JPH0798677B2 - Irregular refractories - Google Patents
Irregular refractoriesInfo
- Publication number
- JPH0798677B2 JPH0798677B2 JP1246695A JP24669589A JPH0798677B2 JP H0798677 B2 JPH0798677 B2 JP H0798677B2 JP 1246695 A JP1246695 A JP 1246695A JP 24669589 A JP24669589 A JP 24669589A JP H0798677 B2 JPH0798677 B2 JP H0798677B2
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- Japan
- Prior art keywords
- weight
- magnesia
- purity
- particle size
- alumina
- Prior art date
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- Ceramic Products (AREA)
- Furnace Housings, Linings, Walls, And Ceilings (AREA)
Description
【発明の詳細な説明】 産業上の利用分野 本発明は、耐スポール性や耐蝕性に優れ、主として、混
銑車炉口内張用に使用される不定形耐火物に関するもの
である。TECHNICAL FIELD The present invention relates to an amorphous refractory having excellent spall resistance and corrosion resistance, which is mainly used for lining a furnace of a mixed pig iron furnace.
従来の技術 近年、溶銑予備処理技術の発達により、混銑車でも脱珪
処理などが行われるようになってきた。そして、この処
理を行うに際し、処理剤としてFeOやFe2O3からなるミル
ケースや酸素ガスなどが用いられるようになっており、
混銑車内張用耐火物に要求される条件も非常に厳しくな
ってきた。そのため、従来、混銑車炉口内張用不定形耐
火物として耐スポール性や耐蝕性が優れていることから
炭化けい素やカーボン類等の非酸化物を配した不定形耐
火物が使用されてきたが、厳しい酸化雰囲気に晒される
ようになったことによって損耗が著しくなってきた。2. Description of the Related Art In recent years, with the development of hot metal pretreatment technology, desiliconization processing has been performed even in mixed pig iron cars. When performing this treatment, a mill case made of FeO or Fe 2 O 3 or oxygen gas is used as a treatment agent.
The requirements for refractory for lining hot metal cars have also become very severe. Therefore, conventionally, amorphous refractory with non-oxides such as silicon carbide and carbons has been used because it has excellent spall resistance and corrosion resistance. However, the wear has become remarkable due to being exposed to a severe oxidizing atmosphere.
この厳しい酸化雰囲気に耐えられる不定形耐火物とし
て、アルミナを主成分とし、これにマグネシアやスピネ
ルを配することによって耐蝕性を高め不定形耐火物が開
発されてした（例えば、特公昭61−328号公報、特公昭
第61−11906号公報）。しかし、このような不定形耐火
物は、溶銑やスラグに浸った部分の内張りであれば使用
可能であったが、第１図に示したように、溶銑２を収容
し、せり出した形状３を有するのみならず、脱珪処理前
後の急昇温、急降温による熱衝撃が大きい混銑車炉口１
のような部位に使用した場合は、スポーリング抵抗性が
小さく、亀裂の発生や剥離、剥落現象が著しいために、
炭化けい素やカーボン類等の非酸化物を配した不定形耐
火物に対する優位性は得られなかった。As an amorphous refractory that can withstand this severe oxidizing atmosphere, an amorphous refractory has been developed, which is mainly composed of alumina and has magnesia or spinel to enhance corrosion resistance (for example, Japanese Patent Publication No. 61-328). Gazette, Japanese Examined Patent Publication No. 61-11906). However, such an amorphous refractory could be used as long as it was lined in the part soaked in the hot metal or slag, but as shown in FIG. Not only does it have a large thermal shock due to the rapid temperature rise and fall before and after desiliconization, but it also has a large thermal shock to the mixed piggy car
When used in areas such as, the spalling resistance is low and cracking, peeling and peeling phenomena are significant,
We could not obtain superiority to amorphous refractories with non-oxides such as silicon carbide and carbons.
発明が解決しようとする課題 従来のアルミナ−スピネル系もしくはアルミナ−マグネ
シア系のような酸化物系不定形耐火物は、炭化けい素や
カーボン類等の非酸化物を配した不定形耐火物と比較し
て、耐蝕性の点では良好な結果が得られているが、耐ス
ポール性の点では著しく劣っている。これは酸化物系不
定形耐火物は、炭化けい素やカーボン類等の非酸化物を
配した不定形耐火物と比較して、特に高温加熱した場
合、焼結が進むことによって高弾性率化するため、熱衝
撃による発生熱応力が増大し、急昇温、急降温時に亀裂
や剥離が発生しやすいためである。同様に、熱間線膨張
係数が大きいことも発生する熱応力が大きくなる原因と
なっている。従って、耐スポール性の向上を図るために
は、即ち、発生熱応力を小さくするためには、熱間線膨
張係数や弾性率を小さくする必要がある。Problems to be Solved by the Invention Conventional oxide-based amorphous refractory materials such as alumina-spinel system or alumina-magnesia system are compared with amorphous refractory materials in which non-oxides such as silicon carbide and carbons are arranged. As a result, good results are obtained in terms of corrosion resistance, but they are significantly inferior in terms of spall resistance. This is because the oxide-based amorphous refractory has a higher elastic modulus than the amorphous refractory in which non-oxides such as silicon carbide and carbons are arranged, especially when it is heated at high temperature due to the progress of sintering. Therefore, the thermal stress generated by the thermal shock increases, and cracks and peeling are likely to occur during rapid temperature rise and temperature drop. Similarly, a large coefficient of linear thermal expansion also causes a large amount of thermal stress. Therefore, in order to improve the spall resistance, that is, in order to reduce the generated thermal stress, it is necessary to reduce the coefficient of linear thermal expansion and the elastic modulus.
課題を解決するための手段 本発明は、0.5〜3mmの粒径の純度90重量％以上のマグネ
シアが３〜15重量％、高純度アルミナセメントが0.5〜
５重量％、残部が純度90重量％以上のアルミナからなる
高耐蝕性、高耐スポール性の不定形耐火物を提供するも
のである。また、本発明は、0.5〜3mmの粒径の純度90重
量％以上のマグネシアが３〜15重量％、高純度アルミナ
セメントが0.5〜５重量％、0.5mm未満の粒径の純度90重
量％以上のマグネシアが１〜５重量％もしくは0.5mm未
満の粒径の純度90重量％以上のスピネルが１〜20重量
％、残部が純度90重量％以上のアルミナからなる高耐蝕
性、高耐スポール性の不定形耐火物を提供するものであ
る。Means for Solving the Problems According to the present invention, 3 to 15% by weight of magnesia having a particle size of 0.5 to 3 mm and a purity of 90% by weight or more and 0.5 to 3% of high-purity alumina cement are used.
It is intended to provide an unshaped refractory having high corrosion resistance and high spall resistance, which is composed of 5% by weight and the balance of alumina having a purity of 90% by weight or more. Further, the present invention is 3 to 15% by weight of magnesia having a particle size of 0.5 to 3 mm and a purity of 90% by weight or more, 0.5 to 5% by weight of high-purity alumina cement, and 90% by weight or more of a particle size of less than 0.5 mm. 1 to 5% by weight of magnesia or 1 to 20% by weight of spinel having a particle size of less than 0.5 mm and a purity of 90% by weight or more, and the balance of alumina having a purity of 90% by weight or more of high corrosion resistance and high spall resistance. It provides an irregular refractory material.
実 施 例 第１表に本発明の実施例及び比較例を示した。なお、第
１表の本発明の実施例及び比較例に使用したアルミナ、
マグネシア及びスピネルの純度はいずれも99重量％であ
る。また、耐スポール性や耐蝕性の評価は以下のように
して行った。まずスポールテストを述べる。４×４×16
cm供試体を1500℃×3hr焼成し、この時の弾性率E0を測
定した。その後これを電気炉にて1500℃×20min急熱の
後急冷した。この急熱・急冷を３サイクル繰り返し、ｎ
サイクル後の弾性率（En）とE0との比（En/E0）を算出
し、この値で評価した。En/E0が１に近いほど耐スポー
ル性が優れている。次に、耐蝕性は誘導炉法を用いて評
価した。この時使用したスラグの塩基度CaO/SiO2＝3.
5、溶銑温度は1600℃である。なお、比較例４は酸化劣
化を考慮して1000℃×3hr酸化処理した供試体にて評価
した。この評価法によって得られた結果は実機での結果
との対応が良好であった。Examples Examples of the present invention and comparative examples are shown in Table 1. In addition, alumina used in Examples and Comparative Examples of the present invention in Table 1,
Both magnesia and spinel have a purity of 99% by weight. The evaluation of spall resistance and corrosion resistance was performed as follows. First, the spall test will be described. 4x4x16
The cm specimen was fired at 1500 ° C. for 3 hours, and the elastic modulus E 0 at this time was measured. Then, this was rapidly heated in an electric furnace at 1500 ° C. for 20 minutes and then rapidly cooled. Repeat this rapid heating / cooling for 3 cycles, n
The ratio (E n / E 0 ) of the elastic modulus (E n ) and E 0 after the cycle was calculated, and this value was evaluated. The closer the E n / E 0 is to 1, the better the spall resistance. Next, the corrosion resistance was evaluated using the induction furnace method. The basicity of the slag used at this time CaO / SiO 2 = 3.
5. Hot metal temperature is 1600 ℃. In addition, Comparative Example 4 was evaluated using a test piece that had been subjected to oxidation treatment at 1000 ° C. for 3 hours in consideration of oxidative deterioration. The results obtained by this evaluation method corresponded well with the results on the actual machine.
比較例１にマグネシアを配さない場合の物性を示した。
この比較例１に対し、実施例１〜実施例３のように１〜
3mmの粒径を持つマグネシアを配した場合、その配合量
が増すにつれて1500℃×3hr焼成後の弾性率は小さくな
り、1500℃×3hr焼成後の熱間線膨張係数も小さくなっ
ており、それにつれて耐スポール性が向上している。こ
れに対して、比較例２のようにマグネシア粒径が0.3mm
以下のものを配した場合は、1500℃×3hr焼成後の弾性
率は増大し、耐スポール性も劣化している。また、比較
例３のようにマグネシアのかわりに1mm以上の粒径を持
つスピネルを配した場合は、アルミナのみの場合よりも
1500℃×3hr焼成後の弾性率はやや低下する。しかし、
熱間線膨張係数がかなり大きくなっているため耐スポー
ル性はむしろ劣化する。Comparative Example 1 shows the physical properties when magnesia is not provided.
In contrast to Comparative Example 1, as in Examples 1 to 3,
When magnesia having a particle size of 3 mm is placed, the elastic modulus after firing at 1500 ° C x 3 hr becomes smaller as the compounding amount increases, and the coefficient of hot linear expansion after firing at 1500 ° C x 3 hr also becomes smaller. As a result, the spall resistance is improved. On the other hand, as in Comparative Example 2, the magnesia particle size is 0.3 mm.
When the following materials are arranged, the elastic modulus after firing at 1500 ° C. for 3 hours increases and the spall resistance also deteriorates. Moreover, when spinel having a particle size of 1 mm or more is arranged instead of magnesia as in Comparative Example 3, it is more than in the case of only alumina.
The elastic modulus after firing at 1500 ° C for 3 hours decreases slightly. But,
Since the hot linear expansion coefficient is considerably large, the spall resistance is rather deteriorated.
この0.5mm以上の以上の粒径を持つマグネシアの耐スポ
ール性向上効果は、以下のような特性によってもたらさ
れる。第１表の実施例や比較例に示した不定形耐火物の
試供体を各々高温（1200℃以上）加熱すると、供試体内
部の粒子、特に0.5mm以上の粒径を持つ粒子は、熱間線
膨張係数と温度とに比例して膨張する。この時、高温加
熱した後、室温まで徐冷した供試体の切断面の走査型電
子顕微鏡写真では、0.5mm以上の粒径を持つアルミナや
スピネルは周囲の微粉部（以下、マトリックスと称す）
と反応、焼結しているが、マグネシアの周囲にはマトリ
ックスとの間に0.03〜0.06mmの空隙が形成されているこ
とが明らかになった。The effect of improving the spall resistance of magnesia having a grain size of 0.5 mm or more is brought about by the following characteristics. When the samples of the amorphous refractories shown in the examples and comparative examples of Table 1 are heated at high temperatures (1200 ° C or higher), the particles inside the samples, especially those with a particle size of 0.5 mm or more It expands in proportion to the linear expansion coefficient and temperature. At this time, in the scanning electron micrograph of the cross section of the specimen that was heated to high temperature and then slowly cooled to room temperature, alumina and spinel having a particle size of 0.5 mm or more had fine particles in the surrounding area (hereinafter referred to as matrix).
It was revealed that a void of 0.03 to 0.06 mm was formed around the magnesia with the matrix though it was reacted and sintered.
この空隙の形成は次のように推察される。即ち、0.5mm
以上の粒径を持つ粒子は、いずれも高温下で膨張してマ
トリックスを押し広げるが、マグネシアの場合はマトリ
ックスと焼結し難いか、あるいは分離しやすいため、冷
却時にはマトリックスと分離してマグネシアのみが大き
く収縮するためマトリックスとの間に空隙が形成され
る。一方、アルミナやスピネルは、周囲のマトリックス
と反応、焼結するため、冷却時にはマトリックスと連動
して収縮する。この空隙を形成するか否かは、1500℃加
熱時を基準として、室温まで冷却した時の供試体の収縮
率にも影響し、マグネシアを配した場合は小さくなり、
スピネルを配した場合は最も大きくなる。また、この空
隙は際加熱時の0.5mm以上の粒径を持つマグネシアやマ
トリックスの熱膨張を吸収する働きをなすため、再加熱
時の熱間線膨張率も小さくなる。更に、この空隙は弾性
率を小さくする効果を有し、ひいては急熱・急冷時の熱
歪みによる弾性エネルギーを吸収する働きもなしてい
る。The formation of these voids is presumed as follows. That is, 0.5 mm
All of the particles with the above particle diameter expand and spread the matrix at high temperature, but in the case of magnesia, it is difficult to sinter with the matrix or it easily separates, so it separates from the matrix during cooling and only magnesia Shrinks significantly, forming voids with the matrix. On the other hand, alumina and spinel react with the surrounding matrix and sinter, so that they contract with the matrix during cooling. Whether or not to form these voids affects the shrinkage rate of the specimen when cooled to room temperature with 1500 ° C heating as the standard, and becomes smaller when magnesia is placed,
It becomes the largest when the spinel is arranged. In addition, since this void serves to absorb the thermal expansion of magnesia or matrix having a particle size of 0.5 mm or more at the time of reheating, the coefficient of linear thermal expansion at the time of reheating becomes small. Furthermore, the voids have the effect of reducing the elastic modulus, and thus also have the function of absorbing elastic energy due to thermal strain during rapid heating / cooling.
なお、第１表に示した熱間線膨張係数値は、1500℃×3h
r焼成後の供試体について測定した値である。これに対
し、110℃を基準とし、昇温時の熱間線膨張率を測定し
た場合は、空隙が未形成のためマグネシアを配した場合
が最も大きい。しかし、実際に使用する場合は乾燥、予
熱等の緩やかな昇温前工程があるため、問題とならな
い。The hot linear expansion coefficient values shown in Table 1 are 1500 ℃ × 3h
r These are the values measured on the test piece after firing. On the other hand, when the hot linear expansion coefficient at the time of temperature rise was measured with 110 ° C. as the reference, the case where magnesia was arranged was the largest because no void was formed. However, when it is actually used, there is a gentle preheating process such as drying and preheating, so there is no problem.
このマグネシアを配することによる空隙の形成の有無
は、その粒径と密接に関わっており、マグネシアの粒径
が0.5mmよりも小さいと、空隙の形成に必要な熱関膨張
の絶対量が不足する。さらアルミナとの反応によるスピ
ネルの生成にともなう体積膨張反応が起こり、組織の緻
密化現象が顕著に現れることによって、耐スポール性の
向上効果が認められなくなる。場合によっては、比較例
２のようにマトリックス組織の緻密化にともなう高弾性
率化によって耐スポール性の劣化もみられるようにな
る。粒径が3mmを超えると空隙が大きくなりすぎるため
か、強度低下が著しくなり好ましくない。Whether or not voids are formed by arranging this magnesia is closely related to the particle size.If the particle size of magnesia is less than 0.5 mm, the absolute amount of thermal expansion required for void formation is insufficient. To do. Furthermore, a volume expansion reaction occurs due to the formation of spinel due to the reaction with alumina, and the densification phenomenon of the structure appears remarkably, so that the effect of improving the spall resistance cannot be recognized. In some cases, as in Comparative Example 2, deterioration of spall resistance is also observed due to the high elastic modulus accompanying the densification of the matrix structure. If the particle size exceeds 3 mm, the voids become too large, and the strength is significantly reduced, which is not preferable.
また、粒径が0.5〜3mmのマグネシアの配合量が３重量％
未満になると、耐スポール性の向上効果が見られなくな
る。また、15重量％を超えるとスラグの浸透が顕著とな
る他、強度低下も著しくなるため好ましくない。The amount of magnesia with a particle size of 0.5 to 3 mm is 3% by weight.
If it is less than this, the effect of improving the spall resistance cannot be seen. On the other hand, if it exceeds 15% by weight, not only is the penetration of slag remarkable, but the strength also significantly decreases, which is not preferable.
マグネシアやアルミナは焼結・電融いずれでも良い。但
し、その純度は90重量％以上でなければならない。低純
度の原料に含まれるSiO2やFe2O3等の不純物は、高温加
熱時の焼結の進行を促すために、高弾性率化し、耐スポ
ール性の劣化が顕著となり好ましくない。第２表に低純
度アルミナを使用した例として実験例１及び２を示した
が、例えば、実験例１に示すように１〜3mmのマグネシ
アを15重量％添加しても十分な耐スポール性が得られな
い。さらに20重量％まで増量しても十分な耐スポール性
が得られず、むしろスラグの浸透が増すようになり、構
造スポーリングによる損耗が懸念されるようになる。ア
ルミナセメントもCaOやSiO2、Fe2O3等を多く含む低純度
品を使用すると、前述した理由と同様に耐スポール性の
劣化が顕著となり好ましくない。しかしながら、高純度
のアルミナセメントもその配合量が５重量％を超えると
十分な仮使時間が得られなくなる他、耐蝕性を損なう、
耐スポール性が劣化するなど好ましくない。また、0.5
重量％未満になると養生後の強度が低下し、構造体とし
て十分なものが得られなくなる。Magnesia or alumina may be either sintered or electrofused. However, its purity must be 90% by weight or more. Impurities such as SiO 2 and Fe 2 O 3 contained in the low-purity raw material promote the progress of sintering during high-temperature heating, so that the elastic modulus is increased and the spall resistance is significantly deteriorated, which is not preferable. Table 2 shows Experimental Examples 1 and 2 as examples using low-purity alumina. For example, as shown in Experimental Example 1, even if 15% by weight of magnesia of 1 to 3 mm is added, sufficient spall resistance can be obtained. I can't get it. Further, even if the amount is increased to 20% by weight, sufficient spall resistance cannot be obtained, rather the penetration of slag is increased, and there is a fear of wear due to structural spalling. If a low-purity alumina cement containing a large amount of CaO, SiO 2 , Fe 2 O 3, etc. is used, the spall resistance is significantly deteriorated for the same reason as described above, which is not preferable. However, even if high-purity alumina cement is added in an amount of more than 5% by weight, sufficient temporary use time cannot be obtained and corrosion resistance is impaired.
It is not preferable because the spall resistance is deteriorated. Also, 0.5
If it is less than wt%, the strength after curing will be reduced, and a sufficient structure cannot be obtained.
耐蝕性をさほど要求しない部位であればマトリックス部
の組成は特に問題としないが、スラグスプラッシュによ
る溶損の著しい部位などに適用する場合は、実施例４、
５のようにマトリックス部に粒径が0.5mm未満のスピネ
ルやマグネシアなどを配することによって高耐蝕性化が
得られる。ここで使用するマグネシアやスピネルも焼結
・電融いずれでも良いが、その純度は90重量％以上でな
ければならない。また、これらの配合量はいずれも１重
量％未満では効果はなく、またマグネシアが５重量％、
スピネルが20重量％を超えると、スラグの浸透が著しく
なり、好ましくない。The composition of the matrix portion is not particularly problematic as long as it does not require much corrosion resistance, but when it is applied to a portion where erosion damage due to slag splash is significant, Example 4,
By disposing spinel or magnesia having a particle size of less than 0.5 mm in the matrix portion as shown in No. 5, high corrosion resistance can be obtained. The magnesia and spinel used here may be either sintered or electrofused, but their purity must be 90% by weight or more. Also, if these compounding amounts are all less than 1% by weight, there is no effect, and magnesia is 5% by weight,
If the spinel content exceeds 20% by weight, the penetration of slag becomes remarkable, which is not preferable.
このようにして得られた不定形耐火物（実施例５）を、
脱珪処理を行っている混銑車の炉口に使用した結果、従
来材の炭化けい素やカーボン類を配した不定形耐火物
（比較例４）や比較例２の不定形耐火物と比較して50％
以上の寿命向上が可能となった。The amorphous refractory material (Example 5) thus obtained was
As a result of using it in the furnace opening of a hot metal car that has undergone desiliconization, it is compared with the amorphous refractory (comparative example 4) and the amorphous refractory of comparative example 2 in which silicon carbide and carbons of conventional materials are arranged. 50%
The above life can be improved.
発明の効果 以上のように、本発明は、純度90重量％以上のマグネシ
アの粒径を0.5〜3mmに限定し、これを純度90重量％以上
のアルミナ質の不定形耐火物に配することによって耐蝕
性、耐スポール性に優れた材料を得ることができた。本
発明は、混銑車で最も高い耐スポール性が要求されると
考えられる部位である炉口の内張用不定形耐火物に最適
なものである。また、本発明は、同じように苛酷な熱衝
撃を受けるランス材などにも適用できる。また、混銑車
炉口ほどの熱衝撃を受けない部位に使用する不定形耐火
物に関しても、本発明を適用することによってより安定
した特性を得ることができる。 As described above, according to the present invention, the particle size of magnesia having a purity of 90% by weight or more is limited to 0.5 to 3 mm, and by arranging this in an alumina amorphous refractory having a purity of 90% by weight or more. A material having excellent corrosion resistance and spall resistance could be obtained. INDUSTRIAL APPLICABILITY The present invention is most suitable for an irregular refractory material for lining the furnace mouth, which is a part of a hot metal car where the highest spall resistance is considered to be required. Further, the present invention can also be applied to a lance material that is similarly subjected to severe thermal shock. Further, by applying the present invention, more stable characteristics can be obtained even with respect to an amorphous refractory used in a portion which is not subjected to a thermal shock as much as that of a mixed pig car furnace.
第１図は、混銑車受銑口部の断面を示した説明図であ
る。FIG. 1 is an explanatory view showing a cross-section of a pig iron receiving portion of a mixed pig car.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 佐藤 高芳 千葉県君津市君津１番地 新日本製鐵株式 会社君津製鐵所内 (72)発明者 上野 尚弘 福岡県北九州市戸畑区牧山新町１番１号 大光炉材株式会社内 (72)発明者 村岡 久義 福岡県北九州市戸畑区牧山新町１番１号 大光炉材株式会社内 (56)参考文献 特開 昭59−128272（ＪＰ，Ａ) 特開 昭60−108374（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Takayoshi Sato, 1 Kimitsu, Kimitsu City, Chiba Prefecture, Nippon Steel Co., Ltd. Inside the Kimitsu Works (72) Inventor, Naohiro Ueno 1-1, Makiyama Shinmachi, Tobata-ku, Kitakyushu, Fukuoka Daiko Furnace Co., Ltd. (72) Inventor Hisashiyoshi Muraoka 1-1 Makiyama Shinmachi, Tobata-ku, Kitakyushu, Fukuoka Daiko Furnace Co., Ltd. (56) Reference JP-A-59-128272 (JP, A) JP-A-60-108374 (JP, A)
Claims (2)
ネアが３〜15重量％、高純度アルミナセメントが0.5〜
５重量％、残部が純度90重量％以上のアルミナからなる
高耐蝕性、高耐スポール性を特徴とする不定形耐火物。1. Magnesia having a particle size of 0.5 to 3 mm and a purity of 90% by weight or more is 3 to 15% by weight, and high purity alumina cement is 0.5 to 3%.
An amorphous refractory material with high corrosion resistance and spall resistance consisting of 5% by weight and the balance 90% by weight or more of alumina.
ネアが３〜15重量％、高純度アルミナセメントが0.5〜
５重量％、0.5mm未満の粒径の純度90重量％以上のマグ
ネシアが１〜５重量％もしくは0.5mm未満の粒径の純度9
0重量％以上のスピネルが１〜20重量％、残部が純度90
重量％以上のアルミナからなる高耐蝕性、高耐スポール
性を特徴とする不定形耐火物。2. Magnesium having a particle size of 0.5 to 3 mm and a purity of 90% by weight or more, 3 to 15% by weight, and high purity alumina cement 0.5 to 3%.
5% by weight, purity of particle size less than 0.5 mm 90% by weight or more of magnesia 1 to 5% by weight or purity of particle size less than 0.5 mm 9
1 to 20% by weight of spinel above 0% by weight, balance 90%
An unshaped refractory material that is characterized by high corrosion resistance and high spall resistance consisting of alumina in an amount of at least wt%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1246695A JPH0798677B2 (en) | 1989-09-22 | 1989-09-22 | Irregular refractories |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1246695A JPH0798677B2 (en) | 1989-09-22 | 1989-09-22 | Irregular refractories |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03109273A JPH03109273A (en) | 1991-05-09 |
| JPH0798677B2 true JPH0798677B2 (en) | 1995-10-25 |
Family
ID=17152254
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1246695A Expired - Fee Related JPH0798677B2 (en) | 1989-09-22 | 1989-09-22 | Irregular refractories |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0798677B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07106946B2 (en) * | 1991-10-02 | 1995-11-15 | 東和耐火工業株式会社 | Unshaped refractory for ladle lining |
-
1989
- 1989-09-22 JP JP1246695A patent/JPH0798677B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH03109273A (en) | 1991-05-09 |
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