JPH0226846A - Production of crystallized glass - Google Patents
Production of crystallized glassInfo
- Publication number
- JPH0226846A JPH0226846A JP17600788A JP17600788A JPH0226846A JP H0226846 A JPH0226846 A JP H0226846A JP 17600788 A JP17600788 A JP 17600788A JP 17600788 A JP17600788 A JP 17600788A JP H0226846 A JPH0226846 A JP H0226846A
- Authority
- JP
- Japan
- Prior art keywords
- glass
- crystallized
- container
- powder
- vessel
- 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
- 239000011521 glass Substances 0.000 title claims abstract description 72
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 239000000843 powder Substances 0.000 claims abstract description 22
- 239000004020 conductor Substances 0.000 claims description 9
- 239000011800 void material Substances 0.000 claims description 3
- 239000006121 base glass Substances 0.000 claims 1
- 239000001506 calcium phosphate Substances 0.000 abstract description 13
- 229910000389 calcium phosphate Inorganic materials 0.000 abstract description 13
- 235000011010 calcium phosphates Nutrition 0.000 abstract description 13
- 238000010438 heat treatment Methods 0.000 abstract description 13
- QORWJWZARLRLPR-UHFFFAOYSA-H tricalcium bis(phosphate) Chemical compound [Ca+2].[Ca+2].[Ca+2].[O-]P([O-])([O-])=O.[O-]P([O-])([O-])=O QORWJWZARLRLPR-UHFFFAOYSA-H 0.000 abstract description 13
- 239000000203 mixture Substances 0.000 abstract description 8
- 239000000463 material Substances 0.000 abstract description 7
- 239000000919 ceramic Substances 0.000 abstract description 4
- 229910052751 metal Inorganic materials 0.000 abstract description 3
- 239000002184 metal Substances 0.000 abstract description 3
- 239000005548 dental material Substances 0.000 abstract description 2
- FUJCRWPEOMXPAD-UHFFFAOYSA-N Li2O Inorganic materials [Li+].[Li+].[O-2] FUJCRWPEOMXPAD-UHFFFAOYSA-N 0.000 abstract 1
- XUCJHNOBJLKZNU-UHFFFAOYSA-M dilithium;hydroxide Chemical compound [Li+].[Li+].[OH-] XUCJHNOBJLKZNU-UHFFFAOYSA-M 0.000 abstract 1
- 229910052737 gold Inorganic materials 0.000 abstract 1
- 229910052709 silver Inorganic materials 0.000 abstract 1
- 238000002425 crystallisation Methods 0.000 description 24
- 230000008025 crystallization Effects 0.000 description 24
- 238000000034 method Methods 0.000 description 13
- 238000009826 distribution Methods 0.000 description 10
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 9
- 239000011449 brick Substances 0.000 description 7
- 239000002245 particle Substances 0.000 description 6
- 239000000377 silicon dioxide Substances 0.000 description 6
- 229910010293 ceramic material Inorganic materials 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 239000007769 metal material Substances 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 238000009413 insulation Methods 0.000 description 3
- 239000010453 quartz Substances 0.000 description 3
- 238000005452 bending Methods 0.000 description 2
- 210000000988 bone and bone Anatomy 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000004031 devitrification Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000000956 alloy Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 239000012620 biological material Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- -1 etc. Substances 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 239000002241 glass-ceramic Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 229910052741 iridium Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000013081 microcrystal Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 230000000877 morphologic effect Effects 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 229910052697 platinum Inorganic materials 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 229910052703 rhodium Inorganic materials 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 210000000332 tooth crown Anatomy 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Landscapes
- Re-Forming, After-Treatment, Cutting And Transporting Of Glass Products (AREA)
- Glass Compositions (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は結晶化ガラスを製造する際の母ガラスの結晶化
の方法に関し、特に高強度の歯科材料あるいは人工骨等
の生体材料に最適の結晶化ガラスの製造方法に関するも
のである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a method of crystallizing mother glass when producing crystallized glass, and particularly relates to a method of crystallizing a mother glass when producing crystallized glass, and is particularly suitable for high-strength dental materials or biomaterials such as artificial bones. The present invention relates to a method for producing crystallized glass.
結晶化ガラスは所定の組成のガラス体を再加熱し、該ガ
ラス内に多数の微結晶を均一に析出成長させることによ
って得られる。結晶化ガラスの製造過程においては、こ
の結晶化のための加熱方法が特に重要とされており、炉
内の温度分布が均一な結晶化炉を精密に制御することが
要求される。Crystallized glass is obtained by reheating a glass body of a predetermined composition to uniformly precipitate and grow a large number of microcrystals within the glass. In the manufacturing process of crystallized glass, the heating method for crystallization is particularly important, and it is required to precisely control a crystallization furnace with a uniform temperature distribution within the furnace.
均一な結晶を得ることは結晶体の強度向上と形態歪の低
減に寄与するものである。しかしながら、炉内の温度分
布を均一に保つことは非常に困難である。そこでこの難
点を解消するためガラス体の内部で温度差が生じないよ
う非常に緩やかな昇温速度で加熱する方法が採られてい
る。Obtaining uniform crystals contributes to improving the strength of the crystal and reducing morphological distortion. However, it is very difficult to maintain a uniform temperature distribution within the furnace. In order to solve this problem, a method has been adopted in which the glass body is heated at a very slow temperature increase rate so that no temperature difference occurs inside the glass body.
また、一般にガラス体より結晶体の方が比重が大きいの
で、結晶化の際には体積収縮が起きる。Further, since a crystalline body generally has a higher specific gravity than a glass body, volumetric contraction occurs during crystallization.
この体積収縮を考慮してあらかじめガラス体を大きくし
て結晶化させるが、この際も温度分布が生じると均一に
収縮せず結晶歪が生じたり、内部にボアなどの欠陥が生
ずる。これを防ぐため耐火物のサヤ中で結晶化して、熱
の伝わり方を緩和する方法も行われている。Taking this volumetric shrinkage into consideration, the glass body is enlarged in advance and crystallized, but if a temperature distribution occurs at this time as well, it will not shrink uniformly and crystal distortion will occur, and defects such as bores will occur inside. In order to prevent this, a method is being used to reduce the heat transfer by crystallizing the refractory in a sheath.
上記のように温度分布軽減のため種々の方法が採られて
いるが、リン酸カルシウム系結晶化ガラスなどのように
ガラスの表面から内部に向がって結晶化が進行する、い
わゆる表面失透型の結晶化機構による結晶化ガラスは特
に温度分布に敏感であり、小形状のものならば時間を掛
けてゆっ(りと加熱することによりはソ゛均一な結晶化
物を得ることはできるが、形状の大きなガラス体や複数
のガラス体を一度に結晶化する場合などは、通常の方法
では均一な結晶化を実現することはほとんど不可能であ
る。また、ガラスを耐火物のサヤに入れて結晶化する方
法でも、耐火物は一般に低熱伝導率であり熱の伝わり方
を緩和することはできても均一な温度分布を実現できる
ものではない。As mentioned above, various methods have been adopted to reduce temperature distribution, but there are so-called surface devitrification types, in which crystallization progresses from the surface of the glass toward the inside, such as calcium phosphate crystallized glass. Crystallized glass produced by the crystallization mechanism is particularly sensitive to temperature distribution, and if it is small in shape, it is possible to obtain a very uniform crystallized product by slowly heating it over time, but if it is in a large shape, a very uniform crystallized product can be obtained. When crystallizing a glass body or multiple glass bodies at once, it is almost impossible to achieve uniform crystallization using normal methods.Also, crystallization is performed by placing the glass in a refractory pod. Even with this method, refractories generally have low thermal conductivity, and although it is possible to moderate the way heat is transmitted, it is not possible to achieve a uniform temperature distribution.
このようにガラス体を加熱結晶化する際に均一な結晶化
を実現するためには均一な温度分布を実現する必要があ
る。In order to achieve uniform crystallization when heating and crystallizing a glass body in this way, it is necessary to achieve a uniform temperature distribution.
一般に結晶化に用いられる加熱炉では、ガラス体への伝
熱は輻射と対流によるものであるから、ガラス体各部と
発熱体との距離やガラス体の各部が発熱体に直接面して
いるか否かにより必然的にガラス体内部に温度分布を生
ずることになる。In heating furnaces generally used for crystallization, heat transfer to the glass body is based on radiation and convection, so the distance between each part of the glass body and the heating element and whether each part of the glass body directly faces the heating element are important. This inevitably results in a temperature distribution inside the glass body.
従って、加熱を伝導伝熱により行えばよいことになる。Therefore, heating may be performed by conduction heat transfer.
これを実現するため本発明はガラスを結晶化させるに際
して、母ガラスを高熱伝導性材料よりなる容器内に入れ
るか、容器内の空隙を高熱伝導性粉末で充填するか、あ
るいは両者を併用して結晶化させることを特徴とするも
のである。In order to achieve this, the present invention, when crystallizing glass, either places the mother glass in a container made of a highly thermally conductive material, fills the void inside the container with highly thermally conductive powder, or uses a combination of both. It is characterized by crystallization.
本発明に用いられる高熱伝導性の材料あるいは粉末とは
金属、セラミックスあるいは両者の複合であり、容器あ
るいは粉体の熱伝導率は20 W/m・K以上であるこ
とが必要で、それ以下では表面失透型において均一な結
晶体ができない。金属としてはAut ag、 Cu、
Alt Ir、 Mo、 W、 Cr、 Ni、 F
e、 Pd。The highly thermally conductive material or powder used in the present invention is metal, ceramics, or a combination of both, and the thermal conductivity of the container or powder must be 20 W/m・K or higher; Uniform crystals cannot be formed in the surface devitrification type. Metals include Aut ag, Cu,
Alt Ir, Mo, W, Cr, Ni, F
e, Pd.
Pt、 Rh、 Siなど、あるいはこれらを主体とす
る合金が通し、セラミックスではSiC+ Bed、
Al2O3lMgOおよびこれらを主体とするセラミッ
クス混合物が適している。金属材料の場合は高温での酸
化・腐食を防ぐため、メツキ、蒸着、溶射などの方法に
より表面コーティングを施すことも可能である。高温で
の酸化・腐食防止の点からはセラミックス材料は好まし
い材料である。また、SiC質などのセラミックス材料
の気孔部分にSiなどの金属材料を注入したり、金属材
料中にセラミックス材料を分散したもの、金属材料とセ
ラミックス材料との混合物などの複合材料も好適である
。Pt, Rh, Si, etc. or alloys mainly composed of these pass through, and ceramics include SiC+ Bed,
Suitable materials are Al2O31MgO and ceramic mixtures based on these. In the case of metal materials, it is also possible to apply a surface coating using methods such as plating, vapor deposition, and thermal spraying to prevent oxidation and corrosion at high temperatures. Ceramic materials are preferred from the viewpoint of preventing oxidation and corrosion at high temperatures. Also suitable are composite materials such as those in which a metal material such as Si is injected into the pores of a ceramic material such as SiC, a ceramic material dispersed in a metal material, and a mixture of a metal material and a ceramic material.
高熱伝導性材料の容器は、通常の箱状でもよいが、本発
明の目的とする伝導伝熱の効果を高めるという上からは
、被加熱物の形状に合わせた容器壁とガラス体ができる
だけ近接するような、例えばブロック体に穿孔した形状
の容器が好ましい。The container made of highly thermally conductive material may be in the shape of an ordinary box, but in order to enhance the effect of conductive heat transfer, which is the objective of the present invention, the container wall and glass body that match the shape of the object to be heated should be placed as close as possible. It is preferable to use a container in the form of, for example, a block with perforations.
均熱性を高める上からは、容器は肉厚、緻密であるほど
好ましいが、溶融体でも焼結体でも構わない。また、高
熱伝導性粉末を充填する場合は粉末の他、塊状、繊維状
などの形態あるいはこれらの混合物でもよいが、できる
だけ高密度に充填する方が効率的で、粒度配合した粉末
材料を用いるなどの方法がよい。From the viewpoint of improving heat uniformity, it is preferable that the container be thicker and denser, but it may be a molten body or a sintered body. In addition, when filling high thermal conductive powder, it may be in the form of lumps, fibers, etc., or a mixture of these in addition to powder, but it is more efficient to fill it as densely as possible, such as using a powder material with a blended particle size. The method is better.
本発明では、高熱伝導性材料の容器のみを用いて、ガラ
ス体との間の空隙はそのま\とするが、任意の粉体など
を充填してもよい。あるいは、容器は任意の材料のもの
とし、その空隙を高熱伝導性粉体で充填することも可能
である。しかし、高熱伝導性材料の容器を用いて、ガラ
ス体との間の空隙には高熱伝導性粉体を高密度充填する
のが最も好ましい方法である。In the present invention, only a container made of a highly thermally conductive material is used, and the gap between the container and the glass body is left as is, but it may be filled with any powder or the like. Alternatively, the container can be made of any material and the voids filled with highly thermally conductive powder. However, the most preferable method is to use a container made of a highly thermally conductive material and fill the gap between the container and the glass body with highly thermally conductive powder at a high density.
さらに、本発明の方法では、−個のガラス体を結晶化さ
せて効果のあることは当然であるが、複数個のガラス体
を同時に結晶化する際に効果的である。その場合には容
器内に充填した粉末中に複数個のガラス体を埋め込むか
、ブロック体中に複数個の穿孔をしてもよい。特に、複
数個のガラス体を一度に結晶化すると同様の結晶化状態
となるため、強度などの特性の揃ったものが得られると
いう利点がある。Furthermore, the method of the present invention is naturally effective when - number of glass bodies are crystallized, but it is also effective when a plurality of glass bodies are crystallized simultaneously. In that case, a plurality of glass bodies may be embedded in the powder filled in the container, or a plurality of holes may be made in the block body. In particular, when a plurality of glass bodies are crystallized at the same time, they are in the same crystallized state, so there is an advantage that glass bodies with uniform properties such as strength can be obtained.
本発明のガラスを結晶化させるに際して母ガラスを高熱
伝導性材料よりなる容器中に入れるか、容器内の空隙を
高熱伝導性粉末で充填するかあるいは両者を併用して結
晶化させる方法によると、ガラス体への伝熱が均一とな
ることから、温度分布が無くなり、理想的な均一な結晶
化が実現可能である。特に、温度分布に敏感な表面失透
型結晶化ガラス、その中でも人工歯冠や人工骨材料とし
て用いられるリン酸カルシウム系結晶化ガラスの結晶化
においてその特徴が発揮される。According to the method of crystallizing the glass of the present invention, the mother glass is placed in a container made of a highly thermally conductive material, or the void in the container is filled with a highly thermally conductive powder, or a combination of both is used for crystallization. Since heat transfer to the glass body becomes uniform, there is no temperature distribution, and ideal uniform crystallization can be achieved. In particular, its characteristics are exhibited in the crystallization of surface-devitrified glass-ceramics, which are sensitive to temperature distribution, and among them, calcium phosphate-based crystallized glass, which is used as artificial tooth crowns and artificial bone materials.
また、従来困難であった複数個のガラス体を一度に同様
の結晶化状態となるよう結晶化することが可能である。Furthermore, it is possible to crystallize a plurality of glass bodies at the same time so that they are in the same crystallized state, which has been difficult in the past.
さらに、高熱伝導性材料を用いることにより、従来のよ
うに結晶化に際し時間をかけて非常にゆっくり昇温する
必要はなく、急速昇温も可能で、結晶化操作に要する時
間が大幅に短縮される。Furthermore, by using a highly thermally conductive material, there is no need to raise the temperature very slowly over a long period of time during crystallization, as is the case with conventional methods, and rapid temperature rise is also possible, significantly shortening the time required for the crystallization operation. Ru.
実施例 l
SiC質の容器内に粒度149μm以下のSiC粉末を
充填し、その中に4.3L i 20 ・38.5Ca
O・9.I Al2O3・48.IP 20 e ナ
ル組成ノリン酸カルシウム系ガラス成形体を5個埋め込
み、昇温速度300℃/hrで昇温し、550〜650
℃で10 hr加熱、結晶化してリン酸カルシウム系結
晶化ガラスを得た。得られた結晶化ガラスは容器内の位
置によらず5個とも同様の均一な結晶化状態を示し、そ
の曲げ強さも1820〜1980kg/cm2と高く、
そのばらつきも小さかった。Example 1 A SiC container is filled with SiC powder with a particle size of 149 μm or less, and 4.3 L i 20 ・38.5 Ca
O・9. I Al2O3・48. IP 20 e Null composition: 5 pieces of calcium phosphate glass molded bodies were embedded, and the temperature was raised at a heating rate of 300°C/hr to 550-650°C.
The mixture was heated and crystallized at ℃ for 10 hours to obtain calcium phosphate crystallized glass. All five of the obtained crystallized glasses showed the same uniform crystallization state regardless of their position in the container, and their bending strength was as high as 1820 to 1980 kg/cm2.
The variation was also small.
実施例 2
大略寸法90 x 65 x 30mmの銅ブロックに
直径25mm、深さ25mmの孔を5個穿孔し、この孔
にそれぞれ充填した粒度149μm以下のSiC粉末中
に実施例1と同様のリン酸カルシウム系ガラス成形体を
埋め込み、同品質の銅板(厚さ5 mm)で蓋をして、
実施例1と同一条件で加熱、結晶化してリン酸カルシウ
ム系結晶化ガラスを得た。この場合も得られた結晶化ガ
ラスは容器内の位置によらず5個とも同様の均一な結晶
化状態を示し、その曲げ強さも1890〜1990kg
/c−であった。Example 2 Five holes with a diameter of 25 mm and a depth of 25 mm were bored in a copper block with approximate dimensions of 90 x 65 x 30 mm, and the same calcium phosphate system as in Example 1 was filled in each hole with SiC powder having a particle size of 149 μm or less. Embed the glass molding and cover with a copper plate (5 mm thick) of the same quality.
It was heated and crystallized under the same conditions as in Example 1 to obtain a calcium phosphate crystallized glass. In this case as well, all five crystallized glasses obtained showed the same uniform crystallization state regardless of their position in the container, and their bending strength was 1890 to 1990 kg.
/c-.
実施例 3
SiC質の容器内に粒度149μm以下の石英粉末を充
填したもの、およびアルミナシリカ質の耐火れんが容器
に粒度149μm以下のSiC粉末を充填したものを用
いてそれぞれ実施例1と同様にリン酸カルシウム系結晶
化ガラスを得た。得られた結晶化ガラスは容器内の位置
によらずいずれもはソ゛同様な結晶化状態を示した。そ
の強度の測定値はSiC質の容器のもので1610〜1
790kg/cm2、アルミナシリカ質の容器で124
0〜1560kg/c−と高く、そのばらつきも比較的
小さかったが、実施例1には及ばなかった。Example 3 Calcium phosphate was prepared in the same manner as in Example 1 using a SiC container filled with quartz powder with a particle size of 149 μm or less and an alumina-silica refractory brick container filled with SiC powder with a particle size of 149 μm or less. A system crystallized glass was obtained. The obtained crystallized glass exhibited a similar crystallization state regardless of its position in the container. The measured value of the strength is 1610~1 for a SiC container.
790kg/cm2, 124 in alumina-silica container
Although it was high at 0 to 1560 kg/c- and the variation was relatively small, it was not as good as Example 1.
比較例 1
アルミナシリカ質の耐火断熱れんが板の上に実施例1と
同じリン酸カルシウム系ガラス成形体5個を置き、昇温
速度を60℃/hrと非常にゆっくりとした以外は実施
例と同一条件で加熱、結晶化してリン酸カルシウム系結
晶化ガラスを得た。得られた結晶化ガラスは耐火断熱れ
んが板上のセット位置により5個それぞれ異なる結晶化
状態を示すと共に、各々の結晶化ガラス自体においても
発熱体に曝される距離も近い上部と下部のれんかに接触
した部分とで異なる結晶化状態を示した。強度も560
〜980 kg/cWI2と、セット位置によりばらつ
きが大きく、個々も部位による結晶化の差により強度も
小さかった。Comparative Example 1 Five pieces of the same calcium phosphate glass moldings as in Example 1 were placed on an alumina-silica fireproof insulation brick board, and the conditions were the same as in Example except that the heating rate was very slow at 60°C/hr. The mixture was heated and crystallized to obtain calcium phosphate crystallized glass. The five crystallized glasses obtained show different crystallization states depending on their set position on the fireproof insulation brick board, and each crystallized glass itself has different crystallization states between the upper and lower bricks, which are exposed to the heating element at a closer distance. The crystallization state differed depending on the contact area. Strength is also 560
~980 kg/cWI2, which varied greatly depending on the setting position, and the strength was also small due to differences in crystallization depending on the individual site.
比較例 2
アルミナシリカ質の耐火れんが容器内に粒度149μm
12L下の石英粉末を充填してリン酸カルシウム系ガラ
ス5個を埋め込み、昇温速度を60℃/hrとした以外
は実施例1と同様に加熱、結晶化してリン酸カルシウム
系結晶化ガラスを得た。得られた結晶化ガラスのそれぞ
れの結晶化ガラス内部での結晶化状態の差は少なかった
もの\、5個の結晶化ガラス間では容器内のセット位置
により結晶化状態に差が見られ、それに対応して強度も
770〜1030kg/cyI2となった。Comparative Example 2 Particle size 149 μm in alumina-silica refractory brick container
A calcium phosphate crystallized glass was obtained by heating and crystallizing in the same manner as in Example 1, except that 12 L of quartz powder was filled and five pieces of calcium phosphate glass were embedded, and the heating rate was 60° C./hr. Although there was little difference in the crystallization state within each of the obtained crystallized glasses, there were differences in the crystallization state among the five crystallized glasses depending on the set position in the container, and Correspondingly, the strength was also 770 to 1030 kg/cyI2.
なお、用いた材料の熱伝導率は―/m・K単位でSiC
容器は120、アルミナシリカ質耐火れんが容器で2.
5、アルミナシリカ質耐火断熱れんが板で0.3、銅ブ
ロックは350であり、粉末はいずれも充填状態でSi
Cは約50、石英的0.1であった。The thermal conductivity of the material used is -/m・K in units of SiC
The container is 120, an alumina-silica refractory brick container and 2.
5. The alumina-silica fireproof insulation brick board has a rating of 0.3, the copper block has a rating of 350, and both powders are filled with Si.
C was about 50, 0.1 like quartz.
Claims (3)
導率が20W/m・K以上の高熱伝導性材料よりなる容
器内で結晶化させることを特徴とする結晶化ガラスの製
造方法。(1) A method for producing crystallized glass, which comprises crystallizing the mother glass in a container made of a highly thermally conductive material having a thermal conductivity of 20 W/m·K or more.
を熱伝導率が20W/m・K以上の高熱伝導性粉末で充
填して結晶化させることを特徴とする結晶化ガラスの製
造方法。(2) A method for producing crystallized glass, which comprises filling the periphery of the base glass with highly thermally conductive powder having a thermal conductivity of 20 W/m·K or more and crystallizing the glass.
導率が20W/m・K以上の高熱伝導性材料よりなる容
器内に入れ、容器内の空隙を熱伝導率が20W/m・K
以上の高熱伝導性粉末で充填して結晶化させることを特
徴とする結晶化ガラスの製造方法。(3) When crystallizing glass, place the mother glass in a container made of a highly thermally conductive material with a thermal conductivity of 20 W/m・K or more, and fill the void inside the container with a thermal conductivity of 20 W/m・K.
A method for producing crystallized glass, characterized by filling the powder with the above highly thermally conductive powder and crystallizing it.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63176007A JP2810996B2 (en) | 1988-07-13 | 1988-07-13 | Method for producing crystallized glass |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63176007A JP2810996B2 (en) | 1988-07-13 | 1988-07-13 | Method for producing crystallized glass |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0226846A true JPH0226846A (en) | 1990-01-29 |
| JP2810996B2 JP2810996B2 (en) | 1998-10-15 |
Family
ID=16006087
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63176007A Expired - Fee Related JP2810996B2 (en) | 1988-07-13 | 1988-07-13 | Method for producing crystallized glass |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2810996B2 (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS48100406A (en) * | 1972-04-01 | 1973-12-18 | ||
| JPS5032216A (en) * | 1973-07-21 | 1975-03-28 |
-
1988
- 1988-07-13 JP JP63176007A patent/JP2810996B2/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS48100406A (en) * | 1972-04-01 | 1973-12-18 | ||
| JPS5032216A (en) * | 1973-07-21 | 1975-03-28 |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2810996B2 (en) | 1998-10-15 |
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