodynamic properties, particularly has excellent properties of high strength, high hardness, wear resistance, corrosion resistance, high temperature softening resistance and the like in the aspect of mechanical behavior, and is a high-performance metal structure material with huge application potential. Currently, the cubic crystal structure high-entropy alloy is more concerned, and the research and the attention of the face-centered cubic structure high-entropy alloy formed by FeNiCrCoMn series quinary alloy and subsets thereof are the most. However, the room temperature yield strength of the face-centered cubic structure high-entropy alloy is low, and the advantage is not obvious compared with the prior austenitic stainless steel (such as 304 and 316 stainless steel), thereby greatly limiting the further development and application of the alloy.
According to the Hall-Petch relationship (σ ═ σ -0+kd-1/2Where σ is yield strength, σ0Lattice frictional stress, d is grain size), the strength of the metal material can be greatly improved by refining the grain size. In addition, the high-entropy alloy has serious lattice distortion, so that larger lattice resistance needs to be overcome when dislocation moves, and the high-entropy alloy has better fine crystal strengthening effect. According to the report of the literature, the Hall-Petch coefficient of the FeNiCrCoMn series high-entropy alloy is as high as 677 MPa.mu.m1 /2This is much higher than the Hall-Petch coefficient of conventional face-centered cubic structure alloys. However, the mechanical properties of high-entropy alloys still follow the inverse relationship between strength and plasticity of conventional metal materials, i.e. an increase in strength usually results in a significant decrease in plasticity. For example, the tensile yield strength of the high-entropy alloy with the face-centered cubic structure can be improved to more than 1GPa through simple cold rolling and annealing treatment at room temperature, but the uniform elongation is reduced to less than 5%, so that the minimum requirement of engineering application on the plasticity of a structural material cannot be met. Therefore, how to improve the toughness matching of the face-centered cubic structure high-entropy alloy is always the focus of attention and research of researchers.
Through the ultra-fining and even the nano-fining of the alloy structure, the strength of the high-entropy alloy with the face-centered cubic structure can be greatly improved, but the premature necking and even the failure of the elastic stage caused by the difficulty in dislocation slippage due to the increase of the density of structural defects (crystal boundary, dislocation and the like) cannot be avoided, and the minimum requirement of engineering structural materials on plasticity cannot be met. Therefore, it is necessary to develop a multi-scale structure design based on the refined grains to further optimize the toughness matching of the material. Wang et al prepared pure copper with dual-scale grain distribution by rolling 93% in a low temperature liquid nitrogen environment and annealing at 180 ℃ for 3min, with the structure of nanocrystals smaller than 300nm surrounding microcrystals. The 'grain size bimodal distribution' structure has the ultrahigh strength of ultrafine grained metal, also gives consideration to the excellent plasticity of coarse grained metal, and shows outstanding toughness matching. The excellent plasticity is mainly due to the fact that a large number of geometrical necessary dislocations are generated in the deformation process so as to meet the large gradient strain at the ultra-fine grain-coarse grain interface, and therefore, the copper of the structure has a more obvious work hardening phenomenon compared with the traditional homogeneous coarse grain copper. Subsequently, a number of heterostructures such as gradient nanostructure materials, heterolamellar structures, etc. were proposed in succession. However, these heterostructure metal materials all have the defect of anisotropic mechanical properties, and the relative volume fractions and spatial distribution states of coarse grains and ultra-fine grains are difficult to control. Therefore, how to keep the advantages of the heterostructure and eliminate the disadvantages of anisotropy through structural design has important significance for the research of ultra-high-toughness metal materials.
Disclosure of Invention
The invention provides a three-dimensional network structure high-entropy alloy and a preparation method thereof, aiming at the problems of low strength of the high-entropy alloy and low plasticity of the nanocrystalline alloy, and the specific technical scheme of the invention is as follows:
the high-entropy alloy with the three-dimensional network structure is characterized by comprising coarse grains and equiaxed ultrafine grains, wherein the spatial distribution of the coarse grains and the equiaxed ultrafine grains is controllable, and the coarse grains are completely wrapped by the equiaxed ultrafine grains, namely a continuous shell layer formed by the equiaxed ultrafine grains surrounds a core formed by the coarse grains to form a three-dimensional network core-shell structure; the volume fraction of the coarse grains is 70-20%, and the average grain size is 8-12.5 μm; the volume fraction of the equiaxed superfine crystal grains is 30-80%, and the average crystal grain size is less than 1 mu m.
Furthermore, the room-temperature tensile yield strength of the high-entropy alloy is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, and the uniform elongation is more than or equal to 11%.
A preparation method of a three-dimensional network structure high-entropy alloy is characterized by comprising the following steps:
s1: the ball milling process comprises the following steps: adding the high-entropy alloy powder into a ball milling container, and carrying out ball milling in an argon atmosphere to obtain ball-milled powder;
s2: the sintering process comprises the following steps: and (5) putting the ball-milled powder obtained in the step (S1) into a die, and sintering in a spark plasma sintering device to obtain the high-entropy alloy block with the three-dimensional network structure.
Further, the ball milling container in the step S1 is a stainless steel ball milling tank, and the ball-to-material ratio is 10: 1, the ball milling medium is a stainless steel ball with the diameter of 3 mm.
Further, the ball milling temperature in the step S1 is 15 ℃ to 35 ℃, the rotation speed of the ball milling container is 200 rpm, the ball milling container stops for 10 minutes after 60 minutes, the turning direction is adjusted, the ball milling container stops for 10 minutes after 60 minutes, and the process is circulated in such a way that the total ball milling time is 50h to 150 h.
Further, in the step S2, the sintering temperature is 950 ℃, the heating rate is 100 ℃/min, and the heating rate is adjusted to 50 ℃/min after the temperature reaches 900 ℃; the sintering pressure is 100MPa, and the pressure increasing rate is 10 MPa/min; the temperature rise and the pressure rise are carried out synchronously; preserving the temperature for 30 minutes; and then rapidly cooling to room temperature along with the furnace and sampling to obtain the high-entropy alloy block with the three-dimensional network structure.
Further, the high-entropy alloy powder adopted in the step S1 is pre-alloyed high-entropy alloy powder Fe prepared by a gas atomization method50Mn30Cr10Co10The concrete components are as follows: fe 49.3 at.%, Mn 28.6 at.%, Cr 9.8 at.%, Co 12.1 at.%, and the balance Si and other unavoidable impurities.
The invention has the beneficial effects that:
1. the high-entropy alloy prepared by adopting the method combining mechanical ball milling and discharge plasma sintering simultaneously comprises ultrafine grains and coarse grains, and the spatial distribution of the ultrafine grains and the coarse grains is controllable, namely, equiaxial ultrafine grains are uniformly wrapped around the coarse grains to form a three-dimensional network structure.
2. The three-dimensional network structure can ensure that the material has ultra-fine grained ultrahigh strength and coarse grained large plasticity, and ensures that the high-entropy alloy has outstanding comprehensive mechanical properties through the coordinated deformation of each characteristic tissue; the yield strength of the high-entropy alloy is between 600 and 960MPa, the tensile strength is between 960 and 1230MPa, and the uniform elongation can reach more than or equal to 11 percent.
3. The invention has simple technical links, only comprises mechanical ball milling and subsequent sintering processes, and is very suitable for near-net forming of various small metal components with complex structures.
Drawings
In order to illustrate embodiments of the present invention or technical solutions in the prior art more clearly, the drawings which are needed in the embodiments will be briefly described below, so that the features and advantages of the present invention can be understood more clearly by referring to the drawings, which are schematic and should not be construed as limiting the present invention in any way, and for a person skilled in the art, other drawings can be obtained on the basis of these drawings without any inventive effort. Wherein:
FIG. 1 is a low power EBSD microstructure of a three-dimensional network structure high-entropy alloy obtained in example 1 of the present invention;
FIG. 2 is a high-power EBSD microstructure diagram of the three-dimensional network structure high-entropy alloy ultra-fine crystal area obtained in example 1 of the present invention;
FIG. 3 is a graph of engineering stress-engineering strain for a three-dimensional network structure high entropy alloy of the present invention.
Detailed Description
In order that the above objects, features and advantages of the present invention can be more clearly understood, a more particular description of the invention will be rendered by reference to the appended drawings. It should be noted that the embodiments of the present invention and features of the embodiments may be combined with each other without conflict.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, however, the present invention may be practiced in other ways than those specifically described herein, and therefore the scope of the present invention is not limited by the specific embodiments disclosed below.
The invention is inspired by special structures such as shells, bamboos, honeycombs and the like with excellent performance in nature, and provides a design idea of a three-dimensional net structure, namely a core formed by coarse crystals is surrounded by a continuous shell layer formed by nano crystals/ultra-fine crystals to form a three-dimensional net core-shell structure. Locally, the grain size of the material is not uniform, namely, the material contains an ultrafine grain shell layer and a coarse grain core; but the material shows a periodical uniform structure in the whole view, which fully ensures the isotropy of the material in macroscopic mechanical properties. The traditional deformation heat treatment process has a challenge in preparing the structure, and the topological distribution of the grain size is hopefully controlled by adopting the powder metallurgy technology: firstly, the surface layer of spherical metal powder is mechanically ground to obtain a plastic deformation layer, then the surface layer of the powder is induced to recrystallize through a high-temperature sintering process to obtain a nanocrystalline/ultrafine-grained shell layer, and the undeformed area of the core part of the powder still keeps the original coarse-grained structure, thereby realizing the preparation of a three-dimensional reticular core-shell structure. The three-dimensional network structure high-entropy alloy prepared by the technology has an important application prospect in the near-net forming aspect of high-performance complex metal components.
The high-entropy alloy with the three-dimensional network structure is characterized by comprising coarse grains and equiaxed ultrafine grains, wherein the spatial distribution of the coarse grains and the equiaxed ultrafine grains is controllable, the coarse grains are completely wrapped by the equiaxed ultrafine grains, namely a continuous shell layer formed by the equiaxed ultrafine grains surrounds a core formed by the coarse grains to form a three-dimensional network core-shell structure; the volume fraction of coarse grains is 70-20%, and the average grain size is 8-12.5 μm; the volume fraction of equiaxed ultrafine grains is 30-80%, and the average grain size is less than 1 μm. The room-temperature tensile yield strength of the high-entropy alloy is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, and the uniform elongation is more than or equal to 11%.
The invention utilizes the powder metallurgy technology to control the grain size and the three-dimensional space distribution of the alloy, and greatly improves the strength of the alloy on the basis of ensuring the plasticity through the microstructure regulation and control on the premise of not changing the chemical components of the alloy. Specifically, the preparation method of the three-dimensional network structure high-entropy alloy is characterized by comprising the following steps:
s1: the ball milling process comprises the following steps: adding the high-entropy alloy powder into a ball milling container, and carrying out ball milling in an argon atmosphere to obtain ball-milled powder;
s2: the sintering process comprises the following steps: and (5) putting the ball-milled powder obtained in the step (S1) into a die, and sintering in a spark plasma sintering device to obtain the high-entropy alloy block with the three-dimensional network structure.
The ball milling container in the step S1 is a stainless steel ball milling tank, and the ball-to-material ratio is 10: 1, the ball milling medium is a stainless steel ball with the diameter of 3 mm.
And step S1, the ball milling temperature is 15-35 ℃, the rotation speed of the ball milling container is 200 r/min, the ball milling container stops for 10 minutes after 60 minutes, the turning is adjusted, the ball milling container stops for 10 minutes after 60 minutes, the operation is circulated, and the total ball milling time is 50-150 h.
In the step S2, the sintering temperature is 950 ℃, the heating rate is 100 ℃/min, and the heating rate is adjusted to 50 ℃/min after the temperature reaches 900 ℃; the sintering pressure is 100MPa, and the pressure increasing rate is 10 MPa/min; the temperature rise and the pressure rise are carried out synchronously; preserving the temperature for 30 minutes; and then rapidly cooling to room temperature along with the furnace and sampling to obtain the high-entropy alloy block with the three-dimensional network structure.
The high-entropy alloy powder adopted in the step S1 is pre-alloyed high-entropy alloy powder Fe prepared by a gas atomization method50Mn30Cr10Co10The concrete components are as follows: fe 49.3 at.%, Mn 28.6 at.%, Cr 9.8 at.%, Co 12.1 at.%, and the balance Si and other unavoidable impurities.
For the convenience of understanding the above technical aspects of the present invention, the following detailed description will be given of the above technical aspects of the present invention by way of specific examples.
The devices in the embodiment all adopt a planetary ball mill and a discharge plasma sintering machine; the adopted high-entropy alloy powder is pre-alloyed high-entropy alloy powder Fe prepared by a gas atomization method50Mn30Cr10Co10The concrete components are as follows: fe 49.3 at.%, Mn 28.6 at.%, Cr 9.8 at.%, Co 12.1 at.%, and the balance Si and other unavoidable impurities.
Example 1
(1) Mechanical ball mill
10g of high-entropy alloy powder with the average grain diameter of about 110 mu m and 100g of stainless steel balls with the diameter of 3mm are sequentially placed into a stainless steel ball milling tank, then the tank body is completely sealed, and the whole process is carried out in a glove box filled with argon.
And then placing the prepared ball milling tank in a planetary ball mill for ball milling, and placing a symmetrical tank with the same mass on the other side to ensure that the ball mill runs stably. The ball milling speed is 200 r/min, the ball milling is stopped for 10min after 60min, the turning direction is adjusted, and the ball milling time is 50 h.
(2) Spark plasma sintering
Putting the ball-milled powder obtained in the step (1) into a graphite die, and placing the graphite die in a spark plasma sintering device for sintering; the sintering temperature is 950 ℃, the heating rate is 100 ℃/min, and the temperature is adjusted to 50 ℃/min after reaching 900 ℃; sintering pressure is 100MPa, pressure increasing rate is 10MPa/min, and temperature rising and pressure increasing are carried out synchronously; the heat preservation time is 30 min; and then rapidly cooling to room temperature along with the furnace and sampling to obtain the high-entropy alloy block with the three-dimensional network structure.
This example gives a high-entropy alloy with a three-dimensional network structure. FIG. 1 is a photograph of a low power EBSD of the sample of this example, in which ultra-fine grains are uniformly wrapped around coarse grains, and which has a typical periodic structure. FIG. 2 is a photograph of a high magnification EBSD of the ultra-fine crystalline regions of the sample of this example, wherein the ultra-fine crystalline particles have equiaxed morphology and an average grain size of 0.83 μm.
The yield strength of the three-dimensional network structure high-entropy alloy obtained in the example is 607MPa, the ultimate tensile strength is 962MPa, and the uniform elongation is 18%. The engineering stress-engineering strain curve of the high-entropy alloy with the three-dimensional network structure is shown in fig. 3, and it can be seen that the high-entropy alloy prepared by the method has excellent strong plasticity matching and can greatly widen the application range of the high-entropy alloy.
Example 2
(1) Mechanical ball mill
10g of high-entropy alloy powder with the average grain diameter of about 110 mu m and 100g of stainless steel balls with the diameter of 3mm are sequentially placed into a stainless steel ball milling tank, and finally, the tank body is completely sealed, and the whole process is carried out in a glove box filled with argon. And then placing the prepared ball milling tank in a planetary ball mill for ball milling, and placing a symmetrical tank with the same mass on the other side to ensure that the ball mill runs stably. The ball milling speed is 200 r/min, the ball milling is stopped for 10min after 60min, the turning direction is adjusted, and the ball milling time is 100 h.
(2) Spark plasma sintering
Putting the ball-milled powder obtained in the step (1) into a graphite die, and placing the graphite die in a spark plasma sintering device for sintering; the sintering temperature is 950 ℃, the heating rate is 100 ℃/min, and the temperature is adjusted to 50 ℃/min after reaching 900 ℃; sintering pressure is 100MPa, pressure increasing rate is 10MPa/min, and temperature rising and pressure increasing are carried out synchronously; the heat preservation time is 30 min; and then rapidly cooling to room temperature along with the furnace and sampling to obtain the high-entropy alloy block with the three-dimensional network structure.
The three-dimensional network structure high-entropy alloy obtained by the embodiment has the yield strength of 740MPa, the ultimate tensile strength of 1016MPa and the uniform elongation of 11%. The engineering stress-engineering strain curve of the high-entropy alloy with the three-dimensional network structure is shown in fig. 3, and it can be seen that the high-entropy alloy prepared by the method has excellent strong plasticity matching and can greatly widen the application range of the high-entropy alloy.
Example 3
(1) Mechanical ball mill
10g of high-entropy alloy powder with the average grain diameter of about 110 mu m and 100g of stainless steel balls with the diameter of 3mm are sequentially placed into a stainless steel ball milling tank, and finally the tank body is completely sealed, and the whole process is carried out in a glove box filled with argon. And then placing the prepared ball milling tank in a planetary ball mill for ball milling, and placing a symmetrical tank with the same mass on the other side to ensure that the ball mill runs stably. The ball milling speed is 200 r/min, the ball milling is stopped for 10min after 60min, the turning direction is adjusted, and the ball milling time is 150 h.
(2) Spark plasma sintering
Putting the ball-milled powder obtained in the step (1) into a graphite die, and placing the graphite die in a spark plasma sintering device for sintering; the sintering temperature is 950 ℃, the heating rate is 100 ℃/min, and the temperature is adjusted to 50 ℃/min after reaching 900 ℃; sintering pressure is 100MPa, pressure increasing rate is 10MPa/min, and temperature rising and pressure increasing are carried out synchronously; the heat preservation time is 30 min; and then rapidly cooling to room temperature along with the furnace and sampling to obtain the high-entropy alloy block with the three-dimensional network structure.
The yield strength of the three-dimensional network structure high-entropy alloy obtained in the example is 960MPa, the ultimate tensile strength is 1228MPa, and the uniform elongation is 12%. The engineering stress-engineering strain curve of the high-entropy alloy with the three-dimensional network structure is shown in fig. 3, and it can be seen that the high-entropy alloy prepared by the method has excellent strong plasticity matching and can greatly widen the application range of the high-entropy alloy.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (1)
1. The preparation method of the three-dimensional network structure high-entropy alloy is characterized in that the high-entropy alloy powder is Fe50Mn30Cr10Co10The concrete components are as follows: 49.3 at.% of Fe, 28.6 at.% of Mn, 9.8 at.% of Cr, 12.1 at.% of Co, and the balance of Si and other unavoidable impurities;
the method comprises the following steps:
s1: the ball milling process comprises the following steps: pre-alloyed high-entropy alloy powder Fe prepared by gas atomization method50Mn30Cr10Co10Adding the mixture into a ball milling container, and carrying out ball milling in an argon atmosphere to obtain ball-milled powder;
the ball milling container is a stainless steel ball milling tank, and the ball material ratio is 10: 1, ball-milling a stainless steel ball with a medium of 3 mm;
the ball milling temperature is 15-35 ℃, the rotation speed of the ball milling container is 200 r/min, the ball milling container rotates for 60 minutes and stops for 10 minutes, the turning is adjusted, the ball milling container rotates for 60 minutes and stops for 10 minutes, the process is circulated, and the total ball milling time is 50-150 hours;
s2: the sintering process comprises the following steps: putting the ball-milled powder obtained in the step S1 into a die, and sintering in a spark plasma sintering device to obtain a high-entropy alloy block with a three-dimensional network structure;
the sintering temperature is 950 ℃, the heating rate is 100 ℃/min, and the heating rate is adjusted to be 50 ℃/min after the temperature reaches 900 ℃; the sintering pressure is 100MPa, and the pressure increasing rate is 10 MPa/min; the temperature rise and the pressure rise are carried out synchronously; preserving the temperature for 30 minutes; then rapidly cooling to room temperature along with the furnace and sampling to obtain a three-dimensional network structure high-entropy alloy block;
the high-entropy alloy comprises coarse grains and equiaxed ultrafine grains, wherein the spatial distribution of the coarse grains and the equiaxed ultrafine grains is controllable, and the coarse grains are completely wrapped by the equiaxed ultrafine grains, namely a continuous shell layer formed by the equiaxed ultrafine grains surrounds a core formed by the coarse grains to form a three-dimensional reticular core-shell structure; the volume fraction of the coarse grains is 70-20%, and the average grain size is 8-12.5 μm; the volume fraction of the equiaxed superfine crystal grains is 30-80%, and the average crystal grain size is less than 1 mu m;
the room-temperature tensile yield strength of the high-entropy alloy is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, and the uniform elongation is more than or equal to 11%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010721605.5A CN111893362B (en) | 2020-07-24 | 2020-07-24 | Three-dimensional network structure high-entropy alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010721605.5A CN111893362B (en) | 2020-07-24 | 2020-07-24 | Three-dimensional network structure high-entropy alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111893362A CN111893362A (en) | 2020-11-06 |
| CN111893362B true CN111893362B (en) | 2021-11-09 |
Family
ID=73189973
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010721605.5A Active CN111893362B (en) | 2020-07-24 | 2020-07-24 | Three-dimensional network structure high-entropy alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111893362B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115404371A (en) * | 2022-08-31 | 2022-11-29 | 昆明理工大学 | Core-shell structure high-entropy alloy and preparation method thereof |
| CN115198162B (en) * | 2022-09-19 | 2022-12-02 | 太原理工大学 | Entropy alloy in high-toughness heterogeneous multi-phase core-shell organization structure and preparation method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108823481A (en) * | 2018-07-10 | 2018-11-16 | 东北大学 | A kind of high-entropy alloy and preparation method thereof |
| CN109295399A (en) * | 2018-12-10 | 2019-02-01 | 西南交通大学 | A kind of high-damping high entropy alloy material and preparation method thereof |
| CN110093548A (en) * | 2019-05-21 | 2019-08-06 | 华南理工大学 | A kind of tough high-entropy alloy of Ultra-fine Grained height and preparation method thereof containing rare-earth Gd |
| CN110172629A (en) * | 2019-04-23 | 2019-08-27 | 镇江汇通金属成型有限公司 | A kind of graphene enhancing high-entropy alloy elevator traction machine composite worm wheel and preparation method thereof |
| CN111151753A (en) * | 2020-01-16 | 2020-05-15 | 中南大学 | Method for manufacturing shear deformation type phase change crack resistance by laser additive manufacturing |
| CN111206174A (en) * | 2020-02-17 | 2020-05-29 | 华南理工大学 | Magnetic ultrafine-grain high-strength high-entropy alloy and preparation method thereof |
-
2020
- 2020-07-24 CN CN202010721605.5A patent/CN111893362B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108823481A (en) * | 2018-07-10 | 2018-11-16 | 东北大学 | A kind of high-entropy alloy and preparation method thereof |
| CN109295399A (en) * | 2018-12-10 | 2019-02-01 | 西南交通大学 | A kind of high-damping high entropy alloy material and preparation method thereof |
| CN110172629A (en) * | 2019-04-23 | 2019-08-27 | 镇江汇通金属成型有限公司 | A kind of graphene enhancing high-entropy alloy elevator traction machine composite worm wheel and preparation method thereof |
| CN110093548A (en) * | 2019-05-21 | 2019-08-06 | 华南理工大学 | A kind of tough high-entropy alloy of Ultra-fine Grained height and preparation method thereof containing rare-earth Gd |
| CN111151753A (en) * | 2020-01-16 | 2020-05-15 | 中南大学 | Method for manufacturing shear deformation type phase change crack resistance by laser additive manufacturing |
| CN111206174A (en) * | 2020-02-17 | 2020-05-29 | 华南理工大学 | Magnetic ultrafine-grain high-strength high-entropy alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111893362A (en) | 2020-11-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Zhang et al. | Phase transformation and microstructure control of Ti2AlNb-based alloys: a review | |
| Li et al. | Effect of aging treatment on the microstructure and mechanical properties of Al-3.02 Mg-0.2 Sc-0.1 Zr alloy printed by selective laser melting | |
| Zhang et al. | AlCoCuFeNi high-entropy alloy with tailored microstructure and outstanding compressive properties fabricated via selective laser melting with heat treatment | |
| CN112391556B (en) | High-strength high-conductivity Cu-Cr-Nb alloy reinforced by double-peak grain size and double-scale nanophase | |
| Zheng et al. | Enhanced ductility in harmonic structure designed SUS316L produced by high energy ball milling and hot isostatic sintering | |
| CN111893362B (en) | Three-dimensional network structure high-entropy alloy and preparation method thereof | |
| Cao et al. | Characterization of fatigue properties of powder metallurgy titanium alloy | |
| CN115198162B (en) | Entropy alloy in high-toughness heterogeneous multi-phase core-shell organization structure and preparation method thereof | |
| Zhang et al. | Microstructures and mechanical behavior of a near α titanium alloy prepared by TiH2-based powder metallurgy | |
| CN106929764A (en) | A kind of nanocrystalline/bimodal block materials of Ultra-fine Grained two-phase and preparation method | |
| McCarley et al. | Influence of the starting microstructure on the hot deformation behavior of a low stacking fault energy Ni-based superalloy | |
| CN113430343A (en) | Novel processing method of nano precipitation strengthening CoCrNi-based high-entropy alloy | |
| CN103589977A (en) | Method for improving the fatigue resistance performance of Al-Cu-Mg alloy | |
| Ding et al. | Microstructure and mechanical properties of PM Ti600 alloy after hot extrusion and subsequent annealing treatment | |
| Chen et al. | Microstructure and tensile properties of metastable Fe50Mn30Co10Cr10 high-entropy alloy prepared via powder metallurgy | |
| Liu et al. | Evolution of the α phase and microhardness for hot isostatic pressed Ti-6Al-4V alloy during multi-pass deformation | |
| Sharath | Multi directional forging: an advanced deforming technique for severe plastic deformation | |
| Yang et al. | Microstructure and properties of Cu-Al-Ni-Mn-Y alloy with precipitation and effective strengthening by aging treatment | |
| CN114535606B (en) | Oxide dispersion strengthening alloy and preparation method and application thereof | |
| CN111944958B (en) | Preparation method of high-strength block 316L stainless steel | |
| Ma et al. | Sustaining an excellent strength–ductility combination for Ti–6Al–4V alloy prepared from elemental powder blends | |
| EP4217202A1 (en) | Powder hot isostatic pressing cycle | |
| Feng et al. | Achieving excellent strength-ductility synergy of Ti6Al4V alloy produced by powder metallurgy and thermo-mechanical treatment | |
| CN115070052B (en) | Novel bimodal tissue nickel-titanium shape memory alloy, 4D printing preparation method and application thereof | |
| Guo et al. | Deformation microstructure and properties control of Cu-0.6 Cr alloy in cryo-equal channel angular pressing |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |