CN115650729A - Di-titanium-vanadium-aluminum-carbon ceramic powder material and preparation method and application thereof - Google Patents
Di-titanium-vanadium-aluminum-carbon ceramic powder material and preparation method and application thereof Download PDFInfo
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Abstract
The invention discloses a di-titanium vanadium aluminum carbon ceramic powder material which is prepared by the following method: (1) Mixing titanium powder, titanium carbide powder and aluminum vanadium alloy powder according to a molar ratio of Ti (Al + V) to C = 2:1-1.5 to obtain a mixture, taking ethanol as a wet grinding agent, fully grinding the mixture, and drying the mixture in vacuum to obtain mixed powder; (2) Putting the mixed powder into a grinding tool, and carrying out hot-pressing sintering under the protection of argon to obtain Ti 2 (AlV) bulk C; (3) Mixing Ti 2 Polishing the surface of the (AlV) C block, grinding and sieving to obtain Ti 2 (AlV) C powder. The di-titanium vanadium aluminum carbon ceramic powder material is applied to the preparation of fusion reactor structural materials, vanadium alloy material reinforcement or corrosion-resistant and wear-resistant coatings on the surfaces of fission reactor components. The invention utilizes low melting point aluminum vanadiumThe intermediate alloy realizes the appearance of V element at the MAX phase A position, and Ti with uniform structure is prepared 2 (AlV) C has important significance for expanding MAX phase material family and promoting MAX phase engineering application.
Description
Technical Field
The invention relates to a di-titanium vanadium aluminum carbon ceramic powder material and a preparation method and application thereof, belonging to the field of ceramic material preparation.
Background
MAX phase is a general name of a ternary compound with a microscopic layered structure, and the chemical formula can be expressed as M n+ 1 AX n M is an early transition metal element of IIIB, IVB, VB or VIB groups, A mainly represents an element of main groups IIIA and IVA, X represents carbon or nitrogen, and n = 1-3. Due to the unique crystal structure and bonding mode of the MAX phase, the MAX phase has the excellent properties of metal and ceramic, such as high elastic modulus, low density, good thermal stability and radiation resistance, excellent heat conduction and electric conduction, and lower hardness, and can be machined. Has wide application prospect in the fields of nuclear energy structure materials, aerospace thermal structure materials, high-temperature electrodes, friction and abrasion and the like.
Ti 2 AlC is currently one of the typical representatives of 211 being the MAX phase. At Ti 2 Ti-C bonds in the AlC ceramic are strong covalent bonds, and Ti and Al planes are weak bonds similar to graphite layers. Relevant researches show that the material has excellent accident fault tolerance capability, can be used as a nano reinforced phase of a base material, and is expected to be applied to national major projects such as a nuclear fuel cladding coating of a pressurized water reactor, a thorium-based molten salt reactor, an accelerator-driven new energy system and the like.
However, ti 2 The poor molten sulfate corrosion resistance of AlC and the problem that long-life radioactive nuclides can be generated under the irradiation condition of high-energy neutrons due to the high Al content limit the application of the aluminum alloy in the environments of fusion reactors and the like. The quaternary solid-solution MAX phase is developed, and Ti is reduced 2 The Al element content in AlC becomes Ti 2 New direction of AlC optimization. In 2018, huang Qing et al synthesized Ti in high-temperature Lewis molten salt by the strategy of A-site element replacement 2 (Al 0.1 Cu 0.9 ) C, the possibility of the presence of a layer of a late transition metal in the MAX phase, and related patent applications, such asWO 2020010783A (a MAX phase material, method of making and use thereof), CN 108793166A (subgroup metal composite MXenes, method of making and use thereof).
Disclosure of Invention
Aiming at the prior art, the invention provides titanium-vanadium-aluminum-carbon [ Ti ] 2 (VAl)C]Ceramic powder material, and a preparation method and application thereof. Ti of the invention 2 (AlV) C is a new way for quaternary MAX phase development, can reduce the content of Al element in A position, and simultaneously V element is the main element of vanadium alloy, ti and the like in high-energy neutron reactor candidate structural material such as fusion reactor 2 The (AlV) C is expected to be used as a strengthening phase of the vanadium alloy to further improve the stability of the vanadium alloy under the conditions of high temperature and strong irradiation, and has wide application prospect. The Ti is prepared by using titanium powder, titanium carbide powder and aluminum-vanadium intermediate alloy powder as raw materials and performing hot-pressing sintering 2 (AlV) C material, realizing the existence of a monoatomic A layer of late transition group metal V in MAX phase.
The invention is realized by the following technical scheme:
a di-titanium vanadium aluminum carbon ceramic powder material is prepared by the following method:
(1) Mixing titanium powder, titanium carbide powder and aluminum-vanadium alloy powder according to the molar ratio of Ti (Al + V) to C = 2:1-1.5 of 1, wet-grinding for 10-15 h by using ethanol as a wet grinding agent, fully grinding and then drying in vacuum to obtain mixed powder;
(2) Putting the mixed powder into a grinding tool, and carrying out hot-pressing sintering under the protection of argon atmosphere, wherein the sintering pressure is 20-30 MPa, the sintering temperature is 1100-1250 ℃, and the heat preservation and pressure maintaining time is 2-3 h to obtain Ti 2 (AlV) bulk C;
(3) Mixing Ti 2 Polishing the surface of the (AlV) C block, grinding and sieving to obtain Ti 2 (AlV) C powder.
Further, in the step (1), the mass percent of vanadium in the aluminum-vanadium alloy powder is 3-40%. The aluminum-vanadium alloy is an alloy consisting of aluminum and vanadium and prepared by a conventional technical means (the principle of the invention is that the aluminum-vanadium alloy is used as an intermediate alloy to directly occupy the position A in a MAX phase, so the aluminum-vanadium alloy is not influenced by the composition range, the preparation process and the like of the aluminum-vanadium alloy in principle).
Further, in the step (1), the average particle sizes of the titanium powder, the titanium carbide powder and the aluminum-vanadium alloy powder are all 300-500 meshes.
Further, in the step (1), the drying temperature of vacuum drying is 150-200 ℃, and the drying time is 4-6 h.
Further, in the step (2), the sintering temperature is increased to 200 ℃ and the temperature increase speed is 3-5 ℃/min, so as to discharge oxygen existing in the powder.
Ti of the invention 2 (AlV) C is a new way for the development of quaternary MAX phase, and enriches the solid solution MAX phase material system. Ti 2 The (AlV) C can be used for fusion reactor structural materials, vanadium alloy material reinforcement, corrosion-resistant and wear-resistant coatings on the surfaces of fission reactor components and the like.
Ti of the invention 2 (AlV) C, not only reduces the content of Al element in A position, but also V element is the main element of vanadium alloy of high-energy neutron reactor candidate structure material such as fusion reactor, ti 2 The (AlV) C is expected to be used as a strengthening phase of the vanadium alloy to further improve the stability of the vanadium alloy under the conditions of high temperature and strong irradiation, and has wide application prospect.
The invention takes titanium powder, titanium carbide powder and aluminum-vanadium alloy powder as raw materials, because the V alloy is a VB group of early transition group element, the performance is similar to Ti (the atomic number of Ti is 22, vanadium is 23), based on the general knowledge of MAX phase alloy powder at present, the V alloy should be at the position of Ti atom by hot pressing sintering of the MAX phase alloy powder of Ti-V-Al-C system, namely (TiV) 2 AlC(Chun-liang Yeh,Wen-jung Yang.Combustion Synthesis of(Ti,V) 2 AlC Solid Solutions[C]Proceedings of 2014 2nd International Conference on Manufacturing 2014, 2014 30-34. The present invention also considers that substitution of V for Al atoms cannot be achieved after sintering before carrying out a specific sintering experiment, but surprisingly and unexpectedly found after the experiment: the sintered powder is Ti 2 The AlC phase and the Ti (Al + V) have the ratio close to 2:1, and the Ti is successfully prepared 2 (AlV) C, realizing the substitution of Al atoms by V.
Ti of the invention 2 (AlV) C belongs to the A-site solid-solution MAX phase. The main method for preparing the A-site solid-solution MAX phase is a molten salt method proposed by Nippon institute of Chinese academy Huang Qing. However, materials such as iodized salts and chloride salts containing V have low melting points and are unstable and are easily decomposed at high temperature, which brings difficulties and challenges for realizing solid solution and replacement of V at a position element by a molten salt method. On the basis of analyzing MAX phase structure (Ti-C is a strong bond, and Al and Ti-C are combined into a molecular bond), the Al powder is replaced by AlV solid solution alloy, and Ti is successfully prepared 2 (AlV)C。
The invention realizes the appearance of V element at the MAX phase A position by utilizing the low-melting-point aluminum-vanadium solid solution alloy, and prepares Ti with uniform structure 2 (AlV) C has important significance for expanding MAX phase material family and promoting MAX phase engineering application.
The various terms and phrases used herein have the ordinary meaning as is well known to those skilled in the art.
Drawings
FIG. 1: XRD spectrogram of the alloy powder.
FIG. 2: the appearance of the alloy powder is shown schematically.
FIG. 3: EDS composition analysis schematic diagram of alloy powder.
Detailed Description
The present invention will be further described with reference to the following examples. However, the scope of the present invention is not limited to the following examples. It will be understood by those skilled in the art that various changes and modifications may be made to the invention without departing from the spirit and scope of the invention.
The instruments, reagents and materials used in the following examples are conventional instruments, reagents and materials known in the art and are commercially available. Unless otherwise specified, the experimental methods and detection methods described in the following examples are conventional experimental methods and detection methods known in the art.
Example 1 preparation of di-titanium vanadium aluminum carbon ceramic powder Material
The method comprises the following steps:
(1) Taking titanium powder, titanium carbide powder and aluminum-vanadium alloy powder (Al + V) with average particle size of 300 meshes according to the molar ratio of Ti (Al + V) to C =2 3 V, the mass percent of V is 38.6%, and the mass percent of Al is 61.4%; the product name of the high-purity aluminum-vanadium alloy powder (68g, 85g and 47g of titanium powder, titanium carbide powder and aluminum-vanadium alloy powder respectively) purchased from Hebei surpass metal alloy materials Co.
(2) And (3) performing ball milling for 10h by using ethanol as a wet grinding agent, fully grinding and mixing, and then performing vacuum drying at the drying temperature of 150 ℃ for 6h to obtain mixed powder.
(3) And (3) putting the mixed powder obtained in the step (2) into a graphite die for sintering, wherein the sintering pressure is 20MPa, the sintering temperature is 1250 ℃, the heat preservation and pressure maintaining time is 3h, and hot-pressing sintering is carried out under the protection of argon. The temperature is raised to 3 ℃/min before 200 ℃; the temperature rising speed is 60 ℃/min at the temperature of 200-1250 ℃; keeping the temperature, and then cooling the mixture along with the furnace in an argon environment to obtain Ti 2 (AlV) C block 180 g.
(4) Ti obtained in the step (3) 2 The (AlV) C block was surface polished to a solid portion, then cleaned with ultrasonic waves in deionized water, and dried in a dry box. Then grinding by using an agate mortar, and sieving by using a 500-mesh sieve to prepare MAX phase powder.
(5) XRD analysis is carried out on the alloy powder obtained in the step (4), and as shown in figures 1 and 2, the alloy powder mainly contains Ti 2 (AlV) a C phase and a minor amount of a TiC phase; EDS component analysis was performed on the alloy powder, and as shown in FIG. 3, the atomic percentage of Ti (Al + V) was 38.89: (15.74 + 6.38) close to 2:1, so that the prepared powder is Ti 2 (AlV) C alloy powder.
Example 2 preparation of di-titanium vanadium aluminum carbon ceramic powder Material
The method comprises the following steps:
(1) According to the molar ratio of Ti (Al + V) to C =2, 1.5.
(2) Alcohol is used as a wet grinding agent, ball milling is carried out for 20 hours, vacuum drying is carried out after full grinding and mixing, the drying temperature is 200 ℃, and the drying time is 10 hours.
(3) And (3) putting the mixed powder obtained in the step (2) into a graphite die for sintering, wherein the sintering pressure is 30MPa, the sintering temperature is 1150 ℃, the heat preservation and pressure maintaining time is 2h, and hot-pressing sintering is carried out under the protection of argon. The temperature is raised to 5 ℃/min before 200 ℃; the temperature rising speed is 60 ℃/min at the temperature of 200-1250 ℃; and cooling along with the furnace in an argon environment after heat preservation. To obtain Ti 2 (AlV) C block 175 g.
(4) Ti obtained in the step (3) 2 The (AlV) C block was surface polished to a solid portion, then cleaned with ultrasonic waves in deionized water, and dried in a dry box. Then grinding by using an agate mortar, and sieving by using a 500-mesh sieve to prepare the Ti 2 (AlV) C powder.
(5) XRD analysis is carried out on the alloy powder obtained in the step (4), and the alloy powder is mainly Ti 2 (AlV) a C phase and a minor amount of a TiC phase; EDS analysis of the alloy powder shows that the atomic percentage of Ti (Al + V) is 36.73 (16.71 + 1.21) and is about 2:1, so that the powder prepared is Ti 2 (AlV) C alloy powder.
The above examples are provided to those of ordinary skill in the art to fully disclose and describe how to make and use the claimed embodiments, and are not intended to limit the scope of the disclosure herein. Modifications apparent to those skilled in the art are intended to be within the scope of the appended claims.
Claims (8)
1. The preparation method of the di-titanium vanadium aluminum carbon ceramic powder material is characterized by comprising the following steps:
(1) Mixing titanium powder, titanium carbide powder and aluminum-vanadium alloy powder according to a molar ratio of Ti (Al + V) to C = 2:1-1.5 of 1, taking ethanol as a wet grinding agent, fully grinding, and then drying in vacuum to obtain mixed powder;
(2) Putting the mixed powder into a grinding tool, and carrying out hot-pressing sintering under the protection of argon atmosphereSintering at 20-30 MPa and 1100-1250 deg.c for 2-3 hr to obtain Ti 2 (AlV) bulk C;
(3) Mixing Ti 2 Polishing the surface of the (AlV) C block, grinding and sieving to obtain Ti 2 (AlV) C powder.
2. The method for preparing a di-titanium vanadium aluminum carbon ceramic powder material according to claim 1, which is characterized by comprising the following steps: in the step (1), the mass percent of vanadium in the aluminum vanadium alloy powder is 3-40%.
3. The method for preparing a di-titanium vanadium aluminum carbon ceramic powder material according to claim 1, which is characterized by comprising the following steps: in the step (1), the average particle sizes of the titanium powder, the titanium carbide powder and the aluminum-vanadium alloy powder are all 300-500 meshes.
4. The method for preparing a di-titanium vanadium aluminum carbon ceramic powder material according to claim 1, which is characterized by comprising the following steps: in the step (1), the wet milling time is 10-15 h.
5. The method for preparing a di-titanium vanadium aluminum carbon ceramic powder material according to claim 1, which is characterized by comprising the following steps: in the step (1), the drying temperature of vacuum drying is 150-200 ℃, and the drying time is 4-6 h.
6. The method for preparing the dititanoaluminate carbon ceramic powder material as claimed in claim 1, wherein the method comprises the following steps: in the step (2), the sintering temperature is increased to 200 ℃, and the temperature rising speed is 3-5 ℃/min.
7. The titanovanadoaluminum carbon ceramic powder material prepared by the method for preparing titanovanadoaluminum carbon ceramic powder material according to any one of claims 1 to 6.
8. The use of the di-titanium vanadium aluminum carbon ceramic powder material of claim 7 as or in the preparation of fusion reactor structural materials, vanadium alloy material reinforcement or corrosion and wear resistant coatings on surfaces of fission reactor components.
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20140178637A1 (en) * | 2012-12-21 | 2014-06-26 | Exxonmobil Research And Engineering Company | Low friction coatings with improved abrasion and wear properties and methods of making |
| CN106882965A (en) * | 2017-03-10 | 2017-06-23 | 东南大学 | A kind of method that normal pressure prepares the aluminium toner body material of high purity titanium two |
| CN108821291A (en) * | 2018-07-10 | 2018-11-16 | 中国科学院宁波材料技术与工程研究所 | A kind of novel tertiary stratiform MAX phase material, preparation method and application |
| CN111943205A (en) * | 2020-08-28 | 2020-11-17 | 郑州轻工业大学 | Method for preparing MAX phase by adopting melt displacement reaction, prepared MAX phase and application |
| CN111977655A (en) * | 2020-08-28 | 2020-11-24 | 郑州轻工业大学 | Preparation method and application of vacancy ternary metal MAX phase |
| CN112010305A (en) * | 2020-08-26 | 2020-12-01 | 盐城工学院 | Preparation (V, Ti)2AlC submicron flake and nanoparticle method |
| CN114956082A (en) * | 2021-02-26 | 2022-08-30 | 苏州北科纳米科技有限公司 | Method for preparing excessive Al-doped MAX phase by low-temperature molten aluminum salt system |
| CN115159525A (en) * | 2022-07-29 | 2022-10-11 | 三亚汉烯石墨烯技术研究所有限公司 | MXene slurry and preparation method thereof |
-
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- 2022-11-04 CN CN202211375913.2A patent/CN115650729B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20140178637A1 (en) * | 2012-12-21 | 2014-06-26 | Exxonmobil Research And Engineering Company | Low friction coatings with improved abrasion and wear properties and methods of making |
| CN106882965A (en) * | 2017-03-10 | 2017-06-23 | 东南大学 | A kind of method that normal pressure prepares the aluminium toner body material of high purity titanium two |
| CN108821291A (en) * | 2018-07-10 | 2018-11-16 | 中国科学院宁波材料技术与工程研究所 | A kind of novel tertiary stratiform MAX phase material, preparation method and application |
| CN112010305A (en) * | 2020-08-26 | 2020-12-01 | 盐城工学院 | Preparation (V, Ti)2AlC submicron flake and nanoparticle method |
| CN111943205A (en) * | 2020-08-28 | 2020-11-17 | 郑州轻工业大学 | Method for preparing MAX phase by adopting melt displacement reaction, prepared MAX phase and application |
| CN111977655A (en) * | 2020-08-28 | 2020-11-24 | 郑州轻工业大学 | Preparation method and application of vacancy ternary metal MAX phase |
| CN114956082A (en) * | 2021-02-26 | 2022-08-30 | 苏州北科纳米科技有限公司 | Method for preparing excessive Al-doped MAX phase by low-temperature molten aluminum salt system |
| CN115159525A (en) * | 2022-07-29 | 2022-10-11 | 三亚汉烯石墨烯技术研究所有限公司 | MXene slurry and preparation method thereof |
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