JP3727746B2 - β-alumina electroformed refractory - Google Patents
β-alumina electroformed refractory Download PDFInfo
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- JP3727746B2 JP3727746B2 JP03697197A JP3697197A JP3727746B2 JP 3727746 B2 JP3727746 B2 JP 3727746B2 JP 03697197 A JP03697197 A JP 03697197A JP 3697197 A JP3697197 A JP 3697197A JP 3727746 B2 JP3727746 B2 JP 3727746B2
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- 229910000873 Beta-alumina solid electrolyte Inorganic materials 0.000 title claims description 33
- 239000013078 crystal Substances 0.000 claims description 15
- 229910052760 oxygen Inorganic materials 0.000 claims description 13
- 229910052593 corundum Inorganic materials 0.000 claims description 12
- 239000010431 corundum Substances 0.000 claims description 12
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 7
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 6
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 5
- 239000003513 alkali Substances 0.000 description 16
- 239000011521 glass Substances 0.000 description 11
- 238000002485 combustion reaction Methods 0.000 description 9
- 238000002844 melting Methods 0.000 description 9
- 230000008018 melting Effects 0.000 description 9
- 239000000203 mixture Substances 0.000 description 9
- 239000011819 refractory material Substances 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 230000003628 erosive effect Effects 0.000 description 8
- 230000000694 effects Effects 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 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000004040 coloring Methods 0.000 description 1
- 238000009841 combustion method Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000010813 internal standard method Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000006060 molten glass Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000011241 protective layer Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 229910052596 spinel Inorganic materials 0.000 description 1
- 239000011029 spinel Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
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Description
【０００１】
【発明の属する技術分野】
本発明は、βアルミナ質電鋳耐火物に関し、特に酸素燃焼によるガラス溶解炉の天井部分に使用するのに適したβアルミナ質電鋳耐火物に関する。
【０００２】
【従来の技術】
ガラス溶解炉に使用されている高アルミナ質電鋳耐火物としては、コランダム質、コランダム−βアルミナ質、βアルミナ質の各種耐火物がある。このうち、βアルミナ質電鋳耐火物は、大部分のＡｌ２Ｏ３と、Ｎａ２ＯあるいはＫ２Ｏと、僅かなＳｉＯ２よりなり、発達したβアルミナの結晶と少量のマトリックスガラスで構成されている。このため、アルカリ蒸気に対して不活性であり、電鋳耐火物の中で最大の熱衝撃抵抗を持っている。これらの特性から、βアルミナ質電鋳耐火物はガラス溶解炉の上部構造に多く使用されている。
【０００３】
【発明が解決しようとする課題】
ガラス溶解炉の上部構造は、天井部分、側壁部分、その他の部分に大きく分けられる。天井部分は、いくつかのブロックを組み合わせてアーチ状に形成して使用されることが多い。アーチの幅が３〜４ｍと小さければ、ブロックに働く荷重は小さい。しかし、アーチの幅が７〜８ｍの大きさになると、ブロックに働く荷重も非常に大きくなる。最近では炉が大型化して、アーチの幅が１０ｍを越えるものもある。ここに使用される耐火物はこの荷重に耐えるだけの大きな圧縮強度が必要である。
【０００４】
しかし、従来のβアルミナ質電鋳耐火物は、大部分が発達したβアルミナ結晶で構成されているため、圧縮強度が３０ＭＰａ程度にすぎず、幅の広い天井部分に使用するには強度が不足していた。
【０００５】
例えば、幅が６ｍ程度の天井部分に使用するには、耐火物の機械的強度は、５０ＭＰａ以上の圧縮強度が必要とされている。幅が１０ｍを越える場合は、耐火物の機械的強度は７０ＭＰａ以上が必要である。
【０００６】
また、最近では、ガラスを溶解する燃焼方法が空気燃焼から酸素燃焼に変わりつつある。酸素燃焼では、燃焼に際して酸素を使用するので、燃焼に必要な気体の量が非常に少なくなる。その結果、炉内の雰囲気、特に溶解室の雰囲気が、空気燃焼の場合と大きく異なる。すなわち、酸素燃焼では、炉内雰囲気は溶解ガラスから揮発するアルカリ濃度が極めて高い。アルカリ濃度の高い雰囲気では、これまで以上にアルカリ雰囲気に強い耐火物が必要となる。
【０００７】
本発明の目的は、圧縮強度が大きく、アルカリによって侵食されにくいβアルミナ質電鋳耐火物を提供することである。
【０００８】
【課題を解決するための手段】
本発明は、請求項１〜３のいずれか１項に記載のβアルミナ質電鋳耐火物、たとえば、重量割合で、Ａｌ ２ Ｏ ３ が８５〜９５％であり、Ｎａ ２ ＯとＫ ２ Ｏの合計が５．０〜７．０％であり、ＭｇＯが０．４〜１．５％であり、ＣａＯとＳｒＯとＢａＯの合計が０．４〜２．０％であり、ＳｉＯ ２ が０．５％以下であり、Ｆｅ ２ Ｏ ３ とＴｉＯ ２ の合計が０．１％以下であり、βアルミナであって、かつ発達していない結晶が互いに交錯した組織であることを特徴とするβアルミナ質電鋳耐火物を要旨としている。
【０００９】
【発明の実施の形態】
本発明のβアルミナ質電鋳耐火物の組成について説明する。
【００１０】
Ｎａ２ＯとＫ２Ｏの合計は４．０〜７．５％、好ましくは５．０〜７．０％である。これらの組成は、Ａｌ２Ｏ３と反応してβアルミナ結晶を生成する。Ｎａ２ＯとＫ２Ｏの合計が４．０％未満であると、コランダムが多量に存在し、アルカリ濃度の高い雰囲気では、コランダムがβアルミナに変化して組織が崩壊する。他方、７．５％を越えると、余分なＮａ２ＯやＫ２Ｏが結晶の間に存在して、湿気や水分によって容易に溶け出して組織が脆くなる。なお、Ｎａ２Ｏ又はＫ２Ｏがゼロのこともありうる。
【００１１】
ＣａＯ，ＳｒＯ，ＢａＯは結晶を過度に成長させない作用がある。これらにＭｇＯを添加すると、βアルミナ結晶同志を互いに交錯させ、組織を強固にする働きがある。すなわち、ＣａＯ，ＳｒＯ，ＢａＯなどと共にＭｇＯを添加することによって、βアルミナであって、かつ、発達していない結晶が互いに交錯した組織が得られる。
【００１２】
図１は、本発明のβアルミナ質電鋳耐火物の結晶構造の一例を示す模式図である。図２は従来のβアルミナ質電鋳耐火物の結晶構造を示す模式図である。従来のものに比較して、本発明のβアルミナ質電鋳耐火物は、結晶が小さくて、より正方形に近い形状である。ＭｇＯは０．２〜２．０％、好ましくは０．４〜１．５％であり、ＣａＯとＳｒＯとＢａＯの合計は０．２〜３．０％、好ましくは０．４〜２．０％である。これよりも少ないと、前述の効果が不十分であり、多すぎると、Ａｌ２Ｏ３とのスピネルが生成して、アルカリによる侵食を受けて、クリープ変形が大きくなる。なお、ＣａＯ，ＳｒＯ，ＢａＯのいずれかがゼロのこともありうる。
【００１３】
ＳｉＯ２はガラス相を形成する組成である。これが多すぎると、クリープ変形が大きくなるので、０．５％以下が好ましい。
【００１４】
Ｆｅ２Ｏ３とＴｉＯ２は合計で０．１％以下が好ましい。これらの両組成は低融点ガラスを形成する。低融点ガラスは耐熱性を損なうので好ましくない。この他に、これらの両組成は製品を着色する作用がある。
【００１５】
コランダム量は５％以下が好ましい。アルカリ濃度の低い雰囲気に晒されると、βアルミナはコランダムに変化して、これが保護層となって侵食を防ぐ。しかし、アルカリ濃度が高い場合、コランダムがβアルミナに変化する。この変化が起こると急激に体積が膨張してクリープ変形が起きる。コランダム量が５％を越えるとクリープ変形が大きくなる。
【００１６】
本発明によれば、重量割合で、Ａｌ２Ｏ３が８５〜９５％であり、Ｎａ２ＯとＫ２Ｏの合計が５．０〜７．０％であり、ＭｇＯが０．４〜１．５％であり、ＣａＯとＳｒＯとＢａＯの合計が０．４〜２．０％であり、ＳｉＯ２が０．５％以下であり、Ｆｅ２Ｏ３とＴｉＯ２の合計が０．１％以下である構成により、比重を大きく変化させることなく、十分な圧縮強度をもち、かつアルカリ濃度の高い雰囲気に晒されても、クリープ変形が小さく、高い耐食性をもつ極めて優れたβアルミナ質電鋳耐火物が得られる。また、マトリックスガラスを数％以下と少なくでき、１８００℃以下の温度であれば、圧縮強度が大きく低下することはない。
【００１７】
【実施例】
【００１８】
本発明の実施例を説明する。
表１に示す所定の組成割合に配合した原料を、アーク炉を用いて溶解し、溶解物を内寸法２３０×２３０×２３０ｍｍのカーボン製鋳型に流し込んで成形した。成形物はアルミナ粉末の中で徐冷した。得られた製品に外観の欠陥はなかった。これらの製品について、種々の特性を測定した。その結果を同じく表１に示す。
【００１９】
【表１】
【００２０】
圧縮強度は、製品の底コーナー部から５０ｍｍの位置で、かつ側面から５０ｍｍの位置から一辺が２５ｍｍの立方体を切り出して試料とし、加圧速度を毎秒１０〜１５ｋｇ／ｃｍ２として測定した。
【００２１】
コランダムの量は、圧縮強度測定後の試料を用いて、Ｘ線を使った内部標準法により定量した。
【００２２】
アルカリ蒸気による侵食試験は次のように行った。
【００２３】
内径８０ｍｍのルツボに、重量割合で、ＳｉＯ２が５４％、ＢａＯが１１％、Ｎａ２Ｏが１５％、Ｋ２Ｏが１３％の侵食剤を入れて、上部を径９０ｍｍ、厚さ２０ｍｍの試料で密封し、電気炉にて１５８０℃で９６時間保持した。その後、試料の中央部分の厚みを測定し、厚みの減量を２４時間当りに換算してアルカリ侵食率として示す。
【００２４】
クリープ特性は、アルカリ蒸気による侵食試験後の試料において、試料の中央部分が軟化変形して膨らんだ膨らみを測定してクリープ変形として示す。
【００２５】
亀裂の数は、アルカリ蒸気による侵食試験後の試料において、この試料を二等分に切断し、その切断面に現われた亀裂を数えた。
【００２６】
本発明の実施例は、一部請求項１の数値範囲外のものもあるが、いずれも、圧縮強度が５０ＭＰａ以上であり、特に、実施例５〜８は、圧縮強度が７０ＭＰａを越えている。また、コランダムの量は５％を越えることはなかった。
【００２７】
比較例１〜７
組成割合が異なる他は前述の実施例と同様に製品を製造し、同様の試験及び測定を行った。その組成割合および結果を表２に示す。
【００２８】
【表２】
【００２９】
比較例２は、ＣａＯとＳｒＯとＢａＯが含まれていない例である。圧縮強度が小さくて、侵食率が大きい。
【００３０】
比較例３は、Ｆｅ２Ｏ３とＴｉＯ２の合計が多い例である。クリープ変形が大きい。
【００３１】
比較例４は、ＳｉＯ２が多い例である。クリープ変形が大きい。
【００３２】
比較例５は、ＭｇＯが含まれていない例である。圧縮強度が低く。クリープ変形が大きい。
【００３３】
比較例６は、Ｎａ２ＯとＫ２Ｏの合計が多い例である。圧縮強度が極めて低く、クリープ変形が大きい。
【００３４】
比較例７は、ＣａＯとＳｒＯとＢａＯの合計が多い例である。侵食率およびクリープ変形が大きい。
【００３５】
【発明の効果】
本発明のβアルミナ質電鋳耐火物は、圧縮強度を５０ＭＰａ以上にするのが容易であり、アルカリ濃度が高い雰囲気に晒されてもクリープが小さく、かつアルカリ蒸気による侵食も少ない。従って、本発明のβアルミナ質電鋳耐火物は、アルカリ濃度が高い雰囲気に晒される、大きな荷重が掛かる部分、例えば酸素燃焼によるガラス溶解炉の天井部分、および生バッチの飛散する部分にも使用可能である。
【図面の簡単な説明】
【図１】 本発明のβアルミナ質電鋳耐火物の結晶構造の一例を示す模式図。
【図２】 従来のβアルミナ質電鋳耐火物の結晶構造を示す模式図。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a β-alumina electrocast refractory, and more particularly to a β-alumina electrocast refractory suitable for use in a ceiling portion of a glass melting furnace by oxygen combustion.
[0002]
[Prior art]
High alumina electrocast refractories used in glass melting furnaces include corundum, corundum-β alumina, and β alumina refractories. Of these, β-alumina electrocast refractories consist of most Al 2 O 3 , Na 2 O or K 2 O, and a small amount of SiO 2 , and consist of developed β-alumina crystals and a small amount of matrix glass. Has been. For this reason, it is inactive against alkali vapor and has the highest thermal shock resistance among electrocast refractories. Because of these characteristics, β-alumina electrocast refractories are often used in the superstructure of glass melting furnaces.
[0003]
[Problems to be solved by the invention]
The upper structure of the glass melting furnace is roughly divided into a ceiling part, a side wall part, and other parts. The ceiling part is often used by combining several blocks to form an arch shape. If the width of the arch is as small as 3 to 4 m, the load acting on the block is small. However, when the width of the arch becomes 7 to 8 m, the load acting on the block becomes very large. Recently, some furnaces have become larger and the arch width exceeds 10 m. The refractory used here needs to have a high compressive strength to withstand this load.
[0004]
However, the conventional β-alumina electrocast refractories are mostly composed of developed β-alumina crystals, so the compressive strength is only about 30 MPa, and the strength is insufficient for use in wide ceiling parts. Was.
[0005]
For example, in order to use the ceiling portion having a width of about 6 m, the mechanical strength of the refractory is required to be a compressive strength of 50 MPa or more. When the width exceeds 10 m, the mechanical strength of the refractory must be 70 MPa or more.
[0006]
Recently, the combustion method for melting glass is changing from air combustion to oxyfuel combustion. In oxyfuel combustion, oxygen is used for combustion, so that the amount of gas required for combustion becomes very small. As a result, the atmosphere in the furnace, particularly the atmosphere in the melting chamber, is greatly different from that in air combustion. That is, in oxyfuel combustion, the atmosphere in the furnace has a very high alkali concentration volatilized from the molten glass. In an atmosphere with a high alkali concentration, a refractory material that is stronger than before is required.
[0007]
An object of the present invention is to provide a β-alumina electroformed refractory material that has a high compressive strength and is not easily eroded by alkali.
[0008]
[Means for Solving the Problems]
The present invention provides the β-alumina electrocast refractory according to any one of claims 1 to 3 , for example , Al 2 O 3 is 85 to 95% by weight , Na 2 O and K 2 O Is 5.0 to 7.0%, MgO is 0.4 to 1.5%, CaO, SrO, and BaO are 0.4 to 2.0%, and SiO 2 is 0. 0.5% or less, the total of Fe 2 O 3 and TiO 2 being 0.1% or less, β-alumina, and a structure in which undeveloped crystals are interlaced with each other The main point is alumina electrocast refractories .
[0009]
DETAILED DESCRIPTION OF THE INVENTION
The composition of the β-alumina electrocast refractory of the present invention will be described.
[0010]
The total of Na 2 O and K 2 O is 4.0 to 7.5% , preferably 5.0 to 7.0%. These compositions react with Al 2 O 3 to produce β alumina crystals. When the total of Na 2 O and K 2 O is less than 4.0%, a large amount of corundum is present, and in an atmosphere having a high alkali concentration, corundum is changed to β-alumina and the structure is collapsed. On the other hand, if it exceeds 7.5%, excess Na 2 O and K 2 O are present between the crystals, and are easily dissolved by moisture and moisture, and the structure becomes brittle. Note that Na 2 O or K 2 O may be zero.
[0011]
CaO, SrO, and BaO have the effect of preventing the crystals from growing excessively. When MgO is added to these, β-alumina crystals are interlaced with each other to strengthen the structure. That is, by adding MgO together with CaO, SrO, BaO, etc., a structure in which crystals that are β-alumina and have not developed are interlaced with each other can be obtained.
[0012]
FIG. 1 is a schematic diagram showing an example of the crystal structure of the β-alumina electrocast refractory of the present invention. FIG. 2 is a schematic diagram showing the crystal structure of a conventional β-alumina electroformed refractory. Compared to the conventional one, the β-alumina electrocast refractory of the present invention has a smaller crystal and a shape closer to a square. MgO is 0.2 to 2.0%, preferably 0.4 to 1.5%, and the total of CaO, SrO and BaO is 0.2 to 3.0%, preferably 0.4 to 2.0. %. If the amount is less than this, the above-described effects are insufficient, and if the amount is too large, spinel with Al 2 O 3 is generated and eroded by alkali, resulting in large creep deformation. Note that any of CaO, SrO, and BaO may be zero.
[0013]
SiO 2 is a composition that forms a glass phase. If this is too much, creep deformation becomes large, so 0.5% or less is preferable.
[0014]
Fe 2 O 3 and TiO 2 0.1% in total less favorable preferable. Both these compositions form a low melting glass. Low melting point glass is not preferable because it impairs heat resistance. In addition, both these compositions have the effect of coloring the product.
[0015]
The corundum amount is preferably 5% or less. When exposed to an atmosphere with a low alkali concentration, β-alumina changes corundum and this acts as a protective layer to prevent erosion. However, when the alkali concentration is high, corundum changes to β alumina. When this change occurs, the volume suddenly expands and creep deformation occurs. When the corundum amount exceeds 5%, the creep deformation increases.
[0016]
According to the present invention, by weight, Al 2 O 3 is 85-95% and the total of Na 2 O and K 2 O is 5 . 0-7. 0 %, and MgO is 0. 4 to 1.5 %, and the total of CaO, SrO, and BaO is 0.00. 4-2. The composition of 0%, SiO 2 of 0.5% or less, and the total of Fe 2 O 3 and TiO 2 of 0.1% or less has sufficient compressive strength without greatly changing the specific gravity. Moreover, even when exposed to an atmosphere with a high alkali concentration, an extremely excellent β-alumina electrocast refractory having low creep deformation and high corrosion resistance can be obtained. Further, the matrix glass can be reduced to a few percent or less, and the compression strength does not significantly decrease at a temperature of 1800 ° C. or less.
[0017]
【Example】
[0018]
Examples of the present invention will be described.
The raw materials blended in the predetermined composition ratios shown in Table 1 were melted using an arc furnace, and the melt was poured into a carbon mold having an inner size of 230 × 230 × 230 mm and molded. The molded product was gradually cooled in alumina powder. The obtained product was free from defects in appearance. Various properties were measured for these products. The results are also shown in Table 1.
[0019]
[Table 1]
[0020]
The compressive strength was measured by cutting a cube with a side of 25 mm from the position of 50 mm from the bottom corner of the product and a side of 50 mm from the side as a sample, and the pressing speed was 10 to 15 kg / cm 2 per second.
[0021]
The amount of corundum was quantified by an internal standard method using X-rays using a sample after measurement of compressive strength.
[0022]
The erosion test with alkali vapor was performed as follows.
[0023]
An crucible having an inner diameter of 80 mm is filled with an erodant containing 54% SiO 2 , 11% BaO, 15% Na 2 O and 13% K 2 O in a weight ratio, and the upper part has a diameter of 90 mm and a thickness of 20 mm. The sample was sealed and held at 1580 ° C. for 96 hours in an electric furnace. Thereafter, the thickness of the central portion of the sample is measured, and the reduction in thickness is converted per 24 hours and indicated as the alkali erosion rate.
[0024]
Creep characteristics are shown as creep deformation in a sample after an erosion test with an alkali vapor by measuring a bulge in which the central portion of the sample is softened and deformed.
[0025]
Regarding the number of cracks, in the sample after the erosion test with alkali vapor, this sample was cut into two equal parts, and the cracks that appeared on the cut surface were counted.
[0026]
Some examples of the present invention are outside the numerical range of claim 1, but all have a compressive strength of 50 MPa or more, and in particular, Examples 5 to 8 have a compressive strength exceeding 70 MPa. . Further, the amount of corundum did not exceed 5%.
[0027]
Comparative Examples 1-7
Except for the different composition ratios, products were manufactured in the same manner as in the previous examples, and the same tests and measurements were performed. The composition ratios and results are shown in Table 2.
[0028]
[Table 2]
[0029]
Comparative Example 2 is an example in which CaO, SrO, and BaO are not included. Low compressive strength and high erosion rate.
[0030]
Comparative Example 3 is an example total more of Fe 2 O 3 and TiO 2. Creep deformation is large.
[0031]
Comparative Example 4 is a SiO 2 are many cases. Creep deformation is large.
[0032]
Comparative Example 5 is an example in which MgO is not included. Low compressive strength. Creep deformation is large.
[0033]
Comparative Example 6 is an example in which the total of Na 2 O and K 2 O is large. Compressive strength is extremely low and creep deformation is large.
[0034]
Comparative Example 7 is an example in which the total of CaO, SrO, and BaO is large. High erosion rate and creep deformation.
[0035]
【The invention's effect】
The β-alumina electrocast refractory of the present invention can easily have a compressive strength of 50 MPa or more, has low creep even when exposed to an atmosphere having a high alkali concentration, and is less eroded by alkali vapor. Therefore, the β-alumina electrocast refractory of the present invention is also used in parts that are exposed to a high alkali concentration and subjected to a large load, for example, the ceiling part of a glass melting furnace by oxygen combustion, and the part where raw batches are scattered. Is possible.
[Brief description of the drawings]
FIG. 1 is a schematic view showing an example of the crystal structure of a β-alumina electrocast refractory according to the present invention.
FIG. 2 is a schematic diagram showing the crystal structure of a conventional β-alumina electroformed refractory.
Claims (3)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03697197A JP3727746B2 (en) | 1997-02-06 | 1997-02-06 | β-alumina electroformed refractory |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03697197A JP3727746B2 (en) | 1997-02-06 | 1997-02-06 | β-alumina electroformed refractory |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH10218676A JPH10218676A (en) | 1998-08-18 |
| JP3727746B2 true JP3727746B2 (en) | 2005-12-14 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03697197A Expired - Fee Related JP3727746B2 (en) | 1997-02-06 | 1997-02-06 | β-alumina electroformed refractory |
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| JP (1) | JP3727746B2 (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2853897B1 (en) * | 2003-04-17 | 2007-05-11 | Saint Gobain Ct Recherches | REFRACTORY PRODUCT FOR STACKING MEMBER OF A REGENERATOR OF A GLUE FURNACE |
| JP2012111667A (en) * | 2010-11-26 | 2012-06-14 | Nippon Electric Glass Co Ltd | Apparatus for manufacturing glass, and method for manufacturing glass using the same |
| MY166938A (en) | 2011-03-11 | 2018-07-25 | Saint Gobain Ceramics | Refractory object, glass overflow forming block, and process for glass object manufacture |
| EP2694452A4 (en) | 2011-03-30 | 2015-03-11 | Saint Gobain Ceramics | Refractory object, glass overflow forming block, and process of forming and using the refractory object |
| EP2697177B1 (en) | 2011-04-13 | 2020-11-18 | Saint-Gobain Ceramics & Plastics, Inc. | Refractory object including beta alumina and processes of making and using the same |
| KR102037046B1 (en) | 2012-01-11 | 2019-10-29 | 생-고뱅 세라믹스 앤드 플라스틱스, 인코포레이티드 | Refractory object and process of forming a glass sheet using the refractory object |
| FR3032962A1 (en) | 2015-02-24 | 2016-08-26 | Saint-Gobain Centre De Rech Et D'Etudes Europeen | REFRACTORY BLOCK AND GLASS FUSION OVEN |
| WO2016138111A1 (en) | 2015-02-24 | 2016-09-01 | Saint-Gobain Ceramics & Plastics, Inc. | Refractory article and method of making |
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1997
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| Publication number | Publication date |
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| JPH10218676A (en) | 1998-08-18 |
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