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CN-121990826-A - MAX phase ceramic microstructure editing composite material and preparation method and application thereof

CN121990826ACN 121990826 ACN121990826 ACN 121990826ACN-121990826-A

Abstract

The invention belongs to the technical field of inorganic materials, and particularly relates to a composite material edited by a MAX phase ceramic microstructure, and a preparation method and application thereof. The composite material comprises a MAX phase and a metal boride phase, wherein the molecular formula of the MAX phase is M 2 AX, and the molecular formula of the metal boride phase is MeB 2 . The material is obtained by taking boride MAX material, M' material and X material as raw materials and sintering the raw materials in situ at high temperature and high pressure. And the mother phase is subjected to lattice editing at high temperature, and meanwhile, a metal boride reinforcing phase grows in situ, and the nucleation position and the material source of the metal boride in the process are precisely controlled by the editing process, so that the directional regulation and control of the morphology of the reinforcing phase are realized. Compared with MAX phase or metal boride ceramic material, the composite material obtained by the invention has obviously improved mechanical properties, and has wide application prospect in the extreme environment fields of advanced nuclear energy, aerospace, marine equipment and the like.

Inventors

  • CHEN KE
  • HE ZONGHUA
  • HUANG QING

Assignees

  • 中国科学院宁波材料技术与工程研究所
  • 宁波杭州湾新材料研究院

Dates

Publication Date
20260508
Application Date
20251216

Claims (10)

  1. 1. A composite material for MAX phase ceramic microstructural editing, wherein the composite material comprises a MAX phase and a metal boride phase; The molecular formula of the MAX phase is M 2 AX, M is one or more combinations of front transition metal groups, A is any one or more combinations of S, se and Te elements, and X is any one or more combinations of C, S, se, P elements; The molecular formula of the metal boride phase is MeB 2 , me is one or a combination of a plurality of IVB and VB transition metals, and B represents boron.
  2. 2. The composite material of claim 1, wherein M is any one or more combinations of elements Ti, zr, hf, V, nb, ta and Me is any one or more combinations of elements Ti, zr, hf, nb, ta, V.
  3. 3. The composite material of claim 1, wherein the volume ratio of the metal boride phase in the composite material is 10-49 wt% and the volume ratio of the MAX phase is 50-89 wt%.
  4. 4. The composite material according to claim 1, wherein the composite material is obtained by in-situ sintering of boride MAX material, m″ material, X material at high temperature and high pressure; the molecular formula of the boride MAX material is M ' 2 AB, M' is one or more combinations in front transition metal groups, A is any one or more combinations of S, se and Te elements, and B represents boron element; the M 'material is M' element simple substance or an alloy formed by M 'element, and M' is one or a combination of a plurality of front transition metal groups; The X material is an X element simple substance or a compound formed by the X element, and X is any one or a combination of a plurality of C, S, se, P elements.
  5. 5. The composite material of claim 4, wherein M' is any one or a combination of elements Ti, zr, hf, V, nb, ta; M '' is any one or more combination of Ti, zr, hf, V, nb, ta elements.
  6. 6. The composite material according to claim 4, wherein the molar ratio of boride MAX material, M '' material, X material is 2 (0-1): (0-2.5); And/or the high-temperature high-pressure reaction condition comprises that the temperature is 1200-1700 ℃, the pressure is 20-80 MPa, and the reaction time is 20-150 min.
  7. 7. The composite material of claim 4 wherein the constituent elements of M 2 AX are derived from M 'inherent in the boride MAX material or from a combination of M' and M '' inherent in the boride MAX material, A is derived from inherent A in the boride MAX material, and X is derived from X in the X material.
  8. 8. The composite material according to claim 4, wherein the nucleation position and the material source of the metal boride MeB 2 are precisely controlled, so that the directional control of the morphology of the metal boride reinforcing phase is realized; {10 } of the metal boride MeB 2 in the lattice of the boride MAX material (M' 2 AB) The 0} surface nucleation has the following composition elements of B from B in boride MAX material, me from M ' element in boride MAX material and/or M ' element in M ' material; the diameter-thickness ratio of the metal boride MeB 2 can be regulated.
  9. 9. The method for preparing a composite material for editing a MAX phase ceramic microstructure according to claim 1, comprising the steps of: And uniformly mixing the boride MAX material, the M '' material and the X material, and carrying out in-situ sintering reaction on the obtained mixture under inert atmosphere and high-temperature and high-pressure conditions, thereby obtaining the composite material edited by the MAX phase ceramic microstructure.
  10. 10. Use of a MAX phase ceramic micro-structure edited composite material as defined in claim 1 in advanced nuclear, aerospace, marine equipment.

Description

MAX phase ceramic microstructure editing composite material and preparation method and application thereof Technical Field The invention belongs to the technical field of inorganic materials, and particularly relates to a composite material edited by a MAX phase ceramic microstructure, and a preparation method and application thereof. Background The MAX phase is a crystal material with a ternary lamellar structure, the crystal structure is a hexagonal system, the space group is P6 3/mmc, and the chemical composition of the MAX phase can be expressed as a molecular general formula of M n+1AXn. Wherein M is a front transition group metal, A is usually a group IIIA and IVA element, X is usually carbon or nitrogen element, and n has a value of 1, 2 or 3. The crystal structure of the MAX phase is generally thought to be formed by alternating stacks of M n+1Xn nanostructure sublayers and a-site monoatomic layers. The MAX phase layered material has the advantages of high temperature resistance, high damage tolerance, thermal shock resistance, easy processing and the like. Compared with the traditional transition metal carbide and nitride ceramic materials, the MAX phase material has relatively more excellent fracture toughness, and meanwhile, the unique layered structure and moderate hardness of the MAX phase material endow good machinability, and the limit that the traditional ceramic is difficult to machine is broken through. Compared with traditional aluminum alloy and other metal materials, the MAX phase material has more excellent high-temperature mechanical property, can still keep higher modulus at 1000 ℃, and can still keep better oxidation resistance at high temperature. The traditional metal material has low hardness, is easy to fail in a wearing environment, has high hardness and low friction coefficient, and has better wear resistance. Therefore, the MAX phase material has potential for application in the extreme environmental fields such as nuclear accidents, aerospace fields and the like. thecovalentMAXphasehasremarkablecovalentbondpropertyofM-Abondbecauseofthenon-metalatomwithstrongelectronegativityoccupiestheAposition,sothattheelectronicstructureandthechemicalbondcombinationmodearebasicallydifferentfromthoseofthetraditionalmetalMAXphase. The strong covalent bond enables the crystal structure of the material to be more stable, and the material has more excellent hardness and strength and stronger corrosion resistance. The covalent MAX phase shows good application prospect in terms of structural materials. ThechalcogenMAXphaseisanimportantcovalentMAXphasematerial,andbecausechalcogenelements(S,SeandTe)occupyAposition,M-Abondshavehigherstrength,higherYoungmodulusandshearmodulusandstrongercorrosionresistance. Zr2SeCisanovelchalcogenMAXphase,andSeatomshavelargersizeandlowerelectronegativitythanSatoms,resultinginaweakerlocalizationofouterelectronsbetweenM-aatomsafterSeatomsoccupythealayer. The electron-donating portion of the thermal conductivity of Zr 2 SeC is therefore significantly activated at 450K, compensating for the decreasing trend of thermal conductivity at high temperatures. However, the orientation of the covalent bonds of the chalcogen MAX phase limits the slip and proliferation of dislocations, resulting in lower fracture toughness than the metallic MAX phase, and more readily initiates cracks under strong load impact, resulting in failure of the chalcogen MAX phase material. In the field of ceramic matrix composite materials, the toughening approaches mainly comprise second phase reinforcement toughening, phase change toughening, in-situ autogenous toughening, nanocrystallization toughening and the like. At present, in the research field of MAX phase ceramic matrix composite materials, research is relatively limited and the use of inorganic fibers as a toughening phase in MAX phase ceramics is focused. For example, xiong et al (Y. Xiong et al, int. J. Appl. Ceram. Technology, 2021, 19, 545-556) prepared SiC f/Ti3SiC2 composite by HIP hot pressing, and under the action of fiber toughening, the fracture toughness reached 6.76 MPa.m 1/2, and the matrix material Ti 3SiC2 ceramic block had a fracture toughness of 5.97 MPa.m 1/2, which was improved by 13% compared to that of 13%, however, due to severe thermal mismatch between the fibers and the matrix, problematic porosity was created. However Bucevac et al (d. Bucevac et al., ceram, int., 2010, 36, 2181-2188) prepared in-situ TiB 2 particle toughened SiC ceramics, the in-situ generated TiB 2 particles improved the sintering driving force to further densify the ceramic material, and at the same time, tiB 2 particles were able to exert various toughening mechanisms to improve the fracture toughness of SiC-based composites to 5.7 MPa-m 1/2, whereas the fracture toughness of SiC ceramics was 4.7 MPa-m 1/2, which was 21% higher than the others. The in-situ self-generated toughening solves the problem of material failure caused by internal gaps