JPH0437645A - Lithia-based ceramics honeycomb structure and its production - Google Patents
Lithia-based ceramics honeycomb structure and its productionInfo
- Publication number
- JPH0437645A JPH0437645A JP2138598A JP13859890A JPH0437645A JP H0437645 A JPH0437645 A JP H0437645A JP 2138598 A JP2138598 A JP 2138598A JP 13859890 A JP13859890 A JP 13859890A JP H0437645 A JPH0437645 A JP H0437645A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- ceramics
- honeycomb structure
- thermal expansion
- al2o3
- 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.)
- Pending
Links
- 239000000919 ceramic Substances 0.000 title claims abstract description 29
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 229910001947 lithium oxide Inorganic materials 0.000 title abstract description 3
- 239000003365 glass fiber Substances 0.000 claims abstract description 13
- 238000001125 extrusion Methods 0.000 claims abstract description 11
- 238000010304 firing Methods 0.000 claims abstract description 11
- HEHRHMRHPUNLIR-UHFFFAOYSA-N aluminum;hydroxy-[hydroxy(oxo)silyl]oxy-oxosilane;lithium Chemical compound [Li].[Al].O[Si](=O)O[Si](O)=O.O[Si](=O)O[Si](O)=O HEHRHMRHPUNLIR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 239000011230 binding agent Substances 0.000 claims abstract description 7
- 239000013078 crystal Substances 0.000 claims abstract description 7
- 229910052670 petalite Inorganic materials 0.000 claims abstract description 7
- CNLWCVNCHLKFHK-UHFFFAOYSA-N aluminum;lithium;dioxido(oxo)silane Chemical compound [Li+].[Al+3].[O-][Si]([O-])=O.[O-][Si]([O-])=O CNLWCVNCHLKFHK-UHFFFAOYSA-N 0.000 claims abstract description 5
- 239000002904 solvent Substances 0.000 claims abstract description 5
- 229910052644 β-spodumene Inorganic materials 0.000 claims abstract description 4
- 238000001035 drying Methods 0.000 claims abstract description 3
- 239000000203 mixture Substances 0.000 claims description 11
- 238000000034 method Methods 0.000 claims description 6
- 239000000843 powder Substances 0.000 claims description 4
- 239000002994 raw material Substances 0.000 claims description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 10
- 229910052593 corundum Inorganic materials 0.000 abstract description 10
- 230000035939 shock Effects 0.000 abstract description 10
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 10
- PEDCQBHIVMGVHV-UHFFFAOYSA-N Glycerine Chemical compound OCC(O)CO PEDCQBHIVMGVHV-UHFFFAOYSA-N 0.000 abstract description 7
- FUJCRWPEOMXPAD-UHFFFAOYSA-N Li2O Inorganic materials [Li+].[Li+].[O-2] FUJCRWPEOMXPAD-UHFFFAOYSA-N 0.000 abstract description 4
- 238000004898 kneading Methods 0.000 abstract description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 abstract description 3
- 239000000314 lubricant Substances 0.000 abstract description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract 6
- 229910052681 coesite Inorganic materials 0.000 abstract 3
- 229910052906 cristobalite Inorganic materials 0.000 abstract 3
- 239000000377 silicon dioxide Substances 0.000 abstract 3
- 235000012239 silicon dioxide Nutrition 0.000 abstract 3
- 239000007858 starting material Substances 0.000 abstract 3
- 229910052682 stishovite Inorganic materials 0.000 abstract 3
- 229910052905 tridymite Inorganic materials 0.000 abstract 3
- XUCJHNOBJLKZNU-UHFFFAOYSA-M dilithium;hydroxide Chemical compound [Li+].[Li+].[OH-] XUCJHNOBJLKZNU-UHFFFAOYSA-M 0.000 abstract 1
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 abstract 1
- 241000264877 Hippospongia communis Species 0.000 description 19
- 229910052744 lithium Inorganic materials 0.000 description 10
- WHXSMMKQMYFTQS-UHFFFAOYSA-N Lithium Chemical compound [Li] WHXSMMKQMYFTQS-UHFFFAOYSA-N 0.000 description 9
- 239000000835 fiber Substances 0.000 description 7
- 229910052878 cordierite Inorganic materials 0.000 description 6
- 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 description 6
- 239000003054 catalyst Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000000465 moulding Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000004372 Polyvinyl alcohol Substances 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 239000000969 carrier Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 235000011187 glycerol Nutrition 0.000 description 2
- 229920000609 methyl cellulose Polymers 0.000 description 2
- 239000001923 methylcellulose Substances 0.000 description 2
- 235000010981 methylcellulose Nutrition 0.000 description 2
- 239000011295 pitch Substances 0.000 description 2
- 229920002451 polyvinyl alcohol Polymers 0.000 description 2
- JFBZPFYRPYOZCQ-UHFFFAOYSA-N [Li].[Al] Chemical compound [Li].[Al] JFBZPFYRPYOZCQ-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000004927 clay Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 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 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910000174 eucryptite Inorganic materials 0.000 description 1
- 238000009472 formulation Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910052863 mullite Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000010349 pulsation Effects 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000001172 regenerating effect Effects 0.000 description 1
- 229910052642 spodumene Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000002918 waste heat Substances 0.000 description 1
Landscapes
- Catalysts (AREA)
- Porous Artificial Stone Or Porous Ceramic Products (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【発明の詳細な説明】
し産業上の利用分野〕
本発明は耐熱衝撃性の優れたセラミックス物品及びその
製造方法に関し、更に詳しくは熱交換器、触媒担体とし
て適するリシア系セラミックス・ハニカム構造体及びそ
の製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a ceramic article with excellent thermal shock resistance and a method for manufacturing the same, and more specifically to a lithium-based ceramic honeycomb structure suitable as a heat exchanger and a catalyst carrier. It relates to its manufacturing method.
β−スポジュメン（Ｌｉ２０ ・Ａｌ２Ｏ３・４Ｓｉ０
２）ヤヘ９ ライ） （Ｌｉ２０ ・Ａｌ２Ｏ３・８Ｓ
ＩＬ）等のリシア系セラミックスは、熱膨張率が小さく
、熱衝撃のかかる熱交換器や触媒担体として利用されて
いる。β-spodumene (Li20 ・Al2O3 ・4Si0
2) Yahe9 Li) (Li20 ・Al2O3・8S
Lithium ceramics such as IL) have a small coefficient of thermal expansion and are used as heat exchangers and catalyst carriers that are subject to thermal shock.
また、リシア系セラミックスより熱膨張率はやや大きい
が、コーディエライトも同様の用途で使用されている。Cordierite is also used for similar purposes, although its coefficient of thermal expansion is slightly larger than that of lithian ceramics.
熱交換器や触媒は作動時に頻繁な熱衝撃を受ける。熱衝
撃抵抗ＲはＤｈ・σアｓ／Ｂ・α（Ｅｌｈ：熱拡散率、
σＴｓ：引張強さ、Ｅ：ヤング率、α：熱膨張係数）で
表される。この内、熱膨張率を除くと同じセラミックス
系では物性の違いは少ない。そこで熱膨張率の小さいβ
−スポジュメンやペタライト等のリシア系セラミックス
が材質的には最適である。しかし、蓄熱型熱交換器のエ
レメントとしてセラミックス・ハニカムが使用されてい
る例は殆んどない。その理由としてハニカム化の困難さ
がある。Heat exchangers and catalysts are subject to frequent thermal shocks during operation. Thermal shock resistance R is Dh・σas/B・α (Elh: thermal diffusivity,
σTs: tensile strength, E: Young's modulus, α: coefficient of thermal expansion). Of these, except for the coefficient of thermal expansion, there are few differences in physical properties among the same ceramics. Therefore, β with a small coefficient of thermal expansion
- Lithian ceramics such as spodumene and petalite are the best materials. However, there are almost no examples of ceramic honeycomb being used as an element in a regenerative heat exchanger. The reason for this is the difficulty of forming honeycombs.
セラミックスが熱交換器用エレメントとして使用されて
いる例としては、硫酸腐食等が問題となる低温部位があ
る。この場合、その目的が、排熱回収ではなく、耐食が
目的であるため、ノ＼二カムの肉厚が厚くても問題はな
い。従ってハニカム部の開孔率は４０％程度である。し
かし、排熱回収を目的とする高温部位はハニカム部の表
面積を大きくする必要があるため、小ピツチで薄肉であ
る必要があり、４０％程度の開孔率のものは使用できず
、６５％以上の開孔率のものが要求される。この開孔率
のものをリシア系セラミックスで製造する場合、反りや
、欠け、亀裂等の欠陥が発生しやすく、製品歩留りが著
しく低下する問題点があった。Examples of ceramics used as heat exchanger elements include low-temperature areas where sulfuric acid corrosion is a problem. In this case, the purpose is not to recover waste heat but to prevent corrosion, so there is no problem even if the thickness of the cam is thick. Therefore, the porosity of the honeycomb portion is approximately 40%. However, in high-temperature parts for the purpose of exhaust heat recovery, the surface area of the honeycomb part needs to be large, so it needs to be thin with small pitches, and a pore area with an open area of about 40% cannot be used; A porosity of at least the above is required. When manufacturing ceramics with this porosity using lithium-based ceramics, defects such as warping, chipping, and cracking are likely to occur, resulting in a significant decrease in product yield.
本発明は上記技術水準に鑑み、開孔率を大きくとれ、し
かも耐衝撃性の優れたリシア系セラミックス・ハニカム
構造体及びその製造方法を提供しようとするものである
。In view of the above-mentioned state of the art, the present invention aims to provide a lithium ceramic honeycomb structure having a large porosity and excellent impact resistance, and a method for manufacturing the same.
すなわち、本発明に係るリシア系セラミックス・ハニカ
ム構造体は、焼成後の結晶構造がβ−スボジュメン（Ｌ
ｉ＝０・Ａｌ２Ｏ３・４Ｓｉ０２）もしくはペタライト
（Ｌ１２０・Ａｌ２Ｏ３・８ＳｉＯ，）となる焼成体に
対して、熱膨張率が３Ｘ１０−６／℃以下となるガラス
繊維を１〜１５重量％含有し、かつノ＼ニカム構造体の
ハニカム部の開孔率が６５％以上であることを特徴とす
るものであり、また、本発明にかかるリシア系セラミッ
クス・ハニカム構造体の製造方法は、５１０２： ７０
〜８０重量％、Ａｌ２Ｏ３： ２０〜２５重量％、Ｌ＋
ｚＯ：２〜３．５重量％のセラミックス粉末１００重量
部に対して、５ｈ０２： ５０重量％以上、Ａｌ２Ｏ３
： ２０重量％以上、ＭｇＯ： １０重量％以上を主成
分とし、かつ、熱膨張率が３ＸｌＯ−’／℃以下である
ガラス繊維を１〜１５重量部添加した後、バインダ、溶
剤等を加えて混練後、押出成形・乾燥・焼成することを
特徴とするものである。That is, the lithium ceramic honeycomb structure according to the present invention has a crystal structure after firing of β-subodumene (L
i = 0・Al2O3・4Si02) or petalite (L120・Al2O3・8SiO,) containing 1 to 15% by weight of glass fiber with a coefficient of thermal expansion of 3X10-6/°C or less, and The honeycomb structure is characterized in that the porosity of the honeycomb portion is 65% or more, and the method for manufacturing a lithium ceramic honeycomb structure according to the present invention is defined in 5102: 70.
~80% by weight, Al2O3: 20-25% by weight, L+
5h02: 50% by weight or more, Al2O3 for 100 parts by weight of ceramic powder of zO: 2 to 3.5% by weight
: 20% by weight or more, MgO: 10% by weight or more as a main component, and after adding 1 to 15 parts by weight of glass fiber having a coefficient of thermal expansion of 3XlO-'/°C or less, and then adding a binder, a solvent, etc. After kneading, it is characterized by extrusion molding, drying, and baking.
以下、本発明の構成を詳細に説明する。 Hereinafter, the configuration of the present invention will be explained in detail.
リチウム・アルミニウムケイ酸塩（以下、ＬＡＳと略す
）としては、β−ユークリプタイト（Ｌｉ、０・＾１，
０３・２Ｓｉ０２）、β−スボジュメン（Ｌ１２０・＾
１２０．・４Ｓ］０２）、ペタライト（Ｌｉ２０・Ａｌ
２Ｏ３・８Ｓ＋０２）がある。ＬＡＳ系セラミックスは
低膨張であり耐熱衝撃性に優れる半面、耐熱性や耐食性
はＬｌ、０を含まないコーディエライトより劣る。Lithium aluminum silicate (hereinafter abbreviated as LAS) includes β-eucryptite (Li, 0.^1,
03.2Si02), β-subodumene (L120.^
120.・4S]02), Petalite (Li20・Al
2O3・8S+02). LAS ceramics have low expansion and excellent thermal shock resistance, but their heat resistance and corrosion resistance are inferior to cordierite, which does not contain Ll and 0.
本発明ではシリア含有量の少ないβ−スボジュメン、ペ
タライト組成の結晶構造を主成分とする。また、本発明
の特徴としてハニカム部の開孔率が６５％以上であるこ
とがあげられる。これは、これまでセラミックス・ハニ
カムが高温部の熱交換用エレメントとして適用されなか
った理由として、セラミックスの脆さから厚肉化し開孔
率を大きく取れない点があった。また、薄肉化すると成
形時の亀裂や変形、焼成時の亀裂や欠けを生じやすく、
製品歩留りが低くコスト的に対応できない点があった。In the present invention, the main component is a crystal structure of β-subodumene and petalite composition with a low Syria content. Further, a feature of the present invention is that the porosity of the honeycomb portion is 65% or more. This is because ceramic honeycombs have not been used as heat exchange elements in high-temperature areas until now because the brittleness of ceramics makes them thicker and makes it difficult to maintain a large porosity. In addition, thinner walls are more likely to cause cracks and deformation during molding, and cracks and chips during firing.
The product yield was low and the cost could not be met.
これを改善するために、ガラス繊維が有効であるが、通
常のガラス繊維は熱衝撃率が５Ｘ１０−６／℃以上と高
く、焼成後の強度を低下させる欠点があった。To improve this, glass fibers are effective, but ordinary glass fibers have a high thermal shock rate of 5×10 −6 /° C. or more and have the disadvantage of lowering the strength after firing.
これに対して、本発明で使用するＳｉｎ、： ５０重量
％以上、＾１２０３： ２０重量％以上、ＭｇＯ：１０
重量％以上を主成分とし、かつ、熱衝撃率が３ｘｌＯ−
’／℃以下であるガラス繊維は、リシア系セラミックス
・ハニカムの焼成後の強度を低下させず、むしろ、向上
させる利点がある。これは、前記成分のものが熱膨張率
がリシア系に続いて小さいコージェライト組成であるた
めである。本発明では、ガラス繊維の添加量を１〜１５
重量％に限定した。これは、１重量％以下では、成形や
焼成時の欠陥を防止できず、１５重量％以上では押出成
形時の成形性が極単に悪くなるた酌である。On the other hand, Sin used in the present invention: 50% by weight or more, ^1203: 20% by weight or more, MgO: 10
% by weight or more as the main component, and has a thermal shock rate of 3xlO-
Glass fibers having a temperature of less than '/°C have the advantage that they do not reduce the strength of the lithium ceramic honeycomb after firing, but rather improve it. This is because the above-mentioned component has a cordierite composition with a coefficient of thermal expansion that is second to the lithia type. In the present invention, the amount of glass fiber added is 1 to 15
% by weight. This is because if the amount is less than 1% by weight, defects during molding or firing cannot be prevented, and if it is more than 15% by weight, the moldability during extrusion molding becomes extremely poor.
５ｉ０２： ７０〜８０重量％以上、Ａｌ２Ｏ３： ２
０〜２５重量％、Ｌｉ、Ｏ： ２〜３．５重量％はリシ
ア系セラミックスの基本組成である。この範囲内で、組
成調合したものは１３００℃の焼成でβスポジュメンも
しくはペタライトの結晶が成長し低熱膨張率となる。ま
た、前述したガラス繊維もコージェライトの結晶が成長
し、全体として低熱膨張率が保たれる。5i02: 70-80% by weight or more, Al2O3: 2
0 to 25% by weight, Li, O: 2 to 3.5% by weight are the basic compositions of lithium ceramics. If the composition is within this range, β-spodumene or petalite crystals will grow when fired at 1300°C, resulting in a low coefficient of thermal expansion. In addition, cordierite crystals grow in the glass fibers mentioned above, and a low coefficient of thermal expansion is maintained as a whole.
本発明体の成形は、押出成形が望ましい。押出成形は、
粉末に流動性をもたせるため、バインダ、溶剤等を加え
る。押出成形で使用するバインダとしてはメチル・セル
ロース、ポリビニール・アルコール等があげられる。こ
れに、潤滑材としてグリセリン、溶剤として水等を加え
るのが好ましい。本発明は押出成形時のバインダ等の組
成を限定するものではないた杓、配合については、後述
する実施例で述べるがその記載に限定されるものではな
い。押出成形でハニカムに成形したものは、乾燥して、
焼成し製品を得る。The body of the present invention is preferably formed by extrusion molding. Extrusion molding is
Binders, solvents, etc. are added to give the powder fluidity. Examples of binders used in extrusion molding include methyl cellulose and polyvinyl alcohol. It is preferable to add glycerin as a lubricant and water as a solvent to this. The present invention does not limit the composition of the binder and the like during extrusion molding.The composition and formulation will be described in the Examples described later, but the invention is not limited to the description thereof. The honeycomb formed by extrusion is dried,
A product is obtained by firing.
以下、本発明の好適な一実施例について詳細に説明する
。Hereinafter, a preferred embodiment of the present invention will be described in detail.
（ハニカム構造体の製造例）
平均粒径が２μｍ程度が、化学組成が５１０２＝７２．
６重量％、Ａ１２０ｓ−２１，３重量％、Ｌ１２０２．
６重量％、その他不純物としてＦｅＪ３＋ Ｔｉ０２−
１．２重量％、ＣａＯ＋ Ｍｇ０＝ ０．５重量％、Ｋ
２０十ＮａＪ＝１．６重量％になるようにベタラント粉
末、粘土等で調整したリシア系セラミックス原料粉末に
、ＳｉＯ□＝６５重量％、＾１２０３＝ ２５重量％、
ＭｇＯ＝ １０重量％の組成で融解・繊維化した市販ガ
ラス繊維を添加したものをセラミックス原料とした。こ
のセラミックス原料１００重量部に対し、メチルセルロ
ース８重量部、ポリビニルアルコール１重量部、グリセ
リン３重量部、水１５重量部をバインダとして加えて、
混練用ニーダで十分に混練して原料坏土とした。これを
１５０口Ｘ６ｍｍピッチ、壁厚１ｍｍのハニカム金型を
装着した押出成形機で成形後、１週間の恒温・恒湿条件
での乾燥を経て、１３００℃で焼成した。製造段階での
組立と製品歩留りとの関係を表１に示す。製品歩留りに
亀裂・割れは大きな影響を与えるが、特に横割れに対し
て大きな効果が得られた。横割れは押出し成形時の脈動
が主な原因になる。成形時の横割れは繊維を添加するこ
とで殆んどなくなる。成形工程で配合された繊維は、押
出方向に配向するためである。この他に、焼成時にも横
割れが発生する。(Manufacturing example of honeycomb structure) When the average particle size is about 2 μm, the chemical composition is 5102=72.
6% by weight, A120s-21, 3% by weight, L1202.
6% by weight, FeJ3+ Ti02− as other impurities
1.2% by weight, CaO + Mg0 = 0.5% by weight, K
SiO□=65 weight%, ^1203=25 weight%,
A ceramic raw material was prepared by adding commercially available glass fibers which had been melted and made into fibers with a composition of MgO = 10% by weight. To 100 parts by weight of this ceramic raw material, 8 parts by weight of methylcellulose, 1 part by weight of polyvinyl alcohol, 3 parts by weight of glycerin, and 15 parts by weight of water were added as a binder.
The mixture was sufficiently kneaded using a kneader for kneading to obtain a raw material clay. This was molded using an extruder equipped with a honeycomb mold of 150 holes x 6 mm pitch and 1 mm wall thickness, dried for one week under constant temperature and humidity conditions, and then fired at 1300°C. Table 1 shows the relationship between assembly at the manufacturing stage and product yield. Although cracks and cracks have a large effect on product yield, a particularly large effect was obtained on horizontal cracks. The main cause of horizontal cracking is pulsation during extrusion molding. Transverse cracks during molding are almost eliminated by adding fibers. This is because the fibers blended in the molding process are oriented in the extrusion direction. In addition, transverse cracks also occur during firing.
この発生には繊維の材質も影響する。The material of the fiber also affects this occurrence.
比較材として示した＾ｈｏ３・ＣａＯ−３１０２は通常
のガラス繊維であるこのものは熱膨張率が６×１０−６
／ｌとシリア系粉末より大きいため、繊維の周囲に応力
が発生し亀裂を生じやすくなる。^ho3・CaO-3102 shown as a comparative material is a normal glass fiber. This material has a thermal expansion coefficient of 6 x 10-6.
/l, which is larger than the Syrian powder, stress is generated around the fibers and cracks are likely to occur.
また、圧縮強度も歪の関係で繊維を添加しないものと比
較しても低下する傾向がある。これに対してＭｇＯ・Ｓ
１０．・へ］２０３繊維を配合したものは焼成後、コー
ジェライト結晶が生成するための熱膨張率の差が少なく
割れに対する効果は勿論、焼成後の強度も上る傾向があ
る。Moreover, the compressive strength also tends to be lower than that without adding fibers due to strain. On the other hand, MgO・S
10. 203 fibers have a small difference in coefficient of thermal expansion due to the formation of cordierite crystals after firing, and tend to not only be effective against cracking but also have higher strength after firing.
（ハニカム構造体の評価試験）
本発明で製造したハニカム構造体の評価試験結果を表２
に示す。本発明で製造したＮαｌ配合のものは、無添加
のものと比較して熱膨張率も変化しておらず優れた耐熱
衝撃性が維持されている。(Evaluation test of honeycomb structure) Table 2 shows the evaluation test results of the honeycomb structure manufactured according to the present invention.
Shown below. The Nαl-containing product manufactured in accordance with the present invention has no change in thermal expansion coefficient and maintains excellent thermal shock resistance compared to the product containing no additive.
また、市販のコージェライト系やムライト系と比較して
熱膨張率が小さく、より高温までの耐熱衝撃性をもつも
のである。In addition, it has a lower coefficient of thermal expansion than commercially available cordierite and mullite types, and has thermal shock resistance up to higher temperatures.
以上のように、本発明方法によれば、従来、ハニカム化
が困難であったリシア系セラミックスの歩留りを飛躍的
に向上させることができ、熱交換器や触媒担体として、
安価で有効な構造体を提供することができる。As described above, according to the method of the present invention, it is possible to dramatically improve the yield of lithium-based ceramics, which have conventionally been difficult to form into honeycombs, and can be used as heat exchangers and catalyst carriers.
An inexpensive and effective structure can be provided.
Claims (2)
タライトとなる焼成体に対して、熱膨張率が３×１０＾
−＾６／℃以下となるガラス繊維を１〜１５重量％含有
し、かつハニカム部の開孔率が６５％以上であることを
特徴とするリシア系セラミックス・ハニカム構造体。(1) For a fired body whose crystal structure after firing is β-spodumene or petalite, the coefficient of thermal expansion is 3 x 10^
A lithian ceramic honeycomb structure containing 1 to 15% by weight of glass fibers having a temperature of -^6/°C or less and having a porosity of 65% or more in the honeycomb portion.
：２０〜２５重量％、Ｌｉ＿２Ｏ：２．０〜３．５重量
％のセラミックス原料粉末１００重量部に対して、 ＳｉＯ＿２：５０重量％以上、Ａｌ＿２Ｏ＿３：２０重
量％以上、ＭｇＯ：１０重量％以上を主成分とし、かつ
、熱膨張率が３×１０＾−＾６／℃以下であるガラス繊
維を１〜１５重量部添加した後バインダ、溶剤等を加え
て混練後押出成形・乾燥・焼成することを特徴とするリ
シア系セラミックス・ハニカム構造体の製造方法。(2) SiO_2: 70-80% by weight, Al_2O_3
SiO_2: 50 wt% or more, Al_2O_3: 20 wt% or more, MgO: 10 wt% or more relative to 100 parts by weight of ceramic raw material powder containing: 20 to 25 wt%, Li_2O: 2.0 to 3.5 wt%. After adding 1 to 15 parts by weight of glass fiber, which is the main component and has a coefficient of thermal expansion of 3 x 10^-^6/℃ or less, a binder, a solvent, etc. are added, and the mixture is kneaded, followed by extrusion molding, drying, and baking. A method for manufacturing a lithian ceramic honeycomb structure characterized by:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2138598A JPH0437645A (en) | 1990-05-30 | 1990-05-30 | Lithia-based ceramics honeycomb structure and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2138598A JPH0437645A (en) | 1990-05-30 | 1990-05-30 | Lithia-based ceramics honeycomb structure and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0437645A true JPH0437645A (en) | 1992-02-07 |
Family
ID=15225836
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2138598A Pending JPH0437645A (en) | 1990-05-30 | 1990-05-30 | Lithia-based ceramics honeycomb structure and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0437645A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0669294A1 (en) * | 1994-02-28 | 1995-08-30 | Corning Incorporated | Extruded ceramic honeycomb and method |
| JP2003267776A (en) * | 2002-03-18 | 2003-09-25 | Iwao Jiki Kogyo Kk | Method for producing β-spodumene honeycomb-shaped heat storage body |
| JP2015174798A (en) * | 2014-03-14 | 2015-10-05 | 日本碍子株式会社 | Plugged honeycomb structure |
| JP2020196954A (en) * | 2018-02-28 | 2020-12-10 | Ｊｆｅスチール株式会社 | Grain-oriented electrical steel sheet having insulating film |
-
1990
- 1990-05-30 JP JP2138598A patent/JPH0437645A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0669294A1 (en) * | 1994-02-28 | 1995-08-30 | Corning Incorporated | Extruded ceramic honeycomb and method |
| JP2003267776A (en) * | 2002-03-18 | 2003-09-25 | Iwao Jiki Kogyo Kk | Method for producing β-spodumene honeycomb-shaped heat storage body |
| JP2015174798A (en) * | 2014-03-14 | 2015-10-05 | 日本碍子株式会社 | Plugged honeycomb structure |
| JP2020196954A (en) * | 2018-02-28 | 2020-12-10 | Ｊｆｅスチール株式会社 | Grain-oriented electrical steel sheet having insulating film |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPS60141667A (en) | Material for ceramic honeycomb structure | |
| US6566290B2 (en) | Lithium aluminosilicate ceramic | |
| EP0037868B1 (en) | Method of producing low-expansion ceramic materials | |
| EP0210813B1 (en) | Aluminum titanate.-mullite base ceramics | |
| US4001028A (en) | Method of preparing crack-free monolithic polycrystalline cordierite substrates | |
| EP1027304B1 (en) | Method for firing ceramic honeycomb bodies | |
| EP0133021A1 (en) | Aluminium titanate-mullite ceramics and production thereof | |
| US5403787A (en) | Extruded ceramic honeycomb and method | |
| JPH0260630B2 (en) | ||
| JPS602270B2 (en) | Cordierite ceramic honeycomb and its manufacturing method | |
| US6770111B2 (en) | Pollucite-based ceramic with low CTE | |
| US3951670A (en) | Cristobalite suppression in high-silica Li2 O-Al2 O-SiO2 devitrified glass frits | |
| US4451516A (en) | Low thermal expansion ceramic article | |
| JPH013067A (en) | Manufacturing method of cordierite honeycomb structure | |
| JPH0437645A (en) | Lithia-based ceramics honeycomb structure and its production | |
| JPS6041022B2 (en) | Manufacturing method for cordierite ceramics | |
| KR19980070463A (en) | Method for preparing beta-lithiapyrite body | |
| JPH0437028B2 (en) | ||
| CN120841944B (en) | An amorphous phase modified cordierite ceramic material and its preparation method | |
| JPH01179740A (en) | Glass-ceramic conjugate material | |
| JPH1192215A (en) | Cordierite-based ceramics sintered body, composition therefor and manufacturing method | |
| CN121270228A (en) | Eutectic modified cordierite ceramic material and preparation method thereof | |
| JPH0436114B2 (en) | ||
| JPH0149664B2 (en) | ||
| JPS61168563A (en) | Manufacture of cordierite ceramic honeycomb |