JPH0474308B2 - - Google Patents
Info
- Publication number
- JPH0474308B2 JPH0474308B2 JP22159082A JP22159082A JPH0474308B2 JP H0474308 B2 JPH0474308 B2 JP H0474308B2 JP 22159082 A JP22159082 A JP 22159082A JP 22159082 A JP22159082 A JP 22159082A JP H0474308 B2 JPH0474308 B2 JP H0474308B2
- Authority
- JP
- Japan
- Prior art keywords
- porous body
- ceramic
- ceramic porous
- dispersed
- internal communication
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 239000000919 ceramic Substances 0.000 claims description 52
- 239000013078 crystal Substances 0.000 claims description 13
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 10
- 238000004891 communication Methods 0.000 claims description 10
- 229910052878 cordierite Inorganic materials 0.000 claims description 7
- JSKIRARMQDRGJZ-UHFFFAOYSA-N dimagnesium dioxido-bis[(1-oxido-3-oxo-2,4,6,8,9-pentaoxa-1,3-disila-5,7-dialuminabicyclo[3.3.1]nonan-7-yl)oxy]silane Chemical compound [Mg++].[Mg++].[O-][Si]([O-])(O[Al]1O[Al]2O[Si](=O)O[Si]([O-])(O1)O2)O[Al]1O[Al]2O[Si](=O)O[Si]([O-])(O1)O2 JSKIRARMQDRGJZ-UHFFFAOYSA-N 0.000 claims description 7
- 230000005484 gravity Effects 0.000 claims description 6
- 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 5
- 229910052863 mullite Inorganic materials 0.000 claims description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 239000011810 insulating material Substances 0.000 description 9
- 239000003623 enhancer Substances 0.000 description 8
- 239000002002 slurry Substances 0.000 description 8
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 6
- 239000012774 insulation material Substances 0.000 description 6
- 230000005855 radiation Effects 0.000 description 6
- 210000004027 cell Anatomy 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 238000000034 method Methods 0.000 description 5
- 229910010293 ceramic material Inorganic materials 0.000 description 4
- 229920005830 Polyurethane Foam Polymers 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000009413 insulation Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000011496 polyurethane foam Substances 0.000 description 3
- 239000000377 silicon dioxide Substances 0.000 description 3
- 229910000314 transition metal oxide Inorganic materials 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 239000000969 carrier Substances 0.000 description 2
- 239000003054 catalyst Substances 0.000 description 2
- 210000000170 cell membrane Anatomy 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 238000005470 impregnation Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 2
- 229910010271 silicon carbide Inorganic materials 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000000191 radiation effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
Landscapes
- Porous Artificial Stone Or Porous Ceramic Products (AREA)
Description
【発明の詳細な説明】
本発明は内部連通空間を有する三次元網状のセ
ル構造をなしたセラミツク多孔体に関し、特に高
温度における強度の大きいセラミツク多孔体に関
する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a ceramic porous body having a three-dimensional network cell structure having internal communication spaces, and particularly to a ceramic porous body having high strength at high temperatures.
内部連通空間を有する三次元網状のセル構造を
なしたセラミツク多孔体は、溶融金属の材、触
媒担体、デイーゼルパテイキユレートフイルタ
ー、更には通過性断熱材等とその用途は広く、工
業的に有用なものである。しかし、これらの用途
に用いる場合、多くは数百度から千数百度にも及
ぶ温度環境で使用されるので、高温時における強
度の大きいセラミツク多孔体が要求される。 Ceramic porous bodies with a three-dimensional network cell structure with internal communication spaces have a wide range of uses, such as molten metal materials, catalyst carriers, diesel particulate filters, and even permeable insulation materials, making them industrially useful. It is something. However, when used in these applications, the porous ceramic material is required to have high strength at high temperatures because it is often used in environments with temperatures ranging from several hundred degrees to several thousand degrees.
このような高温での強度を必要とする場合、セ
ラミツク多孔体をアルミナ或いはコージライト質
を主成分として形成することが好ましいが、更に
高温での強度の大きいセラミツク多孔体が望まれ
る。 When strength at such high temperatures is required, it is preferable to form the ceramic porous body mainly of alumina or cordierite, but a ceramic porous body with even greater strength at high temperatures is desired.
本発明者は上記事情に鑑み、高温での強度の大
きいセラミツク多孔体につき鋭意研究を行なつた
結果、内部連通空間を有する三次元網状のセル構
造をなしたセラミツク多孔体を形成するセラミツ
ク中に針状結晶体が分散している場合、優れた耐
高温クリープ性を有し、高温度での強度が大き
く、このためこのセラミツク多孔体が通気性断熱
材等の高温度にさらされる用途に対し好適に使用
されることを知見したものである。特に、アルミ
ナ又はコージライト質を主成分とするセラミツク
多孔体中にアルミナとシリカより得られるムライ
ト質が分散している場合、高温度で著しく大きい
強度を示すことを知見し、本発明をなすに至つた
ものである。 In view of the above circumstances, the present inventor has conducted intensive research on ceramic porous bodies that have high strength at high temperatures, and has found that a ceramic porous body having a three-dimensional network cell structure with internal communication spaces is formed. When needle-like crystals are dispersed, it has excellent high-temperature creep resistance and high strength at high temperatures, making this porous ceramic suitable for applications exposed to high temperatures such as breathable insulation materials. It has been found that it can be suitably used. In particular, it has been found that when mullite obtained from alumina and silica is dispersed in a ceramic porous body mainly composed of alumina or cordierite, it exhibits significantly high strength at high temperatures. It has been reached.
以下、本発明につき更に詳しく説明する。 The present invention will be explained in more detail below.
本発明のセラミツク多孔体は、内部連通空間を
有する三次元網状のセル構造をなしたもので、多
孔体を形成するセラミツク中に針状結晶体が分散
してなるものである。 The ceramic porous body of the present invention has a three-dimensional network cell structure having an internal communication space, and has needle crystals dispersed in the ceramic forming the porous body.
この場合、多孔体を形成するセラミツクは、ア
ルミナ又はコージライト質を主成分としたものが
好ましく、このセラミツク中にアルミナとシリカ
より得られるムライト質の針状結晶体が分散して
いるものであることが好ましい。更に好ましく
は、アルミナ含量の多いコージライト質をコージ
ライト相の分解温度近く（1350〜1600℃程度）に
加熱することによつて得られたムライト
（3Al2O3・2SiO2）針状結晶分散体が用いられる。
ここで、多孔体を形成するセラミツクとしてアル
ミナを主成分として用いた場合、アルミナ含量は
50〜95重量％とすることが好ましく、またコージ
ライト質を主成分とした場合、その含量は50〜95
重量％とすることが好ましい。更に、前記針状結
晶体の含量は１〜95重量％であることが好まし
い。 In this case, the ceramic forming the porous body is preferably one whose main component is alumina or cordierite, and mullite needle-like crystals obtained from alumina and silica are dispersed in this ceramic. It is preferable. More preferably, mullite (3Al 2 O 3 .2SiO 2 ) needle-like crystal dispersion obtained by heating cordierite with a high alumina content to near the decomposition temperature of the cordierite phase (approximately 1350 to 1600°C) The body is used.
Here, when alumina is used as the main component for the ceramic forming the porous body, the alumina content is
The content is preferably 50 to 95% by weight, and when cordierite is the main component, the content is 50 to 95% by weight.
It is preferable to set it as weight%. Further, the content of the needle-like crystals is preferably 1 to 95% by weight.
上述したようなセラミツク多孔体を得る場合、
セル膜のない軟質ポリウレタンフオームにセラミ
ツク泥漿を付着させ、これを焼結することにより
前記軟質ポリウレタンフオームを炭化除去して製
造したものを用いることが好ましい（このように
セル膜のない軟質ポリウレタンフオームからセラ
ミツク多孔体を形成することにより、正十二面体
の稜の部分のみからなる篭形のセラミツク多孔体
が得られ、これは空隙率が大きいので圧力損失が
少ない状態で排気ガスが通過すると共に、内部連
通空間が入り組んでいるので、例えばこのセラミ
ツク多孔体を通気性断熱材の用途に用いる場合、
排気ガスがこの内部連通空間を通過する際格子と
確実に接触し、熱交換が効率よく行なわれる。）
が、かかる方法でセラミツク多孔体を製造する場
合に、針状結晶体を予じめセラミツク泥漿中に分
散せしめておく方法を採用することができる。し
かし、この方法はセラミツク泥漿の粘度が高くな
る場合があり、このため含浸や余剰泥漿の除去が
困難となつて含浸不良や多孔体の目詰りを招く場
合が生じる。従つて、針状結晶体を含まないセラ
ミツク泥漿を用いて含浸と余剰泥漿の除去、乾燥
を行ない、焼成時に針状結晶体を生成せしめる方
法、或いは得られたセラミツク多孔体を針状結晶
が生成される温度に再加熱する方法が好ましく、
これによつてセラミツクに針状結晶体が分散した
セラミツク多孔体を好適に得ることができる。 When obtaining the ceramic porous body as described above,
It is preferable to use a product manufactured by attaching a ceramic slurry to a soft polyurethane foam without a cell membrane and sintering it to remove carbonization from the soft polyurethane foam. By forming a ceramic porous body, a cage-shaped ceramic porous body consisting only of the edge portion of a regular dodecahedron can be obtained, and since this has a large porosity, exhaust gas can pass through it with little pressure loss. Since the internal communication space is complicated, for example, when this porous ceramic material is used as a breathable heat insulating material,
When the exhaust gas passes through this internal communication space, it comes into reliable contact with the grid, and heat exchange is performed efficiently. )
However, when producing a ceramic porous body by such a method, it is possible to adopt a method in which needle-like crystals are dispersed in the ceramic slurry in advance. However, in this method, the viscosity of the ceramic slurry may become high, which makes impregnation and removal of excess slurry difficult, resulting in poor impregnation and clogging of the porous body. Therefore, a method is proposed in which ceramic slurry that does not contain needle crystals is impregnated, excess slurry is removed, and dried, and needle crystals are produced during firing, or needle crystals are produced in the obtained ceramic porous body. It is preferable to reheat the product to a temperature that
As a result, a ceramic porous body in which needle-like crystals are dispersed in the ceramic can be suitably obtained.
本発明のセラミツク多孔体は、主として高温ガ
スや液体を通過せしめる個所、例えば溶融金属の
材、触媒担体、デイゼルパテイキユレートフイ
ルター、通気性断熱材等の用途に好適に用いら
れ、とりわけ通気性断熱材として効果的に用いら
れる。 The ceramic porous body of the present invention is suitable for use in places where high-temperature gases and liquids pass through, such as molten metal materials, catalyst carriers, diesel particulate filters, and air-permeable heat insulating materials. Effectively used as a material.
本発明のセラミツク多孔体を上述したような用
途に用いる場合、セラミツク多孔体としてはその
嵩比重が0.25〜0.6であり、内部連通空間の平均
直径が0.2〜10mmでいずれの方向にも目詰りのな
いものであり、空隙率が75〜95％であり、かつ空
気の圧力損失が毎秒風速１ｍで１cmの厚みを通過
するのに水柱0.1〜40mmであることが好適である。
とりわけ通気性断熱材として使用する場合は、そ
の嵩比重が0.25〜0.6、好ましくは0.25〜0.5、平
均直径が0.2〜10mm、好ましくは0.2〜５mm、更に
好ましくは0.3〜1.5mm、空隙率が75〜95％、好ま
しくは80〜95％、気の圧力損失が毎秒風速１ｍで
１cmの厚みを通過するのに水柱0.1〜40mm、好ま
しくは５〜30mmであることが必要であり、これに
より通気性と断熱性の両者に優れ、効果の高い通
気性断熱材が得られる。これに対し、上記範囲を
はずれる場合は良好な通気性断熱材とならない。
即ち、嵩比重が0.25より小さいと断熱材としての
強度が不十分であり、嵩比重が0.6より大きいと
目詰りが発生して損失が高くなり、また、平均直
径が0.2mmより小さいと強度が低下し、圧力損失
の上昇を招き、平均直径が10mmより大きくなると
断熱材と排気ガスとの接触が不十分となる上、断
熱材の表面（加熱側）から裏面（排気側）への輻
射熱の漏れが発生するので、良好な通気性断熱材
とならない。更に、空隙率が75％より小さい場合
は、固体内熱伝導が良くなつて断熱材表裏面間の
温度差が小さくなり、このため断熱材裏面（排気
側）からの輻射熱の逸散を招き、また、空隙率が
95％を超えると強度が低下し、なお更に、圧力損
失が40mmを超えるものは、加熱炉等の燃焼に不具
合をもたらす場合が多く、同様に良好な通気性断
熱材が得られないものである。 When the ceramic porous body of the present invention is used in the above-mentioned applications, the bulk specific gravity of the ceramic porous body is 0.25 to 0.6, the average diameter of the internal communication space is 0.2 to 10 mm, and there is no clogging in any direction. It is preferable that the porosity is 75 to 95%, and the pressure loss of air is 0.1 to 40 mm in water column when passing through a thickness of 1 cm at a wind speed of 1 m/s.
Particularly when used as a breathable heat insulating material, the bulk specific gravity is 0.25 to 0.6, preferably 0.25 to 0.5, the average diameter is 0.2 to 10 mm, preferably 0.2 to 5 mm, more preferably 0.3 to 1.5 mm, and the porosity is 75. ~95%, preferably 80-95%, the pressure loss of air passing through a thickness of 1 cm at a wind speed of 1 m/s requires a water column of 0.1-40 mm, preferably 5-30 mm, which improves breathability. The result is a highly effective breathable heat insulating material that has both excellent heat and heat insulation properties. On the other hand, if it deviates from the above range, it will not provide a good breathable heat insulating material.
That is, if the bulk specific gravity is less than 0.25, the strength as a heat insulating material is insufficient, if the bulk specific gravity is greater than 0.6, clogging will occur and the loss will be high, and if the average diameter is less than 0.2 mm, the strength will be insufficient. If the average diameter becomes larger than 10 mm, the contact between the insulation material and the exhaust gas will be insufficient, and the radiant heat will increase from the surface (heating side) of the insulation material to the back surface (exhaust side). It does not provide good breathable insulation as it leaks. Furthermore, if the porosity is less than 75%, the heat conduction within the solid improves and the temperature difference between the front and back surfaces of the insulation material becomes small, leading to the dissipation of radiant heat from the back surface (exhaust side) of the insulation material. In addition, the porosity
If it exceeds 95%, the strength decreases, and furthermore, if the pressure loss exceeds 40 mm, it often causes problems with combustion in heating furnaces, etc., and similarly, good breathable insulation cannot be obtained. .
なお本発明に係るセラミツク多孔体を通気性断
熱材として用いる場合、上述した構成のセラミツ
ク多孔体中に輻射能向上剤を分散させるか又はセ
ラミツク多孔体の格子全体もしくは排気ガス流入
側の格子を輻射能向上剤で被覆することができ、
これにより通気性断熱材の輻射性能をより高くす
ることができる。この場合、輻射能向上剤として
は、炭化硅素や窒化硅素等を使用することもでき
るが、特に顕著な効果を示すものは遷移金属酸化
物であり、パナジウム、クロム、マンガン、鉄、
コバルト、ニツケルの酸化物が好適に使用し得
る。なおこれら輻射能向上剤をセラミツク多孔体
中に分散させる場合は、セラミツク多孔体の製造
時にセラミツク泥漿中に輻射能向上剤を混入して
セラミツク多孔体を形成することにより、輻射能
向上剤をセラミツク多孔体中に分散させることが
でき、また輻射能向上剤をセラミツク多孔体の格
子に被覆させる場合は、形成されたセラミツク多
孔体の全体もしくは一部は水等の溶剤に輻射能向
上剤を分散させてなる分散的中に浸漬し、乾燥或
いは焼結することにより、輻射能向上剤を被覆す
ることができる。前記輻射能向上剤の使用量は、
セラミツク多孔体全重量の０〜90％、特に１〜50
％とすることが好ましく、これにより高い輻射効
果を発揮させることができる。また、上記遷移金
属酸化物のほか、或いは上記遷移金属酸化物に加
えて金属窒化物、金属炭化物の１種又は２種以上
をセラミツク多孔体の格子中に分散又は格子表面
に付着、被覆させることうができ、これによりセ
ラミツク多孔体輻射熱を高めたり、耐熱衝撃性や
耐熱性を高めることができるので、通気性断熱材
等の用途に好適である。窒化物としてはTiN、
ZrN、Si3N4等が挙げられ、炭化物としてはTiC、
ZrC、HfC、VC、TaC、NbC、WC、BiC、SiC
等が挙げられる。また金属硼化物、例えばAlB、
SiB、TiB2、ZrB2、HfB、VB2、TaB、WB等
を格子中に分散又は格子表面に付着させることも
できる。 In addition, when the ceramic porous body according to the present invention is used as a breathable heat insulating material, a radiation enhancer is dispersed in the ceramic porous body having the above-mentioned structure, or the entire lattice of the ceramic porous body or the lattice on the exhaust gas inflow side is radiated. can be coated with a performance enhancer,
This makes it possible to further improve the radiation performance of the breathable heat insulating material. In this case, silicon carbide, silicon nitride, etc. can be used as the radiation enhancer, but transition metal oxides are particularly effective, including panadium, chromium, manganese, iron,
Oxides of cobalt and nickel can be suitably used. In addition, when dispersing these radioactivity enhancers in a ceramic porous body, the radioactivity enhancer is mixed into the ceramic slurry to form a ceramic porous body during the production of the ceramic porous body. It can be dispersed in a porous body, and when coating a lattice of a ceramic porous body with a radiation enhancer, the entire or part of the formed ceramic porous body is dispersed in a solvent such as water. The radiation activity enhancer can be coated by immersing the material in a dispersion made of the above-mentioned material and drying or sintering it. The amount of the radiation enhancer used is:
0 to 90% of the total weight of the ceramic porous body, especially 1 to 50%
%, and thereby a high radiation effect can be exhibited. In addition to the above transition metal oxides, or in addition to the above transition metal oxides, one or more metal nitrides and metal carbides may be dispersed in the lattice of the ceramic porous body or attached to or coated on the lattice surface. This makes it possible to increase the radiant heat of the porous ceramic material, as well as its thermal shock resistance and heat resistance, making it suitable for applications such as breathable heat insulating materials. TiN as a nitride,
Examples include ZrN, Si 3 N 4, etc., and carbides include TiC,
ZrC, HfC, VC, TaC, NbC, WC, BiC, SiC
etc. Also metal borides, such as AlB,
SiB, TiB 2 , ZrB 2 , HfB, VB 2 , TaB, WB, etc. can also be dispersed in the lattice or attached to the lattice surface.
以下、実施例を示す。 Examples are shown below.
セル膜のない軟質ポリウレタンフオームにアル
ミナ85重量％、それにシリカ等を含むセラミツク
原料よりつくつたセラミツク泥漿を付着し、乾燥
後、最高温度1450℃で焼成して、いずれの方向に
も目詰りのない内部連通空間を有する三次元網状
のセル構造をなしたセラミツク多孔体を得た。
Ceramic slurry made from ceramic raw materials containing 85% alumina and silica, etc. is attached to a soft polyurethane foam without a cell membrane, and after drying, it is fired at a maximum temperature of 1450°C to create a product with no clogging in any direction. A ceramic porous body having a three-dimensional network cell structure with internal communication spaces was obtained.
このセラミツク多孔体を約1000倍の電子顕微鏡
写真をとつて観察したところ、針状結晶体（ムラ
イト）が分散していることが確認された。 When this ceramic porous body was observed using an electron microscope photograph with a magnification of approximately 1000 times, it was confirmed that needle-shaped crystals (mullite) were dispersed.
なお、このセラミツク多孔体の嵩比重は0.42、
平均直径は２mm、圧力損失は毎秒風速１ｍで１cm
の厚みを通過するのに水柱10mm、空隙率は87.7％
であつた。 The bulk specific gravity of this porous ceramic material is 0.42,
The average diameter is 2 mm, and the pressure drop is 1 cm at a wind speed of 1 m/s.
It takes 10mm of water column to pass through the thickness of , the porosity is 87.7%
It was hot.
次に、上記セラミツク多孔体（長さ150mm、幅
50mm、厚さ20mm）ａを図面に示すように支持体
ｂ，ｂ上に乗せ、1400℃に加熱してそのときのた
わみ量Δdを測定した結果は０mmであり、耐高温
クリープ性に優れていることが知見された。 Next, the above ceramic porous body (length 150 mm, width
50mm, thickness 20mm) a was placed on supports b and b as shown in the drawing, heated to 1400℃, and the deflection amount Δd at that time was measured. The result was 0 mm, indicating that it has excellent high temperature creep resistance. It was discovered that there were.
図面はセラミツク多孔体のたわみ量の測定方法
の説明図である。
The drawing is an explanatory diagram of a method for measuring the amount of deflection of a porous ceramic body.
Claims (1)
をなしたセラミツク多孔体において、該多孔体を
形成するセラミツク中に針状結晶体が分散してい
ることを特徴とするセラミツク多孔体。 ２ セラミツク多孔体が、嵩比重が0.25〜0.6で
あり、内部連通空間がいずれの方向にも目詰りが
なく、その平均直径が0.2〜10mmであり、圧力損
失が毎秒風速１ｍで１cmの厚みを通過するのに水
柱0.1〜40mmであり、かつ空隙率が75〜95％であ
るものである特許請求の範囲第１項記載のセラミ
ツク多孔体。 ３ セラミツク多孔体がアルミナもしくはコージ
ライト質を主成分としてなり、針状結晶体がムラ
イトからなる特許請求の範囲第１項又は第２項記
載のセラミツク多孔体。[Scope of Claims] 1. A ceramic porous body having a three-dimensional network cell structure having internal communication spaces, characterized in that needle-like crystals are dispersed in the ceramic forming the porous body. Porous body. 2. The ceramic porous body has a bulk specific gravity of 0.25 to 0.6, an internal communication space that is not clogged in any direction, an average diameter of 0.2 to 10 mm, and a pressure loss that can withstand a thickness of 1 cm at a wind speed of 1 m per second. The ceramic porous body according to claim 1, wherein the porous ceramic body has a water column of 0.1 to 40 mm to pass through and a porosity of 75 to 95%. 3. The ceramic porous body according to claim 1 or 2, wherein the ceramic porous body is mainly composed of alumina or cordierite, and the acicular crystal bodies are mullite.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22159082A JPS59111967A (en) | 1982-12-17 | 1982-12-17 | Ceramic porous body |
| US06/469,395 US4560478A (en) | 1982-02-26 | 1983-02-24 | Porous ceramic article |
| DE8383101888T DE3372748D1 (en) | 1982-02-26 | 1983-02-25 | Porous ceramic article |
| EP83101888A EP0087789B1 (en) | 1982-02-26 | 1983-02-25 | Porous ceramic article |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22159082A JPS59111967A (en) | 1982-12-17 | 1982-12-17 | Ceramic porous body |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5278980A Division JP2507976B2 (en) | 1993-10-12 | 1993-10-12 | Method for manufacturing ceramic porous body |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS59111967A JPS59111967A (en) | 1984-06-28 |
| JPH0474308B2 true JPH0474308B2 (en) | 1992-11-25 |
Family
ID=16769130
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP22159082A Granted JPS59111967A (en) | 1982-02-26 | 1982-12-17 | Ceramic porous body |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS59111967A (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61141682A (en) * | 1984-12-12 | 1986-06-28 | 東芝セラミツクス株式会社 | Ceramic foam and manufacture |
| JPH0694065B2 (en) * | 1985-05-13 | 1994-11-24 | 株式会社ブリヂストン | For iron castings |
| JP2507976B2 (en) * | 1993-10-12 | 1996-06-19 | 株式会社ブリヂストン | Method for manufacturing ceramic porous body |
| JP2003007682A (en) | 2001-06-25 | 2003-01-10 | Matsushita Electric Ind Co Ltd | Electrode member for plasma processing equipment |
-
1982
- 1982-12-17 JP JP22159082A patent/JPS59111967A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS59111967A (en) | 1984-06-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US4560478A (en) | Porous ceramic article | |
| CN101323524B (en) | Preparation of oriented hole silicon carbide porous ceramic | |
| JP3548914B2 (en) | Method for producing catalyst carrier | |
| GB2089774A (en) | Activated carbon | |
| Jing et al. | Fabrication and properties of SiC/mullite composite porous ceramics | |
| US10350532B2 (en) | Porous alpha-SiC-containing shaped body having a contiguous open pore structure | |
| JPS6240061B2 (en) | ||
| GB2164580A (en) | Heat-resistant, highly expansible sheet material for supporting catalyst carrier and process for the preparation thereof | |
| JPH05339059A (en) | Si-sic shelf plate and its production | |
| US8475906B2 (en) | Silicon carbide based porous material and method for preparation thereof | |
| US5016610A (en) | Radiant tube type heater | |
| JP2005529052A (en) | Heat resistant products | |
| JPH0474308B2 (en) | ||
| JP2507976B2 (en) | Method for manufacturing ceramic porous body | |
| JP2000016872A (en) | Porous silicon carbide sintered body and its production | |
| JPH0246545B2 (en) | ||
| JPH0624636B2 (en) | Catalyst carrier and method for producing the same | |
| JPH0379310B2 (en) | ||
| KR100369210B1 (en) | Porous Ceramic Heating Element, Its Preparation and Exhaust Gas Filter Using Same | |
| JP4041879B2 (en) | Ceramic porous body and method for producing the same | |
| JP3689408B2 (en) | Silicon carbide honeycomb structure and ceramic filter using the same | |
| JPS59174572A (en) | Manufacture of minute cordierite-silicon nitride sintered body | |
| JP2003181301A (en) | Method for manufacturing catalyst carrier | |
| JPS61259763A (en) | Catalyst carrier made of porous silicon carbide sintered body | |
| JPS6046981A (en) | Ceramic porous body |