JPS62246858A - Magnesia calcta base burnt refractories - Google Patents
Magnesia calcta base burnt refractoriesInfo
- Publication number
- JPS62246858A JPS62246858A JP61091449A JP9144986A JPS62246858A JP S62246858 A JPS62246858 A JP S62246858A JP 61091449 A JP61091449 A JP 61091449A JP 9144986 A JP9144986 A JP 9144986A JP S62246858 A JPS62246858 A JP S62246858A
- Authority
- JP
- Japan
- Prior art keywords
- cao
- clinker
- mgo
- refractories
- refractory
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000011819 refractory material Substances 0.000 title description 26
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 title 2
- 239000000395 magnesium oxide Substances 0.000 title 1
- 239000000292 calcium oxide Substances 0.000 claims description 61
- ODINCKMPIJJUCX-UHFFFAOYSA-N Calcium oxide Chemical compound [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 claims description 35
- 239000013078 crystal Substances 0.000 claims description 24
- 239000011159 matrix material Substances 0.000 claims description 4
- 235000012255 calcium oxide Nutrition 0.000 description 32
- 238000004901 spalling Methods 0.000 description 15
- 238000005260 corrosion Methods 0.000 description 13
- 239000002245 particle Substances 0.000 description 13
- 230000007797 corrosion Effects 0.000 description 12
- 239000002893 slag Substances 0.000 description 9
- 238000010304 firing Methods 0.000 description 7
- 239000011230 binding agent Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000029087 digestion Effects 0.000 description 4
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 4
- 238000002156 mixing Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 229910000514 dolomite Inorganic materials 0.000 description 3
- 239000010459 dolomite Substances 0.000 description 3
- 238000003723 Smelting Methods 0.000 description 2
- 210000001015 abdomen Anatomy 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 230000035515 penetration Effects 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- -1 polypropylene, isocyanate Polymers 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910017344 Fe2 O3 Inorganic materials 0.000 description 1
- 239000004743 Polypropylene Substances 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 102000006463 Talin Human genes 0.000 description 1
- 108010083809 Talin Proteins 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 239000011575 calcium Substances 0.000 description 1
- WETINTNJFLGREW-UHFFFAOYSA-N calcium;iron;tetrahydrate Chemical compound O.O.O.O.[Ca].[Fe].[Fe] WETINTNJFLGREW-UHFFFAOYSA-N 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000011362 coarse particle Substances 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000008240 homogeneous mixture Substances 0.000 description 1
- 238000013003 hot bending Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000012948 isocyanate Substances 0.000 description 1
- 150000002513 isocyanates Chemical class 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 230000000149 penetrating effect Effects 0.000 description 1
- 239000005011 phenolic resin Substances 0.000 description 1
- 229920001155 polypropylene Polymers 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000000644 propagated effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 239000011271 tar pitch Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】
従来の技術及びその問題点
マグネシア−ドロマイト系耐火物は、精錬炉用、特に転
炉用の内張り材として従来より使用されてきた。しかし
ながら近年操業条件が苛酷化し、特に鋼の清浄化の要求
が高まるとともに、従来のマグネシア−ドロマイト系耐
火物よりも優れた耐食性を有する耐大物の開発が望まれ
てきた。この様な状況下に、ドロマイトクリンカ−中の
Ｃａ Ｑの耐食効果を充分に発揮させ、且つ低フラック
ス化を目的として、カルシアクリンカ−を配合したマグ
ネシア−カルシア系耐火物が提案されている（特公昭５
９−１３４６９号及び特開昭５８−７４５６４号）。こ
れらの耐火物は、いずれもＭＱＯに微細化したＣａＯを
添加したものであり、夫々使用条件に応じある程度の構
造スポーリング防止効果をあげている。即ち、ＭｑＯに
Ｃａｏを微細均質に添加することによって、ＭｇＯに耐
熱スポーリング性が付与される。またＣａＯがスラグを
高融点化することによって、耐火物内へのスラグの浸透
が防止される。DETAILED DESCRIPTION OF THE INVENTION Prior Art and its Problems Magnesia-dolomite refractories have traditionally been used as lining materials for smelting furnaces, particularly converters. However, in recent years, operating conditions have become more severe, and as demands for cleaning steel in particular have increased, there has been a desire to develop large-sized refractories with superior corrosion resistance than conventional magnesia-dolomite refractories. Under these circumstances, magnesia-calcia-based refractories containing calcia clinker have been proposed in order to fully demonstrate the anti-corrosion effect of Ca Q in dolomite clinker and to reduce flux. Kosho 5
No. 9-13469 and JP-A-58-74564). All of these refractories are made by adding fine CaO to MQO, and each has a certain degree of structural spalling prevention effect depending on the usage conditions. That is, by adding Cao finely and homogeneously to MqO, heat spalling resistance is imparted to MgO. Further, CaO increases the melting point of the slag, thereby preventing the slag from penetrating into the refractory.
しかしながら、単にＭｇＯに微細化したＣａＯを添加す
るだけでは、以下の如き種々の問題点が生じ好ましくな
い。However, simply adding finely divided CaO to MgO causes various problems as described below, which is not preferable.
１ ）ＣａＯ粒度が微細化すると、耐消化性が低下し、
それに伴い耐火物組織が脆弱化し、熱間特性、特に耐食
性が低下する。また耐スポーリング性も不充分となる。1) When the CaO particle size becomes finer, the digestion resistance decreases,
As a result, the refractory structure becomes brittle, and hot properties, especially corrosion resistance, deteriorate. Furthermore, the spalling resistance is also insufficient.
２）ＣａＯの使用量が増加すると、ＣａＯが含有するＦ
ｅ２Ｏ３、Ｓ ｉｏ２、Ａ＋！２０３ ’４（７）不純
物（Ｎｕｘ）によって、焼成中及び内張り材として炉内
で使用中に、耐火物が過焼結を起し、耐スポーリング性
も低下する。2) When the amount of CaO used increases, the amount of F contained in CaO increases.
e2O3, S io2, A+! 203'4(7) Impurities (Nux) cause oversintering of the refractory during firing and during use in the furnace as a lining material, and the spalling resistance is also reduced.
３） ＣａＯをいくら微細化しても、耐火物中にはＭ
＜ｈｏ−ＭｇＯの網目構造が存在する。このため加熱時
に、ＭｇＯの膨張の内部吸収が不充分となって、構造体
としてのれんが組みの迫り合い応力が発生し、耐火物が
剥落する。3) No matter how fine the CaO is, there is M in the refractory.
<ho-MgO network structure exists. Therefore, during heating, internal absorption of the expansion of MgO becomes insufficient, and stress is generated in the brickwork as a structure, causing the refractory to peel off.
問題点を解決するための手段
本発明者は、上記問題点に鑑み鋭意研究を重ねた結果、
耐火物材料としである特定の大きさの亀裂を右するＭｑ
Ｏ−ＣａＯクリンカーを使用ザることによって、耐構造
スポーリング性及び耐熱スポーリング性に著しく優れた
耐火物が得られることを見出し本発明を完成した。Means for Solving the Problems As a result of intensive research in view of the above problems, the inventor has found that:
Mq to form a crack of a certain size as a refractory material
The present invention was completed based on the discovery that a refractory with extremely excellent structural spalling resistance and heat spalling resistance can be obtained by using O-CaO clinker.
即ち本発明は、ＭｇＯ／ＣａＯ比が２０／８０〜８０／
２０のＭｇＯ−ＣａＯクリンカー又は該ＭｇＯ−ＣａＯ
クリンカーと高純度Ｍ（ＪＯクリンカーとからなり、該
ＭｑＯ−ＣａＯクリンカーには、断面が幅１０〜８０μ
ｍ１長さ１０〜８０μｍの棒状又は板状のＭＱ○結晶が
ＣａＯ結晶マトリックス中に連続することなく存在し、
且つ該ＣａＯ結晶中に幅０．５〜５μｍ、長さ５〜１０
μｍの亀裂が内在することを特徴とするマグネシア−カ
ルシア系焼成耐火物に係る。That is, in the present invention, the MgO/CaO ratio is 20/80 to 80/
20 MgO-CaO clinker or the MgO-CaO
It consists of clinker and high purity M (JO clinker), and the MqO-CaO clinker has a cross section with a width of 10 to 80 μm.
m1 Rod-shaped or plate-shaped MQ○ crystals with a length of 10 to 80 μm exist without being continuous in the CaO crystal matrix,
In addition, the CaO crystal has a width of 0.5 to 5 μm and a length of 5 to 10 μm.
The present invention relates to a magnesia-calcia based fired refractory characterized by the inclusion of μm-sized cracks.
本発明では、耐火物材料として、Ｍｇｂ／ＣａＯ比が２
０／８０〜８０／２０程度のＭＱＯ−ＣａＯクリンカー
を使用する。In the present invention, the refractory material has an Mgb/CaO ratio of 2.
MQO-CaO clinker of about 0/80 to 80/20 is used.
ＭＱＯ含恐が８０重Ｍ％を越えると、ＭｇＯ結。If the MQO content exceeds 80% by weight, MgO binding occurs.
晶の連続組織が生じ易く、耐熱スポーリング性が劣化す
る。また、７ＸＣａＯ／Ｓ ｉ ０２比のスラグには烏
耐食性を示すが、Ｆｅ２０３ 、ＡＴ！２０３等を含有
するスラグに浸透され易く、構造スポーリングが誘発さ
れる。Ｍｇｏ含口が２０ｍｆｆ１％未満では、ＭｇＯ−
ＣａＯタリン力−の耐消化性が低下する。また、Ｆｅ２
Ｏ３、Ａ９２０３等を含有するスラグに浸透され易く、
構造スポーリングが誘発される。ＭｏＯ含母が２０重量
％未満では、ＭｑＯ−ＣａＯクリンカーの耐消化性が低
下する。A continuous structure of crystals tends to occur, and heat spalling resistance deteriorates. In addition, slag with a 7XCaO/S i 02 ratio exhibits corrosion resistance, but Fe203, AT! It is easily penetrated by slag containing 203, etc., and structural spalling is induced. When the Mgo content is less than 20mff1%, MgO-
Digestion resistance of CaO talin decreases. Also, Fe2
Easily penetrated by slag containing O3, A9203, etc.
Structural spalling is induced. If the MoO content is less than 20% by weight, the digestion resistance of the MqO-CaO clinker decreases.
また、Ｆｅ２Ｏ３、Ａｌ２２０３ ｒｆを多徂に含むス
ラグとの接触によって、ＣａＯ−Ｆｅ２Ｏ３−８ｉＯ２
系、ＣａＯ ＡＱ２０３ Ｓ！Ｏｚ系等の低融点生
成物が形成され、耐食性が茗しく低下する。In addition, due to contact with slag containing Fe2O3 and Al2203 rf in various areas, CaO-Fe2O3-8iO2
system, CaO AQ203 S! Low melting point products such as Oz-based products are formed, and the corrosion resistance is severely reduced.
該Ｍ （Ｊ Ｏ−Ｃａ Ｏクリンカーの構造組織内には
、断面が幅１０〜８０μｍ１長さ１０〜８０μｍの棒状
又は板状のＭ（ＪＯ結晶がＣａＯ結晶マトリックス中に
連続することなく存在し、且つ該ＣａＯ結晶中に幅０．
５〜５μｍ、長さ５〜１０μｍの亀裂が内在している。In the structural organization of the M (JO-CaO clinker, rod-shaped or plate-shaped M (JO crystals exist without being continuous in the CaO crystal matrix, and the cross section is 10 to 80 μm wide and 10 to 80 μm long). Moreover, the CaO crystal has a width of 0.
Cracks with a length of 5 to 5 μm and a length of 5 to 10 μm are present.
ＭｇＯ−ＣａＯクリンカーは、予め粒径４４μｍ以下程
度に微細化したＣａＯをＭｇｏと混合して均一化し、焼
結助剤としてｌ”ｅ２０３を０．１〜１．０重量％程度
加え、１８００〜２５００℃程度で焼成して製造される
。焼成時、クリンカー中にはＭｇＯ結晶が連続すること
なく形成され、クリンカーのＣａＯ結晶中には亀裂が生
じる。The MgO-CaO clinker is made by mixing CaO, which has been refined in advance to a particle size of 44 μm or less, with Mgo to make it homogeneous, and then adding about 0.1 to 1.0% by weight of l”e203 as a sintering aid to obtain a particle size of 1800 to 2500 μm. It is manufactured by firing at a temperature of about 0.degree. C. During firing, MgO crystals are formed in the clinker without continuity, and cracks occur in the CaO crystals of the clinker.
こうして得られたＭｇＯ結晶の大きさは、その断面が幅
１０〜８０μｍ程度、長さ１０〜８０μｍ程度であり、
またＣａＯ結晶中の亀裂の大ぎさは幅０．５〜５μｍ程
度、長さ５〜１０μｍ程度である。ＭｇＯ結晶及び亀裂
の大きさは、「ｅ２０３含聞によって決定される。即ち
Ｆｅ２Ｏ３含聞が１．０重量％を越えると、ＭｇＯ結晶
の長さ及び幅が８０μｍを越え、タリン力−の耐食性が
低下する。また亀裂の大きさも幅５μｍ、長さ１０μｍ
を越え、タリン力−の強度が低下してしまう。一方Ｆｅ
２Ｏ３含吊が０．１重量％未満では、ＭＱＯ結晶の長さ
及び幅が１０μｍ未満となり、耐スポーリング性向上効
果が発揮できない。また亀裂の大きさも幅０．５μｍ、
長さ５μｍ未満となる。この場合、亀裂はクリンカーに
伝播してきた応力を充分に吸収できず、耐火物の耐熱ス
ポーリング性が向上しない。The size of the MgO crystal thus obtained is such that its cross section is approximately 10 to 80 μm wide and 10 to 80 μm long,
Moreover, the size of the crack in the CaO crystal is about 0.5 to 5 μm in width and about 5 to 10 μm in length. The size of MgO crystals and cracks is determined by the e203 content. That is, when the Fe2O3 content exceeds 1.0% by weight, the length and width of the MgO crystals exceed 80 μm, and the corrosion resistance of the Tallin force decreases. Also, the size of the crack is 5 μm in width and 10 μm in length.
, the strength of the Tallin force decreases. On the other hand, Fe
If the 2O3 content is less than 0.1% by weight, the length and width of the MQO crystals will be less than 10 μm, and the effect of improving spalling resistance cannot be exhibited. In addition, the size of the crack is 0.5 μm in width.
The length is less than 5 μm. In this case, the cracks cannot sufficiently absorb the stress propagated to the clinker, and the heat spalling resistance of the refractory does not improve.
ＭＱＯ−ＣａＯクリンカーの粒径は特に限定されず、適
宜選択して使用すればよい。The particle size of the MQO-CaO clinker is not particularly limited, and may be appropriately selected and used.
本発明では例えば、粒径１．Ｑｍｍ以下のものを１０〜
６０重量％程度、粒径１．Ｏ〜８．０ＩＩＩＩｌｌ程度
のものを９０〜４０重量％程度使用することが好ましい
。粒径１．０ＩＩＩ１１以下の微細化したＭｇ０−Ｃａ
Ｏクリンカーを７トリツクス中に存在させれば、粗粒子
として使用するよりも表面積が増え、浸透するスラグ中
のＳ！０２成分との反応が起り易くなる。従ってスラグ
浸透防止効果が発揮され、耐食性及び耐構造スポーリン
グ性が向上する。In the present invention, for example, the particle size is 1. Qmm or less 10~
Approximately 60% by weight, particle size 1. It is preferable to use about 90 to 40% by weight of about 0 to 8.0IIIll. Finely refined Mg0-Ca with a particle size of 1.0III11 or less
If O clinker is present in the 7trix, the surface area will increase compared to using it as coarse particles, and S! Reaction with component 02 is likely to occur. Therefore, the effect of preventing slag penetration is exhibited, and corrosion resistance and structural spalling resistance are improved.
本発明において、耐火物材料として、ＭＣｌ０に微細化
したＣａＯを混合し均一化して焼成したＭｑＯ−ＣａＯ
クリンカーを使用する利点は、以下の通りである。In the present invention, as a refractory material, MqO-CaO is prepared by mixing finely divided CaO with MCl0, homogenizing it, and firing it.
The advantages of using clinker are as follows.
（１）予めＭｇＯと微細化したＣａＯとを均一に混合し
て焼成し、ＭｑＯ−ＣａＯクリンカーとすることによっ
て、ＣａＯ結晶はｆｖｌｏ−ＣａＯクリンカー中のカル
シウムフェライト等の酸化被膜で保護され、その上Ｍｇ
Ｏ結晶がＣａＯ結晶と外気との接触を防止する。そのた
め本発明では、微細化したＣａＯを甲に添加することに
よって生じた耐消化性の低下は起らない。(1) By uniformly mixing MgO and finely divided CaO in advance and firing it to form an MqO-CaO clinker, the CaO crystals are protected by an oxide film such as calcium ferrite in the fvlo-CaO clinker, and then Mg
The O crystal prevents contact between the CaO crystal and the outside air. Therefore, in the present invention, the deterioration in digestion resistance caused by adding finely divided CaO to the shell does not occur.
（２）ＭｑＯ−ＣａＯクリンカーがＭｑＯとＣａＯとの
均一混合体であるため、ＣａＯが耐火物組織中に均一分
散している。またクリンカー同士の結合（ＭｇＯ−Ｍｇ
Ｏ結合、ＣａＯ−ＣａＯ結合）が強く、従来の耐火物よ
り高緻密質になり易い。このためスラグの浸透が少なく
なり、耐食性が著しく向上する。(2) Since the MqO-CaO clinker is a homogeneous mixture of MqO and CaO, CaO is uniformly dispersed in the refractory structure. Also, the bond between clinkers (MgO-Mg
O bond, CaO-CaO bond) are strong, and it tends to be more dense than conventional refractories. This reduces slag penetration and significantly improves corrosion resistance.
（３）ＭｑＯ−ＣａＯクリンカーの焼成時にＣａＯ結晶
マトリックス中に生ずる微小クラック及びその他のクラ
ック並びに、耐火物を焼成する際の冷却過程において、
配合された粒子の熱膨張率の違いに起因する微小クラッ
クが熱応力吸収層となり、更にクリンカー中のＭＱＯ結
晶が連続することなく存在することによって、従来の耐
火物より高緻密質であるにもかかわらず、耐熱スポーリ
ング性が向上する。(3) Microcracks and other cracks that occur in the CaO crystal matrix during firing of MqO-CaO clinker, and during the cooling process when firing refractories.
Microcracks caused by differences in the coefficient of thermal expansion of the blended particles become a thermal stress absorbing layer, and because the MQO crystals in the clinker exist without continuity, it is more dense than conventional refractories. Regardless, heat spalling resistance is improved.
本発明では、耐火物の耐食性をより一層向上させるため
に、耐火物材料としてＭｑＯ−ＣａＯクリンカーととも
に高純度Ｍ（ＪＯクリンカーを使用することができる。In the present invention, in order to further improve the corrosion resistance of the refractory, high purity M (JO clinker) can be used together with MqO-CaO clinker as the refractory material.
高純度ＭＱＯクリンカーとしては、例えば、電融ＭＱ○
クリンカー、焼結ＭｑＯクリンカー、又はそれらの混合
物を挙げることができる。高純度ＭＱＯクリンカーの配
合割合は適宜選択できるが例えば耐火物材料全量のうち
２０〜８０重量％程瓜と寸ればよい。またその粒径も特
に限定されないが、例えば粒径１．Ｑｎｖ程度以下のも
のを２０〜８０ｍｍ％程度及び粒径１、 Ｏ−８，Ｃ）
ｅｇ＋Ｐｉ！１ｆｆ１７）ｂ（７）ヲ８０〜２０ｆｆｉ
ｆｆｉ％程度に粒度調整してもよい。As a high purity MQO clinker, for example, electrofused MQ○
Mention may be made of clinker, sintered MqO clinker, or mixtures thereof. The blending ratio of the high-purity MQO clinker can be selected as appropriate, but for example, it may be about 20 to 80% by weight of the total amount of the refractory material. Further, the particle size is not particularly limited, but for example, the particle size is 1. About 20 to 80 mm% of particles below Qnv and particle size 1, O-8, C)
eg+Pi! 1ff17)b(7)wo80~20ffi
The particle size may be adjusted to about ffi%.
本発明耐火物は、常法に従って製造でさ、例えば、耐火
物材料であるＭｃ＋ｏ−ＣａＯクリンカーに、必要なら
ば高純ａＭｇｏクリンカーを加え、有機バインダーを配
合して混練した後、成形し、１５５０〜１７５０℃程度
で焼成すればよい。有機バインダーとしては特に制限さ
れず、ポリプロピレン、イソシアネート、タールピッチ
、フェノール樹脂等を例示できる。The refractory of the present invention is manufactured according to a conventional method. For example, if necessary, high-purity aMgo clinker is added to Mc+o-CaO clinker, which is a refractory material, and an organic binder is mixed and kneaded, followed by molding. What is necessary is just to bake at about 1750 degreeC. The organic binder is not particularly limited, and examples include polypropylene, isocyanate, tar pitch, and phenol resin.
有機バインダーの配合量は適宜選択可能であるが、例え
ば耐火物材料１００１ｊｆｆｉ部に対し、バインダー１
〜５ ｆｆｉ聞部程度を配合すればよい。The amount of the organic binder can be selected as appropriate, but for example, if 1 part of the binder is added to 1001 parts of the refractory material,
Approximately 5 to 5 ffi portions may be blended.
発明の効果
本発明耐火物は、従来のマグネシア−カルシア系耐火物
に比べ、著しく優れた耐消化性、熱間強度、耐スポーリ
ング性、耐食性を有しており、転炉を初めとする各種精
錬炉の内張り耐火物として最適である。Effects of the Invention The refractory of the present invention has significantly superior extinguishing resistance, hot strength, spalling resistance, and corrosion resistance compared to conventional magnesia-calcia-based refractories, and can be used in various applications including converters. Ideal as a refractory lining for smelting furnaces.
１二Ｊｉｆｆ
以下に実施例及び比較例を挙げ、本発明をより一層明瞭
なものとする。12 Jiff Examples and comparative examples are given below to make the present invention even clearer.
実施例１〜３
耐火物材料として、第１表に示す配合９１合（重量％）
でＭｇＯ−ＣａＯクリンカー及び電融ＭｑＯクリンカー
を使用して本発明耐火物を製造した。Examples 1 to 3 As a refractory material, 91 combinations (wt%) shown in Table 1 were used.
A refractory of the present invention was manufactured using a MgO-CaO clinker and an electrofused MqO clinker.
即ち、上記耐火物材料１００重量部に対し、バインダー
としてポリプロビレ２２１聞部及びイソシアネー１〜１
．５重吊部を配合して約１００℃で混練し、この混練物
を７５０ ｋｏ／ ｃ１１２の圧力で並形形状に成形し
、次いで１６５０℃で６時間焼成し、本発明耐火物を製
造した。尚、上記ＭＣ７Ｏ−ＣａＯクリンカーとしては
、ＭＱＯ／Ｃａ０−３０／７０のものを使用し、クリン
カー中のＭｇｏ結晶の平均的な大きさは幅３０μｍ、長
さ５０μｍ、またＣａＯ結晶中の亀裂の平均的な大きさ
は幅１μｍ、長さ７μｍであった。That is, to 100 parts by weight of the above refractory material, 221 parts of polypropylene and 1 to 1 part of isocyanate were added as a binder.
．． A 5-fold suspension was blended and kneaded at about 100°C, and the kneaded product was molded into a regular shape at a pressure of 750 ko/c112, and then fired at 1650°C for 6 hours to produce a refractory of the present invention. The MC7O-CaO clinker used is MQO/Ca0-30/70, and the average size of the Mgo crystals in the clinker is 30 μm in width and 50 μm in length, and the average size of the cracks in the CaO crystals is 30 μm in width and 50 μm in length. The actual size was 1 μm in width and 7 μm in length.
得られた本発明耐火物を性能試験に供した。結果を第１
表に示す。The obtained refractory of the present invention was subjected to a performance test. Results first
Shown in the table.
比較例１〜３
耐火物材料として、第１表に示す配合割合（重量％）で
、ＭｑＯクリンカー及びＣａＯクリンカー （ＣａＯ純
度約９８％）を使用し、実施例と同様にして従来のＭｑ
Ｏ−ＣａＯ系耐火物を製造した。（ｑられた耐火物を性
能試験に供した。結果を第１表に承り。Comparative Examples 1 to 3 MqO clinker and CaO clinker (CaO purity approximately 98%) were used as refractory materials at the compounding ratios (wt%) shown in Table 1, and conventional Mq
An O-CaO-based refractory was manufactured. (The prepared refractories were subjected to performance tests. The results are shown in Table 1.
第 １ 表
註＝１）耐火物をオートクレーブに入れ、４気圧の蒸気
で３時間処理し、その型組増加率を測定した。Notes to Table 1 = 1) The refractories were placed in an autoclave and treated with steam at 4 atm for 3 hours, and the mold increase rate was measured.
２）ロータリー法のスラグテストにより、試薬を調合し
た２種のスラグ（■Ｃａｂ／Ｓ！０２＝２．３、Ｆｅ２
Ｏ３含帛２３重倒％■ＣａＯ／Ｓ ｉ ０２ ＝１．２
、Ｆｅ２Ｏ３含ＦＢ ５ ｍ ｆｎ ％ ） ヲｔ’
用Ｌ／、１７５０℃で５時間耐火物の耐食性テストを行
い、ぞの溶損聞を測定した。2) Two types of slags prepared with reagents (■Cab/S!02=2.3, Fe2
O3 content 23% ■CaO/S i 02 = 1.2
, Fe2O3-containing FB 5 m fn %) Wot'
A corrosion resistance test was conducted on the refractories at 1,750°C for 5 hours, and the corrosion loss of the refractories was measured.
３）耐火物を１２００℃に保持した電気炉中に１５分間
挿入し、その後１５分間空冷するというサイクルを繰り
返して１０回行い、剥落するまでの回数を調べた。3) A cycle of inserting the refractory into an electric furnace maintained at 1200°C for 15 minutes and then cooling it in air for 15 minutes was repeated 10 times, and the number of times until it flaked off was determined.
以上の結果より、本発明耐火物が、ＭｑＯ／ＣａＯ比が
同程度の従来の耐火物に比べ、耐消化性、熱間曲げ強さ
、耐食性及び耐スポーリング性に優れていることがわか
る。The above results show that the refractories of the present invention are superior in extinguishment resistance, hot bending strength, corrosion resistance, and spalling resistance compared to conventional refractories with comparable MqO/CaO ratios.
本発明品（実施例■）及び従来品（比較例■）をＡ社転
炉炉腹部に張り分け、耐用性テストを行った。転炉炉腹
部にＪ３いて１７１チＶ−ジ使用した後、耐火物を回収
して１チャージ当りの溶ｌｘ（ｍｍ）をＸｔｉしたどこ
ろ、本発明品は０．４６ｍｍ／チャージ、従来品は０．
５２１１１１１１／ヂＶ−ジであった。The product of the present invention (Example 2) and the conventional product (Comparative Example 2) were separately placed on the belly of a converter furnace of Company A, and a durability test was conducted. After using J3 in the belly of the converter furnace and using 171 chips, the refractory was collected and the melt lx (mm) per charge was determined to be Xti, and the product of the present invention was 0.46 mm/charge, and the conventional product was 0. ．．
52111111/diV-di.
（以 上）(that's all)
Claims (1)
Ｏ−ＣａＯクリンカー又は該ＭｇＯ−ＣａＯクリンカー
と高純度ＭｇＯクリンカーとからなり、該ＭｇＯ−Ｃａ
Ｏクリンカーには、断面が幅１０〜８０μｍ、長さ１０
〜８０μｍの棒状又は板状のＭｇＯ結晶がＣａＯ結晶マ
トリックス中に連続することなく存在し、且つ該ＣａＯ
結晶中に幅０．５〜５μｍ、長さ５〜１０μｍの亀裂が
内在することを特徴とするマグネシア−カルシア系焼成
耐火物。1 Mg with a MgO/CaO ratio of 20/80 to 80/20
Consisting of an O-CaO clinker or the MgO-CaO clinker and a high-purity MgO clinker, the MgO-Ca
O clinker has a cross section with a width of 10 to 80 μm and a length of 10 μm.
Rod-shaped or plate-shaped MgO crystals of ~80 μm exist without being continuous in the CaO crystal matrix, and the CaO
A magnesia-calcia based fired refractory characterized by having cracks with a width of 0.5 to 5 μm and a length of 5 to 10 μm inherent in the crystal.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61091449A JPS62246858A (en) | 1986-04-21 | 1986-04-21 | Magnesia calcta base burnt refractories |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61091449A JPS62246858A (en) | 1986-04-21 | 1986-04-21 | Magnesia calcta base burnt refractories |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62246858A true JPS62246858A (en) | 1987-10-28 |
Family
ID=14026671
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61091449A Pending JPS62246858A (en) | 1986-04-21 | 1986-04-21 | Magnesia calcta base burnt refractories |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62246858A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1316071C (en) * | 2004-12-21 | 2007-05-16 | 大连理工大学 | Method for preparing magnesia crystal by using temperature control arc furnace |
| JP2013001622A (en) * | 2011-06-21 | 2013-01-07 | Mintekku Japan Kk | Tundish coating material and method for coating tundish using the same |
| JP2014043383A (en) * | 2012-08-28 | 2014-03-13 | Nippon Steel & Sumitomo Metal | Working method of coating material on inner surface of molten steel bath |
-
1986
- 1986-04-21 JP JP61091449A patent/JPS62246858A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1316071C (en) * | 2004-12-21 | 2007-05-16 | 大连理工大学 | Method for preparing magnesia crystal by using temperature control arc furnace |
| JP2013001622A (en) * | 2011-06-21 | 2013-01-07 | Mintekku Japan Kk | Tundish coating material and method for coating tundish using the same |
| JP2014043383A (en) * | 2012-08-28 | 2014-03-13 | Nippon Steel & Sumitomo Metal | Working method of coating material on inner surface of molten steel bath |
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