WO2003070661A1 - Poröse siliciumcarbid-keramik und verfahren zu ihrer herstellung - Google Patents
Poröse siliciumcarbid-keramik und verfahren zu ihrer herstellung Download PDFInfo
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- WO2003070661A1 WO2003070661A1 PCT/DE2003/000532 DE0300532W WO03070661A1 WO 2003070661 A1 WO2003070661 A1 WO 2003070661A1 DE 0300532 W DE0300532 W DE 0300532W WO 03070661 A1 WO03070661 A1 WO 03070661A1
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- silicon carbide
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Definitions
- the invention relates to the field of ceramics and relates to porous silicon carbide ceramics, which can be used, for example, as filter materials, and a method for their production.
- SiC ceramics sintered, highly bonded porous silicon carbide ceramics
- Such ceramics have a high permeability, a high open porosity with good strength and resistance to temperature changes.
- porous SiC ceramics have long been known as such materials.
- Binding is only aimed at at the contact points and is also realized via various binder systems in coordination with the respective SiC material.
- the average pore size can also be set with sufficient accuracy depending on the average SiC grain size.
- the pore volume achieved fluctuates very strongly in some cases between the individual SiC materials due to different sintering mechanisms.
- the primary grain shape also has a decisive influence on the pore volume.
- SiC materials can be divided into two main groups. SiC materials with a silicate bond that are bound to a different species are strongly influenced in their properties by the binding phase. Type-specific SiC materials are advantageous in that the positive properties of SiC are only slightly influenced by a secondary phase.
- Porous liquid-phase sintered SiC materials (DE 19727 115 C2) with a very high SiC content> 90% by mass are known, in which the SiC grains with an aspect ratio ⁇ 3 by SiC and in small amounts by thin Al-containing and Grain boundary phases containing rare earth elements are firmly connected to one another, have a high open porosity between 20 and 65% and have a narrow pore size distribution, the average pore size of which is set to a value between 0.5 ⁇ m and 1 mm.
- the secondary binding phases at the grain boundaries are essentially made up of secondary SiC, which was formed as a function of the sintering conditions and the primary grain by means of dissolution and redeposition processes, and from an oxidic phase, primarily from aluminum-rare earth oxide.
- the main influencing factor on the strength of porous SiC materials is the primary grain size.
- the strength decreases with increasing primary grain size. This phenomenon can be attributed to a lower sintering activity of coarse grains and the resulting poorer bond between the primary grains.
- the different expansion coefficients of SiC and the oxidic sintering additives also have an adverse effect on the strength, this effect being more pronounced in the case of coarse grains.
- the object of the invention is to provide a porous liquid-phase-sintered silicon carbide ceramic with increased strength and an easy to implement method for its production.
- the object is achieved by the invention specified in the claims. Further training is the subject of the subclaims.
- the porous silicon carbide ceramic consists of SiC particles which are sintered together in a framework via a binding phase.
- Binding phase embedded particles whose particle size is smaller than the SiC particles in the framework.
- silicon carbide ceramics according to the invention materials are present which, in addition to a high open porosity of 25 to 65%, are higher to significantly higher, ie. H. Up to 50% higher strength than previously
- the open porosity can have an average pore size between 1 ⁇ m and 1 mm, the average pore size depending on the
- Primary particle size can be adjusted. Both the pore volume and the
- Pore size can be adjusted via the primary grain and are not adversely affected by the addition of the particles for the binding phase.
- the binding phase is understood to mean the material which realizes the framework-like connection of the SiC particles of the framework, which is in ultra-fine crystalline and / or amorphous form and consists of a mixture of different substances or
- the particles incorporated in the binding phase are coarse-crystalline or single-crystal and consist of a substance or a compound and their composition is not changed or is changed only slightly during sintering.
- Particle size of the particles for the binding phase is smaller than the particle size of the
- SiC powder The shaping and sintering is then carried out.
- the silicon carbide ceramics obtained in this way show in the binding phase
- the addition of the particles for the binding phase does not result in a reduction in the pore volume of the porous silicon carbide ceramic. Rather, the particles for the binding phase are stored almost completely and also almost homogeneously distributed in the binding phase and are also used there advantageously to prevent crack propagation, which likewise contributes to an increase in strength.
- porous silicon carbide ceramics according to the invention have advantageously been sintered in the presence of a liquid phase.
- porous silicon carbide ceramics according to the invention should advantageously have a narrow particle size distribution of the SiC particles in the framework. It is also advantageous if the average particle size of the SiC particles in the framework is between> 10 ⁇ m and 3 mm.
- the particles have a narrow particle size distribution in the binding phase.
- the average particle size of the particles in the binding phase is at least 50% smaller than the average particle size of the SiC particles in the framework.
- the average particle size of the SiC particles in the framework is between> 10 ⁇ m and 3 mm and the average particle size of the particles in the binding phase is ⁇ 3 ⁇ m.
- the particles in the binding phase consist of SiC, more advantageously of a sinter-active fine SiC powder.
- the proportion of the binding phase in the ceramic is between 1 and 49% by volume.
- the binding phase advantageously contains an Al-containing and / or rare earth element-containing phase.
- the SiC particles and / or the particles are present in the binding phase in a monomodal particle size distribution. It is too please note that if monomodal particle size distributions are present both the SiC particles in the framework and the particles in the binding phase, only a smaller proportion of both particles should be used, otherwise the porosity of the silicon carbide ceramic would be reduced due to the space requirement of the particles ,
- the particles of the binding phase have the best possible wetting behavior to form a molten liquid phase. This concerns the liquid phase, which may be present during the sintering of the materials used to form the binding phase.
- SiC powder for the SiC framework is added in a narrow particle size distribution.
- Particle size between> 10 ⁇ m and 3 mm can be used.
- SiC powder is added as a particle for the binding phase.
- particles are used for the binding phase with an average particle size of ⁇ 3 ⁇ m.
- Al-containing and / or rare earth elements are also advantageously used as sintering additives.
- shaping aids are added before shaping and / or further auxiliaries and additives known per se.
- the sintering is advantageously carried out under an inert atmosphere and, more advantageously, under an argon atmosphere.
- a ceramic slip is made from 10 kg SiC abrasive powder F100 (d 50 or 130 ⁇ m) with 15 l water.
- SiC abrasive powder F100 d 50 or 130 ⁇ m
- 15 l water for this purpose, in the form of pre-ground to a mixture having a mean particle size of 0.8 microns 260 g Al 2 0 3, Y 2 O 3 140 g, and 400 g of SiC fine powder F1200 (dso "3 microns) was added.
- 250 g wax and 150 g acrylic resin are added as a pressing aid.
- This slurry is produced by spray drying and subsequent uniaxial pressing with 75 MPa pressed granules in the form of plates with the dimensions 60 x 60 x 5 mm 3 .
- the pressing aids are then burned out under an argon atmosphere at 1200 ° C. and the subsequent sintering takes place at 1850 ° C. also under an argon atmosphere.
- the porous silicon carbide ceramic according to the invention thus produced consists of a framework of coarse SiC grains with dso ⁇ 130 microns, which by a very fine crystalline
- Binding phase of Y-Al oxide are connected at the contact points. SiC particles with dso «3 ⁇ m are integrated in the fine crystalline binding phase.
- the open porosity is 45%.
- the pore size determined by means of mercury porosimetry is narrowly distributed at 44 ⁇ m.
- 8 x 5 mm 3 is 30 MPa.
- a ceramic slip is made from 10 kg SiC abrasive powder F100 (d 50 or 130 ⁇ m) with 15 l water.
- 260 g Al 2 O 3 and 140 g Y 2 O 3 are added in the form of a pre-ground mixture with an average grain size of 0.8 ⁇ m.
- 250 g wax and 150 g acrylic resin are added as a pressing aid.
- This slurry is produced by spray drying and subsequent uniaxial pressing with 75 MPa pressed granules in the form of plates with the dimensions 60 x 60 x 5 mm 3 .
- the pressing aids are then burned out under an argon atmosphere at 1200 ° C. and the subsequent sintering takes place at 1850 ° C. also under an argon atmosphere.
- porous silicon carbide ceramic produced in this way consists of a coarse framework
- Oxide are connected at the contact points.
- the open porosity is 45%.
- a ceramic slip is made from 10 kg SiC abrasive powder F100 (d 50 «130 ⁇ m) with 15 l water.
- 10 kg SiC abrasive powder F100 (d 50 «130 ⁇ m) with 15 l water.
- 10 kg SiC abrasive powder F100 (d 50 «130 ⁇ m) with 15 l water.
- in the form of a pre-ground mixture with an average grain size of 0.9 ⁇ m 400 g clay (ball clay), 900 g Al 2 O 3 (d 50 1 ⁇ m) and 100 g K 2 CO 3 , as well as 1400 g SiC Very fine powder F1200 (d 50 «3 ⁇ m) added.
- 250 g wax and 150 g acrylic resin are added as a pressing aid.
- This slurry is produced by spray drying and subsequent uniaxial pressing with 90 MPa pressed granules in the form of plates with the dimensions 75 x 75 x 10 mm 3 .
- the plates are then sintered in air at 1350 ° C.
- the porous silicon carbide ceramic according to the invention thus produced consists of a framework of coarse SiC grains with d 50 130 130 ⁇ m, which are connected by an amorphous aluminosilicate binding phase at the contact points. SiC particles with dso «3 ⁇ m are integrated in the fine crystalline binding phase.
- the open porosity is 45%.
- the pore size determined by means of mercury porosimetry is narrowly distributed at 44 ⁇ m.
- 8 x 5 mm 3 is 50 MPa.
- a ceramic slip is made from 10 kg SiC abrasive powder F100 (d 50 «130 ⁇ m) with 15 l water.
- 400 g clay (ball clay), 900 g Al 2 0 3 (dso «1 ⁇ ), 100 g K 2 CO 3 are added in the form of a pre-ground mixture with an average grain size of 0.9 ⁇ m.
- 250 g wax and 150 g acrylic resin are added as a pressing aid.
- This slurry is produced by spray drying and subsequent uniaxial pressing with 90 MPa pressed granules in the form of plates with the dimensions 75 x 75 x 10 mm 3 .
- the plate is then sintered in air at 1350 ° C.
- porous silicon carbide ceramic produced in this way consists of a coarse framework
- the open porosity is 45%.
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Abstract
Description
Claims
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AU2003215513A AU2003215513A1 (en) | 2002-02-20 | 2003-02-18 | Porous silicon carbide ceramic material and method for the production thereof |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE10207860.2 | 2002-02-20 | ||
DE2002107860 DE10207860B4 (de) | 2002-02-20 | 2002-02-20 | Poröse Siliciumcarbid-Keramik und Verfahren zu ihrer Herstellung |
Publications (1)
Publication Number | Publication Date |
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WO2003070661A1 true WO2003070661A1 (de) | 2003-08-28 |
Family
ID=27674915
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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PCT/DE2003/000532 WO2003070661A1 (de) | 2002-02-20 | 2003-02-18 | Poröse siliciumcarbid-keramik und verfahren zu ihrer herstellung |
Country Status (3)
Country | Link |
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AU (1) | AU2003215513A1 (de) |
DE (1) | DE10207860B4 (de) |
WO (1) | WO2003070661A1 (de) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1785408A1 (de) | 2005-11-15 | 2007-05-16 | L'AIR LIQUIDE, Société Anonyme pour l'Etude et l'Exploitation des Procédés Georges Claude | Verfahren zur Herstellung von porösen keramischen Trägern mit kontrollierter Mikrostruktur |
EP1905752A3 (de) * | 2006-09-14 | 2008-05-21 | Ibiden Co., Ltd. | Verfahren zur Herstellung von wabenförmig strukturierten Körpern und Materialzusammensetzung für einen wabenförmigen gebrannten Körper |
CN108046782A (zh) * | 2017-11-30 | 2018-05-18 | 宁波爱克创威新材料科技有限公司 | 刚玉-铝尖晶石浇注料及其制备方法以及刚玉-铝尖晶石的制备方法 |
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DE102011103106A1 (de) | 2011-05-25 | 2012-11-29 | Erbicol S.A. | Wärmeübertrager aus keramischem Material, insbesondere für Rekuperatorbrenner, und Verfahren zu dessen Herstellung |
DE102014013600A1 (de) | 2014-09-13 | 2016-03-17 | WindplusSonne GmbH | Solarabsorber, Verfahren zu seiner Herstellung und seine Verwendung |
DE102015000814A1 (de) | 2015-01-21 | 2016-07-21 | Smart Material Printing B.V. | Biozide Ausrüstung von Gegenständen mit Polyoxometallat-Mikro- und/oder -Nanopartikeln |
WO2016116259A1 (de) | 2015-01-21 | 2016-07-28 | Smartmaterialprinting B.V. | Biozide ausrüstung von gegenständen und wasserhaltigen reinigungs- und körperpflegemitteln mit polyoxometallat-mikro und/oder - nanopartikeln |
DE102018003906A1 (de) | 2018-05-07 | 2019-11-07 | Smart Material Printing | Verwendung von Polyoxometallaten gegen den Befall von Eukaryotenkulturen, Virenkulturen und Mikroorganismenpopulationen durch Mollicuten sowie mollicutenhemmende und -abtötende polyoxometallathaltige Stoffe und Verfahren |
CN111635246A (zh) * | 2020-06-13 | 2020-09-08 | 李秋惠 | 多孔碳化硅陶瓷及其制备方法 |
WO2023052393A1 (de) | 2021-09-29 | 2023-04-06 | Smart Material Printing B.V. | Mechanochemisch vorbehandelte, schwermetallfreie aktivkohlepartikel a, topische arzneimittel, medizinprodukte und kosmetika, herstellverfahren und verwendungen |
DE102021004905A1 (de) | 2021-09-29 | 2023-03-30 | Smart Material Printing B.V. | Mechanochemisch vorbehandelte, schwermetallfreie Aktivkohlepartikel A |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
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EP0369330A2 (de) * | 1988-11-14 | 1990-05-23 | Norton Company | Hochtemperaturfilter |
DE19727115A1 (de) * | 1996-07-01 | 1998-01-08 | Fraunhofer Ges Forschung | Poröse Siliciumcarbidkeramik und Verfahren zu ihrer Herstellung |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
BE635375A (de) * | 1962-07-24 | |||
DE2045808A1 (en) * | 1970-09-16 | 1972-03-23 | Anna Werk Gmbh | Silicon carbide refractory - produced by firing with tialite |
-
2002
- 2002-02-20 DE DE2002107860 patent/DE10207860B4/de not_active Expired - Lifetime
-
2003
- 2003-02-18 AU AU2003215513A patent/AU2003215513A1/en not_active Abandoned
- 2003-02-18 WO PCT/DE2003/000532 patent/WO2003070661A1/de not_active Application Discontinuation
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0369330A2 (de) * | 1988-11-14 | 1990-05-23 | Norton Company | Hochtemperaturfilter |
DE19727115A1 (de) * | 1996-07-01 | 1998-01-08 | Fraunhofer Ges Forschung | Poröse Siliciumcarbidkeramik und Verfahren zu ihrer Herstellung |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1785408A1 (de) | 2005-11-15 | 2007-05-16 | L'AIR LIQUIDE, Société Anonyme pour l'Etude et l'Exploitation des Procédés Georges Claude | Verfahren zur Herstellung von porösen keramischen Trägern mit kontrollierter Mikrostruktur |
EP1905752A3 (de) * | 2006-09-14 | 2008-05-21 | Ibiden Co., Ltd. | Verfahren zur Herstellung von wabenförmig strukturierten Körpern und Materialzusammensetzung für einen wabenförmigen gebrannten Körper |
CN108046782A (zh) * | 2017-11-30 | 2018-05-18 | 宁波爱克创威新材料科技有限公司 | 刚玉-铝尖晶石浇注料及其制备方法以及刚玉-铝尖晶石的制备方法 |
Also Published As
Publication number | Publication date |
---|---|
DE10207860A1 (de) | 2003-09-04 |
AU2003215513A1 (en) | 2003-09-09 |
DE10207860B4 (de) | 2005-12-22 |
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