CN111875399B - Preparation method of multi-element toughened silicon carbide ceramic matrix composite - Google Patents
Preparation method of multi-element toughened silicon carbide ceramic matrix composite Download PDFInfo
- Publication number
- CN111875399B CN111875399B CN202010756313.5A CN202010756313A CN111875399B CN 111875399 B CN111875399 B CN 111875399B CN 202010756313 A CN202010756313 A CN 202010756313A CN 111875399 B CN111875399 B CN 111875399B
- Authority
- CN
- China
- Prior art keywords
- powder
- ceramic matrix
- matrix composite
- silicon carbide
- carbide ceramic
- 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.)
- Active
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
- C04B35/565—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide
- C04B35/573—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide obtained by reaction sintering or recrystallisation
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3804—Borides
- C04B2235/3813—Refractory metal borides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3817—Carbides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3817—Carbides
- C04B2235/3839—Refractory metal carbides
- C04B2235/3843—Titanium carbides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/40—Metallic constituents or additives not added as binding phase
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/40—Metallic constituents or additives not added as binding phase
- C04B2235/404—Refractory metals
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5216—Inorganic
- C04B2235/524—Non-oxidic, e.g. borides, carbides, silicides or nitrides
- C04B2235/5244—Silicon carbide
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5216—Inorganic
- C04B2235/524—Non-oxidic, e.g. borides, carbides, silicides or nitrides
- C04B2235/5248—Carbon, e.g. graphite
-
- 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
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T50/00—Aeronautics or air transport
- Y02T50/40—Weight reduction
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Structural Engineering (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Ceramic Products (AREA)
Abstract
The invention belongs to the technical field of ceramic matrix composite preparation, and particularly relates to a preparation method of a multi-element toughened silicon carbide ceramic matrix composite. The method is based on a reaction infiltration process, metal Ti powder or TiC powder is mixed into matrix slurry for preparing the silicon carbide ceramic matrix composite, the metal Ti powder or TiC powder and fibers are prepared into prepreg, the prepreg and the fiber are subjected to curing and carbonization processes to obtain a porous body, then Si-B alloy is melted and infiltrated into the porous body at high temperature, and Ti or TiC reacts with C, B to generate Ti in situ in a SiC matrix3SiC2And TiB2Toughening phase to obtain the multi-element toughened fiber reinforced silicon carbide ceramic matrix composite. The method utilizes Ti3SiC2Layered structure of grains themselves, combined with TiB2The columnar structure of the crystal grains and the synergistic effect of the two toughening mechanisms further improve the toughness of the ceramic matrix composite material.
Description
Technical Field
The invention belongs to the technical field of ceramic matrix composite preparation, and particularly relates to a preparation method of a multi-element toughened silicon carbide ceramic matrix composite.
Background
The fiber reinforced silicon carbide ceramic matrix composite has a series of excellent characteristics of high specific strength, high specific modulus, high temperature resistance, ablation resistance and the like, and has wide application prospects in the fields of aviation, aerospace and the like. For certain specific application parts, materials with special functional characteristics are required, such as rotating parts of aircraft engines and the like, and composite materials with higher toughness are required. Because the SiC matrix has the characteristic of high brittleness, the defects such as cracks and the like are not weakened or deflected when the SiC matrix bears load. Therefore, from the perspective of material design, the toughening of the composite material is expected to be realized by modifying the SiC matrix.
A new ternary transition metal compound MAX phase (M: transition metal element; a: main group element; X is C or N; and N is 1 to 3) has attracted attention because of taking into consideration the characteristics of a metal material and a ceramic material. Due to its unique layered structure, when bearing load, the crack will be hindered from propagating to the layer interface and be deflected or passivated, which can effectively weaken the stress concentration at the crack tip, but the mechanical property of the MAX phase is poor, which will limit its application as a structural material alone, and therefore it is often used in combination with other structural ceramics. Representative of the MAX phase is Ti3SiC2The composite material is used as a toughening phase and is compounded with SiC, so that the toughness of the SiC is expected to be increased. At present, researches show that the adoption of a multi-component toughening phase can obtain a remarkable toughening effect. TiB2The grains are columnar, and the grains with larger length-diameter ratio can toughen the material. While TiB2With Ti3SiC2Have similar thermal expansion coefficients, thereby simultaneously introducing Ti into the SiC matrix3SiC2And TiB2The two toughening phases and the two toughening mechanisms act synergistically to ensure that the toughness of the ceramic matrix composite is remarkableAnd (4) improving.
Various means have been used to improve the toughness of silicon carbide. Application Nos. CN201810193507.1 and CN200910129807.4 Using ternary layered Ti3SiC2The toughening effect of the toughened silicon carbide ceramic matrix composite is limited because the toughening mechanism is single. The application numbers CN201710948861.6 and CN201610110058.0 and the like all utilize SiC whisker to toughen the silicon carbide ceramic matrix composite, and the SiC whisker is introduced into a silicon carbide matrix by adopting a pure mechanical mixing method, so that on one hand, the mechanical mixing has great influence on the material performance; on the other hand, the degree of densification of the composite material is difficult due to the bridging effect between the whiskers. The latter adopts an in-situ growth method to synthesize whiskers in a SiC matrix, and the whisker growth is relatively uncontrollable. In addition, the aim of toughening is achieved by introducing nano particles or carbon nano tubes into SiC, the methods adopt a mechanical mixing method to introduce a toughening phase, and in addition, the dispersion stability of the nano particles is poor.
Disclosure of Invention
The invention provides a preparation method of a multi-element toughened silicon carbide ceramic matrix composite. Aims at utilizing the reaction infiltration process to generate Ti in situ in the SiC matrix3SiC2And TiB2Two toughening phases, thereby obtaining a high-toughness matrix and realizing the toughening of the ceramic matrix composite.
The technical solution of the invention comprises the following steps:
step 1: mixing metal Ti powder or TiC powder, a powder dispersing agent, an organic solvent and high carbon residue resin, and performing ball milling for more than 12 hours to prepare mixed slurry;
and 2, step: coating the mixed slurry prepared in the step 1 on a fiber fabric containing an interface layer, and removing an organic solvent by utilizing reduced pressure evaporation to prepare a prepreg;
and 3, step 3: placing the prepreg obtained in the step 2 in a mould, and curing and molding by using a hot press, wherein the curing temperature is set to be 150-300 ℃, the pressure is set to be 0.2-12 MPa, and the time is set to be 1-5 h, so as to obtain a prefabricated body;
and 4, step 4: carbonizing the prefabricated body obtained in the step (3) at 800-1200 ℃ in an inert atmosphere for 30-120 min to obtain a porous body;
and 5: and (3) infiltrating the Si-B alloy into the porous body under the vacuum condition, wherein the infiltration temperature is 1400-1600 ℃, and the reaction time is 5-40 min, so as to obtain the fiber/SiC-Ti 3SiC2-TiB2 composite material.
The slurry comprises metal Ti powder or TiC powder, a powder dispersing agent, an organic solvent, phenolic resin and derivatives thereof in parts by mass: 10-50: 0.2-1: 50-200: 50 to 100.
The organic solvent is one or a mixture of ethanol, methanol, isopropanol, acetone, toluene, xylene, butyl acetate and ethyl acetate.
The fiber fabric is one of SiC fiber fabric and C fiber fabric.
The mass ratio of the Si powder to the B powder is 10-50: 1.
the mass ratio of the Si-B alloy to the porous body is 1-5: 1.
The grain diameter of the metal Ti powder or TiC powder is 0.5-5 mu m, and the purity is not less than 99.9%.
The purity of the silicon powder is not less than 99.9%.
The purity of the boron powder is not less than 99.9%.
The high carbon residue resin is one of phenolic resin and derivatives thereof, furan resin and derivatives thereof.
The invention has the advantages and beneficial effects that:
firstly, Ti3SiC2 and TiB2 are introduced into a SiC matrix by using an in-situ generation method, so that the compatibility of the matrix and a toughening body is good, the interface bonding strength is high, the mechanical property of the obtained material is higher than that of the obtained material by other introduction modes, and meanwhile, the process is simple and the cost is lower; TiB2, Ti3SiC2 and SiC have matched thermal expansion coefficients, so Ti3SiC2 and TiB2 are ideal SiC toughening phases; when bearing load, when the crack extends to the layer interface of the Ti3SiC2 phase, the crack deflects or passivates, the stress concentration of the crack tip can be effectively weakened, the TiB2 crystal grain generated in situ presents columnar crystal with certain length-diameter ratio, and the material toughening is effectively realized mainly by means of the mechanisms of pulling, bridging and crack deflection and the synergistic action of the toughening mechanisms; and fourthly, adding boron powder into the silicon powder, so that the corrosion of silicon to fibers can be reduced.
Detailed Description
The preparation method of the multi-element toughened silicon carbide ceramic matrix composite is described by combining the following specific examples:
example 1:
step 1: mixing 20g of metal Ti powder (the particle size is 0.5 mu m, the purity is 99.9 percent), 0.4g of powder dispersing agent, 150g of absolute ethyl alcohol and 50g of phenolic resin, and performing ball milling for 12 hours to prepare mixed slurry;
step 2: coating the mixed slurry prepared in the step 1 on a SiC fiber fabric containing an interface layer, and removing absolute ethyl alcohol by reduced pressure evaporation to prepare a prepreg;
and step 3: placing the prepreg obtained in the step 2 in a mould, and curing and molding by using a hot press, wherein the curing temperature is set to be 220 ℃, the pressure is set to be 0.2MPa, and the time is set to be 5 hours, so that a prefabricated body is obtained;
and 4, step 4: carbonizing the preform obtained in the step (3) at 1000 ℃ in an inert atmosphere for 60min to obtain a porous body;
and 5: infiltrating Si (99.99%) and B (99.99%) alloy powder with a mass ratio of 50:1 into the porous body under vacuum conditions, wherein the mass ratio of the Si-B alloy to the porous body is 5: 1. the infiltration temperature is 1400 ℃, and the reaction time is 20min, thereby obtaining the SiCf/SiC-Ti3SiC2-TiB2 composite material.
Example 2:
step 1: mixing 35g of TiC (particle size of 1 mu m and purity of 99.9%), 0.7g of powder dispersing agent, 180g of mixture of isopropanol and butyl acetate (mass ratio of 1:2) and 80g of furan resin, and performing ball milling for 24 hours to prepare mixed slurry;
step 2: coating the mixed slurry prepared in the step 1 on a C fiber fabric containing an interface layer, and removing a mixture of isopropanol and butyl acetate by reduced pressure evaporation to prepare a prepreg;
and step 3: placing the prepreg obtained in the step 2 in a mould, and curing and molding by using a hot press, wherein the curing temperature is set to be 150 ℃, the pressure is set to be 0.5MPa, and the time is set to be 2.5 hours, so that a prefabricated body is obtained;
and 4, step 4: carbonizing the prefabricated body obtained in the step (3) at 800 ℃ in an inert atmosphere for 120min to obtain a porous body;
and 5: under the vacuum condition, Si (99.99%) and B (99.99%) alloy powder with the mass ratio of 30:1 are infiltrated into the porous body, wherein the mass ratio of the Si-B alloy to the porous body is 2.5: 1. the infiltration temperature is 1600 ℃, and the reaction time is 10min, thereby obtaining the Cf/SiC-Ti3SiC2-TiB2 composite material.
Example 3:
step 1: mixing 50g of TiC (particle size 5 mu m, purity 99.9%), 1g of powder dispersing agent, 200g of dimethylbenzene and 100g of phenolic resin derivative, and performing ball milling for 30 hours to prepare mixed slurry;
step 2: coating the mixed slurry prepared in the step 1 on a SiC fiber fabric containing an interface layer, and removing xylene by reduced pressure evaporation to prepare a prepreg;
and 3, step 3: placing the prepreg obtained in the step 2 in a mould, and curing and molding by using a hot press, wherein the curing temperature is set to be 300 ℃, the pressure is set to be 12MPa, and the time is set to be 1h, so that a prefabricated body is obtained;
and 4, step 4: carbonizing the preform obtained in the step (3) at 1200 ℃ in an inert atmosphere for 30min to obtain a porous body;
and 5: infiltrating Si (99.9%) and B (99.9%) alloy powder with the mass ratio of 10:1 into the porous body under the vacuum condition, wherein the mass ratio of the Si-B alloy to the porous body is 3: 1. the infiltration temperature is 1420 ℃, and the reaction time is 40min, thereby obtaining the SiCf/SiC-Ti3SiC2-TiB2 composite material.
Claims (7)
1. The preparation method of the multi-element toughened silicon carbide ceramic matrix composite is characterized by comprising the following steps:
step 1: mixing metal Ti powder or TiC powder, a powder dispersing agent, an organic solvent and high carbon residue resin, and ball-milling for more than 12 hours to prepare mixed slurry, wherein the mass part ratio of the metal Ti powder or TiC powder, the powder dispersing agent, the organic solvent and the high carbon residue resin in the mixed slurry is as follows: 10-50: 0.2-1: 50-200: 50-100 parts;
step 2: coating the mixed slurry prepared in the step 1 on a fiber fabric containing an interface layer, and removing an organic solvent by reduced pressure evaporation to prepare a prepreg;
and step 3: placing the prepreg obtained in the step 2 in a mould, and curing and molding by using a hot press, wherein the curing temperature is set to be 150-300 ℃, the pressure is set to be 0.2-12 MPa, and the time is set to be 1-5 h, so that a prefabricated body is obtained;
and 4, step 4: carbonizing the prefabricated body obtained in the step (3) at 800-1200 ℃ in an inert atmosphere for 30-120 min to obtain a porous body;
and 5: and (5) placing the porous body obtained in the step (4) under Si and B powder, wherein the mass ratio of the Si to the B powder is 10-50: 1; under the conditions of vacuum and infiltration temperature of 1400-1600 ℃, the Si and B powder are melted to form Si-B alloy, and the mass ratio of the Si-B alloy to the porous body is 1-5: 1; permeating into the porous body, reacting for 5-40 min to obtain the fiber/SiC-Ti3SiC2-TiB2A composite material.
2. The method for preparing the multi-component toughened silicon carbide ceramic matrix composite material according to claim 1, wherein the method comprises the following steps: the organic solvent is one or a mixture of ethanol, methanol, isopropanol, acetone, toluene, xylene, butyl acetate and ethyl acetate.
3. The method for preparing the multi-component toughened silicon carbide ceramic matrix composite material according to claim 1, wherein the method comprises the following steps: the fiber fabric is one of SiC fiber fabric and C fiber fabric.
4. The method for preparing the multi-component toughened silicon carbide ceramic matrix composite material according to claim 1, wherein the method comprises the following steps: the grain diameter of the metal Ti powder or TiC powder is 0.5-5 mu m, and the purity is not less than 99.9%.
5. The method for preparing the multi-component toughened silicon carbide ceramic matrix composite material according to claim 1, wherein the method comprises the following steps: the purity of the silicon powder is not less than 99.9%.
6. The method for preparing the multi-component toughened silicon carbide ceramic matrix composite material according to claim 1, wherein the method comprises the following steps: the purity of the boron powder is not less than 99.9%.
7. The method for preparing the multi-component toughened silicon carbide ceramic matrix composite material according to claim 1, wherein the method comprises the following steps: the high carbon residue resin is one of phenolic resin and derivatives thereof, and furan resin and derivatives thereof.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN202010756313.5A CN111875399B (en) | 2020-07-31 | 2020-07-31 | Preparation method of multi-element toughened silicon carbide ceramic matrix composite |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN202010756313.5A CN111875399B (en) | 2020-07-31 | 2020-07-31 | Preparation method of multi-element toughened silicon carbide ceramic matrix composite |
Publications (2)
Publication Number | Publication Date |
---|---|
CN111875399A CN111875399A (en) | 2020-11-03 |
CN111875399B true CN111875399B (en) | 2022-07-12 |
Family
ID=73205831
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN202010756313.5A Active CN111875399B (en) | 2020-07-31 | 2020-07-31 | Preparation method of multi-element toughened silicon carbide ceramic matrix composite |
Country Status (1)
Country | Link |
---|---|
CN (1) | CN111875399B (en) |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN113943160B (en) * | 2021-10-15 | 2022-08-09 | 中国航发北京航空材料研究院 | Preparation method of silicon carbide ceramic matrix composite with self-repairing function |
CN114278692B (en) * | 2022-01-05 | 2022-10-04 | 中国人民解放军63963部队 | Disc brake friction pair for heavy-duty vehicle and manufacturing method thereof |
CN114538943A (en) * | 2022-03-04 | 2022-05-27 | 南京航空航天大学 | Selective laser sintering dual-phase toughened SiC ceramic and preparation method thereof |
CN116496097A (en) * | 2023-03-24 | 2023-07-28 | 西北工业大学 | Multi-element silicon carbide ceramic matrix composite material and preparation method thereof |
Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20030209534A1 (en) * | 2002-05-09 | 2003-11-13 | Ferguson Lucian G. | Tapecast electro-conductive cermets for high temperature resistive heating systems |
US20090130324A1 (en) * | 2005-04-21 | 2009-05-21 | Kartik Shanker | Wear resistant ceramic composite coatings and process for production thereof |
CN104140265A (en) * | 2014-07-28 | 2014-11-12 | 中国科学院上海硅酸盐研究所 | Method adopting liquid phase sintering for manufacturing silicon carbide ceramics with zirconium oxide as toughening phase |
CN105174967A (en) * | 2015-09-07 | 2015-12-23 | 厦门理工学院 | Ultra-temperature CNTs/TiB2-SiC ceramic composite material and preparation method thereof |
CN106032322A (en) * | 2015-07-29 | 2016-10-19 | 洛阳新巨能高热技术有限公司 | Preparation method of silicon carbide-titanium carbide-titanium boride composite |
CN108409347A (en) * | 2018-03-09 | 2018-08-17 | 中国航发北京航空材料研究院 | A kind of in-situ preparation Ti3SiC2The preparation method of phase ceramics of silicon carbide toughened based composites |
CN109053206A (en) * | 2018-08-31 | 2018-12-21 | 中国科学院金属研究所 | A kind of short fiber reinforced orientation MAX phase ceramics based composites and preparation method |
CN109439991A (en) * | 2018-11-30 | 2019-03-08 | 江苏海事职业技术学院 | A kind of TiB2Whisker high temperature Strengthening and Toughening Ti (C, N) base metal-ceramic material preparation method |
US20190152865A1 (en) * | 2017-11-23 | 2019-05-23 | National Tsing Hua University | Toughened ceramic material |
CN111233503A (en) * | 2020-02-26 | 2020-06-05 | 中南大学 | Preparation method of fiber-toughened ceramic matrix composite |
-
2020
- 2020-07-31 CN CN202010756313.5A patent/CN111875399B/en active Active
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20030209534A1 (en) * | 2002-05-09 | 2003-11-13 | Ferguson Lucian G. | Tapecast electro-conductive cermets for high temperature resistive heating systems |
US20090130324A1 (en) * | 2005-04-21 | 2009-05-21 | Kartik Shanker | Wear resistant ceramic composite coatings and process for production thereof |
CN104140265A (en) * | 2014-07-28 | 2014-11-12 | 中国科学院上海硅酸盐研究所 | Method adopting liquid phase sintering for manufacturing silicon carbide ceramics with zirconium oxide as toughening phase |
CN106032322A (en) * | 2015-07-29 | 2016-10-19 | 洛阳新巨能高热技术有限公司 | Preparation method of silicon carbide-titanium carbide-titanium boride composite |
CN105174967A (en) * | 2015-09-07 | 2015-12-23 | 厦门理工学院 | Ultra-temperature CNTs/TiB2-SiC ceramic composite material and preparation method thereof |
US20190152865A1 (en) * | 2017-11-23 | 2019-05-23 | National Tsing Hua University | Toughened ceramic material |
CN108409347A (en) * | 2018-03-09 | 2018-08-17 | 中国航发北京航空材料研究院 | A kind of in-situ preparation Ti3SiC2The preparation method of phase ceramics of silicon carbide toughened based composites |
CN109053206A (en) * | 2018-08-31 | 2018-12-21 | 中国科学院金属研究所 | A kind of short fiber reinforced orientation MAX phase ceramics based composites and preparation method |
CN109439991A (en) * | 2018-11-30 | 2019-03-08 | 江苏海事职业技术学院 | A kind of TiB2Whisker high temperature Strengthening and Toughening Ti (C, N) base metal-ceramic material preparation method |
CN111233503A (en) * | 2020-02-26 | 2020-06-05 | 中南大学 | Preparation method of fiber-toughened ceramic matrix composite |
Non-Patent Citations (6)
Title |
---|
In situ synthesis of (TiB2 + SiC)/Ti3SiC2 composites by hot pressing;Song, K et al.;《MATERIALS LETTERS》;20120515;第75卷;全文 * |
TiB2增强SiC基复合材料的研究进展;胡继林等;《人工晶体学报》;20131130;第42卷(第11期);全文 * |
Toughening mechanisms of Ti3SiC2- and TiB2-toughened SiC matrix prepared via reactive melt infiltration;Zhou,YR et al.;《Journal of Material Research》;20211228;第36卷(第24期);全文 * |
原位合成(TiB2+TiC)/Ti3SiC2复相材料及其性能研究;顾巍等;《无机材料学报》;20101031;第25卷(第10期);全文 * |
放电等离子合成Ti_3AlC_2/TiB_2复合材料的制备及性能研究;卢雪飞等;《稀有金属快报》;20070228(第02期);全文 * |
熔融渗透工艺制备SiC-TiSi复相陶瓷的反应机理;周怡然等;《材料工程》;20190630;第47卷(第6期);全文 * |
Also Published As
Publication number | Publication date |
---|---|
CN111875399A (en) | 2020-11-03 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
CN111875399B (en) | Preparation method of multi-element toughened silicon carbide ceramic matrix composite | |
CN102503427B (en) | Preparation method of high-toughness boride-carbide composite ceramic | |
CN110256082B (en) | Method for preparing single crystal silicon carbide nanofiber/silicon carbide ceramic matrix composite material by reaction sintering | |
CN110282993B (en) | Preparation method of ceramic matrix composite containing interface phase | |
CN108409347A (en) | A kind of in-situ preparation Ti3SiC2The preparation method of phase ceramics of silicon carbide toughened based composites | |
CN109851375B (en) | Silicon-boron-carbon-nitrogen ceramic composite material and preparation method thereof | |
CN107759251B (en) | Preparation method of high-toughness ceramic coating on surface of porous ceramic | |
CN1884204A (en) | Process for preparing composite materials capable of forming oxidation-resisting structure on the surface of fiber by in-situ reaction | |
CN112645726B (en) | Silicon carbide whisker ceramic with typical long particle morphology and rich in stacking faults and twin crystals and preparation method thereof | |
CN101265108A (en) | Boride-silicon carbide-boron carbide ternary ceramic-base composite material and preparation method thereof | |
CN113480320A (en) | High-stress-cracking-resistance SiCf/SiC ceramic matrix composite material and preparation method thereof | |
CN113773090B (en) | ZrB2Preparation method of-ZrC-SiC nano composite ceramic material | |
CN109972120B (en) | Preparation method of multi-element composite carbide coating | |
CN112521156B (en) | Hybrid matrix SiCf/SiC composite material and preparation method thereof | |
CN1304331C (en) | Compound phose material of beta cellulose and alpha cellulose and its preparation technology | |
CN103938023A (en) | In-situ titanium-aluminum-carbon toughened TiAl3 intermetallic compound and preparation method thereof | |
CN111499386A (en) | Composite ceramic material and preparation method thereof | |
CN104844214A (en) | Densified high-strength zirconium carbide ceramic material, densified high-strength hafnium carbide ceramic material, and low temperature preparation methods of densified high-strength zirconium carbide ceramic material and densified high-strength hafnium carbide ceramic material | |
CN108585907B (en) | Cr (chromium)2Preparation method of AlC modified self-healing silicon carbide ceramic matrix composite | |
Dong et al. | Research progress in SiC-based ceramic matrix composites | |
CN113943160B (en) | Preparation method of silicon carbide ceramic matrix composite with self-repairing function | |
CN108660398A (en) | A kind of preparation method of graphene-silicon carbide fibre reinforced metal composite material | |
CN108706984B (en) | Thermal shock-resistant and ablation-resistant SiBCN ceramic material modified by zirconium diboride and short carbon fibers and preparation method thereof | |
CN111410539B (en) | Y-Al-Si-O multi-element glass phase reinforced hexagonal boron nitride-based multiphase ceramic | |
CN113957294A (en) | CrCoNi intermediate entropy alloy reinforced Al-based composite material 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 |