CN104788130A - C/(SiC/BN)n compound interface phase coating, coating fiber and preparation method of coating fiber - Google Patents
C/(SiC/BN)n compound interface phase coating, coating fiber and preparation method of coating fiber Download PDFInfo
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Abstract
The invention discloses a C/(SiC/BN)n compound interface phase coating which comprises a C layer and a periodic superposed layer, wherein the periodic superposed layer refers to alternative periodic superposition of SiC layers and BN layers. The coating fiber comprises a fiber base body and the C/(SiC/BN)n compound interface phase coating applied to the surface of the base body, wherein the fiber base body is selected from one of mullite fiber, carbon fiber, silicon carbide fiber and quartz fiber. The preparation method of the coating fiber comprises the following steps: preparing a fiber base body material, and depositing the C layer on the surface of the fiber base body with a chemical vapor deposition method at first; then alternatively depositing the SiC layers and the BN layers on the surface of the C layer with the chemical vapor deposition method, repeating the alternative depositing process 3-5 times, and obtaining the coating fiber. The coating fiber has the advantages of good physical and chemical compatibility, high temperature resistance, oxidation resistance, good toughening effect and the like.
Description
Technical field
The invention belongs to interfacial phase coating and the preparing technical field thereof of ceramic matric composite, particularly relate to a kind of compound interface phase coating and preparation method thereof.
Background technology
Polycrystalline ceramic fiber has the features such as high specific strength, high ratio modulus, high temperature resistant, anti-oxidant, resistance to chemical attack, can be used as the high-performance compound phase of polymer-based carbon, Metal Matrix and Ceramic Matrix Composites.Can be used for the leading-edge field such as space shuttle, high-performance enginer by fibre-reinforced high-performance ceramic based composites, be called as 21 century Aeronautics and Astronautics and high-technology field application novel material.The performance of ceramic fiber and ceramic matrix itself is not only depended in the performance of ceramic matric composite performance, the more important thing is interfacial phase therebetween.The performance of interfacial phase to ceramic matric composite plays decisive role, as the SiC that Siwei L, Litong Z etc. adopts original Niccalon-SiC fiber to prepare through chemical gas phase dipping (CVI) technique
f/ SiC ceramic matrix composite material flexural strength only has 85.0MPa, and fiber surface is after carbon coating deposition, SiC
f/ SiC ceramic matrix composite material interface be improved significantly, flexural strength can bring up to 420.0MPa.Suitable interfacial phase can protect fiber, makes fiber damage reduction in matrix material preparation process; The more important thing is, interfacial phase also can protect fiber from the burn into oxidation in technique and use procedure, interfacial chemical reaction and physical abuse, significantly improves the mechanical property of matrix material.
The interfacial phase coating be applied in ceramic matric composite mainly contains RESEARCH OF PYROCARBON (PyC) coating, boron nitride (BN) coating, silicon carbide (SiC) coating etc.PyC coating significantly can improve the mechanical property of matrix material as interfacial phase, and it is applied in SiC ceramic based composites the earliest as interfacial phase.PyC coating has the layered crystal structure along Fiber Distribution, and has suitable interlaminar shear strength and bonding strength, but the oxidation-resistance of PyC is poor, make the matrix material containing PyC coating interface phase the degradation of high temperature oxidation stability environment serious.BN has and layered crystal structure like graphite-like, and the antioxidant property of BN is better than PyC, is also the conventional interfacial phase coating of ceramic matric composite; But when temperature can be oxidized generation B higher than BN when 850 DEG C
2o
3, cause material property to decline serious, the use temperature of the matrix material therefore containing BN coating interface phase is still limited.The oxidation-resistance of SiC coating is better, can use, but form strong interfacial bond between SiC and mullite fiber, cause easily extending in fiber in the crack growth process of matrix, be unfavorable for the performance of fiber reinforcement effect between 800 DEG C ~ 900 DEG C.
Summary of the invention
Technical problem to be solved by this invention is, overcome the deficiency and defect mentioned in above background technology, the C/ (SiC/BN) that can be used as between the fiber of ceramic matric composite and matrix that a kind of physical chemistry consistency is good, high temperature resistant, anti-oxidant, toughening effect is good is provided
ncompound interface phase coating, also correspondingly provides the aforementioned C/ (SiC/BN) that a kind of technological process is simple, good product performance, cost are low
nthe preparation method of compound interface phase coating.
For solving the problems of the technologies described above, the technical scheme that the present invention proposes is a kind of C/ (SiC/BN) that can be used as between the fiber of ceramic matric composite and matrix
ncompound interface phase coating, described compound interface phase coating has periodic stack structure, and described periodic stack structure specifically refers to the alternating cyclical superposition of SiC layer, BN layer; And what directly contact with C layer in described periodic stack is SiC layer, outermost layer is then preferably BN layer.
Technique scheme of the present invention is mainly based on following thinking: compound interface phase coating is as the connecting material between fiber and matrix, interface bond strength is excessively strong, brittle rupture is produced during ceramic matric composite fracture, be unfavorable for the property sent out of the toughness reinforcing performance of ceramic fiber, and interface bond strength is excessively weak, matrix carry load cannot effectively be passed on, and is unfavorable for the property sent out that ceramic fiber is strengthened the property.And C coating and fibrous physics chemical compatibility good, have along fiber direction distribution laminate structure, interface bond strength and interlaminar shear strength are desirable first floor material, be conducive to crackle in layer deviation, turn to, bifurcated, consume energy-to-break.In the structure design of above-mentioned compound interface phase of the present invention, we creatively select toughening effect preferably BN layer and the good SiC layer of high-temperature oxidation resistance, constitute the C/ (SiC/BN) in compound interface phase coating
nperiodic stack.In this compound interface phase coating, anisotropic C, BN have the laminate structure of stacking, be conducive to matrix cracking turning to and bifurcated in inside, the requirement of low modulus and low sheraing intensity can be met simultaneously, effectively can also make up the textural defect of fiber surface, fiber is strengthened, but aerial C oxidation is by about 450 DEG C, the oxidation of BN is by about 800 DEG C, generally there is passive oxidation in SiC, CVD SiC can play " blocking layer " effect stoping and reflect matrix cracking diffusion in the well-oxygenated environment of 800 DEG C ~ 1000 DEG C.The oxide compound of BN is liquid at relatively high temperatures, can be oxidized the SiO generated with SiC layer
2reaction generates a kind of borosilicate glass, has certain obstruct and Healing to interface oxidation.Therefore, (SiC/BN)
nperiodic structure itself possesses certain resistance of oxidation.Visible, toughening effect preferably BN and the good SiC of high-temperature oxidation resistance is selected in the structure design of interfacial phase of the present invention, periodic stack in composition compound interface phase coating, it is especially suitable for use as the interfacial phase coating between the fiber of ceramic matric composite and matrix.In addition, our research also shows, because C, BN layer forms weak interface cohesion, C, SiC layer form strong interface cohesion, and therefore, the combination of C-BN is unfavorable for the performance of fiber reinforcement effect, and the combination of C-SiC and BN-SiC, then can significantly improve interface bond strength.Visible, the present invention has done accurate design and creationary adjustment to whole coating structure.
Above-mentioned C/ (SiC/BN)
nin compound interface phase coating, preferably, the lamination cycle cycle times of described periodic stack is 3 ~ 5 times; BN layer in described compound interface phase coating has the turbostratic of anisotropic.C/ (SiC/BN)
ncompound interface phase coating preferably comprises multilayer BN turbostratic, just because of the turbostratic that anisotropy BN has, do not refer to that all stacking lamellas are all parallel with fibrous matrix surface, crackle deviation wherein just becomes easy with turning to, crackle along BN stacking lamella direction change and ideally realize turning to, crackle is at C/ (SiC/BN)
nthe subgrade of compound interface phase is inner, between subgrade, there occurs deviation, bifurcated and turn between interface and fibrous matrix, and consume a large amount of energy-to-break, lead crack is divided into multiple tiny crack, and this just can increase toughness of material, improve its damage tolerance.Generally, in same period, the thickness of BN layer should not be less than the thickness of SiC layer, is preferably greater than the thickness of SiC layer.
Above-mentioned C/ (SiC/BN)
nin compound interface phase coating, preferably, the thickness of described C layer is 15.0nm ~ 20.0nm, and the thickness in monolayer of described BN layer is 20.0nm ~ 50.0nm, and the thickness in monolayer of described SiC layer is 8.0nm ~ 25.0nm.
As a total technical conceive, the present invention also provides a kind of coated fibre, comprises the coating of fibrous matrix and fibrous matrix surface-coated, and described coating is above-mentioned C/ (SiC/BN)
ncompound interface phase coating, described fibrous matrix is the one in mullite fiber, carbon fiber, silicon carbide fiber, silica fiber.In coated fibre of the present invention, coating be all be connected in the mode of mechanical bond and chemical bonding between fibrous matrix, each subgrade.
As a total technical conceive, the present invention also provides a kind of preparation method of above-mentioned coated fibre, comprises the following steps:
(1) prepare fiber-based material, adopt chemical gaseous phase depositing process first to deposit one deck C layer on the surface of fiber-based material;
(2) adopt chemical gaseous phase depositing process at the surperficial alternating deposit SiC layer of the C layer of above-mentioned fiber-based material and BN layer, the number of times of repetition alternating deposit 3 ~ 5 times; Obtain coated fibre.
In above-mentioned preparation method, first chemical vapour deposition C layer, and then with liquid precursor (preferred borazine, Polycarbosilane) for raw material, adopt chemical vapour deposition (CVD) technique, by alternately changing the mode of source of the gas in C subgrade surface preparation (SiC/BN)
nperiodically coating.The device preparing BN, SiC subgrade for CVD in the present invention comprises: CVD (Chemical Vapor Deposition) chamber (tube furnace), temperature controlling system, pressure control system, flow control system, vacuum pump, gas import and discharge system etc.
Above-mentioned preparation method, preferably, in described step (1), the chemical vapor deposition conditions of C layer comprises: take propylene as presoma, and precursor gas source flux is 30.0sccm ~ 70.0sccm, and reaction pressure is 50Pa ~ 400Pa, argon gas is carrier gas, argon gas is carrier gas, and depositing temperature is 900 DEG C ~ 1000 DEG C, and depositing time is 30.0min ~ 40.0min.
Above-mentioned preparation method, preferably, in described step (2), the chemical vapor deposition conditions of SiC layer comprises: with liquid Polycarbosilane for presoma, precursor gas source flux is 25.0sccm ~ 60.0sccm, and reaction pressure is 100Pa ~ 400Pa, and carrier gas and carrier gas are argon gas, depositing temperature is 1000 DEG C ~ 1100 DEG C, and depositing time is 20.0min ~ 50.0min.
Above-mentioned preparation method, preferably, in described step (2), the chemical vapor deposition conditions of BN layer comprises: take borazine as presoma, precursor gas source flux is 40.0sccm ~ 80.0sccm, and reaction pressure is 60Pa ~ 300Pa, and carrier gas and carrier gas are hydrogen, depositing temperature is 800 DEG C ~ 1000 DEG C, depositing time 20.0min ~ 40.0min.
Technique scheme of the present invention is mainly based on following thinking: C, BN, SiC are formed multi-layer composite coatings interfacial phase by the present invention, can improve the oxidation-protective effect of interfacial phase coating further, widen the use temperature scope of matrix material.BN has excellent antioxidant property below 900 DEG C, and SiC only could be oxidized formation continuous print SiO more than 900 DEG C
2film and show good oxidation-protective effect, and the oxidation products B of BN, SiC
2o
3, SiO
2formation continuous film can be melted mutually, thus effectively slow down the further oxidation of material.In addition, the first floor adopts C coating, is conducive to the combination between fiber and matrix, and in interfacial phase coating, introduce BN, SiC subgrade, crackle can deflect between each subgrade, there is multistage toughening mechanisms, can play significant toughening effect to matrix material simultaneously.
Compared with prior art, the invention has the advantages that:
1. C/ of the present invention (SiC/BN)
ncompound interface phase coating adopts multi-layer structure design, and make use of combined type and be coated with layer function superposition and mutual supplement with each other's advantages principle, flexible C layer and the BN layer selecting chemical vapour deposition mutually, the two all has random layer stacking feature, is conducive to crackle at C/ (SiC/BN)
nbetween subgrade inside, subgrade, there is deviation, bifurcated between interface and fiber and turn to, consuming energy-to-break, lead crack can be made to be divided into multiple tiny crack, increasing toughness of material, improve its damage tolerance; In addition, C/ (SiC/BN)
ncan there is passive oxidation in the SiC in periodic structure, the vitreous state SiO of generation in 800 DEG C ~ 1000 DEG C well-oxygenated environments
2matrix cracking can be made up, suppress the oxidation of its internal structure and material.Therefore, C/ (SiC/BN)
nperiodic structure itself possesses certain resistance of oxidation, higher relative to simple BN coating use temperature, better relative to simple SiC coating toughening effect.
2. the present invention prepares by CVD the halogenide BX that the maximum precursor of BN coatings applications is boron
3(as BF
3, BCl
3, BBr
3) and NH
3the precursor that SiC coating is commonly used the most is trichloromethyl silane (MTS), but such system exists self and byproduct of reaction corrodibility is strong, serious to equipment corrosion, and by product ammonium salt easy pollution deposit room blocking pipe, reactant and product are to deficiencies such as fiber seriously corrodeds.The precursor that the present invention adopts borazine to prepare as SiC subgrade as BN subgrade, Polycarbosilane, the corrosive elements such as both are all not halogen-containing, can not generate corrosive byproducts, and ceramic conversion rate are high.
3. the present invention is by alternately changing the mode of precursor source of the gas, when not transfer fiber matrix, continues depositing subsequent subgrade, simplifies coating deposition process, improve the consistence of each subgrade mode of deposition.
On the whole, the present invention, by the design to the optimization of processing parameter, coating and subgrade thickness, finally obtains the nanostructure C/ (SiC/BN) that a kind of physical chemistry consistency is good, high temperature resistant, anti-oxidant, toughening effect is good
ncompound interface phase coating, significant to raising FRCMC performance (especially mullite fiber or carbon fiber ceramic based composites).
Accompanying drawing explanation
In order to be illustrated more clearly in the embodiment of the present invention or technical scheme of the prior art, be briefly described to the accompanying drawing used required in embodiment or description of the prior art below, apparently, accompanying drawing in the following describes is some embodiments of the present invention, for those of ordinary skill in the art, under the prerequisite not paying creative work, other accompanying drawing can also be obtained according to these accompanying drawings.
Fig. 1 is C/ (SiC/BN) in the embodiment of the present invention 1
nthe transmission electron microscope picture (low resolution) of compound interface phase coating.
Fig. 2 is C/ (SiC/BN) in the embodiment of the present invention 1
nthe transmission electron microscope picture (high resolution) of compound interface phase coating SiC and BN subgrade.
Fig. 3 is C/ (SiC/BN) in the embodiment of the present invention 1
nthe distribution diagram of element of compound interface phase coating.
Embodiment
For the ease of understanding the present invention, hereafter will do to describe more comprehensively, meticulously to the present invention in conjunction with Figure of description and preferred embodiment, but protection scope of the present invention is not limited to following specific embodiment.
Unless otherwise defined, hereinafter used all technical terms are identical with the implication that those skilled in the art understand usually.The object of technical term used herein just in order to describe specific embodiment is not be intended to limit the scope of the invention.
Unless otherwise specified, the various starting material, reagent, instrument and equipment etc. used in the present invention are all bought by market and are obtained or prepare by existing method.
Embodiment 1:
As shown in Figure 1, Figure 2, Figure 3 shows, a kind of C/ (SiC/BN) that can be used as between the silicon carbide fiber of ceramic matric composite and matrix of the present invention
ncompound interface phase coating, this compound interface phase coating has periodic stack structure, and this periodic stack structure specifically refers to the alternating cyclical superposition of SiC layer, BN layer, and in the present embodiment, the lamination cycle cycle times of periodic stack is 3 times.Concrete, the thickness of C layer is 20.0nm from the inside to the outside, the thickness of SiC first subgrade is 25.0nm, the thickness of BN first subgrade is 25.0nm, the thickness of SiC second subgrade is 8.0nm, the thickness of BN second subgrade be 20.0nm, SiC the 3rd the thickness of subgrade be 20.0nm, BN the 3rd the thickness of subgrade be 50.0nm.
A kind of coated fibre of the present invention, comprise the coating of fibrous matrix and fibrous matrix surface-coated, this coating is the C/ (SiC/BN) of above-mentioned the present embodiment
ncompound interface phase coating, fibrous matrix is silicon carbide fiber.In coated fibre of the present invention, coating be all be connected in the mode of mechanical bond and chemical bonding between fibrous matrix, each subgrade.
The preparation method of the coated fibre of the present embodiment, comprises the following steps:
(1) the surface deposition one deck C layer of method at silicon carbide fiber matrix of chemical vapour deposition is adopted; The mode of deposition of C layer is as follows: propylene is presoma, and precursor gas source flux is 70.0sccm, and reaction pressure is 400Pa, and using argon gas as carrier gas and carrier gas, depositing temperature is 1000 DEG C, depositing time 40.0min;
(2) the C layer surface deposition one deck SiC layer of method at fibrous matrix of chemical vapour deposition is adopted; The mode of deposition of SiC layer is as follows: with liquid Polycarbosilane for presoma, and precursor gas source flux is 60.0sccm, and reaction pressure is 400Pa, take argon gas as carrier gas and carrier gas, and depositing temperature is 1100 DEG C, depositing time 50.0min;
(3) the SiC layer surface deposition one deck BN layer of method at fibrous matrix of chemical vapour deposition is adopted; The mode of deposition of BN layer is as follows: take borazine as presoma, and precursor gas source flux is 40.0sccm, and reaction pressure is 60Pa, take hydrogen as carrier gas and carrier gas, and depositing temperature is 800 DEG C, depositing time 25.0min;
(4) continuing the main operation repeating above-mentioned steps (2) on BN layer surface, is only that depositing time changes 20.0min into;
(5) repeating above-mentioned steps (3), is only that depositing time changes 20.0min into;
(6) repeating above-mentioned steps (4), is only that depositing time changes 40.0min into;
(7) repeating above-mentioned steps (3), is only that depositing time changes 40.0min into;
The device preparing BN, SiC subgrade for CVD in the present embodiment comprises: CVD (Chemical Vapor Deposition) chamber (tube furnace), temperature controlling system, pressure control system, flow control system, vacuum pump, gas import and discharge system etc., obtain coated fibre after having deposited.
By transmission electron microscope observing, C/ (SiC/BN) prepared by the present embodiment
nas shown in Figure 1, transmission electron microscope shows this coating uniform and is intactly covered in SiC fiber surface compound interface phase coating, and coating is combined with fiber surface closely, without defects such as holes.In coating, each subgrade thickness is even, and each subgrade uniform ingredients, the transmission electron microscope picture of compound interface phase coating SiC and BN subgrade as shown in Figure 2, as seen from Figure 2, occurs a small amount of microlitic structure in SiC subgrade, and BN subgrade is non-microstructure.Fig. 3 is C/ (SiC/BN) in the embodiment of the present invention 1
nthe distribution diagram of element of compound interface phase coating, as can be seen from Fig. 3, the Si Elemental redistribution in top coat is mainly in SiC subgrade, and the distribution of first floor C element is comparatively concentrated, N element is mainly distributed in the middle of BN subgrade, illustrates that fiber surface coating sandwich is more obvious.
Embodiment 2:
A kind of C/ (SiC/BN) that can be used as between the silicon carbide fiber of ceramic matric composite and matrix of the present invention
ncompound interface phase coating, this compound interface phase coating has periodic stack structure, and this periodic stack structure specifically refers to the alternating cyclical superposition of SiC layer, BN layer, and in the present embodiment, the lamination cycle cycle times of periodic stack is 5 times.Concrete, from the inside to the outside the thickness of C layer be 15.0nm, SiC first the thickness of subgrade be 8.0nm, BN first the thickness of subgrade be 20.0nm, the thickness of SiC second subgrade is 18.0nm, the thickness of BN second subgrade be 25.0nm, SiC the 3rd the thickness of subgrade be 25.0nm, BN the 3rd the thickness of subgrade be 50.0nm, the thickness of SiC the 4th subgrade is 25.0nm, the thickness of BN the 4th subgrade be 50.0nm, SiC the 5th the thickness of subgrade be 25.0nm, BN the 5th the thickness of subgrade be 50.0nm.
A kind of coated fibre of the present invention, comprise the coating of fibrous matrix and fibrous matrix surface-coated, this coating is the C/ (SiC/BN) of above-mentioned the present embodiment
ncompound interface phase coating, fibrous matrix is carbon fiber.In coated fibre of the present invention, coating be all be connected in the mode of mechanical bond and chemical bonding between fibrous matrix, each subgrade.
The preparation method of the coated fibre of the present embodiment, comprises the following steps:
(1) the surface deposition one deck C layer of method in carbon fiber substrate of chemical vapour deposition is adopted; The mode of deposition of C layer is as follows: propylene is presoma, and precursor gas source flux is 30.0sccm, and reaction pressure is 50Pa, and using argon gas as carrier gas and carrier gas, depositing temperature is 900 DEG C, depositing time 30.0min;
(2) the C layer surface deposition one deck SiC layer of method at fibrous matrix of chemical vapour deposition is adopted; The mode of deposition of SiC layer is as follows: with liquid Polycarbosilane for presoma, and precursor gas source flux is 25.0sccm, and reaction pressure is 100Pa, take argon gas as carrier gas and carrier gas, and depositing temperature is 1100 DEG C, depositing time 20.0min;
(3) the SiC layer surface deposition one deck BN layer of method at fibrous matrix of chemical vapour deposition is adopted; The mode of deposition of BN layer is as follows: take borazine as presoma, and precursor gas source flux is 80.0sccm, and reaction pressure is 60Pa, take hydrogen as carrier gas and carrier gas, and depositing temperature is 1000 DEG C, depositing time 20.0min;
(4) continuing the main operation repeating above-mentioned steps (2) on BN layer surface, is only that depositing time changes 35.0min into;
(5) repeating above-mentioned steps (3), is only that depositing time changes 25.0min into;
(6) repeating above-mentioned steps (4), is only that depositing time changes 50.0min into;
(7) repeating above-mentioned steps (3), is only that depositing time changes 40.0min into;
(8) repeating above-mentioned steps (4), is only that depositing time changes 50.0min into;
(9) repeating above-mentioned steps (3), is only that depositing time changes 40.0min into;
(10) repeating above-mentioned steps (4), is only that depositing time changes 50.0min into;
(11) repeating above-mentioned steps (3), is only that depositing time changes 40.0min into;
The device preparing BN, SiC subgrade for CVD in the present embodiment comprises: CVD (Chemical Vapor Deposition) chamber (tube furnace), temperature controlling system, pressure control system, flow control system, vacuum pump, gas import and discharge system etc., obtain coated fibre after having deposited.
By transmission electron microscope observing, C/ (SiC/BN) prepared by the present embodiment
nin compound interface phase coating, this coating uniform is intactly covered in fiber C surface, and coating is combined with fiber surface closely, without defects such as holes.In coating, each subgrade thickness is even, and each subgrade uniform ingredients, occurs a small amount of microlitic structure in the SiC subgrade of compound interface phase coating, and BN subgrade is non-microstructure.
Claims (8)
1. one kind can be used as the C/ (SiC/BN) between the fiber of ceramic matric composite and matrix
ncompound interface phase coating, is characterized in that, described compound interface phase coating comprises C layer and is coated on the periodic stack on C layer, and described periodic stack specifically refers to the alternating cyclical superposition of SiC layer, BN layer; And what directly contact with C layer in described periodic stack is SiC layer.
2. C/ according to claim 1 (SiC/BN)
ncompound interface phase coating, is characterized in that, the lamination cycle cycle times of described periodic stack is 3 ~ 5 times; In described compound interface phase coating, in same period, the thickness of BN layer is not less than the thickness of SiC layer.
3. C/ according to claim 1 and 2 (SiC/BN)
ncompound interface phase coating, is characterized in that, the thickness of described C layer is 15.0nm ~ 20.0nm, and the thickness in monolayer of described BN layer is 20.0nm ~ 50.0nm, and the thickness in monolayer of described SiC layer is 8.0nm ~ 25.0nm.
4. a coated fibre, comprises the coating of fibrous matrix and fibrous matrix surface-coated, it is characterized in that, the C/ of described coating according to any one of claims 1 to 3 (SiC/BN)
ncompound interface phase coating, described fibrous matrix is the one in mullite fiber, carbon fiber, silicon carbide fiber, silica fiber.
5. a preparation method for coated fibre as claimed in claim 4, comprises the following steps:
(1) prepare fiber-based material, adopt chemical gaseous phase depositing process first to deposit one deck C layer on the surface of fiber-based material;
(2) adopt chemical gaseous phase depositing process at the surperficial alternating deposit SiC layer of the C layer of above-mentioned fiber-based material and BN layer, the number of times of repetition alternating deposit 3 ~ 5 times; Obtain coated fibre.
6. preparation method according to claim 5, it is characterized in that, in described step (1), the chemical vapor deposition conditions of C layer comprises: take propylene as presoma, and precursor gas source flux is 30.0sccm ~ 70.0sccm, and reaction pressure is 50Pa ~ 400Pa, argon gas is carrier gas, argon gas is carrier gas, and depositing temperature is 900 DEG C ~ 1000 DEG C, and depositing time is 30.0min ~ 40.0min.
7. the preparation method according to claim 5 or 6, it is characterized in that, in described step (2), the chemical vapor deposition conditions of SiC layer comprises: with liquid Polycarbosilane for presoma, precursor gas source flux is 25.0sccm ~ 60.0sccm, and reaction pressure is 100Pa ~ 400Pa, and carrier gas and carrier gas are argon gas, depositing temperature is 1000 DEG C ~ 1100 DEG C, and depositing time is 20.0min ~ 50.0min.
8. the preparation method according to claim 5 or 6, it is characterized in that, in described step (2), the chemical vapor deposition conditions of BN layer comprises: take borazine as presoma, precursor gas source flux is 40.0sccm ~ 80.0sccm, and reaction pressure is 60Pa ~ 300Pa, and carrier gas and carrier gas are hydrogen, depositing temperature is 800 DEG C ~ 1000 DEG C, depositing time 20.0min ~ 40.0min.
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| CN113354435A (en) * | 2021-07-08 | 2021-09-07 | 西北工业大学 | SiC fibre reinforcement and toughening (SiC-BN)mMulti-element multi-layer self-healing ceramic matrix composite and preparation method thereof |
| CN114804895A (en) * | 2022-06-02 | 2022-07-29 | 中国航发北京航空材料研究院 | High-temperature self-healing BN/SiC fiber interface coating and preparation method thereof |
| CN116199519A (en) * | 2023-01-17 | 2023-06-02 | 中国科学院上海硅酸盐研究所 | Double BN interface layer fiber reinforced ceramic matrix composite material and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102167612A (en) * | 2011-01-14 | 2011-08-31 | 中国人民解放军国防科学技术大学 | Preparation method of boron nitride coating on fiber surface |
| CN104030715A (en) * | 2014-06-25 | 2014-09-10 | 中国人民解放军国防科学技术大学 | Preparation method of Cf/BN-SiC composite material |
-
2015
- 2015-04-21 CN CN201510190624.9A patent/CN104788130B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102167612A (en) * | 2011-01-14 | 2011-08-31 | 中国人民解放军国防科学技术大学 | Preparation method of boron nitride coating on fiber surface |
| CN104030715A (en) * | 2014-06-25 | 2014-09-10 | 中国人民解放军国防科学技术大学 | Preparation method of Cf/BN-SiC composite material |
Non-Patent Citations (1)
| Title |
|---|
| R.R. NASLAIN ET AL.: "Synthesis of highly tailored ceramic matrix composites by pressure-pulsed CVI", 《SOLID STATE IONICS》 * |
Cited By (18)
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| CN105237020B (en) * | 2015-08-31 | 2018-08-24 | 中国人民解放军国防科学技术大学 | A kind of fibre reinforced ZrB2- ZrN multiphase ceramic matrix composites and preparation method thereof |
| CN105237020A (en) * | 2015-08-31 | 2016-01-13 | 中国人民解放军国防科学技术大学 | Carbon fiber-enhanced ZrB2-ZrN composite ceramic-based composite material and preparation method thereof |
| CN106747671A (en) * | 2016-06-03 | 2017-05-31 | 北京航空航天大学 | The preparation method of superhigh temperature thermostructural composite boundary layer |
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| CN106747671B (en) * | 2016-06-03 | 2017-12-12 | 北京航空航天大学 | The preparation method of superhigh temperature thermostructural composite boundary layer |
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| CN106431448A (en) * | 2016-10-20 | 2017-02-22 | 中南大学 | Boron nitride/silicon carbide composite coating layer and preparation method thereof |
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| CN109608208A (en) * | 2018-12-17 | 2019-04-12 | 中国科学院上海硅酸盐研究所 | A kind of multilayer interface coating and its preparation method and application |
| CN109608208B (en) * | 2018-12-17 | 2021-12-31 | 中国科学院上海硅酸盐研究所 | Multilayer interface coating and preparation method and application thereof |
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| CN113354435A (en) * | 2021-07-08 | 2021-09-07 | 西北工业大学 | SiC fibre reinforcement and toughening (SiC-BN)mMulti-element multi-layer self-healing ceramic matrix composite and preparation method thereof |
| CN114804895A (en) * | 2022-06-02 | 2022-07-29 | 中国航发北京航空材料研究院 | High-temperature self-healing BN/SiC fiber interface coating and preparation method thereof |
| CN116199519A (en) * | 2023-01-17 | 2023-06-02 | 中国科学院上海硅酸盐研究所 | Double BN interface layer fiber reinforced ceramic matrix composite material and preparation method thereof |
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