CN109266946B - Preparation method of Ti-based high-entropy amorphous-dendritic crystal composite material - Google Patents
Preparation method of Ti-based high-entropy amorphous-dendritic crystal composite material Download PDFInfo
- Publication number
- CN109266946B CN109266946B CN201811184433.1A CN201811184433A CN109266946B CN 109266946 B CN109266946 B CN 109266946B CN 201811184433 A CN201811184433 A CN 201811184433A CN 109266946 B CN109266946 B CN 109266946B
- Authority
- CN
- China
- Prior art keywords
- smelting
- intermediate alloy
- composite material
- furnace
- amorphous
- 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.)
- Expired - Fee Related
Links
- 239000002131 composite material Substances 0.000 title claims abstract description 26
- 239000013078 crystal Substances 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 238000003723 Smelting Methods 0.000 claims abstract description 61
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 45
- 239000000956 alloy Substances 0.000 claims abstract description 45
- 238000000034 method Methods 0.000 claims abstract description 14
- 238000005266 casting Methods 0.000 claims abstract description 13
- 239000000126 substance Substances 0.000 claims abstract description 11
- 238000005303 weighing Methods 0.000 claims abstract description 11
- 238000002156 mixing Methods 0.000 claims abstract description 8
- 239000010936 titanium Substances 0.000 claims description 84
- 239000010949 copper Substances 0.000 claims description 49
- 229910052719 titanium Inorganic materials 0.000 claims description 25
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 22
- 229910052802 copper Inorganic materials 0.000 claims description 19
- 239000002994 raw material Substances 0.000 claims description 17
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 14
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 11
- 229910052786 argon Inorganic materials 0.000 claims description 11
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 11
- 229910052735 hafnium Inorganic materials 0.000 claims description 11
- 239000001301 oxygen Substances 0.000 claims description 11
- 229910052760 oxygen Inorganic materials 0.000 claims description 11
- 229910052726 zirconium Inorganic materials 0.000 claims description 11
- 229910052790 beryllium Inorganic materials 0.000 claims description 8
- 229910052758 niobium Inorganic materials 0.000 claims description 8
- 238000004140 cleaning Methods 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 4
- 238000004381 surface treatment Methods 0.000 claims description 4
- 230000008569 process Effects 0.000 claims description 3
- 238000001035 drying Methods 0.000 claims description 2
- 238000002844 melting Methods 0.000 claims 2
- 230000008018 melting Effects 0.000 claims 1
- 238000010309 melting process Methods 0.000 claims 1
- 230000006835 compression Effects 0.000 abstract description 6
- 238000007906 compression Methods 0.000 abstract description 6
- 238000005275 alloying Methods 0.000 abstract description 2
- 238000009776 industrial production Methods 0.000 abstract description 2
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 18
- 239000000463 material Substances 0.000 description 11
- 238000011065 in-situ storage Methods 0.000 description 7
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 239000007789 gas Substances 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000005086 pumping Methods 0.000 description 3
- 229910017532 Cu-Be Inorganic materials 0.000 description 2
- 238000005280 amorphization Methods 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000000861 blow drying Methods 0.000 description 2
- 239000002178 crystalline material Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 238000003889 chemical engineering Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 230000001687 destabilization Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010952 in-situ formation Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000005300 metallic glass Substances 0.000 description 1
- 238000004377 microelectronic Methods 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 239000000075 oxide glass Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
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
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention provides a Ti-based high-entropy amorphous-dendritic crystal composite materialThe preparation method mainly utilizes a vacuum arc furnace to prepare a pre-designed alloy ratio Ti20Zr20Hf20Nb10Cu10Be20Alloying is carried out, and the method comprises the following steps: according to Ti25Zr25Hf25Nb25Weighing each simple substance element with the purity of more than or equal to 99.9 percent according to the atomic ratio, smelting to obtain a first intermediate alloy, and then according to Ti16.67Zr16.67Hf16.67Cu16.67Be33.32Weighing each simple substance element according to the atomic ratio, smelting to obtain a second intermediate alloy, mixing and smelting the first intermediate alloy and the second intermediate alloy, and performing suction casting to obtain the high-entropy amorphous-dendritic crystal composite material Ti20Zr20Hf20Nb10Cu10Be20. The preparation method is simple and easy to operate, the compression performance of the obtained composite material is obviously improved, and the method is suitable for industrial production and popularization.
Description
Technical Field
The invention relates to the technical field of amorphous composite materials or high-entropy alloys, in particular to a preparation method of a Ti-based high-entropy amorphous-dendritic crystal composite material.
Background
Amorphous alloys, also known as metallic glasses, are a material with many new and unique properties. Amorphous refers to the state of long-range disorder and short-range order arrangement of atomic structures in a substance. Unlike conventional oxide glasses, the interatomic bonds in amorphous alloys are metallic, rather than covalent. Due to the unique disordered structure, the amorphous alloy does not have defects such as dislocation, vacancy and the like in a crystalline material, so that the amorphous alloy has excellent mechanical, physical and chemical properties, such as high strength (about 1/50 Young modulus), high corrosion resistance, excellent magnetic properties and superplasticity at a certain temperature. Due to the excellent physical, chemical and mechanical properties and good forming properties, the amorphous alloy has wide application space in the fields of electronics, electric power, chemical engineering, aviation, aerospace, machinery, microelectronics and the like. However, the room temperature brittle failure and stability of the amorphous alloy severely restrict the engineering application of the amorphous alloy.
The conventional amorphous alloy generally has one main element, and in recent years, an amorphous alloy formed by alloying five or more elements at an equal atomic ratio or an approximately equal atomic ratio is called a high-entropy amorphous alloy. Besides the advantages of the amorphous alloy, the high-entropy amorphous alloy has higher strength compared with the traditional amorphous alloy due to the high-entropy effect, and taking Ti-Zr-Ni-Cu-Be system as an example, Ti20Zr20Ni20Cu20Be20The high-entropy amorphous compression strength can reach 2300MPa, and the maximum compression strength of the traditional amorphous alloy of the same system is only 2000 MPa; the high-entropy amorphous has another advantage over the conventional amorphous in that it has better thermal stability, i.e., the time required for the high-entropy amorphous to change from an amorphous structure to a crystalline structure under the same conditions is longer. The excellent physical and mechanical properties make the high-entropy amorphous alloy a potential engineering structure material.
The high-entropy amorphous alloy can be used as a new structural material, and certain plasticity is required to ensure the use safety. However, the existing literature shows that almost all high-entropy amorphous alloys have low plasticity until 2017. It is generally believed that the main reason for limiting the plasticity of high-entropy amorphization is its lack of plastic deformation mechanisms such as dislocation slip, twinning, etc. in crystalline materials, during which high-entropy amorphization undergoes highly localized single shear deformation and brittle fracture along the shear band. Generally, the plastic strain of most high-entropy amorphous alloys in a tensile state is almost zero, and the plastic strain in a compression state is less than 2%. Because it is difficult to obtain high-entropy amorphous materials with high toughness, researches on improving the toughness of high-entropy amorphous alloys are increasing in recent years.
Generally, the introduction of in-situ precipitated second phases in conventional amorphous structures is an effective way to obtain high-toughness amorphous materials. The principle is that the in-situ generated second phase is used for inhibiting the destabilization expansion of a single shear band and promoting the multiple bifurcation and expansion of the single shear band, and the process enables a large number of shear bands with different orientations to exist in the amorphous alloy, thereby providing effective plastic deformation capability. The in-situ formation of the second-phase dendrites in the amorphous alloy is very beneficial to the improvement of mechanical properties.
As the amorphous forming capability of the high-entropy amorphous alloy is far smaller than that of the traditional amorphous alloy, taking Ti-Zr-Ni-Cu-Be system as an example, Ti20Zr20Ni20Cu20Be20The maximum critical dimension of high-entropy amorphous is only 3mm, while Ti40Zr25Ni3Cu12Be20The maximum critical dimension of a conventional amorphous can reach 14 mm. The preparation method for obtaining the high-toughness material by introducing the in-situ precipitated second phase into the amorphous structure requires that the amorphous system has good amorphous forming capability, so that the preparation of the dendritic crystal amorphous composite material by introducing the second phase in situ into the high-entropy amorphous with limited amorphous forming capability is difficult.
Disclosure of Invention
The invention aims to solve the technical defects, and provides a preparation method of a Ti-based high-entropy amorphous-dendritic crystal composite material, which is simple to operate and easy to prepare, wherein a first intermediate alloy and a second intermediate alloy are mixed and smelted to uniformly distribute in-situ precipitated dendritic crystal phases on an amorphous phase matrix, so that the compression plasticity of the high-entropy amorphous-dendritic crystal composite material is effectively improved, and the preparation method is suitable for commercial production.
In order to achieve the purpose, the invention adopts the technical scheme that:
a preparation method of a Ti-based high-entropy amorphous-dendritic crystal composite material comprises the following steps:
s1, surface treatment of raw materials: respectively cleaning and drying the simple substance elements of Ti, Zr, Hf, Nb, Cu and Be, and then according to the Ti20Zr20Hf20Nb10Cu10Be20Calculating the mass of each element according to the atomic percentage of each element and weighing;
s2, alloy smelting: the Ti, Zr, Hf and Nb raw materials after the S1 treatment were processed in accordance with Ti25Zr25Hf25Nb25The atomic ratio of the components is weighed and mixed, high-purity argon is filled to 0.2-0.3 Mpa after vacuum pumping, and smelting is carried outFirstly, smelting a titanium ingot for 2-3 times to absorb oxygen remained in the furnace, and then smelting raw materials in the furnace to obtain a first intermediate alloy Ti25Zr25Hf25Nb25；
The S1-treated Ti, Zr, Hf, Cu and Be were adjusted to Ti16.67Zr16.67Hf16.67Cu16.67Be33.32The method comprises the following steps of weighing and mixing the raw materials according to the atomic ratio, vacuumizing, introducing high-purity argon to 0.2-0.3 Mpa for smelting, smelting a titanium ingot for 2-3 times to absorb residual oxygen in the furnace, and smelting the raw materials in the furnace to obtain a second intermediate alloy Ti16.67Zr16.67Hf16.67Cu16.67Be33.32；
Mixing the first intermediate alloy and the second intermediate alloy according to the mass ratio of 3.33:5, and smelting to obtain Ti20Zr20Hf20Nb10Cu10Be20；
S3, suction casting: ti obtained in S220Zr20Hf20Nb10Cu10Be20Placing the titanium ingot in a water-cooled copper crucible, vacuumizing, introducing high-purity argon to 0.1-0.3 Mpa for smelting, smelting the titanium ingot for 2-3 times to absorb oxygen remained in the furnace, then smelting the alloy in the furnace, performing suction casting after 90-120 s, and taking out a suction casting sample after the furnace is naturally cooled to obtain the Ti-based high-entropy amorphous-dendritic crystal composite material Ti20Zr20Hf20Nb10Cu10Be20。
Preferably, the purity of each of the simple elements Ti, Zr, Hf, Nb, Cu and Be is 99.9% or higher.
Preferably, in S2, the first intermediate alloy, the second intermediate alloy and Ti are prepared by smelting20Zr20Hf20Nb10Cu10Be20And turning over the sample after the sample is smelted and completely cooled, repeating the first smelting process, and smelting for the second time, wherein the smelting time is 8-10 min, and the repeated smelting times are 3-4.
Preferably, in S2, the smelting time of the first intermediate alloy and the second intermediate alloy is 8-10 min, and the smelting current is 120-150A.
Preferably, in S2, Ti20Zr20Hf20Nb10Cu10Be20The smelting time is 8-10 min, and the smelting current is 120-150A.
Preferably, in S3, the natural cooling time is 15-18 min.
Compared with the prior art, the invention has the following beneficial effects:
the invention is realized by adding a first intermediate alloy Ti25Zr25Hf25Nb25And a second intermediate alloy Ti16.67Zr16.67Hf16.67Cu16.67Be33.32The high-entropy amorphous-dendritic crystal composite material obtained by mixing and smelting is composed of two phases, in-situ precipitated dendritic crystal phases are uniformly distributed on an amorphous phase matrix, the material is excellent in performance, the compression plasticity is remarkably improved, and the method is simple to operate, easy to prepare and suitable for industrial production and popularization.
Drawings
FIG. 1 is a schematic structural diagram of a Ti-based high-entropy amorphous-dendritic crystal composite material prepared in example 1 of the present invention;
FIG. 2 is a graph showing the compressive stress-strain curves of the Ti-based high-entropy amorphous-dendritic composite material prepared in example 1 of the present invention and a comparative example.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments. The scope of the invention is not limited to the specific embodiments.
Example 1
Ti-based high-entropy amorphous-dendritic crystal composite material Ti20Zr20Hf20Nb10Cu10Be20The preparation method comprises the following steps:
s1, surface treatment of raw materials: respectively ultrasonically cleaning Ti, Zr, Hf, Nb, Cu and Be of the elementary substance elements with the purity of more than or equal to 99.9 percent for 20min by using acetone and ethanol, blow-drying by using a hair drier, and then respectively weighing the treated elementary substances according to the following mass percentages: 4.73g Ti, 9.02g Zr, 17.63g Hf, 4.59g Nb, 3.14g Cu and 0.89g Be;
s2, alloy smelting: according to Ti25Zr25Hf25Nb25Respectively weighing 4.76g of Ti, 8.89g of Zr, 17.40g of Hf and 9.05g of Nb in the atomic ratio, placing the Ti, Zr, Hf and Nb into a water-cooled copper crucible, placing the copper crucible into a vacuum arc furnace, closing the furnace door, and pumping vacuum to 1 × 10-3Introducing high-purity argon of 0.3MPa into the reactor under the pressure of MPa, after arcing, smelting a titanium ingot for 3 times to absorb oxygen remained in the furnace, then smelting the mixed raw materials, wherein the smelting current is 150A, and the smelting time is 8min to obtain a first intermediate alloy Ti25Zr25Hf25Nb25；
According to Ti16.67Zr16.67Hf16.67Cu16.67Be33.32Respectively weighing 4.79g of Ti, 9.12g of Zr, 17.84g of Hf, 6.35g of Cu and 0.90g of Be into a water-cooled copper crucible, placing the copper crucible into a vacuum arc furnace, closing a furnace door, and pumping vacuum to 1 × 10-3Introducing high-purity argon of 0.3MPa into the titanium ingot, smelting the titanium ingot for 3 times after arcing to absorb oxygen remained in the furnace, smelting the mixed raw materials, wherein the smelting current is 120A, and the smelting time is 8min to obtain a second intermediate alloy Ti16.6 7Zr16.67Hf16.67Cu16.67Be33.32；
Mixing the first intermediate alloy and the second intermediate alloy according to the mass ratio of 3.33:5, and smelting by using a vacuum arc furnace, wherein the smelting current is 150A, and the smelting time is 10min to obtain Ti20Zr20Hf20Nb10Cu10Be20；
S3, suction casting: ti obtained in S220Zr20Hf20Nb10Cu10Be20Placing in a water-cooled copper crucible, placing the water-cooled copper crucible in a vacuum arc furnace, closing a furnace door, vacuumizing, introducing high-purity argon gas of 0.1MPa, after arcing, firstly smelting a titanium ingot for 3 times to absorb oxygen remained in the furnace, then smelting alloy in the furnace, performing suction casting after 90s, naturally cooling in the furnace after 15min, and taking out a suction casting sampleObtaining the Ti-based high-entropy amorphous-dendritic crystal composite material Ti20Zr20Hf20Nb10Cu10Be20。
Comparative example
Ti20Zr20Hf20Cu20Be20The preparation method of the high-entropy amorphous material comprises the following steps:
s1, surface treatment of raw materials: respectively ultrasonically cleaning Ti, Zr, Hf, Cu and Be of the simple substance elements with the purity of more than or equal to 99.9 percent for 20min by using acetone and ethanol, blow-drying by using a hair drier, and then respectively weighing the treated simple substance elements according to the following mass percentages: 3.681g Ti, 7.014g Zr, 13.725g Hf, 4.886g Cu and 0.693g Be;
s2, alloy smelting: according to Ti20Zr20Hf20Cu20Be203.681g Ti, 7.014g Zr, 13.725g Hf, 4.886g Cu and 0.693g Be are weighed respectively and put into a water-cooled copper crucible and put into a vacuum arc furnace, the furnace door is closed, and vacuum is pumped to 1 x 10-3Introducing high-purity argon gas of 0.3MPa, after arcing, smelting a titanium ingot for 3 times to absorb oxygen remained in the furnace, then smelting the mixed raw materials, wherein the smelting current is 120A, and the smelting time is 10min to obtain alloy Ti20Zr20Hf20Cu20Be20
S3, suction casting: ti obtained in S220Zr20Hf20Cu20Be20Placing the alloy in a water-cooled copper crucible, placing the water-cooled copper crucible in a vacuum arc furnace, closing a furnace door, vacuumizing, filling high-purity argon gas of 0.1MPa, after arcing, firstly smelting a titanium ingot for 3 times to absorb oxygen remained in the furnace, then smelting the alloy in the furnace, performing suction casting after 90s, naturally cooling in the furnace after 15min, taking out a suction casting sample, and obtaining Ti20Zr20Hf20Cu20Be20High entropy amorphous material.
Physical property characterization was performed on the sample prepared in example 1, and FIG. 1 shows that Ti-based high-entropy amorphous-dendritic crystal composite material Ti prepared in example 120Zr20Hf20Nb10Cu10Be20The microstructure under a low power optical microscope, FIG. 2 shows the Ti-based high-entropy amorphous-dendritic crystal composite material Ti prepared in example 120Zr20Hf20Nb10Cu10Be20And comparative example Ti20Zr20Hf20Cu20Be20The compressive stress strain curve of the sample is shown.
As can be seen from FIG. 1, the sample structure prepared in example 1 consists of two phases, and in-situ grown dendritic phases are uniformly distributed on an amorphous phase matrix; as can be seen from fig. 2, the yield strength of the sample prepared in example 1 is increased by about 200MPa compared with the pure amorphous material in the comparative example, and the plastic strain is increased by nearly 8 times, which indicates that the plasticity of the amorphous-dendritic crystal composite material in example 1 is significantly improved compared with the pure amorphous material.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that those skilled in the art can make various improvements and modifications without departing from the principle of the present invention, and these improvements and modifications should also be construed as the protection scope of the present invention.
Claims (6)
1. A preparation method of a Ti-based high-entropy amorphous-dendritic crystal composite material is characterized by comprising the following steps:
s1, surface treatment of raw materials: respectively cleaning and drying the simple substance elements of Ti, Zr, Hf, Nb, Cu and Be, and then according to the Ti20Zr20Hf20Nb10Cu10Be20Calculating the mass of each element according to the atomic percentage of each element and weighing;
s2, alloy smelting: the Ti, Zr, Hf and Nb raw materials after the S1 treatment were processed in accordance with Ti25Zr25Hf25Nb25The method comprises the following steps of weighing and mixing the raw materials according to the atomic ratio, vacuumizing, filling high-purity argon to 0.2-0.3 MPa for smelting, smelting a titanium ingot for 2-3 times to absorb residual oxygen in the furnace, and smelting the raw materials in the furnace to obtain a first intermediate alloy Ti25Zr25Hf25Nb25；
Raw materials of S1-treated Ti, Zr, Hf, Cu and Be in accordance with Ti16.67Zr16.67Hf16.67Cu16.67Be33.32The method comprises the following steps of weighing and mixing the raw materials according to the atomic ratio, vacuumizing, filling high-purity argon to 0.2-0.3 MPa for smelting, firstly smelting a titanium ingot for 2-3 times to absorb residual oxygen in the furnace, and then smelting the raw materials in the furnace to obtain a second intermediate alloy Ti16.67Zr16.67Hf16.67Cu16.6 7Be33.32；
Mixing the first intermediate alloy and the second intermediate alloy according to the weight ratio of 3.33:5, and smelting to obtain Ti20Zr20Hf20Nb10Cu10Be20；
S3, suction casting: ti obtained in S220Zr20Hf20Nb10Cu10Be20Placing the titanium ingot in a water-cooled copper crucible, vacuumizing, filling high-purity argon to 0.1-0.3 MPa for smelting, smelting a titanium ingot for 2-3 times to absorb oxygen remained in the furnace, smelting alloy in the furnace, performing suction casting after 90-120 s, and taking out a suction casting sample after the furnace is naturally cooled to obtain the Ti-based high-entropy amorphous-dendritic crystal composite material Ti20Zr20Hf20Nb10Cu10Be20。
2. The method for preparing a Ti-based high-entropy amorphous-dendritic crystal composite material according to claim 1, wherein the purity of each of the simple elements Ti, Zr, Hf, Nb, Cu and Be is greater than or equal to 99.9%.
3. The method of claim 1, wherein in step S2, the first intermediate alloy, the second intermediate alloy and Ti are prepared by melting20Zr20Hf20Nb10Cu10Be20In the process, after the sample is completely melted and cooled, turning the sample over, repeating the first melting process, and performing second melting for 2-3 timesAnd min, wherein the repeated smelting is performed for 3-4 times.
4. The method for preparing the Ti-based high-entropy amorphous-dendritic crystal composite material according to claim 1, wherein in S2, the smelting time of the first intermediate alloy and the second intermediate alloy is 8-10 min, and the smelting current is 120-150A.
5. The method of claim 1, wherein in S2, Ti is added to the Ti-based high-entropy amorphous-dendritic crystal composite material20Zr20Hf20Nb10Cu10Be20The smelting time is 8-10 min, and the smelting current is 120-150A.
6. The method for preparing a Ti-based high-entropy amorphous-dendritic crystal composite material according to claim 1, wherein in S3, the natural cooling time is 15-18 min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811184433.1A CN109266946B (en) | 2018-10-11 | 2018-10-11 | Preparation method of Ti-based high-entropy amorphous-dendritic crystal composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811184433.1A CN109266946B (en) | 2018-10-11 | 2018-10-11 | Preparation method of Ti-based high-entropy amorphous-dendritic crystal composite material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109266946A CN109266946A (en) | 2019-01-25 |
| CN109266946B true CN109266946B (en) | 2020-08-14 |
Family
ID=65195640
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811184433.1A Expired - Fee Related CN109266946B (en) | 2018-10-11 | 2018-10-11 | Preparation method of Ti-based high-entropy amorphous-dendritic crystal composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109266946B (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109881076B (en) * | 2019-03-12 | 2021-06-08 | 西北工业大学 | Wear-resistant amorphous-dendritic crystal composite material and preparation method thereof |
| WO2020223162A1 (en) * | 2019-04-30 | 2020-11-05 | Oregon State University | Cu-based bulk metallic glasses in the cu-zr-hf-al and related systems |
| CN114214574A (en) * | 2021-11-05 | 2022-03-22 | 中国科学院金属研究所 | High-entropy metal glass composite material and preparation method and application thereof |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106756637B (en) * | 2016-12-06 | 2018-06-19 | 太原理工大学 | A kind of high entropy bulk metallic glass matrix composite and preparation method thereof |
-
2018
- 2018-10-11 CN CN201811184433.1A patent/CN109266946B/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| CN109266946A (en) | 2019-01-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109207829B (en) | High-entropy alloy and multicomponent carbide cocrystallizing type composite material and its in-situ preparation method | |
| CN109266946B (en) | Preparation method of Ti-based high-entropy amorphous-dendritic crystal composite material | |
| CN108998715A (en) | Infusibility high entropy alloy material and preparation method thereof with large plastometric set ability | |
| CN110819873B (en) | High Nb-TiAl alloy added with nano yttrium oxide and preparation method thereof | |
| CN113667875B (en) | MoNbTaTiVSix high-entropy alloy and preparation method thereof | |
| CN110396650B (en) | Preparation method of zirconium-based bulk amorphous alloy | |
| CN114457270A (en) | L12Medium-entropy alloy with particles strongly plasticized and preparation method thereof | |
| CN110669977A (en) | Light super-tough high-strength NbTiVAlxZry as-cast high-entropy alloy | |
| CN113373366A (en) | Multi-element refractory high-entropy alloy and preparation method thereof | |
| CN113621861B (en) | MoNbTaTiVCrxHigh-entropy alloy and preparation method thereof | |
| CN114535478A (en) | Rotary die forging preparation method of ultralight high-strength magnesium-lithium alloy | |
| CN113652592B (en) | TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain and preparation method thereof | |
| CN114774752A (en) | High-strength high-toughness TiZrNbMoV refractory high-entropy alloy and preparation method thereof | |
| CN111394665B (en) | TiCuZrPdFe amorphous composite material and preparation method thereof | |
| CN115404385B (en) | Refractory high-entropy alloy with excellent room-temperature tensile ductility and preparation method thereof | |
| CN107937840B (en) | A kind of titanium-aluminium alloy composite material and preparation method | |
| CN112322935B (en) | Titanium-tantalum alloy plate with negative thermal expansion characteristic and preparation method thereof | |
| CN110205566B (en) | Method for improving strength of phase-change Ti-based amorphous composite material by adding Al | |
| CN108265238B (en) | Zirconium-based metallic glass endogenetic composite material and tissue thinning method thereof | |
| CN111500958B (en) | Method for driving amorphous matrix structure to recover and improve mechanical property of amorphous endogenetic composite material through shape memory effect | |
| CN116445763B (en) | Titanium aluminum niobium alloy with room temperature plasticity and preparation method thereof | |
| CN116623107B (en) | Zr-based bulk amorphous alloy with excellent compression plasticity and preparation method thereof | |
| CN116445788A (en) | Refractory multicomponent alloy and preparation method thereof | |
| CN112899517B (en) | Method for improving thermal deformation performance of titanium-based composite material | |
| Zhang et al. | Deformation microstructure of Nb-modified TiAl intermetallics Ti54A16Nb at ambient temperature |
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 | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20200814 |