CN116375474B - A welding type boron carbide composite ceramic and its preparation method and application - Google Patents
A welding type boron carbide composite ceramic and its preparation method and application Download PDFInfo
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- CN116375474B CN116375474B CN202310329222.7A CN202310329222A CN116375474B CN 116375474 B CN116375474 B CN 116375474B CN 202310329222 A CN202310329222 A CN 202310329222A CN 116375474 B CN116375474 B CN 116375474B
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- 229910052580 B4C Inorganic materials 0.000 title claims abstract description 162
- INAHAJYZKVIDIZ-UHFFFAOYSA-N boron carbide Chemical compound B12B3B4C32B41 INAHAJYZKVIDIZ-UHFFFAOYSA-N 0.000 title claims abstract description 162
- 239000002131 composite material Substances 0.000 title claims abstract description 144
- 239000000919 ceramic Substances 0.000 title claims abstract description 137
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 238000005493 welding type Methods 0.000 title claims abstract description 9
- 239000000843 powder Substances 0.000 claims abstract description 146
- 229910052751 metal Inorganic materials 0.000 claims abstract description 87
- 239000002184 metal Substances 0.000 claims abstract description 87
- 239000002002 slurry Substances 0.000 claims abstract description 87
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims abstract description 59
- 239000011248 coating agent Substances 0.000 claims abstract description 45
- 238000000576 coating method Methods 0.000 claims abstract description 45
- 238000005245 sintering Methods 0.000 claims abstract description 31
- 238000002156 mixing Methods 0.000 claims abstract description 30
- 229910044991 metal oxide Inorganic materials 0.000 claims abstract description 16
- 150000004706 metal oxides Chemical class 0.000 claims abstract description 16
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims abstract description 8
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052796 boron Inorganic materials 0.000 claims abstract description 6
- 239000006260 foam Substances 0.000 claims abstract description 6
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 claims abstract 6
- 229910001928 zirconium oxide Inorganic materials 0.000 claims abstract 6
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 114
- 238000001035 drying Methods 0.000 claims description 35
- 239000012299 nitrogen atmosphere Substances 0.000 claims description 16
- 229910001069 Ti alloy Inorganic materials 0.000 claims description 13
- 235000015895 biscuits Nutrition 0.000 claims description 12
- 229910000838 Al alloy Inorganic materials 0.000 claims description 10
- 229910000831 Steel Inorganic materials 0.000 claims description 8
- 229910045601 alloy Inorganic materials 0.000 claims description 8
- 239000000956 alloy Substances 0.000 claims description 8
- 239000000463 material Substances 0.000 claims description 8
- 239000010959 steel Substances 0.000 claims description 8
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- 239000007789 gas Substances 0.000 claims description 6
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- 229910000990 Ni alloy Inorganic materials 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910018575 Al—Ti Inorganic materials 0.000 claims description 3
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims description 3
- 239000000758 substrate Substances 0.000 claims description 3
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 2
- 239000012298 atmosphere Substances 0.000 claims description 2
- 239000011159 matrix material Substances 0.000 abstract description 13
- 239000011224 oxide ceramic Substances 0.000 abstract 2
- 229910052574 oxide ceramic Inorganic materials 0.000 abstract 2
- 238000000498 ball milling Methods 0.000 description 29
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 14
- 239000004721 Polyphenylene oxide Substances 0.000 description 12
- 229920000570 polyether Polymers 0.000 description 12
- 239000007787 solid Substances 0.000 description 10
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- 229920005646 polycarboxylate Polymers 0.000 description 9
- 230000007704 transition Effects 0.000 description 9
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- 229920005830 Polyurethane Foam Polymers 0.000 description 7
- DPXJVFZANSGRMM-UHFFFAOYSA-N acetic acid;2,3,4,5,6-pentahydroxyhexanal;sodium Chemical compound [Na].CC(O)=O.OCC(O)C(O)C(O)C(O)C=O DPXJVFZANSGRMM-UHFFFAOYSA-N 0.000 description 7
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- 235000019812 sodium carboxymethyl cellulose Nutrition 0.000 description 7
- 229920001027 sodium carboxymethylcellulose Polymers 0.000 description 7
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- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 6
- 150000003863 ammonium salts Chemical class 0.000 description 6
- 229910002110 ceramic alloy Inorganic materials 0.000 description 6
- 229910010293 ceramic material Inorganic materials 0.000 description 6
- 238000003466 welding Methods 0.000 description 6
- 238000000034 method Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000001125 extrusion Methods 0.000 description 4
- 239000011148 porous material Substances 0.000 description 4
- 159000000000 sodium salts Chemical class 0.000 description 4
- 239000002253 acid Substances 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 230000001105 regulatory effect Effects 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910018084 Al-Fe Inorganic materials 0.000 description 2
- 229910018192 Al—Fe Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000011065 in-situ storage Methods 0.000 description 2
- 239000002905 metal composite material Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000012071 phase Substances 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000010008 shearing Methods 0.000 description 2
- 229910018507 Al—Ni Inorganic materials 0.000 description 1
- 241000167857 Bourreria Species 0.000 description 1
- 108010015780 Viral Core Proteins Proteins 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 238000004026 adhesive bonding Methods 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- IDGUHHHQCWSQLU-UHFFFAOYSA-N ethanol;hydrate Chemical compound O.CCO IDGUHHHQCWSQLU-UHFFFAOYSA-N 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 238000000462 isostatic pressing Methods 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000007873 sieving Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 238000004901 spalling Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
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- 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
- C04B35/563—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 boron carbide
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F41—WEAPONS
- F41H—ARMOUR; ARMOURED TURRETS; ARMOURED OR ARMED VEHICLES; MEANS OF ATTACK OR DEFENCE, e.g. CAMOUFLAGE, IN GENERAL
- F41H1/00—Personal protection gear
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- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
- C04B2235/3225—Yttrium oxide or oxide-forming salts thereof
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Abstract
本发明涉及一种焊接型碳化硼复合陶瓷及其制备方法与应用。所述复合陶瓷具有碳化硼基体层/氧化铝涂层/氧化锆涂层结构；所述制备方法包括：将碳化硼粉体、第一金属粉体和金属氧化物粉体混合形成碳化硼复合浆料；将氧化铝粉体、第二金属粉体混合形成氧化铝复合浆料；将氧化锆粉体、第三金属粉体混合形成氧化锆复合浆料；将碳化硼复合浆料涂覆在有机泡沫骨架上，加压形成碳化硼陶瓷素坯，经第一次气压烧结，得碳化硼陶瓷预制体；将碳化硼陶瓷预制体浸渗于氧化铝复合浆料中，取出后经第二次气压烧结，制得碳化硼‑氧化铝陶瓷预制体；将碳化硼‑氧化铝陶瓷预制体浸渗于氧化锆复合浆料中，取出后经第三次气压烧结，得焊接型碳化硼复合陶瓷。The present invention relates to a welding type boron carbide composite ceramic and its preparation method and application. The composite ceramic has a boron carbide matrix layer/aluminum oxide coating/zirconium oxide coating structure; the preparation method comprises: mixing boron carbide powder, a first metal powder and a metal oxide powder to form a boron carbide composite slurry; mixing alumina powder and a second metal powder to form an alumina composite slurry; mixing zirconium oxide powder and a third metal powder to form a zirconium oxide composite slurry; coating the boron carbide composite slurry on an organic foam skeleton, pressurizing to form a boron carbide ceramic blank, and sintering the first time with gas pressure to obtain a boron carbide ceramic preform; impregnating the boron carbide ceramic preform in the alumina composite slurry, taking it out and sintering it for the second time with gas pressure to obtain a boron carbide-aluminum oxide ceramic preform; impregnating the boron carbide-aluminum oxide ceramic preform in the zirconium oxide composite slurry, taking it out and sintering it for the third time with gas pressure to obtain a welding type boron carbide composite ceramic.
Description
Technical Field
The invention belongs to the field of boron carbide ceramic materials, and particularly relates to a welded boron carbide composite ceramic, and a preparation method and application thereof.
Background
The ceramic material has the characteristics of good mechanical property, good electrochemical property, wear resistance, corrosion resistance, compact and uniform structure, low density, high strength, high hardness, high compressive strength and the like compared with the metal material. Currently, the bulletproof armor ceramics which are used in engineering at home and abroad mainly comprise boron carbide, aluminum oxide, silicon carbide and the like. In terms of the bulletproof principle of the material, under the action of a large impact force of a warhead, hard ceramic is combined with metal with good toughness, a ceramic material is used as a bullet impact surface of the composite structure, a metal material is used as a back lining surface of the composite structure, the bullets are passivated through the ceramic, the speed and the quality of the bullets are greatly reduced, and the metal material provides a strong back support to further brake the bullets and resist penetration of the bullets, so that the bulletproof effect is achieved.
However, in the actual service process, the constraint of the bulletproof ceramic is mainly that the ceramic sheet and the metal plate are bonded by using an adhesive, and a composite structure is formed by simple lamination. After a single bullet is impacted, the ceramic panel can be cracked and damaged in a larger area, and the bonding interface of the ceramic and the metal plate can also crack and delaminate, so that the composite bulletproof plate loses the ability of continuing to resist bullets. At present, the bulletproof ceramic plate and the metal plate are connected in a glue bonding mode, the constraint capacity of the ceramic-metal composite structure is poor, and the ceramic and metal connection strength is low.
The ceramic can form a firm integral structure with the metal through welding, so that the advantages of the ceramic in the aspects of hardness, modulus, high temperature resistance, corrosion resistance, heat conduction, insulation and the like can be effectively exerted, the defects of low toughness, low plasticity, processability, impact resistance, thermal shock resistance and the like of the ceramic are avoided, the application range of the ceramic material is greatly expanded, and the application value is improved. However, there are two major core difficulties with ceramic to metal solder connections: firstly, the difference of the thermal expansion coefficients of the two is large, and the thermal stress, residual stress and the like generated by heating and cooling can cause the damage of the connecting joint of the two in the welding and using processes; secondly, the wettability of the two is poor.
Disclosure of Invention
Aiming at the technical problems, the invention aims to provide a welded boron carbide composite ceramic and a preparation method and application thereof, so that the problems of difficult connection between the existing boron carbide ceramic and metal, poor bonding strength of a welded joint and the like are solved, and the matching property of the thermal expansion coefficients between the boron carbide ceramic and the metal and the bonding strength of a boron carbide ceramic-metal composite structure are improved.
In a first aspect, the invention provides a welded boron carbide composite ceramic, which has a boron carbide substrate layer/alumina coating/zirconia coating structure, wherein the thickness of the alumina coating is 50nm-300 mu m, and the thickness of the zirconia coating is 50nm-300 mu m;
the preparation method of the welded boron carbide composite ceramic comprises the following steps:
(1) Mixing boron carbide powder, first metal powder and metal oxide powder to form boron carbide composite slurry; based on the total mass of the boron carbide, the first metal and the metal oxide powder being 100%, the mass ratio of the boron carbide is 80-90 wt%, the mass ratio of the first metal is 1-10 wt%, and the mass ratio of the metal oxide is 1-15 wt%;
(2) Mixing alumina powder and second metal powder to form alumina composite slurry; the mass ratio of the aluminum oxide is 62 to 95 weight percent and the mass ratio of the second metal is 5 to 38 weight percent based on 100 percent of the total mass of the aluminum oxide and the second metal powder;
(3) Mixing zirconia powder and third metal powder to form zirconia composite slurry; the weight ratio of the zirconia is 62 to 95 percent and the weight ratio of the third metal is 5 to 38 percent based on 100 percent of the total weight of the zirconia and the third metal powder;
(4) Coating the boron carbide composite slurry on an organic foam skeleton, pressurizing to form a boron carbide ceramic biscuit, drying and performing first air pressure sintering to obtain a boron carbide ceramic preform;
(5) Impregnating the boron carbide ceramic preform into the alumina composite slurry, taking out, drying, and performing secondary air pressure sintering to obtain the boron carbide-alumina ceramic preform; and (3) impregnating the boron carbide-alumina ceramic preform into the zirconia composite slurry, taking out, drying, and performing third air pressure sintering to obtain the welded boron carbide composite ceramic.
Preferably, the first metal is at least one of Al, al-Si alloy, al-Fe alloy, al-Ni alloy and Al-Ti alloy; the second metal is at least one of Cr, mo, ti, ni, cu, WC, mn; the third metal is at least one of Cr, mo, ti, ni, cu, WC, mn.
Preferably, the metal oxide is TiO 2 、ZrO 2 、Y 2 O 3 、WO 2 、Fe 2 O 3 、Nb 2 O 5 、Cr 2 O 3 、CeO 2 At least one of them.
Preferably, the solid phase content of the alumina composite slurry is 75-90wt%; the solid phase content of the zirconia composite slurry is 75-90wt%.
Preferably, the temperature of the first, second and third air pressure sintering is 1350-1550 ℃, the heat preservation time is 1-3.5h, the air pressure is 2.5-4.5MPa, and the atmosphere is nitrogen atmosphere.
In a second aspect, the invention provides an application of the welded boron carbide composite ceramic in bulletproof materials.
Preferably, the ballistic resistant material comprises: the welding type boron carbide composite ceramic and the connecting metal plate welded on the welding type boron carbide composite ceramic.
Preferably, the connecting metal plate is a bulletproof steel plate, an aluminum alloy plate or a titanium alloy plate.
Advantageous effects
According to the invention, the thermal expansion coefficient and wettability of the boron carbide matrix are regulated and controlled through the doping gradient of the metal powder and the ceramic powder, and meanwhile, the composition and thickness of the boron carbide matrix layer/alumina coating/zirconia coating structure are dynamically regulated and controlled, so that the gradient transition of the thermal expansion coefficient is realized, and the residual stress of the composite ceramic material and the connecting joints of different metal plates is reduced. Through component design and transitional coating design, a microscopic region which can react with and combine with metal to a certain extent is formed in welding, wettability between the boron carbide ceramic and the metal is macroscopically increased, metallurgical combination between ceramics and the metal is formed, good welding performance is obtained, and the problems of large difference of thermal expansion coefficients, poor wettability and the like between the boron carbide ceramic and different metals are solved.
Detailed Description
The invention is further illustrated by the following embodiments, it being understood that the following embodiments are merely illustrative of the invention and not limiting thereof.
The invention provides a welded boron carbide composite ceramic and a preparation method thereof, and the welded boron carbide composite ceramic and the metal are connected with each other at high strength, so that the embedding and the combination of the metal and the boron carbide ceramic can be realized, and the problems of surface splashing, integral spalling and the like of a ceramic material under an impact condition can be greatly reduced, so that a bulletproof structure with higher performance can be further prepared.
Hereinafter, a method for preparing the welded boron carbide composite ceramic provided by the present invention is exemplified, and the method may include the following steps.
(1) And (3) preparing boron carbide composite slurry. Mixing boron carbide powder, first metal powder and metal oxide powder, taking absolute ethyl alcohol as a solvent, taking sodium carboxymethylcellulose (CMC) as a thickener, and uniformly mixing through a first ball mill to obtain the boron carbide composite slurry F1.
In some embodiments, the boron carbide powder may have a particle size of 0.5-30 μm.
In some embodiments, the first metal may be selected from at least one of Al, al-Si alloy, al-Fe alloy, al-Ni alloy, al-Ti alloy; the particle size of the first metal powder may be 0.5 to 20 μm. In the Al-Si alloy, the Al-Fe alloy, the Al-Ni alloy and the Al-Ti alloy, si, fe, ni, ti element can effectively improve the strength, the wear resistance, the processing performance, the casting performance and the heat conductivity of an Al alloy system, reduce the expansion coefficient of the Al alloy system, separate out a fine dispersed metastable strengthening phase, delay the migration of a grain boundary and ensure that the alloy has better high-temperature strength. The alloy system with aluminum as the main component can react with metal oxide in situ to generate high-entropy ceramic in the boron carbide matrix, so as to improve the thermal expansion coefficient of the boron carbide ceramic and the wettability with metal; the Si, fe, ni, ti element can also react with metal oxide and boron carbide to generate a new ceramic phase, further increase the thermal expansion coefficient of a matrix and the wettability with metal, and simultaneously promote the reduction of sintering temperature.
In some embodiments, the metal oxideTiO may be selected 2 、ZrO 2 、Y 2 O 3 、WO 2 、Fe 2 O 3 、Nb 2 O 5 、Cr 2 O 3 、CeO 2 At least one of (a) and (b); the particle size of the metal oxide powder may be 1-20 μm.
In some embodiments, the mass ratio of boron carbide may be 80 to 90wt%, the mass ratio of the first metal powder may be 1 to 10wt%, and the mass ratio of the metal oxide powder may be 1 to 15wt%, based on 100% of the total mass of boron carbide, the first metal powder, and the metal oxide powder.
The first ball milling may be planetary ball milling; the grinding ball is B 4 A ball C; the ball milling speed may be 120 to 180rpm and the ball milling time may be 1 to 5 hours, preferably 3 hours.
(2) And (3) preparing the alumina composite slurry. Mixing the alumina powder, the second metal powder, the first dispersing agent and the first defoaming agent, taking deionized water as a solvent, and uniformly mixing through a second ball mill to obtain the alumina composite slurry F2.
In some embodiments, the alumina powder may have a particle size of 0.5 to 20 μm.
In some embodiments, the second metal may be at least one of Cr, mo, ti, ni, cu, WC, mn; the particle size of the second metal powder may be 0.5-20 μm. The addition of the second metal can increase the thermal expansion coefficient of the alumina coating structure, facilitate the establishment of the transition of the thermal expansion coefficient from ceramic to metal, and improve the wettability between the ceramic and the metal.
In some embodiments, the mass ratio of the alumina may be 62 to 95wt% and the mass ratio of the second metal powder may be 5 to 38wt% based on 100% of the total mass of the alumina and the second metal.
In some embodiments, the first dispersant may be a polycarboxylate and the first defoamer may be a polyether.
The second ball milling may be planetary ball milling; the grinding balls are alumina grinding balls, the ball milling rotation speed can be 120-180rpm, and the ball milling time can be 1-5 hours, preferably 3 hours.
In some embodiments, the solid phase content of the alumina composite slurry F2 may be controlled to be 75-90wt%; the content of deionized water, the first dispersing agent, the first defoaming agent and the like is 10-25wt%.
(3) And (3) preparing zirconia composite slurry. Mixing zirconia powder, third metal powder, second dispersant and second defoamer, taking deionized water as a solvent, and uniformly mixing through third ball milling to obtain the zirconia composite slurry F3.
In some embodiments, the zirconia powder may have a particle size of 0.5-20 μm.
In some embodiments, the third metal may be at least one of Cr, mo, ti, ni, cu, WC, mn; the particle size of the third metal powder may be 0.5-20 μm. The addition of the third metal can improve the thermal expansion coefficient of the zirconia coating structure, so that the transition from the thermal expansion coefficient of the ceramic to the thermal expansion coefficient of the metal can be conveniently established, and meanwhile, the wettability between the ceramic and the metal is improved.
In some embodiments, the zirconia may be 62 to 95wt% and the third metal may be 5 to 38wt% based on 100% total zirconia, third metal.
In some embodiments, the second dispersant may be a polycarboxylate and the second defoamer may be a polyether.
The third ball milling may be planetary ball milling; the grinding balls are zirconia grinding balls, the ball milling rotation speed can be 120-180rpm, and the ball milling time can be 2-6 hours, preferably 3 hours.
In some embodiments, the solid phase content of the zirconia composite slurry F3 may be controlled to 75-90wt%; the content of deionized water, the second dispersing agent, the second defoaming agent and the like is 10-25wt%.
(4) And preparing a boron carbide ceramic preform. Uniformly coating the boron carbide composite slurry F1 prepared in the step (1) on organic foam, and uniformly distributing the slurry F1 on a framework of the organic foam through extrusion and air pressure to obtain a boron carbide ceramic biscuit M1; and drying the boron carbide ceramic biscuit M1 in a drying oven at 50-70 ℃ for 8 hours, and then performing first air pressure sintering in a nitrogen atmosphere to obtain the boron carbide ceramic preform M2.
In some embodiments, the organic foam may be a polyurethane foam and the pore size may be 10-300 μm.
In some embodiments, the temperature of the first gas pressure sintering may be 1350-1550 ℃, the holding time may be 1-3.5h, and the gas pressure may be 2.5-4.5MPa.
(5) And preparing the welded boron carbide composite ceramic. Completely impregnating the boron carbide ceramic preform M2 prepared in the step (4) into the alumina composite slurry F2 prepared in the step (2) for 0.1-1 hour, taking out, drying in a drying oven at 50-70 ℃ for 3 hours, and then performing secondary air pressure sintering in a nitrogen atmosphere to prepare the boron carbide ceramic preform M3; and (3) completely impregnating the boron carbide ceramic preform M3 into the zirconia composite slurry F3 prepared in the step (3) for 0.1-1 hour, taking out, drying in a drying box at 50-70 ℃ for 3 hours, and then performing third air pressure sintering in a nitrogen atmosphere to obtain the welded boron carbide composite ceramic.
The reason why the alumina composite slurry and the zirconia composite slurry are sequentially impregnated is that the thermal expansion coefficients of the boron carbide ceramic, the alumina ceramic and the zirconia ceramic, the titanium alloy, the steel, the aluminum alloy and the like of the welded metal matrix are sequentially increased, and the gradient transition of the thermal expansion coefficients from the ceramic matrix to the metal matrix can be realized by impregnating the transition alumina composite slurry and the zirconia composite slurry, so that the influence of the thermal expansion coefficient difference on the ceramic-metal connection is reduced. Wherein the boron carbide has a coefficient of thermal expansion of about (4.5-5.8) x 10 -6 At a temperature of about (6.8-7.6). Times.10 for alumina -6 At a temperature of about (9.0-10.5). Times.10 for zirconia -6 The titanium alloy has a thermal expansion coefficient of about (8.6-9.8). Times.10 at/DEG C -6 The thermal expansion coefficient of the steel is about (10-20) multiplied by 10 at the temperature of/DEG C -6 The thermal expansion coefficient of the aluminum alloy is about (18-23). Times.10 at/DEG C -6 /℃。
In some embodiments, the temperature of the second and third gas pressure sintering may be 1350-1550 ℃, the heat preservation time may be 1-3.5h, and the gas pressure may be 2.5-4.5MPa.
According to the invention, the metal alloy powder and the metal oxide powder react in situ in the boron carbide matrix, so that on one hand, the sintering temperature is reduced, and on the other hand, high-entropy ceramic is generated in the boron carbide matrix, and further, the thermal expansion coefficient of the boron carbide ceramic and the wettability with metal can be improved. Meanwhile, the transition design of the gradient thermal expansion coefficient of the boron carbide ceramic is realized by utilizing the alumina coating/zirconia coating structure.
The welded boron carbide composite ceramic with high strength, high toughness and gradient thermal expansion coefficient transition characteristics, which is obtained by the preparation method provided by the invention, has a boron carbide substrate layer/alumina coating/zirconia coating structure. Wherein the thickness of the alumina coating can be controlled to be 50nm-300 mu m, and the thickness of the zirconia coating can be controlled to be 50nm-300 mu m.
The shearing strength of the welded boron carbide composite ceramic and metal connecting joint provided by the invention is tested by combining an electronic universal tester with a pressing and shearing die. The shear strength of the welded boron carbide composite ceramic and metal connecting joint is 42-85MPa, and the comprehensive performance is excellent.
The welded boron carbide composite ceramic provided by the invention can be applied to bulletproof materials, and the bulletproof materials can comprise: a welded boron carbide composite ceramic, and a connection metal plate welded on the welded boron carbide composite ceramic; the connecting metal plates can be selected from bulletproof steel plates, aluminum alloy plates and titanium alloy plates.
According to the preparation method provided by the invention, the components and the thickness in the boron carbide matrix layer/alumina coating/zirconia coating structure can be dynamically regulated and controlled according to the difference of the connecting metal plates, and the weldable boron carbide ceramic with high strength, high toughness and gradient thermal expansion coefficient transition characteristic is prepared through air pressure sintering. Through the component design and the transitional coating design of the boron carbide composite ceramic, a micro area which is in reaction combination with the connecting metal plate can be formed in welding, the wettability between the boron carbide composite ceramic and the metal is macroscopically increased, the metallurgical combination between the ceramic and the metal is formed, and good welding performance is obtained.
The welded boron carbide composite ceramic provided by the invention can solve the technical problems of excessive interface stress, poor wettability, unsuitable material reaction performance, difficult formation of effective metallurgical bonding and the like caused by mismatch of thermal expansion coefficients between ceramic and metal, in particular bulletproof steel, aluminum alloy and titanium alloy.
The present invention will be described in more detail by way of examples. It should also be understood that the following examples are given by way of illustration only and are not to be construed as limiting the scope of the invention, since various insubstantial modifications and adaptations of the invention to those skilled in the art based on the foregoing disclosure are intended to be within the scope of the invention and the specific process parameters and the like set forth below are merely one example of a suitable range within which one skilled in the art would choose from the description herein without being limited to the specific values set forth below.
Example 1
(1) And (3) preparing boron carbide composite slurry. Taking B 4 C powder (90 wt.%), al-Ti alloy powder (2 wt.%), WO 2 Powder (1.6 wt.%), fe 2 O 3 Powder (1.6 wt.%), zrO 2 Powder (1.6 wt.%), Y 2 O 3 Powder (1.6 wt.%), nb 2 O 5 Mixing the powder (1.6wt%) with absolute ethyl alcohol as solvent, sodium carboxymethylcellulose (CMC) as thickener, adding B 4 And C, grinding the balls, and performing planetary ball milling for 3 hours at the rotating speed of 120rpm to obtain the boron carbide composite slurry F1.
(2) And (3) preparing the alumina composite slurry. Taking Al 2 O 3 Mixing the powder, ni powder, a polycarboxylic acid ammonium salt dispersing agent and a polyether defoaming agent, taking deionized water as a solvent, adding an alumina grinding ball, performing planetary ball milling for 3 hours, and obtaining an alumina composite slurry F2 (Al) with a solid content of 75wt% at a rotating speed of 150rpm 2 O 3 70wt% of powder and 5wt% of Ni powder).
(3) And (3) preparing zirconia composite slurry. Taking ZrO 2 Mixing the powder, WC powder, a polycarboxylic acid ammonium salt dispersing agent and a polyether defoamer, taking deionized water as a solvent, adding zirconia grinding balls, performing planetary ball milling for 3 hours at the rotating speed of 180rpm to obtain solid contentZirconia composite slurry F3 (ZrO 2 80wt% of powder and 10wt% of WC powder.
(4) And preparing a boron carbide ceramic preform. Uniformly coating the boron carbide composite slurry F1 prepared in the step (1) on polyurethane foam with the pore size of 300 mu M, and uniformly distributing the slurry F1 on a framework of the polyurethane foam by extrusion and air pressure to obtain a boron carbide ceramic biscuit M1; and drying the boron carbide ceramic biscuit M1 in a drying oven for 8 hours, and then performing air pressure sintering at 1550 ℃ under the nitrogen atmosphere of 2.5MPa for 1 hour to obtain the boron carbide ceramic preform M2.
(5) And preparing the welded boron carbide composite ceramic. Completely impregnating the boron carbide ceramic preform M2 prepared in the step (4) into the alumina composite slurry F2 prepared in the step (2) for 1 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1550 ℃ for 3.5 hours under the nitrogen atmosphere of 4.5MPa to prepare the boron carbide ceramic preform M3; and (3) completely impregnating the ceramic preform M3 into the zirconia composite slurry F3 prepared in the step (3) for 1 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1550 ℃ for 1.5 hours under the nitrogen atmosphere of 3MPa to obtain the welded boron carbide composite ceramic.
In the welded boron carbide composite ceramic prepared in example 1, the thickness of the alumina coating was about 52 μm, and the thickness of the zirconia coating was 64. Mu.m.
The shear strength of the welded boron carbide composite ceramic and aluminum alloy connecting joint prepared in the embodiment 1 is 42MPa through detection.
Example 2
(1) And (3) preparing boron carbide composite slurry. Taking B 4 C powder (80 wt%), al-Ni alloy powder (5 wt%), tiO 2 Powder (3 wt.%), WO 2 Powder (3 wt.%), zrO 2 Powder (3 wt%), Y 2 O 3 Powder (3 wt%), nb 2 O 5 Mixing the powder (3 wt%) with absolute ethanol as solvent, sodium carboxymethylcellulose (CMC) as thickener, adding B 4 And C, grinding the balls, and performing planetary ball milling for 3 hours at the rotating speed of 180rpm to obtain the boron carbide composite slurry F1.
(2) And (3) preparing the alumina composite slurry. Taking Al 2 O 3 Mixing the powder, ni powder, ti powder, a polycarboxylic acid ammonium salt dispersing agent and a polyether defoamer, taking deionized water as a solvent, adding an alumina grinding ball, performing planetary ball milling for 3 hours at a rotating speed of 150rpm to obtain an alumina composite slurry F2 (Al) with a solid content of 90wt% 2 O 3 80wt% of powder, 8wt% of Ni powder and 2wt% of Ti powder).
(3) And (3) preparing zirconia composite slurry. Taking ZrO 2 Mixing powder, WC powder, cr powder, a polycarboxylate ammonium salt dispersing agent and a polyether defoamer, taking deionized water as a solvent, adding zirconia grinding balls, performing planetary ball milling for 3 hours at a rotating speed of 120rpm to obtain zirconia composite slurry F3 (ZrO) with a solid content of 87wt% 2 78wt% of powder, 4wt% of WC powder and 5wt% of Cr powder.
(4) And preparing a boron carbide ceramic preform. Uniformly coating the boron carbide composite slurry F1 prepared in the step (1) on polyurethane foam with the pore size of 10 mu M, and uniformly distributing the slurry F1 on a framework of the polyurethane foam by extrusion and air pressure to obtain a boron carbide ceramic biscuit M1; and drying the boron carbide ceramic biscuit M1 in a drying oven for 8 hours, and then performing air pressure sintering at 1350 ℃ for 2 hours under a nitrogen atmosphere of 3MPa to obtain the boron carbide ceramic preform M2.
(5) And preparing the welded boron carbide composite ceramic. Completely impregnating the boron carbide ceramic preform M2 prepared in the step (4) into the alumina composite slurry F2 prepared in the step (2) for 0.5 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1350 ℃ for 2.3 hours under the nitrogen atmosphere of 4MPa to prepare the boron carbide ceramic preform M3; and (3) completely impregnating the ceramic preform M3 into the zirconia composite slurry F3 prepared in the step (3) for 0.1 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1350 ℃ for 1.8 hours under a nitrogen atmosphere of 3.6MPa to obtain the welded boron carbide composite ceramic.
In the welded boron carbide composite ceramic prepared in this example 2, the thickness of the alumina coating was 35 μm and the thickness of the zirconia coating was 48. Mu.m.
The shear strength of the welded joint of the welded boron carbide composite ceramic and the bulletproof steel plate prepared in the embodiment 2 is 61MPa through detection.
Example 3
(1) And (3) preparing boron carbide composite slurry. Taking B 4 C powder (86 wt.%), al-Ti alloy powder (4 wt.%), cr 2 O 3 Powder (2 wt.%), tiO 2 Powder (2 wt.%), zrO 2 Powder (2 wt%), Y 2 O 3 Powder (2 wt.%), ceO 2 Mixing the powder (2 wt%) with absolute ethyl alcohol as solvent, sodium carboxymethylcellulose (CMC) as thickener, adding B 4 And C, grinding the balls, and performing planetary ball milling for 3 hours at a rotating speed of 150rpm to obtain boron carbide composite slurry F1.
(2) And (3) preparing the alumina composite slurry. Taking Al 2 O 3 Mixing the powder, cu powder, a polycarboxylate ammonium salt dispersing agent and a polyether defoaming agent, taking deionized water as a solvent, adding an alumina grinding ball, performing planetary ball milling for 3 hours, and obtaining alumina composite slurry F2 (Al) with the solid content of 88wt% at the rotating speed of 180rpm 2 O 3 80wt% of powder and 8wt% of Cu powder).
(3) And (3) preparing zirconia composite slurry. Taking ZrO 2 Mixing powder, WC powder, ti powder, a polycarboxylate ammonium salt dispersing agent and a polyether defoamer, taking deionized water as a solvent, adding zirconia grinding balls, performing planetary ball milling for 3 hours at a rotating speed of 150rpm to obtain zirconia composite slurry F3 (ZrO) with a solid content of 90wt% 2 80wt% of powder, 8wt% of WC powder and 2wt% of Ti powder.
(4) And preparing a boron carbide ceramic preform. Uniformly coating the boron carbide composite slurry F1 prepared in the step (1) on polyurethane foam with the pore size of 30 mu M, and uniformly distributing the slurry F1 on a framework of the polyurethane foam by extrusion and air pressure to obtain a boron carbide ceramic biscuit M1; and drying the boron carbide ceramic biscuit M1 in a drying oven for 8 hours, and then performing air pressure sintering at 1380 ℃ for 2 hours under a nitrogen atmosphere of 3MPa to obtain the boron carbide ceramic preform M2.
(5) And preparing the welded boron carbide composite ceramic. Completely impregnating the boron carbide ceramic preform M2 prepared in the step (4) into the alumina composite slurry F2 prepared in the step (2) for 1 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1380 ℃ for 1.5 hours under the nitrogen atmosphere of 4MPa to prepare the boron carbide ceramic preform M3; and (3) completely impregnating the ceramic preform M3 into the zirconia composite slurry F3 prepared in the step (3) for 0.5 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1380 ℃ for 2 hours under a nitrogen atmosphere of 2.5MPa to obtain the welded boron carbide composite ceramic.
In the welded boron carbide composite ceramic prepared in example 3, the thickness of the alumina coating was 100 μm and the thickness of the zirconia coating was 85. Mu.m.
The shear strength of the welded boron carbide composite ceramic and titanium alloy connecting joint prepared in the embodiment 3 is 85MPa through detection.
Example 4
The preparation process is described in reference to example 1, with the main differences:
(1) And (3) preparing boron carbide composite slurry. Taking B 4 C powder (90 wt.%), al-Si alloy powder (2 wt.%), cr 2 O 3 Powder (1.6 wt.%), fe 2 O 3 Powder (1.6 wt.%), zrO 2 Powder (1.6 wt.%), tiO 2 Powder (1.6 wt.%), Y 2 O 3 Mixing the powder (1.6wt%) with absolute ethyl alcohol as solvent, sodium carboxymethylcellulose (CMC) as thickener, adding B 4 And C, grinding the balls, and performing planetary ball milling for 3 hours at the rotating speed of 120rpm to obtain the boron carbide composite slurry F1.
In the welded boron carbide composite ceramic prepared in example 4, the thickness of the alumina coating was 102 μm and the thickness of the zirconia coating was 78. Mu.m.
The shear strength of the welded boron carbide composite ceramic and aluminum alloy connecting joint prepared in the embodiment 4 is 58MPa through detection.
Example 5
The preparation process is described in reference to example 1, with the main differences:
(1) And (3) preparing boron carbide composite slurry. Taking B 4 C powder (82)wt% (8 wt%) Al-Fe alloy powder and Cr 2 O 3 Powder (2 wt.%), tiO 2 Powder (2 wt.%), fe 2 O 3 Powder (2 wt.%), ceO 2 Powder (2 wt%), nb 2 O 5 Mixing the powder (2 wt%) with absolute ethyl alcohol as solvent, sodium carboxymethylcellulose (CMC) as thickener, adding B 4 And C, grinding the balls, and performing planetary ball milling for 3 hours at the rotating speed of 120rpm to obtain the boron carbide composite slurry F1.
(2) And (3) preparing the alumina composite slurry. Taking Al 2 O 3 Mixing powder, WC powder, a polycarboxylate sodium salt dispersing agent and a polyether defoaming agent, taking deionized water as a solvent, adding an alumina grinding ball, performing planetary ball milling for 3 hours, and obtaining alumina composite slurry F2 (Al) with the solid content of 88wt% at the rotating speed of 130rpm 2 O 3 80wt% of powder and 8wt% of WC powder).
(3) And (3) preparing zirconia composite slurry. Taking ZrO 2 Mixing powder, ni powder, cr powder, a polycarboxylate sodium salt dispersing agent and a polyether defoamer, taking deionized water as a solvent, adding zirconia grinding balls, performing planetary ball milling for 3 hours at a rotating speed of 150rpm to obtain zirconia composite slurry F3 (ZrO) with a solid content of 88wt% 2 80wt% of powder, 5wt% of Ni powder and 3wt% of Cr powder).
In the welded boron carbide composite ceramic prepared in example 5, the thickness of the alumina coating was 30 μm and the thickness of the zirconia coating was 45. Mu.m.
The shear strength of the welded boron carbide composite ceramic and bulletproof steel plate connecting joint prepared in the embodiment 5 is 65MPa through detection.
Example 6
The preparation process is described in reference to example 1, with the main differences:
(1) And (3) preparing boron carbide composite slurry. Taking B 4 C powder (82 wt.%), al-Si alloy powder (6 wt.%), WO 2 Powder (2 wt.%), cr 2 O 3 Powder (2 wt.%), fe 2 O 3 Powder (2 wt%), Y 2 O 3 Powder (2 wt%), nb 2 O 5 Powder (2 wt.%), zrO 2 Powder (2 wt%) was mixed to be free ofAdding sodium carboxymethylcellulose (CMC) as thickener into ethanol water as solvent, adding B 4 And C, grinding the balls, and performing planetary ball milling for 3 hours at the rotating speed of 120rpm to obtain the boron carbide composite slurry F1.
(2) And (3) preparing the alumina composite slurry. Taking Al 2 O 3 Mixing powder, ni powder, mo powder, a polycarboxylate sodium salt dispersing agent and a polyether defoaming agent, taking deionized water as a solvent, adding an alumina grinding ball, performing planetary ball milling for 3 hours at a rotating speed of 150rpm to obtain alumina composite slurry F2 (Al) with a solid content of 89wt% 2 O 3 80wt% of powder, 4wt% of Ni powder and 5wt% of Mo powder).
(3) And (3) preparing zirconia composite slurry. Taking ZrO 2 Mixing powder, cr powder, ti powder, a polycarboxylate sodium salt dispersing agent and a polyether defoamer, taking deionized water as a solvent, adding zirconia grinding balls, performing planetary ball milling for 3 hours at a rotating speed of 160rpm to obtain zirconia composite slurry F3 (ZrO) with a solid content of 89wt% 2 80wt% of powder, 6wt% of Cr powder and 3wt% of Ti powder.
In the welded boron carbide composite ceramic prepared in example 6, the thickness of the alumina coating was 80 μm and the thickness of the zirconia coating was 150. Mu.m.
The shear strength of the welded boron carbide composite ceramic and titanium alloy connecting joint prepared in the embodiment 6 is 76MPa through detection.
As can be seen from examples 1 to 6, the present invention is carried out by Al 2 O 3 、ZrO 2 The metal powder is used as a transition layer design, the porous boron carbide prepared by doping the component design metal and the metal compound is used as a matrix layer, and the easy-to-weld boron carbide bulletproof ceramic with a boron carbide matrix layer/alumina coating/zirconia coating structure can be obtained by adopting a pneumatic sintering mode.
Comparative example 1
(1) And (3) preparing boron carbide composite slurry. As in example 1.
(2) And (3) preparing boron carbide ceramic. Drying, sieving, dry pressing and isostatic pressing the boron carbide composite slurry F1 to obtain a boron carbide ceramic biscuit M1; and drying the boron carbide ceramic biscuit M1 in a drying oven for 8 hours, and then performing air pressure sintering at 1350 ℃ for 2 hours under the nitrogen atmosphere of 3MPa to obtain the boron carbide ceramic.
The shear strength of the boron carbide ceramic and titanium alloy connecting joint prepared in the comparative example 1 is 23MPa through detection.
Comparative example 2
(1) And (3) preparing boron carbide composite slurry. As in example 1.
(2) And (3) preparing the alumina composite slurry. As in example 1.
(3) And preparing a boron carbide ceramic preform. As in example 1.
(4) And preparing the welded boron carbide composite ceramic. And (3) completely impregnating the boron carbide ceramic preform M2 prepared in the step (3) into the alumina composite slurry F2 prepared in the step (2) for 0.5 hour, taking out, drying in a drying oven for 3 hours, and then performing air pressure sintering at 1350 ℃ for 2.3 hours under the nitrogen atmosphere of 4MPa to obtain the welded boron carbide composite ceramic.
The shear strength of the welded boron carbide composite ceramic and titanium alloy connecting joint prepared in the comparative example 2 is 31MPa.
While the present invention has been described in detail through the foregoing description of the preferred embodiment, it should be understood that the foregoing description is not to be considered as limiting the invention. Many modifications and substitutions of the present invention will become apparent to those of ordinary skill in the art upon reading the foregoing. Accordingly, the scope of the invention should be limited only by the attached claims.
Claims (6)
1. The welding type boron carbide composite ceramic is characterized by having a boron carbide substrate layer/aluminum oxide coating/zirconium oxide coating structure, wherein the thickness of the aluminum oxide coating is 50nm-300 mu m, and the thickness of the zirconium oxide coating is 50nm-300 mu m;
the preparation method of the welded boron carbide composite ceramic comprises the following steps:
(1) Mixing boron carbide powder, first metal powder and metal oxide powder to form boron carbide composite slurry; based on the total mass of the boron carbide, the first metal and the metal oxide powder being 100%, the mass ratio of the boron carbide is 80-90 wt%, the mass ratio of the first metal is 1-10 wt%, and the mass ratio of the metal oxide is 1-15 wt%;
(2) Mixing alumina powder and second metal powder to form alumina composite slurry; the mass ratio of the aluminum oxide is 62 to 95 weight percent and the mass ratio of the second metal is 5 to 38 weight percent based on 100 percent of the total mass of the aluminum oxide and the second metal powder;
(3) Mixing zirconia powder and third metal powder to form zirconia composite slurry; the weight ratio of the zirconia is 62 to 95 percent and the weight ratio of the third metal is 5 to 38 percent based on 100 percent of the total weight of the zirconia and the third metal powder;
(4) Coating the boron carbide composite slurry on an organic foam skeleton, pressurizing to form a boron carbide ceramic biscuit, drying and performing first air pressure sintering to obtain a boron carbide ceramic preform;
(5) Impregnating the boron carbide ceramic preform into the alumina composite slurry, taking out, drying, and performing secondary air pressure sintering to obtain the boron carbide-alumina ceramic preform; impregnating the boron carbide-alumina ceramic preform into zirconia composite slurry, taking out, drying, and performing third air pressure sintering to obtain the welded boron carbide composite ceramic;
the first metal is at least one of Al, al-Si alloy, al-Fe alloy, al-Ni alloy and Al-Ti alloy; the second metal is at least one of Cr, mo, ti, ni, cu, WC, mn; the third metal is at least one of Cr, mo, ti, ni, cu, WC, mn;
the metal oxide is TiO 2 、ZrO 2 、Y 2 O 3 、WO 2 、Fe 2 O 3 、Nb 2 O 5 、Cr 2 O 3 、CeO 2 At least one of them.
2. The welded boron carbide composite ceramic of claim 1, wherein the alumina composite slurry has a solid phase content of 75-90wt%; the solid phase content of the zirconia composite slurry is 75-90wt%.
3. The welded boron carbide composite ceramic according to claim 1, wherein the temperature of the first, second and third gas pressure sintering is 1350-1550 ℃, the heat preservation time is 1-3.5h, the gas pressure is 2.5-4.5MPa, and the atmosphere is nitrogen atmosphere.
4. Use of the welded boron carbide composite ceramic of claim 1 in ballistic resistant materials.
5. The use according to claim 4, wherein the ballistic resistant material comprises: the welding type boron carbide composite ceramic and the connecting metal plate welded on the welding type boron carbide composite ceramic.
6. The use according to claim 5, wherein the connecting metal sheet is a ballistic steel sheet, an aluminum alloy sheet, a titanium alloy sheet.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59137379A (en) * | 1983-01-24 | 1984-08-07 | 工業技術院長 | Composite sintered ceramics and metal adhesion |
| JP2011136845A (en) * | 2009-12-25 | 2011-07-14 | Taiheiyo Cement Corp | Preform and metal-ceramic composite material |
| CN103596904A (en) * | 2012-02-28 | 2014-02-19 | 美浓窑业株式会社 | Shock absorbing member and method for producing same |
| CN103613389A (en) * | 2013-11-29 | 2014-03-05 | 宁波伏尔肯机械密封件制造有限公司 | Sintering preparation method of boron carbide ceramic |
| CN107651962A (en) * | 2017-09-30 | 2018-02-02 | 浙江立泰复合材料股份有限公司 | A kind of preparation method of Boral alloy composite plate |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US9011620B2 (en) * | 2009-09-11 | 2015-04-21 | Technip Process Technology, Inc. | Double transition joint for the joining of ceramics to metals |
| US9573354B2 (en) * | 2013-03-15 | 2017-02-21 | Rolls-Royce Corporation | Layered deposition for reactive joining of composites |
| TWI837508B (en) * | 2021-09-07 | 2024-04-01 | 財團法人工業技術研究院 | Composite structure with aluminum-based alloy layer containg boroncarbide and manufacturing method thereof |
-
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- 2023-03-30 CN CN202310329222.7A patent/CN116375474B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59137379A (en) * | 1983-01-24 | 1984-08-07 | 工業技術院長 | Composite sintered ceramics and metal adhesion |
| JP2011136845A (en) * | 2009-12-25 | 2011-07-14 | Taiheiyo Cement Corp | Preform and metal-ceramic composite material |
| CN103596904A (en) * | 2012-02-28 | 2014-02-19 | 美浓窑业株式会社 | Shock absorbing member and method for producing same |
| CN103613389A (en) * | 2013-11-29 | 2014-03-05 | 宁波伏尔肯机械密封件制造有限公司 | Sintering preparation method of boron carbide ceramic |
| CN107651962A (en) * | 2017-09-30 | 2018-02-02 | 浙江立泰复合材料股份有限公司 | A kind of preparation method of Boral alloy composite plate |
Non-Patent Citations (2)
| Title |
|---|
| Crack Repairing of Aluminum Alloy 6061 by Reinforcement of Al2O3and B4C Particles Using Friction Stir Processing;Masroor, Z;《KEY ENGINEERING MATERIALS》;20211029;第238-247页 * |
| 碳化硼抗弹陶瓷研究进展;王正军;;硅酸盐通报(01);第1-8页 * |
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