CN116043090A - Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy and preparation method thereof - Google Patents
Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy and preparation method thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 96
- 239000000956 alloy Substances 0.000 title claims abstract description 96
- 238000002360 preparation method Methods 0.000 title description 8
- 239000010936 titanium Substances 0.000 claims abstract description 57
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 40
- 238000000034 method Methods 0.000 claims abstract description 29
- 238000002844 melting Methods 0.000 claims abstract description 23
- 230000008018 melting Effects 0.000 claims abstract description 23
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 20
- 239000010955 niobium Substances 0.000 claims abstract description 19
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 208000034100 susceptibility to 1 basal cell carcinoma Diseases 0.000 claims abstract description 5
- 208000033079 susceptibility to 2 basal cell carcinoma Diseases 0.000 claims abstract description 5
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 3
- 239000011733 molybdenum Substances 0.000 claims abstract description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 3
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 claims abstract description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 3
- 238000003723 Smelting Methods 0.000 claims description 35
- 239000010949 copper Substances 0.000 claims description 27
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 25
- 229910052802 copper Inorganic materials 0.000 claims description 25
- 229910052720 vanadium Inorganic materials 0.000 claims description 22
- 229910052751 metal Inorganic materials 0.000 claims description 18
- 239000002184 metal Substances 0.000 claims description 18
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 14
- 239000002994 raw material Substances 0.000 claims description 10
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 8
- 239000001301 oxygen Substances 0.000 claims description 8
- 229910052760 oxygen Inorganic materials 0.000 claims description 8
- 229910052786 argon Inorganic materials 0.000 claims description 7
- 229910052726 zirconium Inorganic materials 0.000 claims description 6
- 230000009471 action Effects 0.000 claims description 5
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Abstract
The utility model relates to a Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy, which comprises five elements of titanium (Ti), zirconium (Zr), niobium (Hf), molybdenum (Cu) and vanadium (V), wherein the atomic percentage of Ti is less than or equal to 20 percent and less than or equal to 33.33 percent, the atomic percentage of Zr is less than or equal to 16.67 percent and less than or equal to 20 percent, the atomic percentage of Nb is less than or equal to 16.67 percent and less than or equal to 20 percent, the atomic percentage of Mo is less than or equal to 16.67 percent and less than or equal to 20 percent, and the atomic percentage of V is less than or equal to 16.67 percent and less than or equal to 20 percent; the Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy consists of a BCC1 structure, a BCC2 structure and a HCP structure; the strength and the plasticity are well combined, and the alloy can be prepared by a simpler vacuum arc melting method without any heat treatment process and deformation strengthening process treatment.
Description
Technical Field
The utility model relates to the field of high-strength high-entropy alloy, in particular to Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy and a preparation method thereof.
Background
With the continuous development of aerospace and nuclear power technologies, the traditional single-main-element alloy is more and more difficult to meet the use requirements of the component in extreme environments; as a multicomponent alloy, the high-entropy alloy has excellent performances in the aspects of high strength, high-temperature softening resistance and the like, and has wide application prospect; high-entropy alloy generally tends to form a single-phase solid solution structure due to high entropy effect, and the alloy with the structure cannot well achieve both strength and plasticity; at present, the alloy has better comprehensive mechanical properties by introducing the strong plasticity of the second phase balance alloy, which is a common method; the introduction of the second phase in the alloy is generally realized by a heat treatment process and a deformation strengthening process such as annealing, rolling and the like, and the requirement on the post-treatment process is high.
Disclosure of Invention
The utility model aims to provide a Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy and a preparation method thereof, wherein the high-strength high-entropy alloy consists of a BCC1 structure, a BCC2 structure and a HCP structure, has good strength and plasticity, is not treated by any heat treatment process and deformation strengthening process, and can be prepared by a simpler vacuum arc melting method.
In order to achieve the above purpose, the utility model adopts the following technical scheme: a Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy comprises five elements of titanium (Ti), zirconium (Zr), niobium (Hf), molybdenum (Cu) and vanadium (V), wherein the atomic percentage of Ti is less than or equal to 20 percent and less than or equal to 33.33 percent, the atomic percentage of Zr is less than or equal to 16.67 percent and less than or equal to 20 percent, the atomic percentage of Nb is less than or equal to 16.67 percent and less than or equal to 20 percent, the atomic percentage of Mo is less than or equal to 16.67 percent and less than or equal to 20 percent, and the atomic percentage of V is less than or equal to 16.67 percent and less than or equal to 20 percent; the Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy consists of BCC and HCP structures.
Preferably, the BBC structure is one or both of a BCC1 structure and a BCC2 structure.
Preferably, wherein the atomic percent of Ti is 20%, the atomic percent of Zr is 20%, the atomic percent of Nb is 20%, the atomic percent of Mo is 20%, and the atomic percent of V is 20%.
The other technical scheme of the utility model is as follows: a preparation method of Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy comprises the following steps:
step one: selecting Ti, zr, nb, mo, V metal raw materials with the purity of 99.99%, accurately weighing five raw materials according to the atomic percentage of Ti-Zr-Nb-Mo-V high-strength multiphase high-entropy alloy, placing Ti, V, zr, nb and Mo metal simple substances under the principle that the high melting point is up and the low melting point is down, namely Ti, V and Zr are placed under, mo and Nb are placed at the uppermost part, and stacking in a copper crucible of a vacuum arc melting furnace; simultaneously putting titanium blocks into another copper crucible for absorbing oxygen;
step two: closing the furnace door; vacuumizing smelting equipment to 3X 10-4 Pa, and then filling argon to 0.05MPa;
step three: starting current to smelt pure titanium blocks placed in a central copper crucible, then moving an arc gun to the position of the TiZrNbMoV high-entropy alloy, smelting until the alloy is completely melted and mixed, turning over the freshly smelted button ingot by rotating a mechanical arm after the alloy button ingot is cooled under the action of cooling water, and smelting by using the same method and parameters, wherein the step is repeatedly performed for each button ingot; each alloy button ingot is turned over for 5 times, namely smelting is carried out for 6 times;
step four: after all the TiZrNbMoV high-entropy alloy is smelted, waiting for cooling the copper crucible, opening an air valve, introducing air, opening a furnace door, and taking out the formed high-entropy alloy button ingot.
Preferably, the operations of vacuumizing and filling argon in the second step are repeated for a plurality of times.
Preferably, the specific operation of arc welding in the third step is to adjust the arc gun electrode to the edge of the central crucible, perform arc striking at the position of the electrode 3-4 mm away from the copper crucible, and adjust the height of the arc gun electrode from metal to 8-9 mm after the arc striking is successful.
Preferably, the time for smelting the titanium block in the third step is 2min, and the time for smelting the high-entropy alloy ingot each time is 2-3 min.
Preferably, in the third step, the current for smelting the titanium block is 160-180A, and the current for smelting the high-entropy alloy ingot is 350-380A.
Compared with the prior art, the Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy has the following advantages:
1. the Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy consists of a BCC1 structure, a BCC2 structure and a HCP structure, wherein the yield strength in an as-cast state is about 1588-2222 Mpa (the existing method is about 1400 Mpa), the fracture strain is about 20-25%, and the specific yield strength is about 237-311 KPa m < 3 >. Kg < -1 >; the alloy has excellent strong plastic fit and high specific yield strength in the as-cast state, which exceeds most of the prior high-entropy alloy.
2. The precipitation of the second phase in the Ti-Zr-Nb-Mo-V series high-entropy alloy structure is realized by a simple vacuum arc melting method without complex post-treatment processes such as a heat treatment process, a deformation strengthening process and the like; therefore, the method is beneficial to saving resources and cost and is convenient for commercial industrial production.
Drawings
FIG. 1 is a graph showing the results of EBSD phase analysis of the TiZrNbMoV high-entropy alloy in example 1.
FIG. 2 is a graph of the EBSD phase analysis results of Ti1.5ZrNbMoV high entropy alloy in example 2.
FIG. 3 is a graph showing the results of EBSD phase analysis of the Ti2ZrNbMoV high-entropy alloy in example 1.
FIG. 4 is an EBSD micro morphology plot of the TiZrNbMoV high entropy alloy of example 1.
FIG. 5 is an EBSD micro-morphology of Ti1.5ZrNbMoV high entropy alloy of example 2.
FIG. 6 is an EBSD micro morphology plot of the Ti2ZrNbMoV high entropy alloy of example 3.
FIG. 7 is a plot of room temperature compressive engineering stress strain for the TiZrNbMoV high entropy alloy of examples 1,2, and 3.
Detailed Description
In order that those skilled in the art may better understand the technical solutions of the present utility model, the following detailed description of the present utility model with reference to the accompanying drawings is provided for exemplary and explanatory purposes only and should not be construed as limiting the scope of the present utility model.
Example 1
The embodiment is a TiZrNbMoV high-entropy alloy, which consists of Ti, zr, nb, mo, V elements, wherein the relative atomic percentage content of Ti is 20%, the relative atomic percentage content of Zr is 20%, the relative atomic percentage content of Nb is 20%, the relative atomic percentage content of Mo is 20%, and the relative atomic percentage content of V is 20%; the purity of the Ti, zr, nb, mo, V metal raw material is higher than 99.99wt%.
The preparation method of the TiZrNbMoV high-entropy alloy comprises the following steps:
step one: selecting five metal raw materials with purity of 99.99 percent, namely Ti, zr, nb, mo, V and the like, calculating the mass percent according to the atomic percent of the TiZrNbMoV high-entropy alloy, weighing on a balance to the 3 rd position after decimal point, wherein the sum of the mass of the last five elements is 50g, wherein the Ti is 6.320g, the Zr is 12.040g, the Nb is 12.260g, the Mo is 12.660g and the V is 6.72g; ti, V, zr, nb and Mo metal simple substances are stacked in a copper crucible of a vacuum arc melting furnace according to the principle that the high melting point is above and the low melting point is below, namely Ti, V and Zr are arranged below, mo and Nb are arranged at the uppermost part; simultaneously putting titanium blocks into another copper crucible for absorbing oxygen;
step two: the melting equipment was evacuated to 3X 10-4 Pa and then charged with 99.99wt% high purity argon to 0.05MPa. This process was repeated 3 times repeatedly;
step three: starting current, adjusting an arc gun electrode to the edge of a central crucible, striking an arc at the position 3-4 mm away from the copper crucible, adjusting the height of the arc gun electrode from metal to 8-9 mm after the arc striking is successful, smelting a pure titanium block placed in the central copper crucible, and absorbing the oxygen content in a vacuum cavity, wherein the smelting current of the titanium block is 160A, and the smelting time is 2min; then the arc gun is moved to the position of the TiZrNbMoV high-entropy alloy, and the alloy is smelted until the alloy is completely melted and uniformly mixed, the current is kept at 380A, and the smelting time is 2-3 min; then reducing current, raising an arc gun and extinguishing arc; after alloy button ingots are cooled under the action of cooling water, turning over the button ingots which are just smelted by rotating a mechanical arm, smelting by using the same method and parameters, and repeating the step for each button ingot; in order to ensure that the alloy components are fully and uniformly mixed, each alloy button ingot is subjected to 5 times of turn-over, namely smelting for 6 times;
step four: after smelting is completed, waiting for the copper crucible to cool to room temperature, opening an air valve, introducing air, opening a furnace door, and taking out the formed high-entropy alloy button ingot.
Example 2
The embodiment is a Ti1.5ZrNbMoV high-entropy alloy, which consists of five elements Ti, zr, nb, mo, V, wherein the relative atomic percentage content of Ti is 27.27%, the relative atomic percentage content of Zr is 18.18%, the relative atomic percentage content of Nb is 18.18%, the relative atomic percentage content of Mo is 18.18%, and the relative atomic percentage content of V is 18.19%; the purity of the Ti, zr, nb, mo, V metal raw material is higher than 99.99wt%;
the preparation method of the TiZrNbMoV high-entropy alloy comprises the following steps:
step one: selecting five metal raw materials with purity of 99.99 percent, namely Ti, zr, nb, mo, V and the like, calculating the mass percent according to the atomic percent of the Ti1.5ZrNbMoV high-entropy alloy, weighing on a balance to the 3 rd position after decimal point, wherein the sum of the mass of the last five elements is 50g, wherein the Ti is 8.915g, the Zr is 11.320g, the Nb is 11.530g, the Mo is 11.025 g and the V is 6.325g; ti, V, zr, nb and Mo metal simple substances are stacked in a copper crucible of a vacuum arc melting furnace according to the principle that the high melting point is above and the low melting point is below, namely Ti, V and Zr are arranged below, mo and Nb are arranged at the uppermost part, and simultaneously, a titanium block is arranged in another copper crucible for absorbing oxygen;
step two: vacuumizing smelting equipment to 3X 10-4 Pa, then filling 99.99wt% high-purity argon to 0.05MPa, and repeating the process for 3 times;
step three: starting current, adjusting an arc gun electrode to the edge of a central crucible, striking an arc at the position 3-4 mm away from the copper crucible, adjusting the height of the arc gun electrode from metal to 8-9 mm after the arc striking is successful, smelting a pure titanium block placed in the central copper crucible, and absorbing the oxygen content in a vacuum cavity, wherein the smelting current of the titanium block is 170A, and the smelting time is 2min; then the arc gun is moved to the position of Ti1.5ZrNbMoV high-entropy alloy, and the alloy is smelted until the alloy is completely melted and uniformly mixed, the current is kept at 370A, and the smelting time is 2-3 min; then reducing current, raising an arc gun and extinguishing arc; after alloy button ingots are cooled under the action of cooling water, turning over the button ingots which are just smelted by rotating a mechanical arm, smelting by using the same method and parameters, and repeating the step for each button ingot; in order to ensure that the alloy components are fully and uniformly mixed, each alloy button ingot is subjected to 5 times of turn-over, namely smelting for 6 times;
step four: after smelting is completed, waiting for the copper crucible to cool to room temperature, opening an air valve, introducing air, opening a furnace door, and taking out the formed high-entropy alloy button ingot.
Example 3
The embodiment is a Ti2ZrNbMoV high-entropy alloy, which consists of Ti, zr, nb, mo, V elements, wherein the relative atomic percentage content of Ti is 33.33%, the relative atomic percentage content of Zr is 16.67%, the relative atomic percentage content of Nb is 16.67%, the relative atomic percentage content of Mo is 16.66%, and the relative atomic percentage content of V is 16.67%; the purity of the Ti, zr, nb, mo, V metal raw material is higher than 99.99wt%.
The preparation method of the Ti2ZrNbMoV high-entropy alloy comprises the following steps:
step one: five metal raw materials Ti, zr, nb, mo, V with the purity of 99.99% are selected, the mass percentage is calculated according to the atomic percentage of the TiZrNbMoV high-entropy alloy, the weight is weighed on a balance to be 3 rd position after decimal point, the sum of the mass of the last five elements is 50g, wherein the Ti is 11.220g, the Zr is 10.690g, the Nb is 10.885g, the Mo is 11.235g, and the V is 5.970g. Ti, V, zr, nb and Mo metal simple substances are stacked in a copper crucible of a vacuum arc melting furnace according to the principle that the high melting point is above and the low melting point is below, namely Ti, V and Zr are arranged below, mo and Nb are arranged at the uppermost part; simultaneously putting titanium blocks into another copper crucible for absorbing oxygen;
step two: vacuumizing smelting equipment to 3X 10-4 Pa, and then filling 99.99wt% high-purity argon to 0.05MPa; this process was repeated 3 times repeatedly;
step three: starting current, adjusting an arc gun electrode to the edge of a central crucible, striking an arc at the position 3-4 mm away from the copper crucible, adjusting the height of the arc gun electrode from metal to 8-9 mm after the arc striking is successful, smelting a pure titanium block placed in the central copper crucible for absorbing the oxygen content in a vacuum cavity, wherein the smelting current of the titanium block is kept to be about 160A, and the smelting time is 2min; then the arc gun is moved to the position of Ti2ZrNbMoV high-entropy alloy, and the alloy is smelted until the alloy is completely melted and uniformly mixed, the current is kept to be about 370A, and the smelting time is 2-3 min; then reducing current, raising an arc gun and extinguishing arc; after alloy button ingots are cooled under the action of cooling water, turning over the button ingots which are just smelted by rotating a mechanical arm, smelting by using the same method and parameters, and repeating the step for each button ingot; in order to ensure that the alloy components are fully and uniformly mixed, each alloy button ingot is subjected to 5 times of turn-over, namely smelting for 6 times;
step four: after smelting is completed, waiting for the copper crucible to cool to room temperature, opening an air valve, introducing air, opening a furnace door, and taking out the formed high-entropy alloy button ingot.
The high-entropy alloy button ingots obtained in example 1, example 2 and example 3 are respectively subjected to EBSD microstructure observation and room temperature compression mechanical property test to obtain an EBSD phase analysis result diagram, an EBSD microstructure morphology diagram and a room temperature compression engineering stress strain curve diagram shown in figures 1-7
As shown in fig. 1-3, the EBSD experimental results show that the alloy is composed of a BCC phase and a HCP phase, and that as the Ti content increases, the HCP phase duty ratio decreases and the BCC phase duty ratio increases.
As shown in fig. 4-6, the grain size of the alloy is refined after the Ti content is increased.
As shown in the room temperature compression experiment of fig. 7, as the Ti content of the alloy increases, the plasticity of the alloy is improved, because the alloy grains are refined; the yield strength of the TiZrNbMoV high-entropy alloy in the as-cast state is about 1588-2222 Mpa, the specific yield strength is about 237-311 KPa.m3.kg-1, and the compression fracture strain is 20-25%; the TiZrNbMoV high-strength high-entropy alloy has excellent comprehensive mechanical properties due to the multiphase heterostructure and the grain refining effect of Ti element.
It should be noted that, in this document, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
The principles and embodiments of the present utility model have been described herein with reference to specific examples, the above examples being provided only to assist in understanding the methods of the present utility model and the core ideas thereof; the foregoing is merely illustrative of the preferred embodiments of this utility model, and it is noted that there is objectively no limit to the specific structure disclosed herein, since numerous modifications, adaptations and variations can be made by those skilled in the art without departing from the principles of the utility model, and the above-described features can be combined in any suitable manner; such modifications, variations and combinations, or the direct application of the inventive concepts and aspects to other applications without modification, are contemplated as falling within the scope of the present utility model.
Claims (8)
1. A Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy comprises five elements of titanium (Ti), zirconium (Zr), niobium (Hf), molybdenum (Cu) and vanadium (V), wherein the atomic percentage of Ti is less than or equal to 20 percent and less than or equal to 33.33 percent, the atomic percentage of Zr is less than or equal to 16.67 percent and less than or equal to 20 percent, the atomic percentage of Nb is less than or equal to 16.67 percent and less than or equal to 20 percent, the atomic percentage of Mo is less than or equal to 16.67 percent and less than or equal to 20 percent, and the atomic percentage of V is less than or equal to 16.67 percent and less than or equal to 20 percent; the Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy consists of a BCC structure and a HCP structure.
2. The Ti-Zr-Nb-Mo-V system high-strength high-entropy alloy according to claim 1, wherein the BCC structure is one or both of a BCC1 structure and a BCC2 structure.
3. The Ti-Zr-Nb-Mo-V based high strength and high entropy alloy according to claim 1, wherein the Ti is 20 atomic percent, the Zr is 20 atomic percent, the Nb is 20 atomic percent, the Mo is 20 atomic percent, and the V is 20 atomic percent.
4. A method for producing a Ti-Zr-Nb-Mo-V based high-strength and high-entropy alloy according to any one of claims 1 to 3, comprising the steps of:
step one: selecting Ti, zr, nb, mo, V metal raw materials with the purity of 99.99%, accurately weighing five raw materials according to the atomic percentage of Ti-Zr-Nb-Mo-V high-strength multiphase high-entropy alloy, placing Ti, V, zr, nb and Mo metal simple substances under the principle that the high melting point is up and the low melting point is down, namely Ti, V and Zr are placed under, mo and Nb are placed at the top, stacking in a copper crucible of a vacuum arc melting furnace, and simultaneously placing titanium blocks in another copper crucible for absorbing oxygen;
step two: closing the furnace door; vacuumizing smelting equipment to 3X 10-4 Pa, and then filling argon to 0.05MPa;
step three: starting current to smelt pure titanium blocks placed in a central copper crucible, then moving an arc gun to the position of the TiZrNbMoV high-entropy alloy, smelting until the alloy is completely melted and mixed, turning over the freshly smelted button ingot by rotating a mechanical arm after the alloy button ingot is cooled under the action of cooling water, and smelting by using the same method and parameters, wherein the step is repeatedly performed for each button ingot; each alloy button ingot is turned over for 5 times, namely smelting is carried out for 6 times;
step four: after all the TiZrNbMoV high-entropy alloy is smelted, waiting for cooling the copper crucible, opening an air valve, introducing air, opening a furnace door, and taking out the formed high-entropy alloy button ingot.
5. The method for producing a Ti-Zr-Nb-Mo-V based high-strength and high-entropy alloy according to claim 4, wherein the operations of vacuum pumping and argon filling in the second step are repeated a plurality of times.
6. The method for producing a Ti-Zr-Nb-Mo-V based high-strength high-entropy alloy according to claim 4, wherein the specific operation of arc welding in step three is to adjust the arc gun electrode to the edge of the central crucible, striking an arc at a height of 3 to 4mm from the copper crucible, and adjusting the height of the arc gun electrode to 8 to 9mm from the metal after the striking is successful.
7. The method for producing a Ti-Zr-Nb-Mo-V based high-strength and high-entropy alloy according to claim 4, wherein the time for melting the titanium ingot in the third step is 2 minutes, and the time for melting the high-entropy alloy ingot each time is 2 to 3 minutes.
8. The method for producing a Ti-Zr-Nb-Mo-V based high-strength and high-entropy alloy according to claim 4, wherein the current for melting the titanium ingot in the third step is 160 to 180A, and the current for melting the high-entropy alloy ingot is 350 to 380A.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103602872A (en) * | 2013-10-31 | 2014-02-26 | 北京科技大学 | TiZrNbVMo[x] high entropy alloy and preparation method thereof |
| KR20200004566A (en) * | 2018-07-04 | 2020-01-14 | 국방과학연구소 | High-entropy based composite and its manufacturing method |
| CN111270094A (en) * | 2020-03-20 | 2020-06-12 | 苏州天峰动立合金科技有限公司 | Refractory high-entropy alloy and forming method thereof |
| CN111549270A (en) * | 2020-05-22 | 2020-08-18 | 北京工业大学 | Low-density high-strength high-plasticity high-entropy alloy material and preparation method thereof |
| CN114774752A (en) * | 2022-03-25 | 2022-07-22 | 江苏理工学院 | High-strength high-toughness TiZrNbMoV refractory high-entropy alloy and preparation method thereof |
| CN114836667A (en) * | 2022-04-07 | 2022-08-02 | 山东大学 | Light high-temperature high-entropy alloy and preparation process of rod material thereof |
-
2022
- 2022-12-28 CN CN202211692835.9A patent/CN116043090B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103602872A (en) * | 2013-10-31 | 2014-02-26 | 北京科技大学 | TiZrNbVMo[x] high entropy alloy and preparation method thereof |
| KR20200004566A (en) * | 2018-07-04 | 2020-01-14 | 국방과학연구소 | High-entropy based composite and its manufacturing method |
| CN111270094A (en) * | 2020-03-20 | 2020-06-12 | 苏州天峰动立合金科技有限公司 | Refractory high-entropy alloy and forming method thereof |
| CN111549270A (en) * | 2020-05-22 | 2020-08-18 | 北京工业大学 | Low-density high-strength high-plasticity high-entropy alloy material and preparation method thereof |
| CN114774752A (en) * | 2022-03-25 | 2022-07-22 | 江苏理工学院 | High-strength high-toughness TiZrNbMoV refractory high-entropy alloy and preparation method thereof |
| CN114836667A (en) * | 2022-04-07 | 2022-08-02 | 山东大学 | Light high-temperature high-entropy alloy and preparation process of rod material thereof |
Non-Patent Citations (4)
| Title |
|---|
| FUYANG TIAN、LAJOS KAROLY VARGA等: "Ab initio design of elastically isotropic TiZrNbMoVx high-entropy alloys", JOURNAL OF ALLOYS AND COMPOUNDS, vol. 599, 7 February 2014 (2014-02-07), pages 19 - 25 * |
| TIANXIN LI、JUNWEI MIAO等: "Effect of Zr on the as-cast microstructure and mechanical properties of lightweight Ti2VNbMoZrx refractory high-entropy alloys", INTERNATIONAL JOURNAL OF REFRACTORY METALS AND HARD MATERIALS, vol. 103, 22 December 2021 (2021-12-22), pages 1 - 8, XP086940485, DOI: 10.1016/j.ijrmhm.2021.105762 * |
| Y.D. WU, Y.H. CAI等: "Phase composition and solid solution strengthening effect in TiZrNbMoV high-entropy alloys", MATERIALS & DESIGN, vol. 83, 1 June 2015 (2015-06-01), pages 651 - 660 * |
| ZHENGHANG CA、YANG HAI等: "Effect of Ti content on the microstructure and mechanical properties of Ti xZrNbMoV lightweight refractory high-entropy alloys", INTERNATIONAL JOURNAL OF REFRACTORY METALS AND HARD MATERIALS, vol. 119, 3 January 2024 (2024-01-03), pages 1 - 9, XP087458655, DOI: 10.1016/j.ijrmhm.2023.106547 * |
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