CN110629059A - Heterogeneous high-entropy alloy material and preparation method thereof - Google Patents
Heterogeneous high-entropy alloy material and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a heterogeneous high-entropy alloy material and a preparation method thereof, wherein the preparation method comprises the following steps: the method comprises four steps of chip making, chip mixing, pre-compaction, plastic deformation treatment and annealing treatment, wherein two or more high-entropy alloys with single-phase and double-phase structures and different grain refining effects are selected, the chips are fully mixed and then are subjected to plastic deformation, and the chips are fully and mechanically alloyed through high temperature and high strain, so that a compact and multi-component mixed heterogeneous high-entropy alloy block blank is obtained. And forming a multi-scale grain mixed heterostructure through subsequent annealing heat treatment. The soft-hard combined heterostructure can form obvious back stress strengthening in the deformation process, so that the heterogeneous high-entropy alloy with high strength and toughness is prepared.
Description
Technical Field
The invention relates to a heterogeneous high-entropy alloy material and a preparation method thereof, belonging to the field of metal material preparation.
Background
The high-entropy alloy is a novel metal material formed by mixing five or more elements together in an equal atomic ratio or approximate equal atomic ratio mode, wherein the atomic content percentage of each element is between 5 and 35 percent. By reasonably optimizing the types and the proportions of the elements, the high-entropy alloy can form a single solid solution structure such as a body-centered cubic structure, a face-centered cubic structure, a two-phase mixed structure and the like, thereby showing some excellent performances such as good corrosion resistance, radiation resistance, thermal stability, higher strength, hardness and wear resistance. However, as with conventional metallic materials, the strength and toughness of high entropy alloys still exist for spearheads, which are characterized by hard and brittle or soft and tough textures. How to simultaneously improve the strength and toughness of the high-entropy alloy and prepare a material with high toughness is a research hotspot in the field of metal materials at present.
A literature search of the prior art has revealed that X.L.Wu et al, Proceedings of the National Academy of Science of the United States of America, 2015, 112 (47): 14501-. The pure titanium material has a hard ultrafine-grained and soft coarse-grained mixed layer sheet structure, and can obtain the high strength of ultrafine grains and the high toughness of coarse grains to a certain extent through back stress reinforcement induced by soft-hard heterogeneous structure deformation coordination, so that the mechanical property of pure titanium is greatly improved. However, the mixed crystal pure titanium material prepared by the technology has single component and poor thermal stability.
The pressure processing composite method is another effective method for preparing high-strength and high-toughness metal composite materials, and further retrieval finds that Chinese invention patent CN106064504A introduces a preparation method of high-strength and high-toughness magnesium-lithium alloy laminated composite materials, and the principle is that alpha-Mg single-phase magnesium-lithium alloy plates with higher strength and beta-Li single-phase magnesium-lithium alloy plates with good plasticity and toughness are combined together through accumulative pack rolling and annealing treatment processes, so that alpha/beta alternating magnesium-lithium alloy laminated composite materials are prepared, and the composite plates have high strength and good plasticity. Meanwhile, the formation of a 'rolling area' is realized by utilizing the difference of plastic deformation capacity between the alpha-Mg phase and the beta-Li phase, and the interface combination effect of the composite board is good. However, the method has the limitation that the preparation process of the composite plate is complicated, the plate for rolling needs to be cut, polished, fixed and heated for many times, and the production efficiency is low.
Disclosure of Invention
The invention aims to provide a heterogeneous high-entropy alloy material and a preparation method thereof aiming at the defects in the prior art.
The invention is realized by the following technical scheme, which comprises the following steps:
step one, chip preparation: according to the mechanical property difference of the high-entropy alloy, at least one high-entropy alloy is selected from FCC (face-centered cubic) single-phase structures and FCC + BCC (face-centered cubic + body-centered cubic) double-phase structures; the high-entropy alloy has different grain refining effects in the subsequent deformation and heat treatment processes.
Carrying out chip milling on the high-entropy alloy cast ingot, wherein the feeding amount of chips is controlled to be 0.01-0.5 mm; and finely crushing the milled coarse scraps, so that the size of the scraps is further reduced, and the size of the scraps is more uniform.
Further, a miniature vertical milling machine is adopted for chip milling, and then a miniature crusher is adopted for fine crushing.
In order to avoid the problems of poor material interface bonding property and the like caused by oxidation of high-entropy alloy scraps, a high-entropy alloy scrap making process is carried out in an inert gas (argon) protective box in an oxygen-isolated inert gas (argon) atmosphere.
Secondly, mixing scraps and pre-compacting: fully stirring and mixing the dissimilar high-entropy alloy cuttings by a ball mill in an oxygen-isolated inert gas (argon) atmosphere; controlling the time of mixing the scraps to be between 0.5 and 2 hours, and setting the vibration stirring frequency of the ball mill to be between 10 and 300 Hz; and after the mixed chip process is finished, filling the mixed chips into a mold, placing the mold on a press machine, and pressing the mold into an initial mixed chip prefabricated block.
Furthermore, the working pressure of the press is 100-3000 MPa, the pressing temperature is 25-300 ℃, the pressure maintaining time is controlled between 10-60 minutes, and the density of the obtained precast block is 80-98%.
And further, after the precast block is pressed, carrying out vacuum packaging on the sample, and then taking out the sample from the argon protection box for later use.
Further, a high-energy ball mill is adopted to fully stir and mix the dissimilar high-entropy alloy cuttings.
Thirdly, plastic deformation treatment: the deformation treatment is carried out by two steps of conventional extrusion and room temperature rolling; firstly, preheating a pre-pressed blank in a vacuum furnace, wherein the preheating temperature is set to 400-; then, extruding and deforming the pre-pressed blank at an extrusion ratio of 5:1 to 50: 1; and finally, rolling the plate obtained by extrusion at room temperature, wherein the rolling deformation is 50-90%.
Fourthly, annealing treatment: and annealing the rolled sample, wherein the annealing temperature is set to 700-750 ℃, and the annealing time is 60-90 minutes. The defects generated in the deformation process are eliminated, and soft and hard heterogeneous structures with different fine grain strengthening effects are formed in the block material.
Compared with the prior art, the invention has the following remarkable advantages:
1. the invention adopts a double-alloy or multi-alloy scrap mixed mechanical alloying technology, has great microstructure design directivity and regulation and control flexibility, can adjust alloy selection according to requirements, prepares a series of soft and hard combined heterogeneous high-entropy alloys, and the prepared alloys have high strength of hard phases and high toughness of soft phases to a certain extent, thereby obtaining high-strength and high-toughness double-series or multi-series heterogeneous high-entropy alloys with excellent comprehensive performance.
2. The heterogeneous high-entropy alloy with the combination of hardness and hardness prepared by the invention has good thermal stability, and the microstructure with mixed multi-grain size has no obvious directionality, so that the heterogeneous high-entropy alloy is suitable for being applied to multidirectional stress components.
3. The invention can prepare large-size high-entropy alloy plates and has lower requirements on equipment and dies.
4. The raw materials used in the invention can be industrial scraps, and the preparation process is simple and convenient, low in cost, high in recovery rate, high in safety, energy-saving and environment-friendly. Compared with the traditional industrial waste chip recovery, the method has greater adaptability to the common problems of waste chip purification, waste chip classification and the like.
Drawings
FIG. 1 is a schematic diagram of chip making, chip mixing and flow of the present invention.
FIG. 2 is a schematic diagram of a pre-compaction process according to the present invention.
FIG. 3 is a schematic view of the plastic deformation process of the present invention.
FIG. 4 is a schematic view of the microstructure of a material prepared according to the present invention.
FIG. 5 is a mechanical property diagram of the prepared heterogeneous high-entropy alloy material.
Detailed Description
The following is a detailed description by way of example.
Example 1
As shown in fig. 1-4, the following example includes four steps, respectively: chip making, chip mixing and pre-compaction, plastic deformation treatment and annealing treatment, wherein:
as shown in FIG. 1, in a vacuum glove box 1 filled with argon shield, CoCrFeNiMn (face centered cubic single phase structure) and Al were aligned using a micro vertical milling machine 20.3Two high-entropy alloys of CoCrFeNi (a face centered cubic + body centered cubic dual-phase structure) are subjected to chip preparation, and milling feed is 0.2mm, so that coarse chips with the thickness of about 0.2mm are obtained. And then finely crushing the milled coarse scraps by using a miniature crusher 3, and reducing and homogenizing the length of the scraps to 0.2-0.3mm for later use.
As shown in FIG. 2, CoCrFeNiMn and Al were mixed in a vacuum glove box 1 filled with argon gas by using a micro ball mill 40.3The CoCrFeNi high-entropy alloy scraps are subjected to mechanical alloying mixing such as vibration, stirring, shaking and the like, the scrap mixing time is 60 minutes, and the frequency of vibration stirring of a ball millThe rate is 100 hz. After the mixing of chips was completed sufficiently, the chips were filled into a steel pressing mold 5 having a square cavity size of 50X 50 mm. And (3) carrying out pre-pressing forming on the scraps by using a micro-press 6, wherein the working pressure of the press is 300 MPa, the pressing temperature is 250 ℃, and the pressure maintaining time is 30 minutes, so that the precast block 7 with the density of about 80% is obtained. And after pressing is finished, vacuum packaging is carried out on the prefabricated sample, and the prefabricated sample is taken out of the glove box for later use.
As shown in fig. 3, a vacuum furnace 8 is adopted to preheat the prepressed scrap-mixed high-entropy alloy ingot 7 in an argon atmosphere, the heating temperature is 550 ℃, and the heating time is 30 minutes; then, the extrusion die 9 is used for carrying out conventional extrusion deformation of 50mm multiplied by 50mm to 30mm multiplied by 30mm on the pre-pressed blank; finally, the sheet obtained by extrusion is rolled on a rolling mill 10 at room temperature, and the rolling deformation is 90 percent, so that the compactness of the material is remarkably improved to more than 99 percent.
As shown in fig. 4, a high-temperature vacuum furnace 11 is adopted to perform annealing treatment at 700 ℃ on the rolled high-entropy alloy sample under the argon protection atmosphere, the annealing time is 60 minutes, and the heterogeneous high-entropy alloy material combining hardness and softness is obtained, and the schematic microstructure diagram of the heterogeneous high-entropy alloy material is shown in fig. 4 b. Due to CoCrFeNiMn and Al0.3The CoCrFeNi high-entropy alloy has different grain refining effects under the annealing treatment at 700 ℃, thereby forming a multi-scale grain mixed microstructure.
Example 2
As shown in fig. 1-4, the following example includes four steps, respectively: chip making, chip mixing and pre-compaction, plastic deformation treatment and annealing treatment, wherein:
as shown in FIG. 1, in a vacuum glove box 1 filled with argon shield, CoCrFeNiMn (face centered cubic single phase structure) and Al were aligned using a micro vertical milling machine 20.3Two high-entropy alloys of CoCrFeNi (a face centered cubic + body centered cubic dual-phase structure) are subjected to chip preparation, and milling feed is 0.1mm, so that coarse chips with the thickness of about 0.1mm are obtained. And then finely crushing the milled coarse scraps by using a miniature crusher 3, and reducing and homogenizing the length of the scraps to 0.1-0.2mm for later use.
As shown in FIG. 2, in a vacuum glove box 1 filled with argon gas, microsphericals are usedMill 4 pairs of CoCrFeNiMn and Al0.3And (3) carrying out mechanical alloying mixing such as vibration, stirring, shaking up and the like on the CoCrFeNi high-entropy alloy scraps, wherein the scrap mixing time is 90 minutes, and the vibration stirring frequency of the ball mill is 200 Hz. After the mixing of chips was completed sufficiently, the chips were filled into a steel pressing mold 5 having a square cavity size of 50X 50 mm. And (3) carrying out pre-pressing forming on the scraps by using a micro-press 6, wherein the working pressure of the press is 500 MPa, the pressing temperature is 250 ℃, and the pressure maintaining time is 60 minutes, so that the precast block 7 with the density of about 85% is obtained. And after pressing is finished, vacuum packaging is carried out on the prefabricated sample, and the prefabricated sample is taken out of the glove box for later use.
As shown in fig. 3, a vacuum furnace 8 is adopted to preheat the prepressing scrap-mixing high-entropy alloy ingot 7 in an argon atmosphere, the heating temperature is 550 ℃, and the heating time is 60 minutes; then, the extrusion die 9 is used for carrying out conventional extrusion deformation of 50mm multiplied by 50mm to 30mm multiplied by 30mm on the pre-pressed blank; finally, the sheet obtained by extrusion is rolled on a rolling mill 10 at room temperature, and the rolling deformation is 90 percent, so that the compactness of the material is remarkably improved to more than 99 percent.
As shown in fig. 4, a high-temperature vacuum furnace 11 is adopted to carry out annealing treatment at 700 ℃ on the rolled high-entropy alloy sample under the argon protection atmosphere, the annealing time is 90 minutes, and the high-strength high-toughness heterogeneous high-entropy alloy with multi-scale crystal grains mixed is prepared.
Example 3
As shown in fig. 1-4, the following example includes four steps, respectively: chip making, chip mixing and pre-compaction, plastic deformation treatment and annealing treatment, wherein:
as shown in FIG. 1, in a vacuum glove box 1 filled with argon shield, CoCrFeNiMn (face centered cubic single phase structure) and Al were aligned using a micro vertical milling machine 20.3Two high-entropy alloys of CoCrFeNi (a face centered cubic + body centered cubic dual-phase structure) are subjected to chip preparation, and milling feed is 0.1mm, so that coarse chips with the thickness of about 0.1mm are obtained. And then finely crushing the milled coarse scraps by using a miniature crusher 3, and reducing and homogenizing the length of the scraps to 0.1-0.2mm for later use.
As shown in FIG. 2, CoCrFeNiMn and Al were mixed in a vacuum glove box 1 filled with argon gas by using a micro ball mill 40.3And (3) carrying out mechanical alloying mixing on the CoCrFeNi high-entropy alloy scraps such as vibration, stirring, shaking up and the like, wherein the scrap mixing time is 120 minutes, and the vibration stirring frequency of the ball mill is 300 Hz. After the mixing of chips was completed sufficiently, the chips were filled into a steel pressing mold 5 having a square cavity size of 50X 50 mm. And (3) carrying out pre-pressing forming on the scraps by using a micro-press 6, wherein the working pressure of the press is 500 MPa, the pressing temperature is 300 ℃, and the pressure maintaining time is 60 minutes, so that the precast block 7 with the density of about 90% is obtained. And after pressing is finished, vacuum packaging is carried out on the prefabricated sample, and the prefabricated sample is taken out of the glove box for later use.
As shown in fig. 3, a vacuum furnace 8 is adopted to preheat the prepressing scrap-mixing high-entropy alloy ingot 7 in an argon atmosphere, the heating temperature is 550 ℃, and the heating time is 60 minutes; then, the extrusion die 9 is used for carrying out conventional extrusion deformation of 50mm multiplied by 50mm to 30mm multiplied by 30mm on the pre-pressed blank; finally, the sheet obtained by extrusion is rolled on a rolling mill 10 at room temperature, and the rolling deformation is 90 percent, so that the compactness of the material is remarkably improved to more than 99 percent.
As shown in fig. 4, a high-temperature vacuum furnace 11 is adopted to perform annealing treatment at 725 ℃ on a rolled high-entropy alloy sample in an argon protective atmosphere, wherein the annealing time is 90 minutes, and the high-strength and toughness heterogeneous high-entropy alloy with multi-scale crystal grains mixed is prepared.
The tensile strength and the elongation at break of the original CoCrFeNiMn high-entropy alloy are respectively 650MPa and 40 percent, and the alloy is characterized by low strength and good tensile plasticity; while the original Al0.3The CoCrFeNi high-entropy alloy is characterized by hard and brittle texture, the tensile strength of the alloy is as high as 1000MPa, but the elongation at break of the alloy is only 8 percent. The high-strength and high-toughness isomeric high-entropy alloy prepared by the invention fully combines the advantages of the two materials, the tensile strength is up to 950MPa, and the elongation at break is 35%.
Claims (7)
1. The preparation method of the isomeric high-entropy alloy material is characterized by comprising the following steps
Step one, chip preparation: according to the mechanical property difference of the high-entropy alloy, at least one high-entropy alloy is selected from the high-entropy alloys with an FCC single-phase structure and an FCC + BCC double-phase structure; carrying out chip milling on the high-entropy alloy cast ingot, wherein the feeding amount of chips is controlled to be 0.01-0.5 mm; finely crushing the milled coarse scraps;
secondly, mixing scraps and pre-compacting: fully stirring and mixing the dissimilar high-entropy alloy cuttings by a ball mill in an oxygen-isolated inert gas atmosphere; controlling the time of mixing the scraps to be between 0.5 and 2 hours, and setting the vibration stirring frequency of the ball mill to be between 10 and 300 Hz; after the mixed chip process is finished, putting the mixed chips into a mold and placing the mold on a press machine, and pressing the mixed chips into an initial mixed chip prefabricated block;
thirdly, plastic deformation treatment: firstly, preheating a pre-pressed blank in a vacuum furnace, wherein the preheating temperature is set to 400-; then, extruding and deforming the pre-pressed blank at an extrusion ratio of 5:1 to 50: 1; finally, rolling the plate obtained by extrusion at room temperature, wherein the rolling deformation is 50-90%;
fourthly, annealing treatment: annealing the rolled sample, wherein the annealing temperature is set to 700-750 ℃, and the annealing time is 60-90 minutes; the defects generated in the deformation process are eliminated, and soft and hard heterogeneous structures with different fine grain strengthening effects are formed in the block material.
2. The method for preparing the isomeric high-entropy alloy material according to claim 1, wherein a miniature vertical milling machine is used for chip milling, and a miniature crusher is used for fine crushing.
3. A method for producing a isomeric high-entropy alloy material according to claim 1, wherein the chipmaking is performed in an inert gas atmosphere that is oxygen-barrier.
4. The preparation method of the isomeric high-entropy alloy material according to claim 1, wherein the working pressure of the press is 100-3000 MPa, the pressing temperature is 25-300 ℃, the dwell time is controlled within 10-60 minutes, and the density of the obtained precast block is 80-98%.
5. The method for preparing the isomeric high-entropy alloy material according to claim 1, wherein after the precast block is pressed, a sample is subjected to vacuum packaging and then taken out from an argon protection box for later use.
6. The method for preparing the isomeric high-entropy alloy material according to claim 1, wherein the heterogeneous high-entropy alloy cuttings are fully stirred and mixed by a high-energy ball mill.
7. A heterogeneous high-entropy alloy material, characterized in that it is obtained by the method of any one of claims 1 to 6.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112143924A (en) * | 2020-09-25 | 2020-12-29 | 西安稀有金属材料研究院有限公司 | Preparation method of multi-scale high-strength high-entropy alloy material for corrosive environment |
| CN112547798A (en) * | 2020-10-30 | 2021-03-26 | 南京理工大学 | Method for preparing high-strength heterogeneous high-entropy alloy through accumulative pack rolling |
| CN115041702A (en) * | 2022-06-17 | 2022-09-13 | 南京理工大学 | Preparation method of medium/high entropy alloy with isomeric components |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130108502A1 (en) * | 2011-10-27 | 2013-05-02 | Ut-Battelle, Llc | Multi-Component Solid Solution Alloys having High Mixing Entropy |
| CN105648297A (en) * | 2016-01-18 | 2016-06-08 | 南京工程学院 | Preparation method for high-entropy alloy composite material with externally-added nanometer ceramic phase reinforced and toughened |
| WO2016112210A1 (en) * | 2015-01-09 | 2016-07-14 | Scoperta, Inc. | High entropy alloys with non-high entropy second phases |
| CN105861909A (en) * | 2016-06-14 | 2016-08-17 | 济南大学 | FeSiBAlNiCo block high-entropy alloy and preparation method thereof |
| EP3173498A1 (en) * | 2014-07-23 | 2017-05-31 | Hitachi, Ltd. | Alloy structure and method for producing alloy structure |
| CN107523740A (en) * | 2017-09-20 | 2017-12-29 | 湘潭大学 | CuCrFeNiTi high entropy alloy materials and preparation method thereof |
| CN107893184A (en) * | 2017-11-08 | 2018-04-10 | 太原理工大学 | A kind of nanometer Ultra-fine Grained high-entropy alloy and preparation method thereof |
-
2018
- 2018-06-25 CN CN201810657004.5A patent/CN110629059B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130108502A1 (en) * | 2011-10-27 | 2013-05-02 | Ut-Battelle, Llc | Multi-Component Solid Solution Alloys having High Mixing Entropy |
| EP3173498A1 (en) * | 2014-07-23 | 2017-05-31 | Hitachi, Ltd. | Alloy structure and method for producing alloy structure |
| WO2016112210A1 (en) * | 2015-01-09 | 2016-07-14 | Scoperta, Inc. | High entropy alloys with non-high entropy second phases |
| CN105648297A (en) * | 2016-01-18 | 2016-06-08 | 南京工程学院 | Preparation method for high-entropy alloy composite material with externally-added nanometer ceramic phase reinforced and toughened |
| CN105861909A (en) * | 2016-06-14 | 2016-08-17 | 济南大学 | FeSiBAlNiCo block high-entropy alloy and preparation method thereof |
| CN107523740A (en) * | 2017-09-20 | 2017-12-29 | 湘潭大学 | CuCrFeNiTi high entropy alloy materials and preparation method thereof |
| CN107893184A (en) * | 2017-11-08 | 2018-04-10 | 太原理工大学 | A kind of nanometer Ultra-fine Grained high-entropy alloy and preparation method thereof |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112143924A (en) * | 2020-09-25 | 2020-12-29 | 西安稀有金属材料研究院有限公司 | Preparation method of multi-scale high-strength high-entropy alloy material for corrosive environment |
| CN112143924B (en) * | 2020-09-25 | 2021-06-25 | 西安稀有金属材料研究院有限公司 | Preparation method of multi-scale high-strength high-entropy alloy material for corrosive environment |
| CN112547798A (en) * | 2020-10-30 | 2021-03-26 | 南京理工大学 | Method for preparing high-strength heterogeneous high-entropy alloy through accumulative pack rolling |
| CN115041702A (en) * | 2022-06-17 | 2022-09-13 | 南京理工大学 | Preparation method of medium/high entropy alloy with isomeric components |
| CN115041702B (en) * | 2022-06-17 | 2024-02-13 | 南京理工大学 | Preparation method of component isomerism medium/high entropy alloy |
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