CN109735779A - A kind of preparation method improving SiC fiber-Ni based composite material interface binding performance - Google Patents
A kind of preparation method improving SiC fiber-Ni based composite material interface binding performance Download PDFInfo
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Abstract
The present invention relates to W metal based composites technical fields, and disclose a kind of preparation method for improving SiC fiber-Ni based composite material interface binding performance, comprising the following steps: S1. weighs 50-70 parts of nickel powders, 9-12 parts of SiC fiber powder, 2-4 parts of Al2O3Powder, 2-4 part carbon fiber powder, it is spare；S2. with PbO, B2O3、SiO2、Bi2O3、TiO2For raw material, glass powder is prepared；S3. 7.88 parts of dioctyl phthalates, 3.76 parts of allyl methacrylates, 2.84 parts of n,N-Dimethylformamide are taken, it is spare；S4. by the standby raw material in step S1, the glass powder in step S2, the standby raw material compression moulding under stress in step S3, it is placed in vacuum drying oven again, and 2h is kept the temperature under 1200-1300 DEG C, 4-6MPa, cool down later, SiC fiber-Ni based composites are prepared.The existing method for prepare SiC fiber-Ni based composites of the present invention, there is technical issues that at the interface cohesion of prepared composite material crackle and.
Description
Technical field
The present invention relates to W metal based composites technical field, specially a kind of raising SiC fiber-Ni based composites
The preparation method of interfacial combined function.
Background technique
SiC fiber reinforcement Ni based composites can significantly improve the specific stiffness and specific strength of Ni sill, reduce material
The weight of component especially still shows good mechanical property in superhigh temperature field, and satisfaction prepares advanced aerospace hair
High performance requirements of the motivation critical component to material.
But during preparing SiC fiber reinforcement Ni based composites, SiC fiber can be sent out at high temperature with Ni matrix
Raw interfacial reaction, the reactant that interfacial reaction generates will seriously reduce the mechanical property of SiC fiber；The especially line of SiC
The coefficient of expansion 4.7 × 10-6/ the linear expansion coefficient 13.2 × 10 DEG C with Ni-6/ DEG C difference is larger, so SiC fiber and Ni matrix
The thermal expansion coefficient of material mismatches, this will lead in SiC fiber reinforcement Ni based composites during making and using, material
Material interface can crack and defect；And Al2O3Linear expansion coefficient 8.1 × 10-6/ DEG C between both above-mentioned substances,
Select Al2O3Outermost layer as fiber coat to be effectively relieved SiC/Ni interfacial stress and Ni is stopped to spread into fiber,
Select C, SiO2Layer is used as fiber internal layer, can be avoided interfacial stress damage caused by fiber surface, further functions as protection
Fiber and the effect for inhibiting interfacial reaction.
But passing through 150h, after 850-950 DEG C of vacuum heat treatment, SiO2-Al2O3SiO in composite coating2Layer and SiC
Fiber interface junction produces crackle, and C-Al2O3There are diffusion phenomena in C layer in composite coating, therefore prepare
SiC fiber reinforcement Ni based composites are still unable to satisfy advanced aerospace engine to the high performance requirements of material.
The present invention provides a kind of preparation method for improving SiC fiber-Ni based composite material interface binding performance, it is intended to solve
The existing method for preparing SiC fiber-Ni based composites there are crackle and expands at the interface cohesion of prepared composite material
Scattered technical problem.
Summary of the invention
(1) the technical issues of solving
In view of the deficiencies of the prior art, the present invention provides a kind of raising SiC fiber-Ni based composite material interface associativities
The preparation method of energy, solves the existing method for preparing SiC fiber-Ni based composites, the boundary of prepared composite material
Face junction there is technical issues that crackle with.
(2) technical solution
To achieve the above object, the invention provides the following technical scheme:
A kind of preparation method improving SiC fiber-Ni based composite material interface binding performance, comprising the following steps:
S1. 50-70 parts of nickel powders, 9-12 parts of SiC fiber powder, 2-4 parts of Al are weighed2O3Powder, 2-4 part carbon fiber powder, it is spare；
S2. with PbO, B2O3、SiO2、Bi2O3、TiO2For raw material, glass powder is prepared；
S3. 7.88 parts of dioctyl phthalates, 3.76 parts of allyl methacrylates, 2.84 parts of N are successively measured respectively,
Dinethylformamide, it is spare；
S4. the standby raw material in step S1, the glass powder in step S2, the standby raw material in step S3 are pressed under stress
Type is made, then is placed in vacuum drying oven, and keeps the temperature 2h under 1200-1300 DEG C, 4-6MPa, cools down later, SiC fibre is prepared
Dimension-Ni based composites.
Preferably, in the step S1, average particle size≤100nm, SiC fiber powder average grain diameter≤50um of nickel powder,
Al2O3Average grain diameter≤50um of average grain diameter≤100nm of powder, carbon fiber powder.
Preferably, in the step S2, glass powder is by 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm's
B2O3, 2g average grain diameter≤50nm SiO2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm composition.
Preferably, the standby raw material in step S1, the glass powder in step S2, standby in step S3 in the step S4
With raw material compression moulding under the pressure of 50-80MPa.
Preferably, in the step S4, after cooling, 1h is kept the temperature when being cooled to 800-1000 DEG C.
(3) beneficial technical effect
Compared with prior art, the present invention has following beneficial technical effect:
The density for the SiC fiber-Ni based composites that the present invention prepares is 3.05-3.17g/cm3, and passing through
150h, after 900 DEG C of vacuum heat treatments, fiber is evenly distributed, at interface cohesion without it is cracked, also do not spread,
To solve the existing method for preparing SiC fiber-Ni based composites, deposited at the interface cohesion of prepared composite material
The technical issues of crackle is with diffusion.
Specific embodiment
Embodiment one:
SiC fiber-Ni based composites include following raw material: 55g average particle size≤100nm nickel powder, 10g average grain diameter
SiC fiber powder, the 2g average grain diameter≤100nm Al of≤50um2O3Powder, 2g average grain diameter≤50um carbon fiber powder, 16g
Average grain diameter≤2.5um glass powder, 8mL dioctyl phthalate (ρ 0.985g/mL), 4mL allyl methacrylate
(ρ 0.94g/mL), 3mLN, dinethylformamide (ρ 0.945g/cm3)；
Wherein, glass powder by 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm B2O3, 2g average grain diameter
The SiO of≤50nm2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm TiO2Composition；
The preparation methods of above-mentioned SiC fiber-Ni based composites the following steps are included:
S1. successively weigh respectively 55g average particle size≤100nm nickel powder, 10g average grain diameter≤50um SiC fiber powder,
2g average grain diameter≤100nm Al2O3Powder, 2g average grain diameter≤50um carbon fiber powder, it is spare；
S2. the B of 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm are successively weighed respectively2O3, 2g is averaged grain
Diameter≤50nm SiO2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm, be configured to glass powder；
S3. 8mL dioctyl phthalate, 4mL allyl methacrylate, 3mLN, N- dimethyl are successively measured respectively
Formamide, it is spare；
S4. the standby raw material in step S1, the glass powder in step S2, the standby raw material in step S3 are placed in height together
In fast mixer, after mixing 3h under 500r/min, the compression moulding under the pressure of 70MPa, then being placed in preheating temperature is 800 DEG C
Vacuum drying oven in, be warming up to 1200 DEG C with the heating rate of 10 DEG C/min, and keep the temperature 2h under 1200 DEG C, 6MPa, carry out later
Cooling, keeps the temperature 1h when being cooled to 900 DEG C with the annealing rate of 15 DEG C/min, taking-up when being cooled to 50 DEG C, and SiC fibre is prepared
Dimension-Ni based composites；
S5. the SiC fiber-Ni based composites in step S4 are tested, the SiC fiber-Ni based composites
Density is 3.05g/cm3, and passing through 150h, after 900 DEG C of vacuum heat treatments, fiber is evenly distributed, and does not go out at interface cohesion
Existing crackle is not also spread.
Embodiment two:
SiC fiber-Ni based composites include following raw material: 70g average particle size≤100nm nickel powder, 9g average grain diameter
SiC fiber powder, the 3g average grain diameter≤100nm Al of≤50um2O3Powder, 3g average grain diameter≤50um carbon fiber powder, 16g
Average grain diameter≤2.5um glass powder, 8mL dioctyl phthalate, 4mL allyl methacrylate, 3mLN, N- dimethyl
Formamide；
Wherein, glass powder by 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm B2O3, 2g average grain diameter
The SiO of≤50nm2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm TiO2Composition；
The preparation methods of above-mentioned SiC fiber-Ni based composites the following steps are included:
S1. successively weigh respectively 70g average particle size≤100nm nickel powder, 9g average grain diameter≤50um SiC fiber powder,
3g average grain diameter≤100nm Al2O3Powder, 3g average grain diameter≤50um carbon fiber powder, it is spare；
S2. the B of 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm are successively weighed respectively2O3, 2g is averaged grain
Diameter≤50nm SiO2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm, be configured to glass powder；
S3. 8mL dioctyl phthalate, 4mL allyl methacrylate, 3mLN, N- dimethyl are successively measured respectively
Formamide, it is spare；
S4. the standby raw material in step S1, the glass powder in step S2, the standby raw material in step S3 are placed in height together
In fast mixer, after mixing 3h under 500r/min, the compression moulding under the pressure of 50MPa, then being placed in preheating temperature is 600 DEG C
Vacuum drying oven in, be warming up to 1200 DEG C with the heating rate of 10 DEG C/min, and keep the temperature 2h under 1200 DEG C, 5MPa, carry out later
Cooling, keeps the temperature 1h when being cooled to 1000 DEG C with the annealing rate of 15 DEG C/min, taking-up when being cooled to 50 DEG C, and SiC fibre is prepared
Dimension-Ni based composites；
S5. the SiC fiber-Ni based composites in step S4 are tested, the SiC fiber-Ni based composites
Density is 3.12g/cm3, and passing through 150h, after 900 DEG C of vacuum heat treatments, fiber is evenly distributed, and does not have at interface cohesion
It is cracked, also do not spread.
Embodiment three:
SiC fiber-Ni based composites include following raw material: 50g average particle size≤100nm nickel powder, 12g average grain diameter
SiC fiber powder, the 4g average grain diameter≤100nm Al of≤50um2O3Powder, 4g average grain diameter≤50um carbon fiber powder, 16g
Average grain diameter≤2.5um glass powder, 8mL dioctyl phthalate, 4mL allyl methacrylate, 3mLN, N- dimethyl
Formamide；
Wherein, glass powder by 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm B2O3, 2g average grain diameter
The SiO of≤50nm2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm TiO2Composition；
The preparation methods of above-mentioned SiC fiber-Ni based composites the following steps are included:
S1. successively weigh respectively 50g average particle size≤100nm nickel powder, 12g average grain diameter≤50um SiC fiber powder,
4g average grain diameter≤100nm Al2O3Powder, 4g average grain diameter≤50um carbon fiber powder, it is spare；
S2. the B of 6g average grain diameter≤2.5um PbO, 3g average grain diameter≤50nm are successively weighed respectively2O3, 2g is averaged grain
Diameter≤50nm SiO2, 4g average grain diameter≤50nm Bi2O3, 1g average grain diameter≤50nm, be configured to glass powder；
S3. 8mL dioctyl phthalate, 4mL allyl methacrylate, 3mLN, N- dimethyl are successively measured respectively
Formamide, it is spare；
S4. the standby raw material in step S1, the glass powder in step S2, the standby raw material in step S3 are placed in height together
In fast mixer, after mixing 3h under 500r/min, the compression moulding under the pressure of 80MPa, then being placed in preheating temperature is 700 DEG C
Vacuum drying oven in, be warming up to 1300 DEG C with the heating rate of 10 DEG C/min, and keep the temperature 2h under 1300 DEG C, 4MPa, carry out later
Cooling, keeps the temperature 1h when being cooled to 800 DEG C with the annealing rate of 15 DEG C/min, taking-up when being cooled to 50 DEG C, and SiC fibre is prepared
Dimension-Ni based composites；
S5. the SiC fiber-Ni based composites in step S4 are tested, the SiC fiber-Ni based composites
Density is 3.17g/cm3, and passing through 150h, after 900 DEG C of vacuum heat treatments, fiber is evenly distributed, and does not go out at interface cohesion
Existing crackle is not also spread.
Claims (5)
1. a kind of preparation method for improving SiC fiber-Ni based composite material interface binding performance, which is characterized in that including following
Step:
S1. 50-70 parts of nano-nickel powders, 9-12 parts of SiC fiber micron powder, 2-4 parts of nanometer Al are weighed2O3Powder, 2-4 part carbon fiber
Micron powder is tieed up, it is spare；
S2. with PbO, B2O3、SiO2、Bi2O3、TiO2For raw material, glass powder is prepared；
S3. 7.88 parts of dioctyl phthalates, 3.76 parts of allyl methacrylates, 2.84 parts of N, N- bis- are successively measured respectively
Methylformamide, it is spare；
S4. the standby raw material in step S1, the glass powder in step S2, the standby raw material in step S3 are pressed under stress
Type, then be placed in vacuum drying oven, and keep the temperature 2h under 1200-1300 DEG C, 4-6MPa, cool down later, SiC fiber-Ni is prepared
Based composites.
2. preparation method according to claim 1, which is characterized in that in the step S1, the average particle size of nickel powder≤
Average grain diameter≤50um, Al of 100nm, SiC fiber powder2O3The average grain diameter of average grain diameter≤100nm of powder, carbon fiber powder
≤50um。
3. preparation method according to claim 1, which is characterized in that in the step S2, glass powder is by 6g average grain diameter
The B of PbO, 3g average grain diameter≤50nm of≤2.5um2O3, 2g average grain diameter≤50nm SiO2, 4g average grain diameter≤50nm
Bi2O3, 1g average grain diameter≤50nm composition.
4. preparation method according to claim 1, which is characterized in that in the step S4, standby raw material in step S1,
Standby raw material compression moulding under the pressure of 50-80MPa in glass powder, step S3 in step S2.
5. preparation method according to claim 1, which is characterized in that in the step S4, in a vacuum furnace, keep the temperature 2h
Afterwards, 1h is kept the temperature when being cooled to 800-1000 DEG C.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102605208A (en) * | 2012-04-13 | 2012-07-25 | 上海交通大学 | High thermal conductivity metal-based composite material with hierarchical structure, and preparation method thereof |
| CN104862531A (en) * | 2015-06-05 | 2015-08-26 | 中国科学院上海应用物理研究所 | Nanometer silicon carbide particle-enhanced nickel-based composite material and reactor core structure component of molten salt reactor |
| CN104947010A (en) * | 2015-06-24 | 2015-09-30 | 芜湖鼎恒材料技术有限公司 | Nickel-based carbon fiber composite material |
| CN105839034A (en) * | 2016-05-24 | 2016-08-10 | 苏州创浩新材料科技有限公司 | Preparation process of low-thermal-expansion wear resistant shaft sleeve |
-
2019
- 2019-03-07 CN CN201910170733.2A patent/CN109735779A/en not_active Withdrawn
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102605208A (en) * | 2012-04-13 | 2012-07-25 | 上海交通大学 | High thermal conductivity metal-based composite material with hierarchical structure, and preparation method thereof |
| CN104862531A (en) * | 2015-06-05 | 2015-08-26 | 中国科学院上海应用物理研究所 | Nanometer silicon carbide particle-enhanced nickel-based composite material and reactor core structure component of molten salt reactor |
| CN104947010A (en) * | 2015-06-24 | 2015-09-30 | 芜湖鼎恒材料技术有限公司 | Nickel-based carbon fiber composite material |
| CN105839034A (en) * | 2016-05-24 | 2016-08-10 | 苏州创浩新材料科技有限公司 | Preparation process of low-thermal-expansion wear resistant shaft sleeve |
Non-Patent Citations (1)
| Title |
|---|
| 林海涛等: "SiC纤维表面扩散障碍涂层对SiCf／Ni复合材料界面反应的影响", 《金属学报》 * |
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