JPH03223184A - Porous ceramic material - Google Patents
Porous ceramic materialInfo
- Publication number
- JPH03223184A JPH03223184A JP34058390A JP34058390A JPH03223184A JP H03223184 A JPH03223184 A JP H03223184A JP 34058390 A JP34058390 A JP 34058390A JP 34058390 A JP34058390 A JP 34058390A JP H03223184 A JPH03223184 A JP H03223184A
- Authority
- JP
- Japan
- Prior art keywords
- porosity
- weight
- slurry
- foam
- ceramic
- 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.)
- Granted
Links
- 229910010293 ceramic material Inorganic materials 0.000 title abstract 4
- 239000000919 ceramic Substances 0.000 claims abstract description 29
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 abstract description 38
- 239000000463 material Substances 0.000 abstract description 19
- 239000006260 foam Substances 0.000 abstract description 17
- 239000011148 porous material Substances 0.000 abstract description 17
- 239000002002 slurry Substances 0.000 abstract description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 abstract description 10
- 239000000843 powder Substances 0.000 abstract description 7
- 238000000034 method Methods 0.000 abstract description 6
- 239000003381 stabilizer Substances 0.000 abstract description 6
- ODINCKMPIJJUCX-UHFFFAOYSA-N Calcium oxide Chemical compound [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 abstract description 4
- 239000000292 calcium oxide Substances 0.000 abstract description 4
- 235000012255 calcium oxide Nutrition 0.000 abstract description 4
- 238000010438 heat treatment Methods 0.000 abstract description 4
- 239000011230 binding agent Substances 0.000 abstract description 3
- 239000002270 dispersing agent Substances 0.000 abstract description 3
- 238000003756 stirring Methods 0.000 abstract description 3
- 238000002156 mixing Methods 0.000 abstract description 2
- 238000010791 quenching Methods 0.000 abstract 1
- 230000000171 quenching effect Effects 0.000 abstract 1
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 16
- 238000005452 bending Methods 0.000 description 11
- 238000010304 firing Methods 0.000 description 11
- 230000005484 gravity Effects 0.000 description 8
- 239000000395 magnesium oxide Substances 0.000 description 8
- 238000013001 point bending Methods 0.000 description 6
- 239000002994 raw material Substances 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- QGZKDVFQNNGYKY-UHFFFAOYSA-O Ammonium Chemical compound [NH4+] QGZKDVFQNNGYKY-UHFFFAOYSA-O 0.000 description 4
- 229920005822 acrylic binder Polymers 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 4
- 229940088990 ammonium stearate Drugs 0.000 description 4
- JPNZKPRONVOMLL-UHFFFAOYSA-N azane;octadecanoic acid Chemical compound [NH4+].CCCCCCCCCCCCCCCCCC([O-])=O JPNZKPRONVOMLL-UHFFFAOYSA-N 0.000 description 4
- JRPBQTZRNDNNOP-UHFFFAOYSA-N barium titanate Chemical compound [Ba+2].[Ba+2].[O-][Ti]([O-])([O-])[O-] JRPBQTZRNDNNOP-UHFFFAOYSA-N 0.000 description 4
- 229910002113 barium titanate Inorganic materials 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000001035 drying Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 229920000058 polyacrylate Polymers 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000005187 foaming Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- JOYRKODLDBILNP-UHFFFAOYSA-N Ethyl urethane Chemical compound CCOC(N)=O JOYRKODLDBILNP-UHFFFAOYSA-N 0.000 description 2
- 239000003990 capacitor Substances 0.000 description 2
- 239000002612 dispersion medium Substances 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000011347 resin Substances 0.000 description 2
- 229920005989 resin Polymers 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229920005830 Polyurethane Foam Polymers 0.000 description 1
- 239000012615 aggregate Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- CETPSERCERDGAM-UHFFFAOYSA-N ceric oxide Chemical compound O=[Ce]=O CETPSERCERDGAM-UHFFFAOYSA-N 0.000 description 1
- 229910000422 cerium(IV) oxide Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000001066 destructive effect Effects 0.000 description 1
- 239000012776 electronic material Substances 0.000 description 1
- 238000009408 flooring Methods 0.000 description 1
- 239000012774 insulation material Substances 0.000 description 1
- QSHDDOUJBYECFT-UHFFFAOYSA-N mercury Chemical compound [Hg] QSHDDOUJBYECFT-UHFFFAOYSA-N 0.000 description 1
- 229910052753 mercury Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 229920000642 polymer Polymers 0.000 description 1
- 239000011496 polyurethane foam Substances 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- -1 silica compound Chemical class 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 229910002076 stabilized zirconia Inorganic materials 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Porous Artificial Stone Or Porous Ceramic Products (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明はセラミックス多孔体に関し、特に電子部品焼成
などに使用される多孔質道具材、床材。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to porous ceramic bodies, particularly porous tool materials and flooring materials used for firing electronic parts.
壁材等の軽量構造材、冷蔵庫、家屋等の断熱材、エア、
水等のフィルター材、人口骨材、基板、振動子等のエレ
クトロニクス材等の各種の用途に用いられるものである
。Lightweight structural materials such as wall materials, insulation materials for refrigerators and houses, air,
It is used for various purposes such as filter materials for water, artificial aggregates, substrates, electronic materials such as vibrators, etc.
［従来の技術と課題］
従来、例えば電子部品焼成用の軽量道具材として、アル
ミナファイバーを主成分としこれをシリカ化合物等で結
合したものが使用されていた。[Prior Art and Problems] Conventionally, for example, as a lightweight tool material for firing electronic parts, a material made of alumina fiber as a main component and bonded with a silica compound or the like has been used.
ところで、電子部品材料としては、チタン酸バリウムな
とによるコンデンサーやフェライトなどが代表的である
が、チタン酸バリウムはアルミナと反応するため焼成用
道具材にはジルコニアコーティングか施されていた。ま
た、ジルコニア質の軽量道具材として、一部では網目構
造をもったセラミックも使用されており、大型炉用とし
てはジルコニア質の耐火物が使用されている。By the way, typical electronic component materials include capacitors and ferrite made of barium titanate, but since barium titanate reacts with alumina, firing tool materials were coated with zirconia. Ceramics with a mesh structure are also used as lightweight zirconia tool materials, and zirconia refractories are used for large furnaces.
しかしながら、アルミファイバーにジルコニアコーティ
ングを施しである軽量道具材においては、基材のアルミ
ナとジルコニアの熱膨張率が異なるため、使用における
加熱冷却の繰り返しによりジルコニアコーティングの剥
離が起こり、ジルコニア片が焼成物に付着したり１むき
出しになったアルミナと焼成物が反応するという問題点
を有している。また、ジルコニア質耐火物性の道具材は
、その重量・熱容量ともに大きいという問題点を有して
いる。However, in lightweight tool materials made of aluminum fiber coated with zirconia, the thermal expansion coefficients of the base material alumina and zirconia are different, so repeated heating and cooling during use causes the zirconia coating to peel off, causing zirconia pieces to form in the fired product. There is a problem in that the fired product reacts with the alumina that adheres to or is exposed. Additionally, zirconia refractory tool materials have the problem of being large in weight and heat capacity.
また、ジルコニア質の網目構造をもったセラミックは、
例えばウレタンフオームのような網目構造をもった下地
に、セラミック原料スラリーを付着させ、乾燥・焼成し
て得られるものであり、その製造方法の制約から大きな
網目構造のものしか得られない。このため、例えばチッ
プコンデンサのような小さな被焼成物を焼成する際に被
焼成物が大きな網目構造に入り込み、うまく焼成できな
いという問題点を有している。更に、同様に製造上の制
約から、この網目構造をもったセラミックはそのセラミ
ック部分の内部にポリマー下地に起因する孔か有り、そ
のうえほとんどのものでは、そのセラミック部分に亀裂
か多数生しており、強度が著しく低くなっている。この
ため、このような軽量道具材ては、数回の使用で破損し
てしまうという問題を有している。In addition, ceramics with a zirconia network structure are
For example, it is obtained by adhering a ceramic raw material slurry to a base with a network structure such as urethane foam, drying and firing it, and due to limitations in the manufacturing method, only those with a large network structure can be obtained. For this reason, when firing a small object to be fired, such as a chip capacitor, for example, there is a problem that the object to be fired gets into a large network structure and cannot be fired properly. Furthermore, due to similar manufacturing constraints, ceramics with this network structure have pores inside the ceramic part due to the polymer base, and most of them also have many cracks in the ceramic part. , the strength is significantly lower. Therefore, such lightweight tool materials have the problem of being damaged after being used several times.
本発明は上記事情に鑑みてなされたもので、軽量で熱容
量が小さく、高温で長時間使用でき、かつ急熱急冷に耐
えうるセラミックス多孔体を提供することを目的とする
。The present invention was made in view of the above circumstances, and an object of the present invention is to provide a ceramic porous body that is lightweight, has a small heat capacity, can be used at high temperatures for a long time, and can withstand rapid heating and cooling.
［課題を解決するための手段と作用］
本発明は、気孔率１０％以下のセラミックス骨材から構
成され、かつ全体の気孔率か３０〜９８％の多孔体であ
ることを特徴とする多孔質道具材である。[Means and effects for solving the problems] The present invention provides a porous body comprising ceramic aggregate with a porosity of 10% or less and having an overall porosity of 30 to 98%. It is a tool material.
本発明において、全体の気孔率を３０〜９８９６と規定
としたのは、気孔率が９８％を越えると、網目構造を構
成する緻密なセラミックス網の直径が小さくなりすぎて
、使用上必要とされる十分な強度が得られず、製作も困
難になるためである。また、気孔率が３０％未満の場合
、熱容量が大きくなりすぎて本発明の効果が十分得られ
ないからである（第１図及び第２図参照）、、ここで、
第１図はＺｒＯ２多孔体の場合を示し、第２図はＭｇＯ
多孔体の場合を示す。In the present invention, the overall porosity is specified as 30 to 9896.If the porosity exceeds 98%, the diameter of the dense ceramic network that makes up the network structure becomes too small, which is not necessary for use. This is because sufficient strength cannot be obtained and manufacturing becomes difficult. In addition, if the porosity is less than 30%, the heat capacity becomes too large and the effects of the present invention cannot be obtained sufficiently (see FIGS. 1 and 2).Here,
Figure 1 shows the case of ZrO2 porous body, and Figure 2 shows the case of MgO2 porous body.
The case of a porous body is shown.
本発明において、セラミックス骨材の気孔率を１０％以
下とするのは、１０％を越えると強度か低下するためで
ある（第３図及び第４図参照）。ここで、第３図はＺｒ
Ｏ２における気孔率と曲げ強さとの関係を示し、第４図
はＭｇＯにおける気孔率と曲げ強さとの関係を示す。セ
ラミックス部分の気孔率の測定は、次のようにして求め
る。まず、比重ビンを用いて粗砕したサンプルと微粉砕
したサンプルの比重を測定する。ここで、本発明品のセ
ラミック部分は概略全て閉気孔であるため、粗砕したサ
ンプルの比重はかさ比重、微粉砕したサンプルの比重は
真比重と考える事ができる。従って、前記気孔率は、以
下の式により求める事ができる。In the present invention, the reason why the porosity of the ceramic aggregate is set to 10% or less is that if it exceeds 10%, the strength will decrease (see FIGS. 3 and 4). Here, Figure 3 shows Zr
The relationship between porosity and bending strength in O2 is shown, and FIG. 4 shows the relationship between porosity and bending strength in MgO. The porosity of the ceramic portion is determined as follows. First, the specific gravity of the coarsely crushed sample and the finely crushed sample is measured using a specific gravity bottle. Here, since the ceramic part of the product of the present invention has almost all closed pores, the specific gravity of the coarsely crushed sample can be considered to be the bulk specific gravity, and the specific gravity of the finely crushed sample can be considered to be the true specific gravity. Therefore, the porosity can be determined by the following formula.
気孔率−（１−（真比重−かさ比重）／真比重）Ｘ１０
０ （％）
なお、上記気孔率は、望ましくは５％以下が好ましい。Porosity-(1-(true specific gravity-bulk specific gravity)/true specific gravity)X10
0 (%) The above porosity is preferably 5% or less.
本発明において、本発明に係るセラミックス多孔体を電
子部品焼成などの多孔質道具材として使用する場合は、
表面部分の気孔径を５μｍ〜２ｍｍにするのが望ましい
。この理由は、気孔径か２ｍｍを越えると小さな被焼成
物、大きさ数ｍｍの焼成に不都合であり、気孔径が５μ
ｍ未満の場合セラミック部分の直径か小さくなりすぎて
使用上ｇ 要とされる十分な強度か得られないからであ
る。In the present invention, when the ceramic porous body according to the present invention is used as a porous tool material for firing electronic parts, etc.,
It is desirable that the pore diameter of the surface portion be 5 μm to 2 mm. The reason for this is that if the pore diameter exceeds 2 mm, it is inconvenient for firing small objects to be fired, or those with a size of several mm.
This is because if it is less than m, the diameter of the ceramic portion becomes too small and sufficient strength required for use cannot be obtained.
本発明において、セラミックスとしては、純ジルコニア
、あるいはジルコニアをカルシア、マグネンア、イツト
リア、セリアなどで部分安定化又は全安定化したものが
挙げられ、これらを単一あるいは複数混合して用いても
よい。なお、緻密な安定化されていないジルコニアの場
合、相転移温度における急激な体積変化から生ずる応力
によって破壊してしまうが、本発明品の場合にはその構
造中に多量に存在する空間が応力を緩和し、破壊する事
がない。しかし、相転移温度における体積変化が起こる
事は避けられないため、望ましくは安定化したジルコニ
アを使用したほうがよい。また、上記セラミックスとし
ては、高純度（９９νｔ％以上）なマグネシアを用いる
ことができる。In the present invention, examples of the ceramic include pure zirconia, or zirconia partially or fully stabilized with calcia, magneur, ittria, ceria, etc., and these may be used singly or in combination. In the case of dense, unstabilized zirconia, it will break due to the stress caused by the rapid volume change at the phase transition temperature, but in the case of the product of the present invention, the large amount of space existing in its structure suppresses the stress. Alleviating and non-destructive. However, since a volume change at the phase transition temperature is unavoidable, it is preferable to use stabilized zirconia. Further, as the ceramic, highly pure (99vt% or more) magnesia can be used.
本発明において、三次元網目構造を有するセラミック多
孔体の骨格における気孔率の測定は、股に行われるでい
るようなような水銀圧入法等では、三次元網目構造に起
因する気孔であるのか骨格中に存在する気孔に起因する
ものであるか区別かつかず測定不可能である。しかし、
非測定物を樹脂包埋した後これを研磨し顕微鏡を使用し
てその８１織を観測し画像処理によって骨格中の気孔部
分を特定して、骨格中の気孔率を測定することにより骨
格中の気孔率を求める事ができる。In the present invention, the porosity of the skeleton of a ceramic porous body having a three-dimensional network structure is measured by the mercury intrusion method, etc., which is carried out on the crotch. It is impossible to distinguish whether this is due to the pores present in the pores and cannot be measured. but,
After embedding the object to be measured in resin, polishing it and observing its 81 textures using a microscope, identifying the pores in the skeleton through image processing and measuring the porosity in the skeleton. Porosity can be determined.
次に、網目構造をもつセラミック骨材から構成される多
孔体は、例えばセラミック粉末と分散媒をバインダー、
分散剤、整泡剤、泡安定剤のうち少なくとも一つと共に
混合して原料スラリーとして、これを攪拌して泡立て成
形することにより作られる。ここで、バインダーは、乾
燥後の成形体強度を増し作業を容易にするため、またス
ラリーの粘度を増して泡立ての効率を増し泡の安定化を
計る目的で添加される。分散剤は、分散媒中でセラミッ
ク粉を分散して原料スラリーの高濃度化を可能にし、成
形体のセラミック部分の密度を増加する目的で添加され
る。整泡剤は、原料スラリーの泡立ちを助は成形体の気
孔率を増す目的で添加される。泡安定剤は、泡立てによ
って生じた原料スラリーの泡を安定化し、成形体が乾燥
する間に泡が消失しないように添加される。以上のよう
に多孔体は成形体を乾燥、焼成して作製されるか、焼成
の方法１条件等は緻密なセラミックスの場合と同様でよ
い。また、前記多孔体の気孔率は、原料スラリーに添加
する整泡剤の量や攪拌の度合いによって調整することが
できる。Next, a porous body made of a ceramic aggregate with a network structure is made by combining ceramic powder and a dispersion medium with a binder, for example.
It is produced by mixing with at least one of a dispersant, a foam stabilizer, and a foam stabilizer to form a raw material slurry, which is then stirred and foam-molded. Here, the binder is added for the purpose of increasing the strength of the molded product after drying and making the work easier, and also for the purpose of increasing the viscosity of the slurry, increasing the efficiency of foaming, and stabilizing the foam. The dispersant is added for the purpose of dispersing the ceramic powder in the dispersion medium, making it possible to increase the concentration of the raw material slurry, and increasing the density of the ceramic portion of the molded body. The foam stabilizer is added for the purpose of assisting foaming of the raw material slurry and increasing the porosity of the molded article. The foam stabilizer is added to stabilize the foam of the raw material slurry generated by foaming and to prevent the foam from disappearing while the molded product is drying. As described above, the porous body may be produced by drying and firing a molded body, or the firing method and conditions may be the same as those for dense ceramics. Further, the porosity of the porous body can be adjusted by adjusting the amount of foam stabilizer added to the raw material slurry and the degree of stirring.
以下、本発明の実施例について説明する。Examples of the present invention will be described below.
［実施例１］
平均粒径１μｍでＣａＯを５％含んだジルコニア粉１０
０重量部にポリアクリル酸アンモニウム１重量部、イオ
ン交換水１００重量部、ＰＶＡ２重量部をボールミルに
て１昼夜混合した。次に、これに、ステアリン酸アンモ
ニウム１重量部、アクリル系バインダー５重量部、イオ
ン交換水２０重量部を混合しながら攪拌機で泡立てた。[Example 1] Zirconia powder 10 containing 5% CaO with an average particle size of 1 μm
0 parts by weight, 1 part by weight of ammonium polyacrylate, 100 parts by weight of ion-exchanged water, and 2 parts by weight of PVA were mixed day and night in a ball mill. Next, 1 part by weight of ammonium stearate, 5 parts by weight of an acrylic binder, and 20 parts by weight of ion-exchanged water were mixed into the mixture and foamed with a stirrer.
次いで、泡が安定した後、乾燥機で乾燥して成形体を得
た。Then, after the foam became stable, it was dried in a drier to obtain a molded article.
この成形体を空気中、 １７００℃で２時間焼成したと
ころ、得られた網目構造をもった多孔体は、表面部分の
最大機構径が約５００μｍであり、気孔の平均の大きさ
は１００μｍ１気孔率は８５％、かさ密度は０．９ｇ／
ｃｍ３であった。When this molded body was fired in air at 1700°C for 2 hours, the resulting porous body with a network structure had a maximum mechanical diameter of about 500 μm on the surface, and an average pore size of 100 μm. is 85%, bulk density is 0.9g/
It was cm3.
この網目構造をもった多孔体を２００ｍｍ Ｘ １ｏｏ
ＩＩ＋ｍ×５ｍ１ｌｌに加工しチタン酸バリウムの焼成
に使用したところ、１３００℃で破損することなく１０
０回の使用に耐えた。The porous material with this network structure is 200mm x 1oo
When it was processed into a size of II+m x 5ml and used for firing barium titanate, it was heated at 1300℃ without breaking.
Withstood 0 uses.
［実施例２］
平均粒径３μｍでＣａＯを５％含んだジルコニア粉１０
０重量部にポリアクリル酸アンモニウム１重量部、イオ
ン交換水１００重量部、ＰＶＡ２重量部をボールミルに
て１昼夜混合した。次に、これに、ステアリン酸アンモ
ニウム０．５〜ｌＯ重量部、アクリル系バインダー５重
量部、イオン交換水２０重量部を混合しながら攪拌機で
泡立てた。次いで、泡が安定した後、乾燥機で乾燥して
気孔率の異なる成形体を数種類得た。[Example 2] Zirconia powder 10 containing 5% CaO with an average particle size of 3 μm
0 parts by weight, 1 part by weight of ammonium polyacrylate, 100 parts by weight of ion-exchanged water, and 2 parts by weight of PVA were mixed day and night in a ball mill. Next, 0.5 to 10 parts by weight of ammonium stearate, 5 parts by weight of an acrylic binder, and 20 parts by weight of ion-exchanged water were mixed into the mixture and foamed with a stirrer. Next, after the foam became stable, it was dried in a dryer to obtain several types of molded bodies with different porosity.
この成形体を空気中、 １７００℃で２時間焼成して得
られた気孔率の異なる網目構造をもった多孔体を、４
ｍｍＸ ３１ＤＩＩＩＸ ４ＤＩに加工しそれらの三点
曲げ強さを測定した。この結果から得た気孔率と曲げ強
さの関係の一例は、第１図に示す通りである。This molded body was fired in air at 1700°C for 2 hours, and a porous body with a network structure with different porosity was obtained.
The three-point bending strength of the three-point bending strength was measured. An example of the relationship between porosity and bending strength obtained from this result is as shown in FIG.
同図より、気孔率が９８％を超えると、曲げ強さか著し
く低下することか明らかである。From the figure, it is clear that when the porosity exceeds 98%, the bending strength decreases significantly.
〔実施例３コ
平均粒径１μｍで純度９９．５％のマグネシア粉１００
重量部にポリアクリル酸アンモニウム１重量部、イオン
交換水１００重量部、ＰＶＡ２重量部をボールミルにて
１昼夜混合した。次に、これに、ステアリン酸アンモニ
ウム１重量部、アクリル系バインダー５重量部、イオン
交換水２０重量部を混合しながら攪拌機で泡立てた。次
いで、泡が安定した後、乾燥機で乾燥して成形体を得た
。[Example 3 Magnesia powder 100 with an average particle size of 1 μm and a purity of 99.5%]
1 part by weight of ammonium polyacrylate, 100 parts by weight of ion-exchanged water, and 2 parts by weight of PVA were mixed in a ball mill for one day and night. Next, 1 part by weight of ammonium stearate, 5 parts by weight of an acrylic binder, and 20 parts by weight of ion-exchanged water were mixed into the mixture and foamed with a stirrer. Then, after the foam became stable, it was dried in a drier to obtain a molded article.
この成形体を空気中、 １７００℃で２時間焼成したと
ころ、得られた網目構造をもった多孔体は、表面部分の
最大気孔径が約５００μｍであり、気孔の平均の大きさ
は１００μｍ１気孔率は８５％、かさ密度は０．５ｇ／
ｃ１１３であった。When this molded body was fired in air at 1700°C for 2 hours, the resulting porous body with a network structure had a maximum pore diameter of about 500 μm on the surface, and an average pore size of 100 μm. is 85%, bulk density is 0.5g/
It was c113.
この網目構造をもった多孔体を２００ｍｍ Ｘ １００
ｍｍ×５１１１ｍに加工し、チタン酸バリウムの焼成に
使用したところ、１３００℃で破損や製品と反応するこ
となく１００回の使用に耐えた。The porous body with this network structure is 200 mm x 100
When it was processed into a size of 5111 mm x 5111 m and used for firing barium titanate, it withstood 100 uses at 1300°C without breaking or reacting with the product.
［実施例４コ
平均粒径３μｍで純度９９，５％のマグネシア粉１００
重量部にポリアクリル酸アンモニウム１重量部、イオン
交換水１００重量部、ＰＶＡ２重量部をボールミルにて
１昼夜混合した。次に、これに、ステアリン酸アンモニ
ウム０．５〜１０重量部、アクリル系バインダー５重量
部、イオン交換水２０重量部を混合しながら攪拌機で泡
立てた。次いて、泡が安定した後、乾燥機で乾燥して気
孔率の異なる成形体を数種類書た。[Example 4] Magnesia powder 100 with an average particle size of 3 μm and a purity of 99.5%
1 part by weight of ammonium polyacrylate, 100 parts by weight of ion-exchanged water, and 2 parts by weight of PVA were mixed in a ball mill for one day and night. Next, 0.5 to 10 parts by weight of ammonium stearate, 5 parts by weight of an acrylic binder, and 20 parts by weight of ion-exchanged water were mixed into the mixture and foamed with a stirrer. Next, after the foam became stable, it was dried in a dryer to form several types of molded bodies with different porosity.
これらの成形体を空気中、 １７００℃で２時間焼成し
て得られた気孔率の異なる網目構造をもった多孔体を、
４ ｎｕｎＸ ３ ｍｍＸ ４０ｍｍに加工しそれらの
三点曲げ強さを測定した。この結果から得た気孔率と曲
げ強さの関係の一例は、第２図に示す通りである。同図
より、気孔率が９８％を超えると、曲げ強さが著しく低
下することか明らかである。These molded bodies were fired in air at 1,700°C for 2 hours, and the resulting porous body had a network structure with different porosity.
It was processed into 4 mm x 3 mm x 40 mm and its three-point bending strength was measured. An example of the relationship between porosity and bending strength obtained from this result is as shown in FIG. From the figure, it is clear that when the porosity exceeds 98%, the bending strength decreases significantly.
また、実施例１及び実施例３において作製した多孔体を
樹脂包埋した後これを研磨し、顕微鏡を使用して組織を
画像処理により骨格中の気孔部分を特定して、骨格中の
気孔率を測定した。測定は、それぞれの試料につき１０
０本の骨格を測定しその平均値を求めた。なお、気孔径
０．５μｍ以上を測定の対象としたか、これは顕微鏡の
解像度とαｊ定の簡便さのために設定したものて、でき
うる限り小さい径の気孔まで測定する事が望ましい。し
かしながら、気孔が機械的強度に及ぼす影響はその気孔
径の大きいものはと顕著であるため実際上あまり問題に
はならない。骨格中の気孔率（％）は、実施例１の場合
が１，５、実施例３の場合が３．０であった。更に、実
施例２について、実施例１の場合と同様な測定方法を用
いて骨材の気孔率を調べたところ（平均粒径３μｍのマ
グネシア、全体気孔率８５％のもの） 、５．０であっ
た。更には、実施例４についても、全体気孔率８５％の
ものについて、同様に測定したところ、６．５％であっ
た。In addition, the porous bodies produced in Example 1 and Example 3 were embedded in resin, polished, and the pores in the skeleton were identified by image processing of the structure using a microscope, and the porosity in the skeleton was determined. was measured. Measurements are made on 10 samples for each sample.
0 skeletons were measured and the average value was determined. Note that although the pore diameter of 0.5 μm or more was the object of measurement, this was set for the resolution of the microscope and the ease of determining αj, and it is desirable to measure pores with a diameter as small as possible. However, since the influence of pores on mechanical strength is more pronounced as the pores have larger diameters, this does not pose much of a problem in practice. The porosity (%) in the skeleton was 1.5 in Example 1 and 3.0 in Example 3. Furthermore, regarding Example 2, when the porosity of the aggregate was examined using the same measuring method as in Example 1 (magnesia with an average particle size of 3 μm, total porosity of 85%), it was found to be 5.0. there were. Furthermore, in Example 4, the overall porosity of 85% was similarly measured and found to be 6.5%.
［比較例１，２］
ポリウレタンフォームにジルコニア及びマグネシアのス
ラリーを付着させこれを乾燥した後、１７００℃で２時
間焼成しこれらをそれぞれ比較例１゜比較例２とした。[Comparative Examples 1 and 2] A slurry of zirconia and magnesia was applied to a polyurethane foam, dried, and then baked at 1700° C. for 2 hours to form Comparative Example 1 and Comparative Example 2, respectively.
これらについて上述した方法にて骨格中の気孔率（％）
を測定した。また、多孔体の気孔率（％）、三点曲げ強
度（ＭＰａ）を測定した。その結果、比較例１の場合は
骨格中の気孔率４０％、気孔率８２９６．三点曲げ強度
１．２ＭＰａで、比較例２の場合は骨格中の気孔率４０
％、気孔率８７％、三点曲げ強度０．７ＭＰａであった
。The porosity (%) in the skeleton was calculated using the method described above.
was measured. In addition, the porosity (%) and three-point bending strength (MPa) of the porous body were measured. As a result, in the case of Comparative Example 1, the porosity in the skeleton was 40%, and the porosity was 8296. The three-point bending strength was 1.2 MPa, and the porosity in the skeleton was 40 in the case of Comparative Example 2.
%, porosity was 87%, and three-point bending strength was 0.7 MPa.
このように、ウレタンフオームにセラミックスラリ−を
付着させる方法で得られた多孔体は、実施例２及び実施
例４に示めされる、同気孔率の本発明品と比較して著し
く低い三点曲げ強さを示し、実施例１．実施例３に示さ
れる本発明品と比較して非常に大きな骨格中の気孔率を
もつことが分かる。As described above, the porous body obtained by the method of attaching ceramic slurry to urethane foam has a significantly lower three points than the products of the present invention having the same porosity as shown in Examples 2 and 4. The bending strength is shown in Example 1. It can be seen that compared to the product of the present invention shown in Example 3, it has a very large porosity in the skeleton.
［発明の効果］
以上詳述した如く本発明によれば、軽量で熱容量が小さ
く、高温で長時間使用でき、かつ急熱急冷に耐えうる高
信頼性のセラミックス多孔体を提供できる。[Effects of the Invention] As detailed above, according to the present invention, it is possible to provide a highly reliable ceramic porous body that is lightweight, has a small heat capacity, can be used at high temperatures for a long time, and can withstand rapid heating and cooling.
第１図は本発明に係るＺｒＯ２多孔体の気孔率と曲げ強
さ、熱容量との関係を示す特性図、第２図は本発明に係
るＭｇＯ多孔体の気孔率と曲げ強さ、熱容量との関係を
示す特性図、第３図はＺｒＯ２の気孔率と曲げ強さとの
関係を示す特性図、第４図はＭｇＯの気孔率と曲げ強さ
との関係を示す特性図である。Figure 1 is a characteristic diagram showing the relationship between the porosity, bending strength, and heat capacity of the ZrO2 porous body according to the present invention, and Figure 2 is a characteristic diagram showing the relationship between the porosity, bending strength, and heat capacity of the MgO porous body according to the present invention. FIG. 3 is a characteristic diagram showing the relationship between the porosity of ZrO2 and bending strength, and FIG. 4 is a characteristic diagram showing the relationship between the porosity of MgO and bending strength.
Claims (1)
つ全体の気孔率が３０〜９８％であることを特徴とする
セラミックス多孔体。A porous ceramic body comprising a ceramic aggregate having a porosity of 10% or less, and having an overall porosity of 30 to 98%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2340583A JP2510044B2 (en) | 1989-12-28 | 1990-11-30 | Ceramic porous body |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1-343617 | 1989-12-28 | ||
| JP34361789 | 1989-12-28 | ||
| JP2340583A JP2510044B2 (en) | 1989-12-28 | 1990-11-30 | Ceramic porous body |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03223184A true JPH03223184A (en) | 1991-10-02 |
| JP2510044B2 JP2510044B2 (en) | 1996-06-26 |
Family
ID=26576738
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2340583A Expired - Lifetime JP2510044B2 (en) | 1989-12-28 | 1990-11-30 | Ceramic porous body |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2510044B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5895897A (en) * | 1996-12-26 | 1999-04-20 | Ishikawajima-Harima Heavy Industries Co., Ltd. | Light-weight ceramic acoustic absorber and method of manufacturing the same |
| JP2004337833A (en) * | 2003-01-17 | 2004-12-02 | Toshiba Ceramics Co Ltd | Member for separating gas |
| WO2012008352A1 (en) * | 2010-07-13 | 2012-01-19 | 三井金属鉱業株式会社 | Heat insulating refractory and method for producing same |
| CN114095597A (en) * | 2020-08-24 | 2022-02-25 | Oppo广东移动通信有限公司 | Ceramic composite material, manufacturing method thereof, shell of electronic equipment and electronic equipment |
| CN114532618A (en) * | 2022-02-28 | 2022-05-27 | 山东国瓷功能材料股份有限公司 | Porous ceramic tape-casting slurry, porous ceramic atomizing core and preparation method |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| US5895897A (en) * | 1996-12-26 | 1999-04-20 | Ishikawajima-Harima Heavy Industries Co., Ltd. | Light-weight ceramic acoustic absorber and method of manufacturing the same |
| JP2004337833A (en) * | 2003-01-17 | 2004-12-02 | Toshiba Ceramics Co Ltd | Member for separating gas |
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| CN114095597A (en) * | 2020-08-24 | 2022-02-25 | Oppo广东移动通信有限公司 | Ceramic composite material, manufacturing method thereof, shell of electronic equipment and electronic equipment |
| CN114532618A (en) * | 2022-02-28 | 2022-05-27 | 山东国瓷功能材料股份有限公司 | Porous ceramic tape-casting slurry, porous ceramic atomizing core and preparation method |
| CN114532618B (en) * | 2022-02-28 | 2023-01-31 | 山东国瓷功能材料股份有限公司 | Porous ceramic tape-casting slurry, porous ceramic atomizing core and preparation method |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2510044B2 (en) | 1996-06-26 |
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