CN116144968A - Ti with excellent room temperature plasticity 2 Preparation method of AlNb-based composite material - Google Patents
Ti with excellent room temperature plasticity 2 Preparation method of AlNb-based composite material Download PDFInfo
- Publication number
- CN116144968A CN116144968A CN202310150011.7A CN202310150011A CN116144968A CN 116144968 A CN116144968 A CN 116144968A CN 202310150011 A CN202310150011 A CN 202310150011A CN 116144968 A CN116144968 A CN 116144968A
- Authority
- CN
- China
- Prior art keywords
- alnb
- composite material
- based composite
- powder
- room temperature
- 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.)
- Granted
Links
- 239000002131 composite material Substances 0.000 title claims abstract description 50
- 238000002360 preparation method Methods 0.000 title claims abstract description 21
- 239000000843 powder Substances 0.000 claims abstract description 58
- 238000005245 sintering Methods 0.000 claims abstract description 38
- 238000000498 ball milling Methods 0.000 claims abstract description 30
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 17
- 239000000956 alloy Substances 0.000 claims abstract description 17
- 238000000034 method Methods 0.000 claims abstract description 16
- 230000003014 reinforcing effect Effects 0.000 claims abstract description 13
- 239000011159 matrix material Substances 0.000 claims abstract description 10
- 238000002156 mixing Methods 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- 229910002804 graphite Inorganic materials 0.000 claims description 8
- 239000010439 graphite Substances 0.000 claims description 8
- 239000011812 mixed powder Substances 0.000 claims description 8
- 238000007731 hot pressing Methods 0.000 claims description 6
- 239000000463 material Substances 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 4
- 230000003647 oxidation Effects 0.000 claims description 4
- 238000007254 oxidation reaction Methods 0.000 claims description 4
- 238000004806 packaging method and process Methods 0.000 claims description 4
- 239000002994 raw material Substances 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 2
- 230000002159 abnormal effect Effects 0.000 claims 1
- 239000010936 titanium Substances 0.000 abstract description 62
- 239000013078 crystal Substances 0.000 abstract description 9
- 238000011065 in-situ storage Methods 0.000 abstract description 8
- 238000006243 chemical reaction Methods 0.000 abstract description 6
- 238000003723 Smelting Methods 0.000 abstract description 5
- 239000002245 particle Substances 0.000 abstract description 5
- 238000005204 segregation Methods 0.000 abstract description 4
- 229910052719 titanium Inorganic materials 0.000 abstract description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract description 3
- 238000005516 engineering process Methods 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 13
- 238000001878 scanning electron micrograph Methods 0.000 description 8
- 238000009835 boiling Methods 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000005266 casting Methods 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000011156 metal matrix composite Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 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
- C22C14/00—Alloys based on titanium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1039—Sintering only by reaction
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Ceramic Products (AREA)
Abstract
Ti with excellent room temperature plasticity 2 A preparation method of AlNb-based composite material relates to Ti 2 A preparation method of an AlNb-based composite material. The invention aims to solve the technical problems that the discontinuous reinforced titanium-based composite material has poor reinforcing effect and high room temperature brittleness, and the traditional smelting technology has serious segregation and poor tissue uniformity. The invention adopts a low-energy ball milling method to lead TiB to be 2 The powder is uniformly adhered to Ti 2 Selecting reasonable ball milling parameters on the surfaces of AlNb prealloyed powder particles to ensure Ti 2 The AlNb powder keeps good sphericity in the powder mixing process; then in-situ autogenous reaction promotes TiBw to grow near the surface of the spherical matrix alloy in the hot-press sintering process, thus not only restricting the further growth of crystal grains, but also obtaining a uniform network structure, wherein the network structure can inhibit the growth of the crystal grains in the sintering process, thus obtaining Ti with excellent room temperature performance 2 An AlNb-based composite material.
Description
Technical Field
The invention relates to a Ti 2 A preparation method of an AlNb-based composite material.
Background
The new generation of aircrafts has higher thrust-weight ratio to engines, and meets the requirement of long-time high-temperature environment service, while Ti 2 The AlNb alloy has excellent high-temperature performance, higher specific strength and good room-temperature plasticity, and is mainly applied to high-temperature parts on an aerospace aircraft engine. But as an intermetallic compound, ti 2 The plasticity of the AlNb alloy cannot meet the requirements of the new generation of aircrafts, which also limits Ti 2 The AlNb alloy is widely applied to the field of aerospace and automobile engines. To further improve Ti 2 The room temperature property of the AlNb alloy can be utilized to obtain Ti with excellent properties by introducing a ceramic reinforcing phase into the matrix alloy by an in-situ autogenous or externally-added method by utilizing the characteristics of high strength and high rigidity of the ceramic material 2 An AlNb-based composite material.
The discontinuous reinforced metal matrix composite material has the advantages of higher specific strength, higher specific rigidity, higher heat resistance limit and the like compared with the matrix alloy. Japanese scholars Emura et al were first presented in Ti 2 Introducing in-situ authigenic boride reinforcing phase into AlNb alloy to prepare discontinuous reinforcing Ti 2 An AlNb-based composite material. The reinforcing phase has very good reinforcing effect and remarkably improves Ti 2 High temperature mechanical properties of the AlNb-based composite material; enhancement of Ti with boride 2 During the research process of the AlNb-based composite material, cowen et al of American scholars found that the reduction of the size of the reinforcing phase and the improvement of the compactness of the material are key to the improvement of the comprehensive mechanical property of the composite material. However, according to the prior art, in Ti 2 High introduction into AlNb alloyThe strength of the reinforcing phase can be greatly increased, and the plasticity is greatly reduced.
Ti prepared by traditional smelting method 2 As the difference of melting boiling points of Ti, al and Nb is larger, the boiling point of Al element is far lower than that of Nb element, and Ti is melted and cast in the smelting and casting process 2 The phenomenon of serious volatilization of Al element (the mass fraction of volatilization burning loss reaches 5% -10%) and serious segregation of Nb element occur in the AlNb-based alloy, so that indexes such as the accuracy of final alloy components, the uniformity of tissues, the compactness of alloy cast ingots and the like are difficult to ensure. Compared with the traditional smelting method, the powder metallurgy method can obtain a uniform microstructure without segregation phenomenon.
Disclosure of Invention
The invention aims to solve the technical problems of poor reinforcing effect and high room temperature brittleness of a discontinuous reinforced titanium-based composite material, serious segregation and poor tissue uniformity of the traditional smelting technology, and provides Ti with excellent room temperature plasticity 2 A preparation method of an AlNb-based composite material.
Ti having excellent room temperature plasticity of the present invention 2 The preparation method of the AlNb-based composite material comprises the following steps:
with TiB 2 The granular powder is used as reinforcing phase and takes Ti as raw material 2 The AlNb prealloy powder is used as a matrix alloy to make TiB 2 Particulate powder and Ti 2 Pouring AlNb prealloy powder into a ball milling tank together for ball milling and mixing, packaging the mixed powder into a graphite mold after ball milling, then placing the graphite mold into a vacuum hot-pressing sintering furnace, vacuumizing to avoid powder oxidation pollution caused by contact with air, sintering for 1-5 h at 1250-1330 ℃ and sintering pressure of 30-45 MPa, and cooling along with the furnace after sintering to obtain TiBw/Ti 2 An AlNb-based composite material;
the TiB is 2 The mass of the granular powder is TiB 2 Particulate powder and Ti 2 0.1 to 0.2 percent of the total mass of the AlNb prealloy powder.
The invention adopts the preparation method of low-energy ball milling and vacuum hot-pressing sintering, and combines with the in-situ autogenous reaction technologyPreparing TiBw/Ti with excellent room temperature plasticity 2 An AlNb-based composite material. Ti and TiB 2 The equation of in situ autogenous reaction is Ti+TiB 2 =2tib, first using low energy ball milling method to make TiB 2 The powder is uniformly adhered to Ti 2 On the surface of AlNb prealloyed powder particles, reasonable ball milling parameters are selected simultaneously to ensure Ti 2 The AlNb powder is not deformed in the powder mixing process, and good sphericity is maintained; then in-situ self-generating reaction promotes TiBw (TiB whisker) to grow near the surface of the spherical matrix alloy in the hot-press sintering process, so that further growth of crystal grains can be limited, a uniform three-dimensional reticular structure is obtained, the reticular structure has a very good grain boundary strengthening effect, and the TiBw strengthening phase of in-situ self-generating reaction can be connected with adjacent titanium crystal grains like pins to coordinate integral deformation of the material, and can effectively improve the plasticity and toughness of the composite material; the mesh structure can inhibit the growth of crystal grains in the sintering process; the three-dimensional network structure has the characteristic of introducing ceramic phase into the grain boundary, can achieve the aim of improving the room temperature strong plasticity of the composite material, and can obtain TiBw/Ti with excellent room temperature performance 2 The AlNb-based composite material has tensile strength of more than 1050MPa and elongation of more than 12%.
The invention is based on the design principle of damage tolerance, and improves Ti as much as possible while maintaining the same strength 2 Room temperature plasticity of AlNb-based composite material to obtain Ti with excellent strong plasticity matching 2 An AlNb-based composite material.
Drawings
FIG. 1 is a low magnification SEM image of a mixed powder (before sintering) after testing a ball mill;
FIG. 2 is a high magnification SEM image of the mixed powder (before sintering) after testing a ball mill;
FIG. 3 shows TiBw/Ti obtained after completion of sintering 2 A low magnification SEM image of the ainb-based composite;
FIG. 4 shows TiBw/Ti obtained after completion of sintering 2 High magnification SEM image of AlNb-based composite material;
FIG. 5 shows TiBw/Ti obtained after completion of sintering 2 Room temperature tensile stress-strain curve of an ainb-based composite.
Detailed Description
The first embodiment is as follows: the present embodiment is a Ti having excellent room temperature plasticity 2 The preparation method of the AlNb-based composite material comprises the following steps:
with TiB 2 The granular powder is used as reinforcing phase and takes Ti as raw material 2 The AlNb prealloy powder is used as a matrix alloy to make TiB 2 Particulate powder and Ti 2 Pouring AlNb prealloy powder into a ball milling tank together for ball milling and mixing, packaging the mixed powder into a graphite mold after ball milling, then placing the graphite mold into a vacuum hot-pressing sintering furnace, vacuumizing to avoid powder oxidation pollution caused by contact with air, sintering for 1-5 h at 1250-1330 ℃ and sintering pressure of 30-45 MPa, and cooling along with the furnace after sintering to obtain TiBw/Ti 2 An AlNb-based composite material;
the TiB is 2 The mass of the granular powder is TiB 2 Particulate powder and Ti 2 0.1 to 0.2 percent of the total mass of the AlNb prealloy powder.
The second embodiment is as follows: the first difference between this embodiment and the specific embodiment is that: the TiB is 2 The purity of the granular powder is more than 99.5%. The other is the same as in the first embodiment.
And a third specific embodiment: this embodiment differs from the first or second embodiment in that: the ball milling is carried out on a planetary ball mill. The other embodiments are the same as those of the first or second embodiment.
The specific embodiment IV is as follows: this embodiment differs from one of the first to third embodiments in that: the ball milling rotation speed is 200 rpm-240 rpm. The other is the same as in one of the first to third embodiments.
Fifth embodiment: the fourth difference between this embodiment and the third embodiment is that: the mass ratio of the ball materials is (2-4) 1 during ball milling. The other is the same as in the fourth embodiment.
Specific embodiment six: the fifth difference between this embodiment and the third embodiment is that: the ball milling time is 3-6 h. The other is the same as in the fifth embodiment.
Seventh embodiment: the sixth embodiment differs from the first embodiment in that: the TiB is 2 The mass of the granular powder is TiB 2 Particulate powder and Ti 2 0.125% of the sum of the mass of the AlNb prealloyed powder. The other is the same as in the sixth embodiment.
Eighth embodiment: the present embodiment is different from the seventh embodiment in that: vacuumizing to a vacuum degree of 10 - 2 Pa. The other is the same as in the seventh embodiment.
Detailed description nine: this embodiment differs from the eighth embodiment in that: the sintering temperature is 1300 ℃, and the heat preservation time is 2 hours. The other is the same as in the eighth embodiment.
Detailed description ten: this embodiment differs from the ninth embodiment in that: the sintering pressure was 35MPa. The other steps are the same as those in the embodiment nine.
The invention was verified with the following test:
test one: the test is Ti with excellent room temperature plasticity 2 The preparation method of the AlNb-based composite material comprises the following steps:
with TiB 2 The granular powder is used as reinforcing phase and takes Ti as raw material 2 The AlNb prealloy powder is used as a matrix alloy to make TiB 2 Particulate powder and Ti 2 Pouring AlNb prealloy powder into a ball milling tank together for ball milling and mixing, packaging the mixed powder into a graphite mold after ball milling, then placing the graphite mold into a vacuum hot-pressing sintering furnace, vacuumizing to avoid powder oxidation pollution caused by contact with air, sintering for 2h under the conditions of 1300 ℃ and 35MPa of sintering temperature, and cooling along with the furnace after sintering to obtain TiBw/Ti 2 An AlNb-based composite material;
the TiB is 2 The purity of the granular powder is more than 99.5%, and the average grain diameter is less than or equal to 10 mu m;
said Ti is 2 The grain diameter of the AlNb prealloy powder ranges from 75 mu m to 125 mu m;
the TiB is 2 The mass of the granular powder is TiB 2 Particulate powderTi 2 0.125% of the sum of the mass of the AlNb prealloyed powder;
the ball milling rotating speed is 220rpm, the ball milling time is 5h, and the mass ratio of the ball materials is 3:1.
FIG. 1 is a low-magnification SEM image of the mixed powder after ball milling (before sintering), and FIG. 2 is a high-magnification SEM image of the mixed powder after ball milling (before sintering), from which TiB can be seen 2 The powder is uniformly adhered to Ti 2 On the AlNb prealloyed powder such that Ti 2 The surface of the AlNb prealloy powder is not smooth, and the periphery of the AlNb prealloy powder is free from scattered powder particles, most of Ti 2 The morphology of the AlNb powder particles is not changed in the process of low-energy powder mixing, and the near-spherical morphology is still maintained, so that an ideal mixing effect is achieved.
FIG. 3 shows TiBw/Ti obtained after completion of sintering 2 FIG. 4 is a low magnification SEM image of an AlNb-based composite material, showing TiBw/Ti obtained after completion of sintering 2 The high-magnification SEM image of the AlNb-based composite material can be seen from the image that the preparation method of low-energy ball milling and vacuum hot-pressing sintering is adopted to realize the design of a three-dimensional quasi-continuous network structure of the composite material, so that honeycomb arrangement is formed; secondly, in-situ autogenous reaction promotes TiBw to grow near the surface of the spherical matrix alloy in the hot-press sintering process, thus not only restricting further growth of crystal grains, but also promoting TiBw at the crystal boundary to grow from the crystal boundary to the inside of the crystal, connecting adjacent matrix particles like pins, coordinating deformation of each part, thereby achieving the purpose of improving TiBw/Ti 2 The AlNb-based composite material has strong plasticity at room temperature.
FIG. 5 shows TiBw/Ti obtained after completion of sintering 2 Room temperature stretching stress-strain curve of AlNb base composite material, room temperature stretching experiment is carried out on electronic universal tester equipment, tiBw/Ti is obtained through experiment 2 The tensile strength of the AlNb-based composite material is 1055MPa, the plasticity is 14.7%, and the Ti is realized 2 And the room-temperature tensile strength and the plasticity of the AlNb-based composite material are comprehensively improved.
And (2) testing II: the first difference between this test and the test is: the TiB is 2 The mass of the granular powder is TiB 2 Particulate powder and Ti 2 AlNb presynthesis0.15% of the sum of the mass of the gold powder. The others are the same as in test one.
The obtained net structure TiBw/Ti 2 The room temperature tensile strength of the AlNb-based composite material is 1100MPa, and the elongation rate can reach 13.8%.
And (3) test III: the first difference between this test and the test is: sintering for 2h at 1330 ℃ and 45 MPa. The others are the same as in test one.
The obtained net structure TiBw/Ti 2 The room temperature tensile strength of the AlNb-based composite material is 1085MPa, and the elongation rate can reach 15.7%.
Claims (10)
1. Ti with excellent room temperature plasticity 2 A process for producing AlNb-based composite material characterized by having excellent room temperature plasticity of Ti 2 The preparation method of the AlNb-based composite material comprises the following steps:
with TiB 2 The granular powder is used as reinforcing phase and takes Ti as raw material 2 The AlNb prealloy powder is used as a matrix alloy to make TiB 2 Particulate powder and Ti 2 Pouring AlNb prealloy powder into a ball milling tank together for ball milling and mixing, packaging the mixed powder into a graphite mold after ball milling, then placing the graphite mold into a vacuum hot-pressing sintering furnace, vacuumizing to avoid powder oxidation pollution caused by contact with air, sintering for 1-5 h at 1250-1330 ℃ and sintering pressure of 30-45 MPa, and cooling along with the furnace after sintering to obtain TiBw/Ti 2 An AlNb-based composite material;
the TiB is 2 The mass of the granular powder is TiB 2 Particulate powder and Ti 2 0.1 to 0.2 percent of the total mass of the AlNb prealloy powder.
2. Ti having excellent room temperature plasticity according to claim 1 2 A preparation method of the AlNb-based composite material is characterized by comprising the following steps of 2 The purity of the granular powder is more than 99.5%.
3. A kind of excellent product according to claim 1Ti with plasticity at abnormal room temperature 2 The preparation method of the AlNb-based composite material is characterized in that the ball milling is carried out on a planetary ball mill.
4. Ti having excellent room temperature plasticity according to claim 1 2 The preparation method of the AlNb-based composite material is characterized in that the ball milling rotating speed is 200 rpm-240 rpm.
5. Ti having excellent room temperature plasticity according to claim 1 2 The preparation method of the AlNb-based composite material is characterized in that the mass ratio of the ball materials is (2-4): 1 during ball milling.
6. Ti having excellent room temperature plasticity according to claim 1 2 The preparation method of the AlNb-based composite material is characterized in that the ball milling time is 3-6 hours.
7. Ti having excellent room temperature plasticity according to claim 1 2 A preparation method of the AlNb-based composite material is characterized by comprising the following steps of 2 The mass of the granular powder is TiB 2 Particulate powder and Ti 2 0.125% of the sum of the mass of the AlNb prealloyed powder.
8. Ti having excellent room temperature plasticity according to claim 1 2 The preparation method of the AlNb-based composite material is characterized by vacuumizing to a vacuum degree of 10 -2 Pa。
9. Ti having excellent room temperature plasticity according to claim 1 2 The preparation method of the AlNb-based composite material is characterized in that the sintering temperature is 1300 ℃, and the heat preservation time is 2 hours.
10. Ti having excellent room temperature plasticity according to claim 1 2 The preparation method of the AlNb-based composite material is characterized in that the sintering pressure is 35MPa.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310150011.7A CN116144968B (en) | 2023-02-22 | 2023-02-22 | Ti with excellent room temperature plasticity2Preparation method of AlNb-based composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310150011.7A CN116144968B (en) | 2023-02-22 | 2023-02-22 | Ti with excellent room temperature plasticity2Preparation method of AlNb-based composite material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN116144968A true CN116144968A (en) | 2023-05-23 |
| CN116144968B CN116144968B (en) | 2024-04-26 |
Family
ID=86355990
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202310150011.7A Active CN116144968B (en) | 2023-02-22 | 2023-02-22 | Ti with excellent room temperature plasticity2Preparation method of AlNb-based composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN116144968B (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101333607A (en) * | 2008-07-31 | 2008-12-31 | 哈尔滨工业大学 | Process for preparing TiBw/Ti alloy-based composite material |
| CN109759665A (en) * | 2019-03-22 | 2019-05-17 | 中山大学 | A kind of ceramic/metal connector preparation method of the TiB whisker reinforcement with three-dimensional netted distribution |
| CN114150238A (en) * | 2021-11-26 | 2022-03-08 | 中国航发北京航空材料研究院 | Ti-Al-Nb-based composite material and preparation method thereof |
-
2023
- 2023-02-22 CN CN202310150011.7A patent/CN116144968B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101333607A (en) * | 2008-07-31 | 2008-12-31 | 哈尔滨工业大学 | Process for preparing TiBw/Ti alloy-based composite material |
| CN109759665A (en) * | 2019-03-22 | 2019-05-17 | 中山大学 | A kind of ceramic/metal connector preparation method of the TiB whisker reinforcement with three-dimensional netted distribution |
| CN114150238A (en) * | 2021-11-26 | 2022-03-08 | 中国航发北京航空材料研究院 | Ti-Al-Nb-based composite material and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN116144968B (en) | 2024-04-26 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110273092B (en) | CoCrNi particle reinforced magnesium-based composite material and preparation method thereof | |
| CN112011702A (en) | Method for preparing nano-phase reinforced nickel-based high-temperature alloy by adopting micro-ceramic particles | |
| CN109338172A (en) | A kind of 2024 aluminum matrix composites and preparation method thereof of high-entropy alloy enhancing | |
| CN112267038B (en) | Preparation method of BN nanosheet/1060 Al composite material | |
| Teng et al. | Effects of processing temperatures on FGH4097 superalloy fabricated by hot isostatic pressing: microstructure evolution, mechanical properties and fracture mechanism | |
| CN112695262B (en) | Titanium alloy-based composite material with micro-structure and preparation method thereof | |
| CN108097962B (en) | Preparation method of Nb-toughened titanium-aluminum-based alloy composite material | |
| CN114645180B (en) | Double-phase reinforced aluminum alloy and preparation method thereof | |
| CN114150238B (en) | Ti-Al-Nb-based composite material and preparation method thereof | |
| CN113862540A (en) | MAX phase added molybdenum alloy and preparation method thereof | |
| CN114799155A (en) | Preparation method of ceramic particle reinforced refractory high-entropy alloy | |
| CN113430417A (en) | High-performance titanium alloy added with rare earth oxide and preparation method thereof | |
| CN112775427B (en) | Preparation method of high-density near-net-shape titanium alloy | |
| CN116144968B (en) | Ti with excellent room temperature plasticity2Preparation method of AlNb-based composite material | |
| CN112647029B (en) | TiB enhanced TMCs with three-dimensional pellet composite structure and preparation method thereof | |
| CN114959358B (en) | Titanium-aluminum-based intermetallic compound material and preparation method thereof | |
| CN114643359B (en) | Preparation method of high-strength powder metallurgy Ti-W alloy bar | |
| CN113134626A (en) | Additive manufacturing method of titanium alloy hydrogen pump impeller for ultralow temperature environment | |
| CN111485141A (en) | SiC particle reinforced aluminum titanium matrix composite material and preparation method thereof | |
| CN116254433B (en) | Preparation method of low-density high-strength high-toughness AlMoNbTaTiZr refractory high-entropy alloy | |
| CN113774265B (en) | High-entropy intermetallic compound with high strength and wide-temperature-range wear-resistant characteristics | |
| CN115772615B (en) | Three-dimensional pellet micro-configuration high-temperature titanium alloy-based composite material and preparation method thereof | |
| CN116005084B (en) | W particle-TiB whisker hybridization reinforced titanium-based composite material and preparation method thereof | |
| CN111020299B (en) | Co-Al-W-TiO2 alloy bar and preparation method thereof | |
| CN115921874A (en) | TiAl-based composite material with two-stage reinforced three-dimensional network structure and preparation method thereof |
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 |