JPH05185202A - Monolithic refractorie for ladle - Google Patents
Monolithic refractorie for ladleInfo
- Publication number
- JPH05185202A JPH05185202A JP3316557A JP31655791A JPH05185202A JP H05185202 A JPH05185202 A JP H05185202A JP 3316557 A JP3316557 A JP 3316557A JP 31655791 A JP31655791 A JP 31655791A JP H05185202 A JPH05185202 A JP H05185202A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- alumina
- amorphous
- fine particles
- silica fine
- 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.)
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- Compositions Of Oxide Ceramics (AREA)
- Ceramic Products (AREA)
- Treatment Of Steel In Its Molten State (AREA)
- Furnace Housings, Linings, Walls, And Ceilings (AREA)
- Carbon Steel Or Casting Steel Manufacturing (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、溶銑鍋、溶滓鍋、取
鍋、転炉、タンディッシュなど、溶銑、溶滓或いは溶鋼
を入れるための鍋に内張りされる不定形耐火物、ことに
溶鋼鍋の湯当り部用材料として用いるのに適した不定形
耐火物に関する。FIELD OF THE INVENTION The present invention relates to an amorphous refractory material lined in a ladle for containing molten pig iron, molten slag or molten steel, such as a molten pig ladle, a slag ladle, a ladle, a converter and a tundish. The present invention relates to an amorphous refractory suitable for use as a material for a hot water contact part of a molten steel ladle.
【０００２】[0002]
【従来の技術】溶鋼鍋を例にとっていえば、かゝる鍋で
は近年、操業条件の苛酷化やジルコン原料の価格高騰な
どに伴い、そのライニング材、ことにメタルライン用側
壁材は従来のセミジルコン質不定形耐火物や高アルミナ
質レンガから高純度アルミナを主体とし、これに耐蝕性
を高めるためにスピネルなどを配したキャスタブル耐火
物へと変化している。敷部や湯当たり部についても同様
で、同材質の材料が適用されるようになってきた。2. Description of the Related Art Taking a molten steel ladle as an example, in such a ladle, the lining material, especially the side wall material for metal lines, is the same as that of conventional semi-zircon due to severe operating conditions and rising prices of zircon raw materials. Amorphous refractories and high-alumina bricks have been transformed into castable refractories mainly composed of high-purity alumina and spinel etc. arranged to enhance corrosion resistance. The same applies to the floor part and the hot water contact part, and the same material has come to be applied.
【０００３】湯当り部については元来、受鋼時の溶湯の
落下による衝撃や流体摩耗によってことに局部損耗が起
り易いことから予め、一般敷部ライニングよりも大幅に
厚く形成されているが、湯当たり部は敷部の中心部に位
置する場合が多く、周囲からの熱間膨脹による拘束圧に
より迫り出しや剥離を起し易い。そのため従来の材料で
は、耐蝕性の大幅な劣化などを伴うにもかゝわらず、ス
ティールファイバーを添加することにより迫り出しや剥
離の防止を図っている。Originally, the hot water contact portion is formed to be much thicker than the general floor lining because the local wear is likely to occur due to the impact and fluid wear caused by the drop of the molten metal at the time of receiving steel. In many cases, the hot water contact portion is located at the center of the floor portion, and it is easy for the hot water contact portion to be pushed out or peeled off due to the restraining pressure due to hot expansion from the surroundings. Therefore, although the conventional materials are accompanied by a significant deterioration in corrosion resistance, the addition of steel fibers is intended to prevent squeeze-out and peeling.
【０００４】[0004]
【発明が解決使用とする課題】本発明は、不定形耐火
物、ことに湯当たり部に用いられる不定形耐火物の耐用
向上を図ろうとするものであるが、従来の材料では、上
述するような対策を施してもなお、十分な耐用を得るこ
とはできない。すなわち図１に示すように、耐用延長の
ため湯当たり部１の厚みを一般敷部ライニング２より厚
くしておいても、１０〜２０チャージ程度受鋼すると、
湯当たり部１が図２に示すように、周囲のライニングと
同程度の厚みまで全面剥離してしまう。こうした剥離を
防止するために耐火物中へスティールファイバーを添加
すると、これにより流動性が損なわれ、良好な施工性を
確保するために混練水量が増し、その結果、材料の圧縮
強度が低下し、それに伴って熱間摩耗抵抗性が劣化し、
湯当たり部の局部摩耗が増大する。しかも受鋼時には稼
働面の温度が１６００゜Ｃ以上にも達するため、稼働面
近くのスティールファイバーが溶融、酸化、拡散し、耐
蝕性の劣化をもたらすようになる。SUMMARY OF THE INVENTION The present invention is intended to improve the durability of irregular refractory materials, especially irregular refractory materials used in hot water contact parts. Even if all the measures are taken, it is not possible to obtain sufficient durability. That is, as shown in FIG. 1, even if the thickness of the hot water contact portion 1 is made thicker than that of the general floor lining 2 for extending the service life, if the steel is received for about 10 to 20 charges,
As shown in FIG. 2, the hot water contact portion 1 is entirely peeled off to the same thickness as the surrounding lining. When steel fiber is added to the refractory to prevent such peeling, the fluidity is impaired by this, the amount of kneading water increases to ensure good workability, and as a result, the compressive strength of the material decreases, Along with that, the hot wear resistance deteriorates,
The local wear of the hot water contact part increases. Moreover, since the temperature of the working surface reaches 1600 ° C. or higher during steel receiving, the steel fibers near the working surface are melted, oxidized and diffused, resulting in deterioration of corrosion resistance.
【０００５】本発明は、湯当たり部に用いられる不定形
耐火物の耐用の大幅な向上を図るため種々検討を重ねた
結果なされたもので、剥離を起こし難く、しかも耐蝕性
や、熱間摩耗抵抗性に優れた不定形耐火物を提供するこ
とを目的とする。The present invention has been made as a result of various investigations in order to significantly improve the durability of the amorphous refractory used for the hot water contact part, and it is difficult to cause peeling, and corrosion resistance and hot wear The object is to provide an amorphous refractory material having excellent resistance.
【０００６】[0006]
【課題の解決手段及び作用】本発明の不定形耐火物は、
非晶質シリカ微粒子が０．３〜５重量％、高アルミナセ
メントが０．５〜４重量％、残部がアルミナからなる
か、或いは非晶質シリカ微粒子が０．３〜３重量％、高
アルミナセメントが０．５〜４重量％、スピネル若しく
はマグネシアがＭg Ｏ組成に換算して２〜１５重量％、
残部がアルミナからなるもので、非晶質シリカ微粒子と
高アルミナセメントとの適正な組合わせによって、アル
ミナ質不定形耐火物に１４００℃以上の高温下において
適度の荷重軟化性を付与せしめるとともに、全ゆる温度
域における組織の強化をもたらすようにしたことを特徴
とするものである。The amorphous refractory material of the present invention is
Amorphous silica fine particles are 0.3 to 5% by weight, high alumina cement is 0.5 to 4% by weight, and the balance is alumina, or amorphous silica fine particles are 0.3 to 3% by weight, high alumina. 0.5 to 4% by weight of cement, 2 to 15% by weight of spinel or magnesia converted into MgO composition,
The balance consists of alumina, and the proper combination of amorphous silica fine particles and high-alumina cement gives the alumina-amorphous refractory a moderate load softening property at high temperatures of 1400 ° C or higher. It is characterized in that the tissue is strengthened in a loose temperature range.
【０００７】湯当たり部に置かれた本発明に係る不定形
耐火物構造体によれば、その周囲に施工される材料の熱
間膨脹によって受ける拘束圧を適度の荷重軟化性によっ
て吸収することができ、迫り出しや剥離を防止すること
ができるほか、組織の強化によって湯当たり時に受ける
機械的衝撃に対する抵抗力を高めることができるように
なる。以下にその詳細を説明する。According to the irregular shaped refractory structure according to the present invention placed in the hot water contact portion, the restraining pressure received by the hot expansion of the material around it can be absorbed by the moderate load softening property. In addition to being able to prevent squeeze-out and peeling, strengthening of the structure makes it possible to increase the resistance to mechanical shock received during hot water contact. The details will be described below.
【０００８】高アルミナセメントは、耐蝕性の点から少
ない程望ましいが、一方では受鋼時の機械的衝撃や流体
摩耗に耐えられるような機械的強度が要求されることか
ら、０．５ ％以下の配合量では充分な強度が得られな
くなり好ましくない。また配合量が４％以上となり、そ
の量が増すほど耐蝕性の劣化が増大するうえ、アルミナ
セメントクリンカー鉱物のＣa Ｏ・Ａl2Ｏ3 がＡl2Ｏ3
と高温下で反応してなるＣa Ｏ・６Ａl2Ｏ3 の生成量が
多くなり、このＣa Ｏ・６Ａl2Ｏ3 がシリカと共存する
と、その粒成長が促進され、材料に異常膨脹をもたらす
ようになるため、剥離がむしろ助長され好ましくない。Higher alumina cement is more desirable in terms of corrosion resistance, but on the other hand, it is required to have mechanical strength capable of withstanding mechanical shock and fluid abrasion when receiving steel. With the compounding amount of, sufficient strength cannot be obtained, which is not preferable. In addition, the amount of compounding is 4% or more, and as the amount increases, the deterioration of corrosion resistance increases, and the alumina cement clinker mineral Ca 2 O 3 Al 2 O 3 becomes Al 2 O 3
When CaO · 6Al 2 O 3 coexists with silica, the amount of CaO · 6Al 2 O 3 formed by reacting with it increases at a high temperature. Therefore, peeling is rather promoted, which is not preferable.
【０００９】次に非晶質微粒子について説明する。非晶
質微粒子の効果に関しては、スピネルやマグネシアのよ
うなＭg Ｏ源の有無によって高温下における挙動に違い
がある。そこで先ず、スピネルやマグネシアを含まない
場合について説明する。図３は、高アルミナセメントを
２％配合したアルミナ質キャスタブルに非晶質シリカ微
粒子を０〜６％加えた場合の熱間曲げ強度を示すもの
で、図から見られるように、１２００℃での熱間曲げ強
度は非晶質シリカ微粒子の添加量を増す程高くなるが、
１４５０℃では挙動が異なってくる。すなわち非晶質シ
リカ微粒子の添加量が５％以下においては、高温下で液
相を生成するため熱間曲げ強度が低下するが、５％を越
えると、シリカはアルミナと反応してムライトを生成
し、液相が消滅するため熱間曲げ強度も高くなる。Next, the amorphous fine particles will be described. Regarding the effect of the amorphous fine particles, there is a difference in behavior at high temperature depending on the presence or absence of a MgO source such as spinel or magnesia. Therefore, first, the case where spinel and magnesia are not included will be described. FIG. 3 shows the hot bending strength when 0 to 6% of amorphous silica fine particles are added to an alumina castable containing 2% of high-alumina cement. As shown in FIG. The hot bending strength increases as the amount of amorphous silica particles added increases,
The behavior is different at 1450 ° C. That is, when the amount of the amorphous silica fine particles added is 5% or less, the liquid phase is generated at a high temperature, so that the hot bending strength is lowered, but when it exceeds 5%, the silica reacts with alumina to form mullite. However, since the liquid phase disappears, the hot bending strength also increases.
【００１０】以上のように、１４５０℃の高温下では非
晶質シリカ微粒子の添加量が５％であると、液相を生成
し荷重軟化性を示すが、５％を越えると、ムライト生成
が促進されて液相生成量が減少し、荷重軟化性を示さな
くなる。次にスピネルやマグネシアを含む系における非
晶質シリカ微粒子の効果について説明する。As described above, at a high temperature of 1450 ° C., when the addition amount of the amorphous silica fine particles is 5%, a liquid phase is formed and the softening property under load is exhibited, but when it exceeds 5%, mullite is formed. As a result, the amount of liquid phase produced is reduced and the softening property under load is not exhibited. Next, the effect of amorphous silica fine particles in a system containing spinel and magnesia will be described.
【００１１】図４は、表４の比較例７を基本配合とした
アルミナ−スピネル−マグネシア質キャスタブルの熱間
曲げ強度に対する非晶質シリカ微粉粒子添加の効果を表
わすもので、１４５０℃の高温下では非晶質シリカ微粒
子の添加量が増す程、液相生成量が増大し、熱間曲げ強
度が大きく低下する。非晶質シリカ微粒子の配合量が３
％を越えると、液相生成量が急増するため、荷重軟化性
を示す図５に見られるように、荷重を解放しても軟化し
ゞけるようになり、高温加熱後、過度の収縮が起こるよ
うになる。FIG. 4 shows the effect of adding fine particles of amorphous silica on the hot bending strength of alumina-spinel-magnesia castables based on Comparative Example 7 of Table 4 at a high temperature of 1450 ° C. However, as the addition amount of the amorphous silica fine particles increases, the liquid phase production amount increases, and the hot bending strength largely decreases. Amount of amorphous silica particles is 3
%, The amount of liquid phase generated increases sharply, and as shown in FIG. 5 showing the load softening property, it becomes soft even when the load is released, and excessive shrinkage occurs after heating at high temperature. Like
【００１２】なお、図５に示す荷重軟化性のテストは、
後述する実施例６（非晶質シリカ微粒子配合量１．５
％）、比較例１（同０％）、比較例７（同４％）のアル
ミナ質不定形耐火物のそれぞれについて、１５００℃に
達するまで５℃／min の昇温速度で加熱し、１５００℃
に暫時持続させたのち加熱を停止する間、加熱を停止す
るまでは２ｋｇ／cm2 、加熱停止後は０．３ｋｇ／cm2
の載荷荷重を掛けてその間の線変化率％を測定した結果
である。The load softening test shown in FIG.
Example 6 described later (amorphous silica fine particle content of 1.5)
%), Comparative Example 1 (0%) and Comparative Example 7 (4%), and heated at a heating rate of 5 ° C./min until reaching 1500 ° C. and 1500 ° C., respectively.
2kg / cm 2 until the heating is stopped and 0.3kg / cm 2 after the heating is stopped.
Is the result of measuring the line change rate% during that time by applying the load.
【００１３】以上のように、非晶質シリカ微粒子を適量
配合することにより１４００℃以上の高温下において少
量の液相が生成され、適度の荷重軟化性を示すようにな
る。湯当たり部に用いた場合でも、適度な荷重軟化性に
よって周囲の材料の熱間膨脹によって受ける拘束圧を吸
収できるようになり、全面剥離を起こさなくなる。非晶
質シリカ微粒子の添加にはこのほか、機械的強度の向上
効果もある。特に６００〜１２００℃付近の温度域での
冷・熱間強度の向上効果が大きく、その結果として熱間
摩耗抵抗性も向上する。As described above, by mixing a proper amount of the amorphous silica fine particles, a small amount of liquid phase is produced at a high temperature of 1400 ° C. or higher, and a proper load softening property is exhibited. Even when it is used in the hot water contact part, it becomes possible to absorb the restraining pressure received by the hot expansion of the surrounding material due to the appropriate load softening property, and the whole surface peeling does not occur. In addition to this, the addition of the amorphous silica fine particles has the effect of improving the mechanical strength. In particular, the effect of improving the cold / hot strength in the temperature range around 600 to 1200 ° C. is great, and as a result, the resistance to hot abrasion is also improved.
【００１４】溶鋼の湯当たりによる機械的衝撃に耐える
には、全ゆる温度域で十分な強度を有していなければな
らず（因に受鋼直前のライニング材の温度は１０００℃
程度の与熱温度以下である）、また受鋼時の衝撃は内部
まで伝播されるため内部組織も強固でなければならな
い。非晶質シリカ微粒子の配合は、全ゆる温度域におけ
る組織強化をもたらし、熱間摩耗抵抗性の向上に寄与す
るが、０．３％以下の配合量では充分な機械的強度の向
上効果が得られない。In order to withstand the mechanical impact of molten steel hitting the molten steel, it must have sufficient strength in all temperature ranges (the temperature of the lining material immediately before steel receiving is 1000 ° C.).
The internal structure must be strong because the impact at the time of steel receiving is propagated to the inside. The compounding of amorphous silica fine particles brings about the strengthening of the structure in all temperature ranges and contributes to the improvement of the hot abrasion resistance. However, the compounding amount of 0.3% or less gives a sufficient effect of improving the mechanical strength. I can't.
【００１５】不定形耐火物に要求されることにはまた、
耐蝕性に優れていることが挙げられ、この点、高純度ア
ルミナ質不定形耐火物は溶鋼取鍋スラグや転炉スラグな
ど高塩基度スラグに対し、良好な耐蝕性を示すが、スラ
グが浸透し易い欠点を有している。非晶質シリカ微粒子
は、その添加量によってはアルミナ質不定形耐火物への
スラグの浸透を抑制する効果もある。図６は、非晶質シ
リカ微粒子を添加した高純度アルミナ質不定形耐火物構
造体を誘導炉内（１７００℃）に設置し、転炉スラグの
浸蝕度合についてテストした結果を示すもので、非晶質
シリカ微粒子を添加しないときの浸蝕指数を１００とし
てある。図から見られるように、非晶質シリカ微粒子を
２〜３％配合した場合には、スラグの浸透を抑制する効
果があり、結果として耐蝕性の向上効果が認られるが、
添加量が６％を越えると、耐蝕性の劣化が顕著となり好
ましくない。また、とくにＦe Ｏを多く含む高塩基度ス
ラグに対しては、スピネルやマグネシアの添加が耐蝕性
向上に有効である。スピネル系不定形耐火物の耐蝕性は
Ｍg Ｏ組成源がスピネル、マグネシアいづれであっても
Ｍg Ｏ組成に換算して６〜１２％程度の領域が最も優れ
ている（図７参照）。Ｍg Ｏ組成源が２％以下では耐蝕
性の効果が薄く、１５％を越えると、耐蝕性の劣化のみ
ならず、スラグの浸透が顕著に増大し、構造スポールの
原因となるため好ましくない。The requirements for amorphous refractories also include:
It is said that it has excellent corrosion resistance.In this respect, high purity alumina amorphous refractory shows good corrosion resistance to high basicity slag such as molten steel ladle slag and converter slag, but slag penetrates It has a drawback that it is easy to do. The amorphous silica fine particles also have the effect of suppressing the penetration of slag into the alumina amorphous refractory material depending on the amount added. FIG. 6 shows the results of testing a high-purity amorphous alumina refractory structure containing amorphous silica fine particles in an induction furnace (1700 ° C.) and testing the erosion degree of converter slag. The erosion index when the crystalline silica fine particles are not added is 100. As can be seen from the figure, when 2 to 3% of amorphous silica fine particles are blended, it has an effect of suppressing the penetration of slag, and as a result, an effect of improving corrosion resistance is recognized,
If the addition amount exceeds 6%, the corrosion resistance is significantly deteriorated, which is not preferable. Further, especially for high basicity slag containing a large amount of Fe 2 O 3, addition of spinel or magnesia is effective for improving the corrosion resistance. Corrosion resistance of spinel type amorphous refractory is best in the range of about 6 to 12% in terms of MgO composition, regardless of whether the MgO composition source is spinel or magnesia (see FIG. 7). If the MgO composition source is less than 2%, the effect of corrosion resistance is weak, and if it exceeds 15%, not only the corrosion resistance deteriorates but also the penetration of slag remarkably increases, which causes structural spalls, which is not preferable.
【００１６】図７は、換算Ｍg Ｏ組成源がないときの浸
蝕指数を１００とした換算Ｍg Ｏ組成の浸蝕指数を示す
もので、図６の非晶質シリカ微粒子と同様の方法によっ
て得られたものである。Ｍg Ｏ組成源を配合しない場合
及びＭg Ｏ組成源としてスピネルのみを配合した場合
は、１５００℃にて焼成した場合の残存収縮性を示す。
一般敷部の材料は一般に、残存膨脹性のものを用いてい
るため、湯当たり部用の材料のある程度の伸縮性は、周
囲の膨脹によって相殺されるが、過度の収縮は収縮亀裂
の原因となり、地金差しなどが懸念されるようになる。
この収縮を防止するにはマグネシアの微粉を２％以上配
合するとよいが、一方ではマグネシアとアルミナとの高
温下でのスピネル生成反応が大きな体積膨脹を伴うた
め、マグネシアを６％以上配合すると、過度の膨脹によ
る迫り出し及び剥離が問題となってきて好ましくない。
過度の膨脹を抑制しつゝマグネシアの増量を図るにはマ
グネシアの一部を粗粒化するとよい。FIG. 7 shows the erosion index of the converted MgO composition with the erosion index in the absence of the converted MgO composition source as 100, and was obtained by the same method as the amorphous silica fine particles of FIG. It is a thing. When the MgO composition source is not blended and when only spinel is blended as the MgO composition source, the residual shrinkage when fired at 1500 ° C. is exhibited.
Since the material of the general flooring material generally uses a residual expandable material, some stretchability of the material for the hot water contact part is offset by the expansion of the surroundings, but excessive shrinkage causes shrinkage cracks. , There is a concern about bullion insertion.
In order to prevent this shrinkage, it is advisable to add 2% or more of fine powder of magnesia, but on the other hand, since the spinel formation reaction between magnesia and alumina at high temperature causes a large volume expansion, if 6% or more of magnesia is added, it becomes excessive. The swelling and peeling due to the expansion of the resin becomes a problem, which is not preferable.
In order to suppress excessive expansion and increase the amount of magnesia, it is advisable to coarsen a part of magnesia.
【００１７】非晶質シリカ微粒子としては、例えば日本
アエロジル社製ＯＸ−５０などの気相法生成非晶質無水
シリカ、シオノギ社製カーブレックスなどの湿式法生成
非晶質含水シリカ等を用いることができ、このほかシリ
カフラワーなどの副製品、シリカゾル等を用いることが
できるが、シリカゾルをマグネシアと併用する場合に
は、ゲル化反応が急速に起こるため、混練から施工迄の
時間的制約を受ける。As the amorphous silica fine particles, for example, vapor-phase-method produced amorphous anhydrous silica such as OX-50 manufactured by Nippon Aerosil Co., Ltd., wet-process produced amorphous hydrous silica such as Curvex manufactured by Shionogi, etc. are used. In addition to this, by-products such as silica flour, silica sol, etc. can be used, but when silica sol is used in combination with magnesia, the gelation reaction occurs rapidly, so there is a time restriction from kneading to construction. ..
【００１８】珪石粉などの結晶質シリカ微粒子は、高温
下における荷重軟化性の付与には効果があるが、強度向
上効果は１２００℃以上のより高い温度でなければなら
ず、低い温度域では結晶の相転移により強度の低下をも
たらすため好ましくない。The crystalline silica fine particles such as silica stone powder have an effect of imparting load softening property at high temperature, but the strength improving effect must be at a higher temperature of 1200 ° C. or higher, and the crystal can be crystallized in a low temperature range. This is not preferable because it causes a decrease in strength due to the phase transition.
【００１９】[0019]
【００２０】[0020]
【実施例１】 非晶質シリカ微粒子１．０重量％、高ア
ルミナセメント２．０重量％、残部がアルミナからなる
不定形耐火物に水５．５重量％を加えて混練し、ブロッ
ク状に形成して乾燥させた不定形耐火物構造体につい
て、１０００℃及び１５００℃で焼成後の残存線変化、
１０００℃での圧縮強度、熱間摩耗量、荷重軟化性、誘
導炉浸蝕テスト結果及び実炉損耗速度を計測した。その
結果を表１に示す。Example 1 Amorphous refractory composed of 1.0% by weight of amorphous silica fine particles, 2.0% by weight of high-alumina cement, and the balance of alumina was added with 5.5% by weight of water and kneaded to form a block. The change in residual line after firing at 1000 ° C and 1500 ° C for the formed and dried amorphous refractory structure,
The compressive strength at 1000 ° C., the amount of hot wear, the load softening property, the induction furnace erosion test result, and the actual furnace wear rate were measured. The results are shown in Table 1.
【００２１】なお、熱間摩耗量の計測は次のようにして
行った。予め炉５内を１６００℃に加熱し、この中に不
定形耐火物構造体である供試体６をセットし、バーナー
７で加熱した（図８）。そして供試体表面温度が１６０
０℃になってから２０分間保持したのちバーナー７を素
早く抜取り、サンドブラストノズル８をセットして粒径
５〜３mm、重さ４．６００ｇの電融アルミナ粒子９を供
試体６に叩き付けた（図９）。その後、炉５より取出し
た供試体６を最損耗箇所で切断し、損耗した断面積cm2
を求めた。The amount of hot wear was measured as follows. The inside of the furnace 5 was heated to 1600 ° C. in advance, the specimen 6 which was an amorphous refractory structure was set in the furnace, and it was heated by the burner 7 (FIG. 8). And the surface temperature of the specimen is 160
After holding the temperature for 20 minutes at 0 ° C., the burner 7 was quickly removed, the sandblast nozzle 8 was set, and the fused alumina particles 9 having a particle diameter of 5 to 3 mm and a weight of 4.600 g were struck on the specimen 6 (FIG. 9). After that, the specimen 6 taken out of the furnace 5 was cut at the most worn portion, and the worn cross-sectional area cm 2
I asked.
【００２２】[0022]
【実施例２】 高アルミナセメント２．０重量％、非晶
質シリカ微粒子２．０重量％、残部がアルミナからなる
材料に水を５．３重量％加えて不定形耐火物構造体を
得、実施例１と同様な各種テストを行った。その結果を
表１に示す。Example 2 Water was added to a material containing 2.0% by weight of high-alumina cement, 2.0% by weight of amorphous silica fine particles, and the balance being alumina to obtain 5.3% by weight of water to obtain an amorphous refractory structure. Various tests similar to those in Example 1 were conducted. The results are shown in Table 1.
【００２３】[0023]
【実施例３】 高アルミナセメント２．０重量％、非非
晶質シリカ微粒子４．０重量％、残部がアルミナからな
る材料に水を５．０重量％加えて不定形耐火物構造体を
得、実施例１と同様な各種テストを行った。その結果を
表１に示す。Example 3 Amorphous refractory structure was obtained by adding 5.0% by weight of water to a material containing 2.0% by weight of high alumina cement, 4.0% by weight of non-amorphous silica fine particles and the balance being alumina. Various tests similar to those in Example 1 were performed. The results are shown in Table 1.
【００２４】[0024]
【実施例４】 非晶質シリカ微粒子を２．０重量％、高
アルミナセメントを４．０重量％とし、水の添加量を
５．６重量％とする以外は実施例３と同様にして不定形
耐火物構造体を得て、実施例３と同様な各種テストを行
った。その結果を表１に示す。Example 4 The procedure of Example 3 was repeated except that the amorphous silica fine particles were 2.0% by weight, the high alumina cement was 4.0% by weight, and the amount of water added was 5.6% by weight. A standard refractory structure was obtained and various tests similar to those in Example 3 were performed. The results are shown in Table 1.
【００２５】[0025]
【実施例５】 粒径０．０７４mm以下のスピネル２５重
量％、非晶質シリカ微粒子０．５重量％、高アルミナセ
メント４．０重量％、残部がアルミナからなる不定形耐
火物に水５．８重量％を加えて実施例１と同様にして不
定形耐火物構造体を得、実施例１と同様な各種テストを
行った。その結果を表１に示す。Example 5 25% by weight of spinel having a particle size of 0.074 mm or less, 0.5% by weight of amorphous silica fine particles, 4.0% by weight of high-alumina cement, and the balance of alumina was water. An amorphous refractory structure was obtained in the same manner as in Example 1 by adding 8% by weight, and various tests similar to those in Example 1 were conducted. The results are shown in Table 1.
【００２６】[0026]
【実施例６】 粒径０．０７４mm以下のスピネル２０重
量％、粒径０．０７４mm以下のマグネシア３．０重量
％、非晶質シリカ微粒子１．５重量％、高アルミナセメ
ント２．０重量％、残部がアルミナからなる不定形耐火
物に水５．６重量％を加えて実施例１と同様にして不定
形耐火物構造体を得、実施例１と同様な各種テストを行
った。その結果を表２に示す。Example 6 20% by weight of spinel having a particle size of 0.074 mm or less, 3.0% by weight of magnesia having a particle size of 0.074 mm or less, 1.5% by weight of amorphous silica fine particles, 2.0% by weight of high alumina cement. An amorphous refractory structure was obtained in the same manner as in Example 1 except that 5.6% by weight of water was added to the amorphous refractory having the balance being alumina, and various tests similar to those in Example 1 were conducted. The results are shown in Table 2.
【００２７】[0027]
【実施例７】 粒径０．０７４mm以下のスピネル２０重
量％、粒径０．０７４mm以下のマグネシア３．０重量
％、非晶質シリカ微粒子３．０重量％、高アルミナセメ
ント２．０重量％、残部がアルミナからなる材料に水
５．３重量％を加えて不定形耐火物構造体を得、実施例
１と同様な各種テストを行った。その結果を表２に示
す。Example 7 20% by weight of spinel having a particle size of 0.074 mm or less, 3.0% by weight of magnesia having a particle size of 0.074 mm or less, 3.0% by weight of amorphous silica fine particles, 2.0% by weight of high alumina cement Then, 5.3% by weight of water was added to a material whose balance was alumina to obtain an amorphous refractory structure, and various tests similar to those in Example 1 were conducted. The results are shown in Table 2.
【実施例８】 粒径０．０７４mm以下のスピネル２０重
量％、粒径３〜０．０７４mmのマグネシア４．０重量
％、粒径０．０７４mm以下のマグネシア３．０重量％、
非晶質シリカ微粒子１．５重量％、高アルミナセメント
２．０重量％、残部がアルミナからなる材料に水５．６
重量％を加えて不定形耐火物構造体を得、実施例１と同
様な各種テストを行った。その結果を表２に示す。Example 8 20% by weight of spinel having a particle size of 0.074 mm or less, 4.0% by weight of magnesia having a particle size of 3 to 0.074 mm, 3.0% by weight of magnesia having a particle size of 0.074 mm or less,
1.5% by weight of amorphous silica fine particles, 2.0% by weight of high-alumina cement, the balance consisting of alumina is water 5.6.
The amorphous refractory structure was obtained by adding wt%, and various tests similar to those in Example 1 were performed. The results are shown in Table 2.
【実施例９】 粒径０．０７４mm以下のスピネル２０重
量％、粒径０．０７４mm以下のマグネシア３．０重量
％、非晶質シリカ微粒子１．５重量％、高アルミナセメ
ント２．０重量％、残部がアルミナからなる不定形耐火
物に水５．６重量％を加えて実施例１と同様にして不定
形耐火物構造体を得、実施例１と同様な各種テストを行
った。その結果を表２に示す。[Example 9] Spinel having a particle size of 0.074 mm or less 20% by weight, magnesia having a particle size of 0.074 mm or less 3.0% by weight, amorphous silica fine particles 1.5% by weight, high alumina cement 2.0% by weight An amorphous refractory structure was obtained in the same manner as in Example 1 except that 5.6% by weight of water was added to the amorphous refractory having the balance being alumina, and various tests similar to those in Example 1 were conducted. The results are shown in Table 2.
【００２８】[0028]
【比較例１】 高アルミナセメントを２．０重量％、残
部をアルミナとする不定形耐火物に水６．１重量％を加
え、混練して得たブロック状の不定形耐火物構造体につ
いて、上述の各種テストを行った。結果を表２に示す。
この例では、非晶質シリカ微粒子が無添加のため強度が
低いうえ、荷重軟化性が小さく、しかも熱間摩耗量も大
であった。Comparative Example 1 A block-shaped amorphous refractory structure obtained by adding 6.1% by weight of water to an amorphous refractory containing 2.0% by weight of high-alumina cement and the balance alumina, and kneading the mixture. The various tests described above were performed. The results are shown in Table 2.
In this example, since the amorphous silica fine particles were not added, the strength was low, the load softening property was small, and the hot wear amount was large.
【００２９】[0029]
【比較例２】 非晶質シリカ微粒子６．０重量％、高ア
ルミナセメント２．０重量％残部がアルミナよりなる材
料に水を４．９重量％加え混練して得たブロック状の不
定形耐火物構造体について、前記した各種テストを行っ
た。結果を表３に示す。この例では、非晶質シリカ微粒
子が６．０重量％と過剰のため耐蝕性の劣化が著しく、
１５００°Ｃ焼成後の残存収縮が大きく、かつ荷重軟化
性も小さい。Comparative Example 2 Amorphous silica fine particles 6.0% by weight, high-alumina cement 2.0% by weight A block-shaped amorphous fireproof obtained by kneading 4.9% by weight of water with a material consisting of the balance alumina. The various tests described above were performed on the object structure. The results are shown in Table 3. In this example, the amorphous silica fine particles are in excess of 6.0% by weight, so that the corrosion resistance is significantly deteriorated,
The residual shrinkage after firing at 1500 ° C is large and the softening property under load is small.
【００３０】[0030]
【比較例３】 非晶質シリカ微粒子１．０重量％、高ア
ルミナセメント５．０重量％残部がアルミナよりなる材
料に水を６．１重量％加え混練して得たブロック状の不
定形耐火物構造体について、前記した各種テストを行っ
た。結果を表３に示す。この例では、高アルミナセメン
ト量が過剰なため耐蝕性の劣化が著しい。Comparative Example 3 Amorphous silica fine particles 1.0% by weight, high-alumina cement 5.0% by weight Block-shaped amorphous fireproof obtained by kneading by adding 6.1% by weight of water to a material whose balance is alumina. The various tests described above were performed on the object structure. The results are shown in Table 3. In this example, since the amount of high alumina cement is excessive, the corrosion resistance is significantly deteriorated.
【００３１】[0031]
【比較例４】 スピネル２０重量％、高アルミナセメン
ト２．０重量％、残部がアルミナからなる材料に水６．
１重量％を加え、実施例１と同様にして不定形耐火物構
造体を得、上述と同じテストを行った。結果を表３に示
す。この例では、非晶質シリカ微粒子無添加のため強度
が低く、荷重軟化性が小さく、かつ熱間摩耗量も大であ
る。COMPARATIVE EXAMPLE 4 Spinel 20% by weight, high alumina cement 2.0% by weight, the balance consisting of alumina was mixed with water 6.
1% by weight was added to obtain an amorphous refractory structure in the same manner as in Example 1, and the same test as described above was performed. The results are shown in Table 3. In this example, since the amorphous silica fine particles are not added, the strength is low, the load softening property is small, and the hot wear amount is large.
【００３２】[0032]
【比較例５】 粒径０．０７４ｍｍ以下のスピネル２０
重量％、粒径０．０７４ｍｍ以下のマグネシア３．０重
量％、高アルミナセメント２．０重量％、残部がアルミ
ナよりなる材料に、水を６．２重量％加え混練して得た
ブロック状の不定形耐火物構造体について、前記した各
種テストを行った。結果を表３に示す。この例では、非
晶質シリカ微粒子無添加のため強度が低く、荷重軟化性
が小さいうえ、熱間摩耗量も大である。これを実炉に供
したところ損耗速度が大きいうえ全面剥離が生じた。Comparative Example 5 Spinel 20 having a particle size of 0.074 mm or less
% Of magnesia having a particle size of 0.074 mm or less, 2.0% by weight of high-alumina cement, and the balance of alumina, and 6.2% by weight of water. The above-mentioned various tests were conducted on the amorphous refractory structure. The results are shown in Table 3. In this example, since the amorphous silica fine particles are not added, the strength is low, the load softening property is small, and the hot wear amount is large. When this was put into an actual furnace, the wear rate was high and the entire surface was peeled off.
【００３３】[0033]
【比較例６】 スティールファイバーを３．０重量％添
加し、水の添加量を６．５重量％とする以外は比較例５
と同様にして不定形耐火物構造体を得て上述と同じテス
トを行った。結果を表３に示す。この例では、スティー
ルファイバー添加により荷重軟化性は改善されて適度に
大きくなるが、耐蝕性や熱間摩耗量が著しく増大する。Comparative Example 6 Comparative Example 5 except that 3.0% by weight of steel fiber was added and the amount of water added was 6.5% by weight.
An amorphous refractory structure was obtained in the same manner as above and the same test as described above was performed. The results are shown in Table 3. In this example, the addition of steel fiber improves the load softening property and increases it moderately, but the corrosion resistance and the amount of hot wear remarkably increase.
【００３４】[0034]
【比較例７】 粒径０．０７４ｍｍ以下のスピネル２０
重量％、粒径０．０７４ｍｍ以下のマグネシア３．０重
量％、非晶質シリカ微粒子４．０重量％、高アルミナセ
メント２．０重量％、残部がアルミナよりなる材料に、
水を５．１重量％加え混練して得たブロック状の不定形
耐火物構造体について、前記した各種テストを行った。
結果を表４に示す。この例では、非晶質シリカ微粒子が
４．０重量％と過剰添加となり、高温下での液相生成量
の増大に伴い荷重軟化性が過度なものとなっている。し
かも１５００°Ｃでの収縮量も大きい。Comparative Example 7 Spinel 20 having a particle size of 0.074 mm or less
% By weight, 3.0% by weight of magnesia having a particle size of 0.074 mm or less, 4.0% by weight of amorphous silica fine particles, 2.0% by weight of high-alumina cement, and the balance being alumina.
The above-mentioned various tests were performed on the block-shaped amorphous refractory structure obtained by adding 5.1% by weight of water and kneading.
The results are shown in Table 4. In this example, the amorphous silica fine particles were added in an excessive amount of 4.0% by weight, and the load softening property became excessive as the amount of liquid phase produced increased at high temperature. Moreover, the amount of shrinkage at 1500 ° C is also large.
【００３５】[0035]
【比較例８】 スピネル２５重量％、高アルミナセメン
ト７．０重量％、残部がアルミナからなる不定形耐火物
に水６．４％を加え、実施例１と同様にして不定形耐火
物構造体を得て上述と同じテストを行った。結果を表４
に示す。この例では、非晶質シリカ微粒子無添加のため
荷重軟化性が小さい。これを実炉に供したところ全面剥
離を生じた。[Comparative Example 8] An amorphous refractory structure was prepared in the same manner as in Example 1 except that 6.4% of water was added to an amorphous refractory consisting of spinel 25% by weight, high alumina cement 7.0% by weight, and the balance being alumina. Then, the same test as described above was performed. The results are shown in Table 4.
Shown in. In this example, since the amorphous silica fine particles are not added, the softening property under load is small. When this was put into an actual furnace, the entire surface was peeled off.
【００３６】[0036]
【比較例９】 粒径０．０７４ｍｍ以下のスピネル２５
重量％、非晶質シリカ微粒子０．５重量％、高アルミナ
セメント７．０重量％、残部がアルミナよりなる材料
に、水を６．３重量％加え混練して得たブロック状の不
定形耐火物構造体について、前記の各種テストを行っ
た。結果を表４に示す。この例では、アルミナセメント
が過剰に含まれているため、非晶質シリカ微粒子を添加
すると、荷重軟化性は大きくなるが、１５００°Ｃでの
残存膨張量が著しく増大するため迫り出し剥離が発生し
やすくなる。Comparative Example 9 Spinel 25 with a particle size of 0.074 mm or less
Wt%, amorphous silica fine particles 0.5 wt%, high-alumina cement 7.0 wt%, balance 6.3 wt% to a material consisting of alumina, and block-shaped amorphous fire resistance obtained by kneading The various tests described above were performed on the object structure. The results are shown in Table 4. In this example, since the alumina cement is excessively contained, the addition of the amorphous silica fine particles increases the load softening property, but the residual expansion amount at 1500 ° C remarkably increases, so that the exfoliation occurs. Easier to do.
【００３７】[0037]
【比較例１０】 粒径０．０７４ｍｍ以下のスピネル１
０重量％、粒径０．０７４ｍｍ以下のマグネシア７．０
重量％、非晶質シリカ微粒子１．５重量％、高アルミナ
セメント２．０重量％、残部がアルミナよりなる材料
に、水を５．７重量％加え混練して得たブロック状の不
定形耐火物構造体について、前記した各種テストを行っ
た。結果を表４に示す。この例では、マグネシア微粉の
添加量が多いため、１５００°Ｃでの残存膨張量が著し
く増大するため迫り出しや、剥離が発生しやすくなる。Comparative Example 10 Spinel 1 having a particle size of 0.074 mm or less
Magnesia 7.0 with 0% by weight and a particle size of 0.074 mm or less
Wt%, amorphous silica fine particles 1.5 wt%, high-alumina cement 2.0 wt%, the balance consisting of alumina, and 5.7 wt% of water and kneaded to obtain block-shaped amorphous fire resistance The various tests described above were performed on the object structure. The results are shown in Table 4. In this example, since the magnesia fine powder is added in a large amount, the residual expansion amount at 1500 ° C. remarkably increases, so that the protrusion and the peeling are likely to occur.
【００３８】[0038]
【比較例１１】 スピネル２７．５重量％、粒径３〜
０．０７４ｍｍのマグネシア１０重量％、粒径０．０７
４ｍｍ以下のマグネシア２．０重量％、非晶質シリカ微
粒子１．５重量％、高アルミナセメント２．０重量％、
残部がアルミナからなる不定形耐火物に水５．７％を加
えて実施例１と同様にして不定形耐火物構造体を得て上
述と同じテストを行った。結果を表４に示す。Comparative Example 11 Spinel 27.5% by weight, particle size 3 to
0.074 mm magnesia 10% by weight, particle size 0.07
2.0% by weight of magnesia of 4 mm or less, 1.5% by weight of amorphous silica fine particles, 2.0% by weight of high alumina cement,
Water 5.7% was added to an amorphous refractory having the balance being alumina, and an irregular refractory structure was obtained in the same manner as in Example 1, and the same test as above was conducted. The results are shown in Table 4.
【００３９】この例では、ＭｇＯ含有量が過多のため、
スラグの浸透量が非常に多く、構造スポールを起こし易
い。In this example, since the MgO content is excessive,
The penetration amount of slag is so large that structural spalls easily occur.
【００４０】以上述べた各実施の例不定形耐火物構造体
によれば、いずれも耐蝕性が良好で、熱間摩耗量も少な
く、１４００°Ｃ以上の高温下で過度の荷重軟化性を示
す。特に実施例１及び実施例９を実炉に供したところ、
全面剥離することもなく、損耗速度が大幅に向上した。
上記実施例により得られた材料は、以下の比較例に示し
た材料のみならず、従来使用していたＡｌ2 Ｏ3 −Ｍｇ
Ｏ−Ｃ質（実炉損耗速度３．８ｍｍ／ｃｈ）と比較して
も倍以上の優れた耐用を示した。なおこの材料は湯当た
り部用として用いるのに適するが、実施例５や実施例６
のように適度の残存膨張性を備えたものは、各種鍋の一
般敷部や側壁にも適用可能である。According to the irregular refractory structures of the respective examples described above, all of them have good corrosion resistance and a small amount of hot wear, and exhibit excessive softening under load at a temperature of 1400 ° C. or higher. .. In particular, when Example 1 and Example 9 were subjected to an actual furnace,
The wear rate was greatly improved without peeling off the entire surface.
The materials obtained by the above examples are not only the materials shown in the following comparative examples, but also Al 2 O 3 --Mg which has been conventionally used.
Even when compared with the O-C quality (real furnace wear rate 3.8 mm / ch), it showed more than double the excellent durability. Although this material is suitable for use as a hot water contact part,
Those having a suitable residual expansivity as described above can be applied to general floors and side walls of various pots.
【００４１】[0041]
【発明の効果】本発明の不定形耐火物は以上のように、
１４００℃以上の高温下で適度な荷重軟化性を示すこと
により湯当たり部に用いた場合、その周囲に施工された
材料の熱間膨脹によって受ける拘束圧を吸収することが
できるため、迫り出しや剥離が生じにくゝなり、しかも
熱間摩耗抵抗性に優れるため、湯当たり部として用いた
場合に局部摩耗が抑制され、耐用を大幅に向上させるこ
とができる。As described above, the amorphous refractory material of the present invention has
When it is used in the hot water contact part by exhibiting an appropriate load softening property at a high temperature of 1400 ° C or higher, it can absorb the binding pressure received by the hot expansion of the material constructed around it, so that it can be pushed out. Since peeling is less likely to occur and the hot-wear resistance is excellent, local wear is suppressed when used as a hot water contact part, and durability can be greatly improved.
【００４２】Ｍg Ｏ組成源を配合しない不定形耐火物に
添加されるシリカ微粒子は２〜３重量％にすれば、耐蝕
性を向上させることができる。Ｍg Ｏ組成源を配合した
不定形耐火物においては、Ｍg Ｏ組成源を６〜１２重量
％にした場合、耐蝕性に最も優れ、またマグネシアを２
〜６重量％配合すると過度の収縮を防止することができ
る。Corrosion resistance can be improved if the silica fine particles added to the amorphous refractory containing no MgO composition source is 2 to 3% by weight. In the case of the amorphous refractory containing the MgO composition source, when the MgO composition source is 6 to 12% by weight, the corrosion resistance is the best and the magnesia content is 2%.
When it is mixed in an amount of ˜6% by weight, excessive shrinkage can be prevented.
【図１】 溶鋼取鍋の断面図。FIG. 1 is a sectional view of a molten steel ladle.
【図２】 湯当たり部が全面剥離した状態を示す図。FIG. 2 is a view showing a state in which a hot water contact portion is entirely peeled off.
【図３】 アルミナ質キャスタブルにおける非晶質シリ
カ微粒子の添加量と熱間曲げ強度の関係を示すグラフ。FIG. 3 is a graph showing the relationship between the addition amount of amorphous silica fine particles in alumina castable and hot bending strength.
【図４】 アルミナースピネルーマグネシア質キャスタ
ブルにおける非晶質シリカ微粒子の添加量と、熱間曲げ
強度の関係を示すグラフ。FIG. 4 is a graph showing the relationship between the amount of amorphous silica fine particles added to alumina-spinel-magnesia castables and hot bending strength.
【図５】 荷重軟化テスト結果を示すグラフ。FIG. 5 is a graph showing the results of a load softening test.
【図６】 非晶質シリカ微粒子の添加量と浸蝕指数を示
すグラフ。FIG. 6 is a graph showing the addition amount of amorphous silica fine particles and the erosion index.
【図７】 換算Ｍg Ｏ組成と浸蝕指数の関係を示すグラ
フ。FIG. 7 is a graph showing the relationship between the converted Mg 2 O composition and the erosion index.
【図８】 熱間摩耗テストに用いる炉体をセットした状
態を示す断面図。FIG. 8 is a sectional view showing a state in which a furnace body used for a hot wear test is set.
【図９】 同テストにおいて電融アルミナ粒子を叩き付
けるときの状態を示す図。FIG. 9 is a view showing a state in which the fused alumina particles are struck in the same test.
１・・・湯当たり部 ２・・・一
般敷部ライニング ５・・・炉 ６・・・供
試体 ７・・・バーナ ８・・・サ
ンドブラストノズル ９・・・電融アルミナ粒子1 ... Hot water contact area 2 ... General floor lining 5 ... Furnace 6 ... Specimen 7 ... Burner 8 ... Sandblast nozzle 9 ... Electrofused alumina particles
【表１】 [Table 1]
【表２】 [Table 2]
【表３】 [Table 3]
【表４】 注 荷重軟化性の判定基準は、図５において１５００℃での
載荷荷重を２kg／cm2 から０．３kg／cm2 に減らしても
収縮を続けるものを特大、載荷荷重を軽減すると、収縮
しなくなるものを大、１５００℃に保っても軟化を示さ
ないものを小とした。実炉損耗速度において、（ ）内
の数値は全面剥離を起こす前までの損耗速度を示す。[Table 4] Note: The criterion for load softening is that the shrinkage is oversized when the load at 1500 ° C in Fig. 5 is reduced from 2kg / cm 2 to 0.3kg / cm 2 , and it does not shrink when the load is reduced. The large ones were designated as small, and those not showing softening even at 1500 ° C. were designated as small. In the actual furnace wear rate, the values in parentheses indicate the wear rate before the entire surface is peeled off.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 西川 千春 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 大場 遵 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 ─────────────────────────────────────────────────── --- Continuation of the front page (72) Inventor Chiharu Nishikawa 1-1, Makiyama Shinmachi, Tobata-ku, Kitakyushu, Fukuoka Daiko Furnace Co., Ltd. No. 1 Daiko Furnace Material Co., Ltd.
Claims (6)
％、高アルミナセメントが０．５〜４重量％、残部がア
ルミナからなる鍋用不定形耐火物。1. An amorphous refractory for a pot, which comprises 0.3 to 5% by weight of amorphous silica fine particles, 0.5 to 4% by weight of high alumina cement, and the balance being alumina.
る請求項１記載の鍋用不定形耐火物。2. The amorphous refractory material for a pot according to claim 1, wherein the amorphous silica fine particles are 2 to 3% by weight.
％、高アルミナセメントが０．５〜４重量％、スピネル
若しくはマグネシアがＭg Ｏ組成に換算して２〜１５重
量％、残部がアルミナからなる鍋用不定形耐火物。3. Amorphous silica fine particles are 0.3 to 3% by weight, high alumina cement is 0.5 to 4% by weight, spinel or magnesia is 2 to 15% by weight in terms of MgO composition, and the balance is Amorphous refractory made of alumina for pots.
成に換算して６〜１２重量％である請求項３記載の鍋用
不定形耐火物。4. The amorphous refractory for a pot according to claim 3, wherein the spinel or magnesia is 6 to 12% by weight in terms of MgO composition.
３記載の鍋用不定形耐火物。5. The amorphous refractory material for a pot according to claim 3, wherein the magnesia content is 2 to 6% by weight.
項５のいづれかの請求項に記載の鍋用不定形耐火物。6. The irregular refractory material for a pot according to claim 1, which is used in a hot water contact part.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3316557A JP2769400B2 (en) | 1991-11-29 | 1991-11-29 | Irregular refractories for hot metal parts |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3316557A JP2769400B2 (en) | 1991-11-29 | 1991-11-29 | Irregular refractories for hot metal parts |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05185202A true JPH05185202A (en) | 1993-07-27 |
| JP2769400B2 JP2769400B2 (en) | 1998-06-25 |
Family
ID=18078428
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3316557A Expired - Fee Related JP2769400B2 (en) | 1991-11-29 | 1991-11-29 | Irregular refractories for hot metal parts |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2769400B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5972102A (en) * | 1996-10-29 | 1999-10-26 | North American Refractories Co. | Hydraulically-bonded monolithic refractories containing a calcium oxide-free binder comprised of a hydratable alumina source and magnesium oxide |
| JP2015166290A (en) * | 2014-03-03 | 2015-09-24 | 黒崎播磨株式会社 | Monolithic refractory for tundish lining |
| JP2018177570A (en) * | 2017-04-10 | 2018-11-15 | 新日鐵住金株式会社 | Anchor brick |
| JP2020059613A (en) * | 2018-10-04 | 2020-04-16 | 日本製鉄株式会社 | Method for evaluating peeling resistance of alumina-magnesia quality castable refractory |
| JP2020059612A (en) * | 2018-10-04 | 2020-04-16 | 日本製鉄株式会社 | Method for evaluating peeling resistance of alumina-magnesia quality castable refractory |
| JP2021513498A (en) * | 2018-02-09 | 2021-05-27 | ベスビウス ユーエスエー コーポレイション | Refractory composition and oxidation-resistant barrier layer formed during use |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52123306A (en) * | 1976-04-09 | 1977-10-17 | Nippon Steel Corp | Repairing method for refractory lining of fireproof vessel |
| JPS5496506A (en) * | 1978-01-17 | 1979-07-31 | Nippon Steel Corp | End overlapping repair using nonshaped refractory |
| JPH02274371A (en) * | 1989-04-17 | 1990-11-08 | Nippon Steel Corp | Structure of bedding part of ladle for receiving molten metal |
| JPH0323275A (en) * | 1989-06-17 | 1991-01-31 | Kurosaki Refract Co Ltd | Monolithic refractory for casting |
-
1991
- 1991-11-29 JP JP3316557A patent/JP2769400B2/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52123306A (en) * | 1976-04-09 | 1977-10-17 | Nippon Steel Corp | Repairing method for refractory lining of fireproof vessel |
| JPS5496506A (en) * | 1978-01-17 | 1979-07-31 | Nippon Steel Corp | End overlapping repair using nonshaped refractory |
| JPH02274371A (en) * | 1989-04-17 | 1990-11-08 | Nippon Steel Corp | Structure of bedding part of ladle for receiving molten metal |
| JPH0323275A (en) * | 1989-06-17 | 1991-01-31 | Kurosaki Refract Co Ltd | Monolithic refractory for casting |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5972102A (en) * | 1996-10-29 | 1999-10-26 | North American Refractories Co. | Hydraulically-bonded monolithic refractories containing a calcium oxide-free binder comprised of a hydratable alumina source and magnesium oxide |
| JP2015166290A (en) * | 2014-03-03 | 2015-09-24 | 黒崎播磨株式会社 | Monolithic refractory for tundish lining |
| JP2018177570A (en) * | 2017-04-10 | 2018-11-15 | 新日鐵住金株式会社 | Anchor brick |
| JP2021513498A (en) * | 2018-02-09 | 2021-05-27 | ベスビウス ユーエスエー コーポレイション | Refractory composition and oxidation-resistant barrier layer formed during use |
| US11746053B2 (en) | 2018-02-09 | 2023-09-05 | Vesuvius Usa Corporation | Refractory compositions and in situ anti-oxidation barrier layers |
| JP2020059613A (en) * | 2018-10-04 | 2020-04-16 | 日本製鉄株式会社 | Method for evaluating peeling resistance of alumina-magnesia quality castable refractory |
| JP2020059612A (en) * | 2018-10-04 | 2020-04-16 | 日本製鉄株式会社 | Method for evaluating peeling resistance of alumina-magnesia quality castable refractory |
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| Publication number | Publication date |
|---|---|
| JP2769400B2 (en) | 1998-06-25 |
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