CN101066885A - Collidal forming process for preparing high strength light ceramic material - Google Patents
Collidal forming process for preparing high strength light ceramic material Download PDFInfo
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- CN101066885A CN101066885A CN 200710099623 CN200710099623A CN101066885A CN 101066885 A CN101066885 A CN 101066885A CN 200710099623 CN200710099623 CN 200710099623 CN 200710099623 A CN200710099623 A CN 200710099623A CN 101066885 A CN101066885 A CN 101066885A
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- 229910010293 ceramic material Inorganic materials 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title abstract description 4
- BFYCFODZOFWWAA-UHFFFAOYSA-N 2,4,6-trimethylpyridine-3-carbaldehyde Chemical compound CC1=CC(C)=C(C=O)C(C)=N1 BFYCFODZOFWWAA-UHFFFAOYSA-N 0.000 title 1
- 239000000919 ceramic Substances 0.000 claims abstract description 45
- 239000000178 monomer Substances 0.000 claims abstract description 33
- 239000002904 solvent Substances 0.000 claims abstract description 33
- 238000000034 method Methods 0.000 claims abstract description 28
- 239000000843 powder Substances 0.000 claims abstract description 25
- 238000005245 sintering Methods 0.000 claims abstract description 22
- 239000003999 initiator Substances 0.000 claims abstract description 11
- 239000000725 suspension Substances 0.000 claims abstract description 9
- 239000011230 binding agent Substances 0.000 claims abstract description 7
- 238000001035 drying Methods 0.000 claims abstract description 7
- 238000011065 in-situ storage Methods 0.000 claims abstract description 7
- 238000006116 polymerization reaction Methods 0.000 claims abstract description 6
- 238000004132 cross linking Methods 0.000 claims abstract description 3
- 239000000758 substrate Substances 0.000 claims description 25
- 230000015572 biosynthetic process Effects 0.000 claims description 20
- 239000002994 raw material Substances 0.000 claims description 20
- 229920000642 polymer Polymers 0.000 claims description 19
- 239000007787 solid Substances 0.000 claims description 17
- 239000011800 void material Substances 0.000 claims description 14
- 230000006835 compression Effects 0.000 claims description 12
- 238000007906 compression Methods 0.000 claims description 12
- 239000004793 Polystyrene Substances 0.000 claims description 10
- DKGAVHZHDRPRBM-UHFFFAOYSA-N Tert-Butanol Chemical compound CC(C)(C)O DKGAVHZHDRPRBM-UHFFFAOYSA-N 0.000 claims description 10
- PXAJQJMDEXJWFB-UHFFFAOYSA-N acetone oxime Chemical compound CC(C)=NO PXAJQJMDEXJWFB-UHFFFAOYSA-N 0.000 claims description 10
- 239000004800 polyvinyl chloride Substances 0.000 claims description 10
- 238000002360 preparation method Methods 0.000 claims description 10
- 239000003352 sequestering agent Substances 0.000 claims description 10
- HRPVXLWXLXDGHG-UHFFFAOYSA-N Acrylamide Chemical compound NC(=O)C=C HRPVXLWXLXDGHG-UHFFFAOYSA-N 0.000 claims description 9
- 238000002156 mixing Methods 0.000 claims description 8
- 238000000498 ball milling Methods 0.000 claims description 7
- 238000002425 crystallisation Methods 0.000 claims description 6
- 230000008025 crystallization Effects 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 6
- 238000012545 processing Methods 0.000 claims description 5
- 239000004160 Ammonium persulphate Substances 0.000 claims description 4
- 239000004372 Polyvinyl alcohol Substances 0.000 claims description 4
- ROOXNKNUYICQNP-UHFFFAOYSA-N ammonium persulfate Chemical compound [NH4+].[NH4+].[O-]S(=O)(=O)OOS([O-])(=O)=O ROOXNKNUYICQNP-UHFFFAOYSA-N 0.000 claims description 4
- 235000019395 ammonium persulphate Nutrition 0.000 claims description 4
- 239000003795 chemical substances by application Substances 0.000 claims description 4
- KZHJGOXRZJKJNY-UHFFFAOYSA-N dioxosilane;oxo(oxoalumanyloxy)alumane Chemical compound O=[Si]=O.O=[Si]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O KZHJGOXRZJKJNY-UHFFFAOYSA-N 0.000 claims description 4
- 229910052863 mullite Inorganic materials 0.000 claims description 4
- 229920002451 polyvinyl alcohol Polymers 0.000 claims description 4
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims description 4
- IXPNQXFRVYWDDI-UHFFFAOYSA-N 1-methyl-2,4-dioxo-1,3-diazinane-5-carboximidamide Chemical compound CN1CC(C(N)=N)C(=O)NC1=O IXPNQXFRVYWDDI-UHFFFAOYSA-N 0.000 claims description 3
- 230000000694 effects Effects 0.000 claims description 3
- 235000011194 food seasoning agent Nutrition 0.000 claims description 3
- ZIUHHBKFKCYYJD-UHFFFAOYSA-N n,n'-methylenebisacrylamide Chemical compound C=CC(=O)NCNC(=O)C=C ZIUHHBKFKCYYJD-UHFFFAOYSA-N 0.000 claims description 3
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical group O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 3
- 229910010271 silicon carbide Inorganic materials 0.000 claims description 3
- 235000010413 sodium alginate Nutrition 0.000 claims description 3
- 229940005550 sodium alginate Drugs 0.000 claims description 3
- 239000000661 sodium alginate Substances 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- KFZMGEQAYNKOFK-UHFFFAOYSA-N Isopropanol Chemical compound CC(C)O KFZMGEQAYNKOFK-UHFFFAOYSA-N 0.000 claims description 2
- 229910052581 Si3N4 Inorganic materials 0.000 claims description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 2
- 230000006698 induction Effects 0.000 claims description 2
- 150000003839 salts Chemical class 0.000 claims description 2
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 claims description 2
- 238000003672 processing method Methods 0.000 claims 1
- 238000005516 engineering process Methods 0.000 abstract description 12
- 239000011148 porous material Substances 0.000 abstract description 6
- 239000007790 solid phase Substances 0.000 abstract 2
- 235000015895 biscuits Nutrition 0.000 abstract 1
- 239000002738 chelating agent Substances 0.000 abstract 1
- 238000007711 solidification Methods 0.000 abstract 1
- 230000008023 solidification Effects 0.000 abstract 1
- 239000000463 material Substances 0.000 description 11
- 229920002223 polystyrene Polymers 0.000 description 8
- 229920000915 polyvinyl chloride Polymers 0.000 description 8
- 239000000243 solution Substances 0.000 description 8
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 5
- CRPUJAZIXJMDBK-UHFFFAOYSA-N camphene Chemical compound C1CC2C(=C)C(C)(C)C1C2 CRPUJAZIXJMDBK-UHFFFAOYSA-N 0.000 description 4
- 239000002706 dry binder Substances 0.000 description 4
- 239000011224 oxide ceramic Substances 0.000 description 4
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 description 4
- 229910001928 zirconium oxide Inorganic materials 0.000 description 4
- PXRCIOIWVGAZEP-UHFFFAOYSA-N Primaeres Camphenhydrat Natural products C1CC2C(O)(C)C(C)(C)C1C2 PXRCIOIWVGAZEP-UHFFFAOYSA-N 0.000 description 2
- XCPQUQHBVVXMRQ-UHFFFAOYSA-N alpha-Fenchene Natural products C1CC2C(=C)CC1C2(C)C XCPQUQHBVVXMRQ-UHFFFAOYSA-N 0.000 description 2
- 229930006739 camphene Natural products 0.000 description 2
- ZYPYEBYNXWUCEA-UHFFFAOYSA-N camphenilone Natural products C1CC2C(=O)C(C)(C)C1C2 ZYPYEBYNXWUCEA-UHFFFAOYSA-N 0.000 description 2
- 239000003054 catalyst Substances 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 238000009413 insulation Methods 0.000 description 2
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 2
- 239000000395 magnesium oxide Substances 0.000 description 2
- AXZKOIWUVFPNLO-UHFFFAOYSA-N magnesium;oxygen(2-) Chemical compound [O-2].[Mg+2] AXZKOIWUVFPNLO-UHFFFAOYSA-N 0.000 description 2
- SIWVEOZUMHYXCS-UHFFFAOYSA-N oxo(oxoyttriooxy)yttrium Chemical compound O=[Y]O[Y]=O SIWVEOZUMHYXCS-UHFFFAOYSA-N 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009423 ventilation Methods 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 239000004964 aerogel Substances 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000012620 biological material Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000004821 distillation Methods 0.000 description 1
- 238000007429 general method Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
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- Compositions Of Oxide Ceramics (AREA)
Abstract
The present invention belongs to the field of ceramic material preparing technology, and is especially colloidal state forming process for preparing light high strength ceramic material. The process includes the following steps: preparing suspension with very low solid phase content with special organic monomer, solvent, initiator or chelating agent, and ceramic powder; in-situ solidification through gel polymerization of monomer or high molecular cross-linking to obtain ceramic biscuit; drying, removing binder and no-pressure high temperature sintering to obtain light high strength ceramic material. The present invention can control the porosity and pore size of the ultimate product through altering the solid phase content in the suspension, the sintering condition and the powder size. The present invention has simple technological process, low cost, environment friendship and other advantages, and the produced ceramic material has wide application range.
Description
Technical field
The invention belongs to ceramic materials preparation technology field, particularly a kind of novel method of utilizing colloidal formation prepared lightweight, high strength ceramic material.
Background technology
High temperature resistant, corrosion-resistant, outstanding features such as intensity is high, hardness height that stupalith has, in numerous areas such as chemical industry, aerospace, biology, the energy, environmental protection, often need to have extremely-low density, internal microstructure evenly and have a light ceramic material of higher-strength, such as in aerospace craft, alleviating of material weight can make the power consumption rate reduce greatly; As biomaterial also require to have low density, high-intensity characteristics, for addressing that need, common solution is the preparation foamed ceramics, the void content of foamed ceramics can reach more than 90%, but main problem is that the intensity of material is very low, void content generally is lower than 1MPa (document 1:J.Am.Ceram.Soc. in the foamed ceramics intensity more than 90%, 2006,89[6]: 1771-1789), and the intensity of base substrate is also very low, and one of the main reasons wherein is the inhomogeneous of microtexture.Also can prepare extra light stupalith (void content surpass 95%), but its intensity is then lower, and cost is very high, thereby is difficult to prepare the ceramic component that has precise measure and complicated shape and be applicable to practical application by the method for aerogel.
Colloidal formation technology was widely used in the production of stupalith in the last few years, its basis is to become with ceramic powder and solvent preparation to be similar to the colloidal suspensoid, by wherein monomer or polymer substance generation physics or chemical transformation are realized in-situ solidifying, molding blank.The outstanding feature of colloidal formation technology is to prepare complex-shaped, near net-shape, the uniform ceramic component of internal structure, prepared blank strength height, and technology is simple, with low cost, organic content is low.But colloidal formation technology is mainly used in preparing the ceramic component field of high-compactness for a long time, this is because if the suspensoid solid load is too low, obtain wet base substrate therefrom serious contraction and cracking can take place in drying process, thereby the shape that can't keep near net-shape, this makes colloidal formation technology bringing into play its advantage aspect the preparation ultralight ceramics.This one of them core difficult problem is choice of Solvent, if certain solvent highly volatile, and can realize in-situ solidifying based on its suspensoid, then can reduce the shrinking percentage in the body drying process on the one hand, improve blank strength simultaneously.Therefore, if can go out extra light stupalith by the colloidal formation prepared based on certain material system, keep the plurality of advantages of colloidal formation technology simultaneously, to be great expansion, have great importance for the development of ceramic material craft science to its Application Areas.
According to the retrieval, also do not pass through the report of colloidal formation prepared ultralight matter, high strength ceramic material at present both at home and abroad.
Summary of the invention
The purpose of this invention is to provide a kind of colloidal formation prepared lightweight, high strength ceramic material method utilized, it is characterized in that the concrete processing step of this method comprises:
1) preparation of base substrate: with monomer (comprising organic monomer and inorganic monomer), high molecular polymer, solvent, initiator or sequestrant and ceramic powder is raw material, preparation becomes the suspensoid that solid volume content is 5～45vol%, adopt monomer gel polymerisation or the crosslinked mode of polymer to realize the suspensoid in-situ solidifying, prepare low density, high-intensity ceramic body:
2) will wet after the base substrate demoulding, under the temperature condition of solvent evaporates, carry out air seasoning, guarantee dry shrinkage amount＜1% of base substrate simultaneously;
3) temperature rise rate according to 2～5 ℃/min rises to organism evaporable temperature in heating binder removal stove, and is incubated 1.5～3h, to get rid of organism wherein;
4) in the pressure less high temperature sintering oven,, under 1000～2000 ℃ temperature, be incubated 1～3h, the lightweight, the high-strength ceramic parts that finally obtain whole void content and be 50%～90%, ultimate compression strength surpass 10MPa according to the difference of ceramic raw material character.
Described organic monomer gel polymerisation mode, with organic monomer, solvent, initiator or sequestrant and ceramic powder is raw material, with organic raw material and solvent according to greater than the ratio of 5wt% prewired be mixing solutions, add ceramic powder according to the solid load that accounts for mixing solutions 5vol%～30vol% again, through ball milling 24 hours under 25～30 ℃ condition, obtain stable ceramic suspension body; Earlier suspensoid is cooled to and is lower than the monomer polymerization temperature, be higher than the solvent crystallization temperature, add initiator or sequestrant then therein, stir, inject the mould of definite shape, make the monomer generation polymerization in the suspensoid obtain having the wet base substrate that ultimate compression strength surpasses 1MPa by heating induction; Drying removes linear shrinkage ratio＜1% of base substrate in the process of solvent.
When described monomer was the organic monomer acrylamide, methylene-bisacrylamide was a linking agent, and ammonium persulphate is an initiator; When described monomer was the inorganic monomer sodium alginate, Ca salt was sequestrant;
Described solvent is the trimethyl carbinol or Virahol.
Described polymer crosslinking curing mode, with high molecular polymer, solvent and ceramic powder is raw material, under the temperature that is higher than 10 ℃～20 ℃ of solvent crystallization temperature, with organic raw material and solvent according to greater than the ratio of 5wt% prewired be mixing solutions, add ceramic powder according to the solid load that accounts for mixing solutions 5vol%～45vol% again, 50～75 ℃ condition lower seal ball millings 24 hours, obtain stable ceramic suspension body.Suspensoid is injected mould, temperature is reduced to room temperature, solvent after directly distillation removes in the suspensoid, realize each other between the polymer crosslinked, thereby make blank forming curing, the demoulding and obtain base substrate.
Described high molecular polymer is polyvinyl alcohol (PVA), polyvinyl chloride (PVC) or polystyrene (PS).Described solvent is the trimethyl carbinol, amphene or acetoxime.
Described ceramic powder is aluminum oxide (Al
2O
3), zirconium white (ZrO
2), mullite, silicon carbide (SiC) or silicon nitride (Si
3N
4).
The outstanding feature that the invention has the beneficial effects as follows colloidal formation technology is to prepare complex-shaped, near net-shape, the uniform ceramic component of internal structure, prepared blank strength height, and technology is simple, with low cost, organic content is low, compliance with environmental protection requirements, expand its Application Areas, processing condition of the present invention are easy to realize, suitable material system scope is wide, and ultralight matter, the high strength ceramic material of being produced is applicable to as multiple uses such as strainer, support of the catalyst, biological ceramics, space flight light structures parts.
Embodiment
The invention provides a kind of colloidal formation prepared lightweight, high strength ceramic material method utilized, the concrete processing step of this method comprises:
1) preparation of base substrate: with monomer (comprising organic monomer and inorganic monomer), high molecular polymer, solvent, initiator or sequestrant and ceramic powder is raw material, preparation becomes the suspensoid that solid volume content is 5～45vol%, adopt monomer gel polymerisation or the crosslinked mode of polymer to realize the suspensoid in-situ solidifying, prepare low density, high-intensity ceramic body:
2) will wet after the base substrate demoulding, under the temperature condition of solvent evaporates, carry out air seasoning, guarantee dry shrinkage amount＜1% of base substrate simultaneously;
3) temperature rise rate according to 2～5 ℃/min rises to organism evaporable temperature in heating binder removal stove, and is incubated 1.5～3h, to get rid of organism wherein;
4) in the pressure less high temperature sintering oven,, under 1000～2000 ℃ temperature, be incubated 1～3h, the lightweight, the high-strength ceramic parts that finally obtain whole void content and be 50%～90%, ultimate compression strength surpass 10MPa according to the difference of ceramic raw material character.
Below in conjunction with embodiment the present invention is further specified.
Embodiment one: the trimethyl carbinol/acrylamide system prepares the high-strength alumina-ceramic of ultralight
Under 25 ℃ temperature, acrylamide monomer, methylene-bisacrylamide and the trimethyl carbinol are become prewired solution according to 14.5: 0.5: 85 mass ratio mixed preparing, solid volume fraction adding submicron order according to 5vol% is alumina powder jointed, ball milling is 24 hours under 25～30 ℃ condition, obtains stable ceramic suspension body.The adding massfraction is 40% ammonium persulphate or sodium alginate aqueous solution in suspensoid, the ammonium persulphate consumption is 4% of a suspensoid gross weight, inject mould after stirring, subsequently suspensoid is placed 40 ℃ of water-baths together with mould, acrylamide monomer in the suspensoid can be finished polymerization about 30min, thereby makes the base substrate in-situ solidifying.The wet base substrate of low density is placed air dry oven, at 40 ℃ of following complete dryinies, the body drying linear shrinkage ratio that obtain this moment is lower than 0.3%, and ultimate compression strength surpasses 1MPa, temperature rise rate according to 2 ℃/min rises to 500 ℃ in heating binder removal stove then, and insulation 2h is to get rid of organism wherein; Taking-up is placed in the pressure less high temperature sintering oven, rises to 1400 ℃ according to the speed of 5 ℃/min, and insulation 2h finally obtains the ultralight matter high-strength alumina parts that whole void content is about 90%, ultimate compression strength surpasses 10MPa.When sintering temperature rose to 1500 ℃, whole void content was about 83%, ultimate compression strength surpasses 30MPa; When sintering temperature rose to 1550 ℃, whole void content was about 75%, ultimate compression strength surpasses 50MPa.Can in the scope of 5vol%～30vol%, change the solid load of suspensoid according to final material density and performance demands simultaneously.
Embodiment two: PVC/ amphene system prepares the high-strength ceramic component of ultralight
Under 55 ℃ temperature, PVC and amphene (Camphene) are become prewired solution according to 10: 90 mass ratio mixed preparing, solid volume fraction adding submicron order according to 5vol% is alumina powder jointed, 55～60 ℃ condition lower seal ball millings 24 hours, obtain stable ceramic suspension body.Suspensoid is injected mould, temperature is reduced to room temperature (about 20 ℃), the amphene generation crystallization in the suspensoid, the PVC polymer is crosslinked simultaneously, thereby blank forming is solidified; The base substrate demoulding with after solidifying makes the solvent camphene directly distil under room temperature (25 ℃) ventilation condition, and the PVC polymer is further crosslinked simultaneously, and acquisition ultimate compression strength is 5% ultralight matter base substrate above 0.5MPa, relative density.Binder removal subsequently, agglomerating technological process process and sintering temperature are similar with " embodiment one " for effect of material performance.Also can in the scope of 5vol%～45vol%, change the solid load of suspensoid according to final material density and performance demands.
Embodiment three: PS/ acetoxime system prepares the high-strength ceramic component of ultralight
Under 65 ℃ temperature, PS and acetoxime are become prewired solution according to 10: 90 mass ratio mixed preparing, it is alumina powder jointed to add submicron order according to the solid volume fraction of 5vol%, 65～70 ℃ condition lower seal ball millings 24 hours, obtains stable ceramic suspension body.Suspensoid is injected mould, temperature is reduced to room temperature (about 25 ℃), the acetoxime generation crystallization in the suspensoid, the PS polymer is crosslinked simultaneously, thereby blank forming is solidified; The base substrate demoulding with after solidifying makes the solvent acetone oxime directly distil under the room temperature ventilation condition, and the PS polymer is further crosslinked simultaneously, and acquisition ultimate compression strength is 5% ultralight matter base substrate above 0.5MPa, relative density.Binder removal subsequently, agglomerating technological process process and sintering temperature are similar with " embodiment one " for effect of material performance.Also can in the scope of 5vol%～30vol%, change the solid load of suspensoid according to final material density and performance demands.
Embodiment four: with ZrO
2, mullite, SiC, Si
3N
4Deng being the high-strength ceramic component of feedstock production ultralight.
1) with ZrO
2Powder is a raw material, adopts the trimethyl carbinol/acrylamide system among the embodiment one, or the PVC/ amphene system among the embodiment two, or the PS/ acetoxime system of embodiment three, respectively according to preparing suspensoid, forming and hardening, dry binder removal with embodiment one, embodiment two, embodiment three similar methods.During sintering, need to carry out pre-burning at 900 ℃ earlier, be warming up to 1300 ℃～1600 ℃ then and carry out sintering; The final lightweight zirconium oxide ceramic component of void content in 50%～90% scope that obtain.
2) with the mullite powder be raw material, adopt the trimethyl carbinol/acrylamide system among the embodiment one, or the PVC/ amphene system among the embodiment two, or the PS/ acetoxime system of embodiment three, prepare suspensoid according to the method identical respectively with embodiment one, embodiment two, embodiment three, forming and hardening, dry binder removal.Sintering temperature is in 1200 ℃～1500 ℃ scopes; The final lightweight zirconium oxide ceramic component of void content in 50%～90% scope that obtain.
3) be raw material with the SiC powder, need in powder raw material, add 1% magnesium oxide, 0.5% yttrium oxide, 0.5% silicon oxide as sintering agent, adopt the trimethyl carbinol/acrylamide system among the embodiment one, or the PVC/ amphene system among the embodiment two, or the PS/ acetoxime system of embodiment three, prepare suspensoid, forming and hardening, dry binder removal according to the method identical respectively with embodiment one, embodiment two, embodiment three.Sintering temperature is more than 1700 ℃; The final lightweight zirconium oxide ceramic component of void content in 50%～90% scope that obtain.
4) with Si
3N
4Powder is a raw material, need in powder raw material, add 8% yttrium oxide, 2.5% aluminum oxide, 1.5% magnesium oxide as sintering agent, adopt the trimethyl carbinol/acrylamide system among the embodiment one, or the PVC/ amphene system among the embodiment two, or the PS/ acetoxime system of embodiment three, prepare suspensoid, forming and hardening, dry binder removal according to the method identical respectively with embodiment one, embodiment two, embodiment three.Sintering temperature is more than 1650 ℃; The final lightweight zirconium oxide ceramic component of void content in 50%～90% scope that obtain.
Above-mentioned technology is to the control of density, intensity and pore size: realize the control of (comprising density, intensity and pore size etc.) of the final performance of stupalith by changing suspensoid solid load, sintering temperature and sintering time.General method is: improve the suspensoid solid load, can improve the intensity of base substrate and sintered compact, reduce average pore size; Improve sintering temperature or prolong sintering time, can improve the intensity of sintered compact, increase average pore size.
By changing suspensoid solid load, sintering condition, diameter of particle, realize control to the final void content of material, pore size.Processing condition of the present invention are easy to realize that suitable material system scope is wide that ultralight matter, the high strength ceramic material of being produced is applicable to as multiple uses such as strainer, support of the catalyst, biological ceramics, space flight light structures parts.
Claims (8)
1. a processing method of utilizing colloidal formation prepared lightweight, high strength ceramic material is characterized in that, the concrete processing step of this method comprises:
1) preparation of base substrate: with monomer, high molecular polymer, solvent, initiator or sequestrant and ceramic powder is raw material, preparation becomes the suspensoid that solid volume content is 5～45vol%, adopt monomer gel polymerisation or the crosslinked mode of polymer to realize the suspensoid in-situ solidifying, prepare low density, high-intensity ceramic body, wherein monomer is organic monomer or inorganic monomer;
2) will wet after the base substrate demoulding, under the temperature condition of solvent evaporates, carry out air seasoning, guarantee dry shrinkage amount＜1% of base substrate simultaneously;
3) temperature rise rate according to 2～5 ℃/min rises to organism evaporable temperature in heating binder removal stove, and is incubated 1.5～3h, to get rid of organism wherein;
4) in the pressure less high temperature sintering oven,, under 1000～2000 ℃ temperature, be incubated 1～3h, the lightweight, the high-strength ceramic parts that finally obtain whole void content and be 50%～90%, ultimate compression strength surpass 10MPa according to the difference of ceramic raw material character.
2. according to described colloidal formation prepared lightweight, the high strength ceramic material method utilized of claim 1, it is characterized in that, described monomer gel polymerisation mode, with monomer, solvent, initiator or sequestrant and ceramic powder is raw material, with raw material monomer and solvent according to greater than the ratio of 5wt% prewired be mixing solutions, add ceramic powder according to the solid load that accounts for mixing solutions 5vol%～30vol% again, through ball milling 24 hours under 25～30 ℃ condition, obtain stable ceramic suspension body; Earlier suspensoid is cooled to and is lower than the monomer polymerization temperature, be higher than the solvent crystallization temperature, add initiator or sequestrant then therein, stir, inject the mould of definite shape, make monomer in the suspensoid that polymerization take place under the effect of initiator or sequestrant by heating induction and obtain having the wet base substrate of ultimate compression strength above 1MPa; Drying removes linear shrinkage ratio＜1% of base substrate in the process of solvent.
3. according to claim 1 or 2 described colloidal formation prepared lightweight, the high strength ceramic material methods utilized, it is characterized in that when described monomer was the organic monomer acrylamide, methylene-bisacrylamide was a linking agent, ammonium persulphate is an initiator; When described monomer was the inorganic monomer sodium alginate, Ca salt was sequestrant.
4. according to claim 1 or 2 described colloidal formation prepared lightweight, the high strength ceramic material methods utilized, it is characterized in that described solvent is the trimethyl carbinol or Virahol.
5. according to the described colloidal formation prepared lightweight of utilizing of claim 1, the high strength ceramic material method, it is characterized in that, described polymer crosslinking curing mode, with high molecular polymer, solvent and ceramic powder are raw material, under the temperature that is higher than 10 ℃～20 ℃ of solvent crystallization temperature, with organic raw material and solvent according to greater than the ratio of 5wt% prewired be mixing solutions, add ceramic powder according to the solid load that accounts for mixing solutions 5vol%～45vol% again, 50～75 ℃ condition lower seal ball millings 24 hours, obtain stable ceramic suspension body, suspensoid is injected mould, temperature is reduced to room temperature, after solvent directly distils and removes in the suspensoid, realize crosslinked between the polymer each other, thereby blank forming is solidified, and the base substrate ultimate compression strength after the demoulding surpasses 0.5MPa, and drying removes linear shrinkage ratio＜1% of base substrate in the process of solvent.
6. according to claim 1 or 5 described colloidal formation prepared lightweight, the high strength ceramic material methods utilized, it is characterized in that described high molecular polymer is polyvinyl alcohol (PVA), polyvinyl chloride (PVC) or polystyrene (PS).
7. according to claim 1 or 5 described colloidal formation prepared lightweight, the high strength ceramic material methods utilized, it is characterized in that described solvent is the trimethyl carbinol, amphene or acetoxime.
8. according to described colloidal formation prepared lightweight, the high strength ceramic material method utilized of claim 1, it is characterized in that described ceramic powder is aluminum oxide, zirconium white, mullite, silicon carbide or silicon nitride.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2007100996239A CN100482614C (en) | 2007-05-25 | 2007-05-25 | Collidal forming process for preparing high strength light ceramic material |
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| CN102070336A (en) * | 2010-11-19 | 2011-05-25 | 南京工业大学 | Preparation method of zirconia ceramic |
| CN102344297A (en) * | 2011-06-30 | 2012-02-08 | 西安交通大学 | Forming method for preparing Si3N4 porous ceramic through tertiary butyl alcohol (TBA)-based gel casting method |
| CN101555159B (en) * | 2009-04-07 | 2012-05-23 | 同济大学 | Directional orifice carbide biological ceramic material and preparation method thereof |
| CN102757226A (en) * | 2011-04-26 | 2012-10-31 | 中国科学院声学研究所 | Preparation method of fine piezoelectric ceramic tube |
| CN103072182A (en) * | 2013-01-08 | 2013-05-01 | 清华大学 | Gellan gum gel-based ceramic gel injection molding method |
| CN103641509A (en) * | 2013-12-09 | 2014-03-19 | 中国建筑材料科学研究总院 | Porous carbon preform for reactive sintering, as well as preparation method and application thereof |
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| CN101555159B (en) * | 2009-04-07 | 2012-05-23 | 同济大学 | Directional orifice carbide biological ceramic material and preparation method thereof |
| CN102070336B (en) * | 2010-11-19 | 2013-05-08 | 南京工业大学 | Preparation method of zirconia ceramic |
| CN102070336A (en) * | 2010-11-19 | 2011-05-25 | 南京工业大学 | Preparation method of zirconia ceramic |
| CN102757226B (en) * | 2011-04-26 | 2014-10-08 | 中国科学院声学研究所 | Preparation method of fine piezoelectric ceramic tube |
| CN102757226A (en) * | 2011-04-26 | 2012-10-31 | 中国科学院声学研究所 | Preparation method of fine piezoelectric ceramic tube |
| CN102344297A (en) * | 2011-06-30 | 2012-02-08 | 西安交通大学 | Forming method for preparing Si3N4 porous ceramic through tertiary butyl alcohol (TBA)-based gel casting method |
| CN103072182A (en) * | 2013-01-08 | 2013-05-01 | 清华大学 | Gellan gum gel-based ceramic gel injection molding method |
| CN103072182B (en) * | 2013-01-08 | 2014-09-24 | 清华大学 | Gellan gum gel-based ceramic gel injection molding method |
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| CN103771863B (en) * | 2014-01-08 | 2015-04-15 | 清华大学 | Method for solidifying ceramic slurry through controlling high-valent contra-ion by slowly adjusting pH value |
| CN104387036A (en) * | 2014-11-04 | 2015-03-04 | 中国科学院上海硅酸盐研究所 | Novel connection method of ceramic bodies |
| CN104557131A (en) * | 2014-12-30 | 2015-04-29 | 中国科学院重庆绿色智能技术研究院 | Super-hydrophobic foam ceramic and preparation method thereof |
| CN104909752A (en) * | 2015-05-19 | 2015-09-16 | 铜陵宏正网络科技有限公司 | Alumina fiber reinforced gypsum ceramic matrix composite and preparation method thereof |
| CN105060894A (en) * | 2015-08-05 | 2015-11-18 | 西北农林科技大学 | Method for preparing zirconium carbide wood ceramic |
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| CN108358660A (en) * | 2016-05-12 | 2018-08-03 | 王维娜 | A kind of porous ceramics and preparation method thereof |
| CN108358660B (en) * | 2016-05-12 | 2020-07-17 | 馆陶县陶山黑陶科技有限公司 | Porous ceramic and preparation method thereof |
| CN106187292A (en) * | 2016-07-12 | 2016-12-07 | 广西南宁桂尔创环保科技有限公司 | A kind of new ceramic material utilizing mud |
| CN107082638A (en) * | 2017-05-12 | 2017-08-22 | 青岛大学 | A kind of ceramic viscose rayon spinning head preparation method |
| CN107082638B (en) * | 2017-05-12 | 2020-11-06 | 青岛大学 | Preparation method of ceramic viscose fiber spinning jet |
| CN107903080A (en) * | 2017-12-12 | 2018-04-13 | 武汉钢铁有限公司 | A kind of preparation method of zirconia/mullite high porosity ceramic material |
| CN107903080B (en) * | 2017-12-12 | 2020-12-29 | 武汉钢铁有限公司 | Preparation method of zirconia-mullite high-porosity ceramic material |
| CN113105269A (en) * | 2021-05-07 | 2021-07-13 | 中国石油化工股份有限公司 | Pore filler for ceramic heat transfer element, method for filling pores in ceramic heat transfer element, and ceramic heat transfer element |
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