JPH07291714A - Basic refractory - Google Patents
Basic refractoryInfo
- Publication number
- JPH07291714A JPH07291714A JP6101629A JP10162994A JPH07291714A JP H07291714 A JPH07291714 A JP H07291714A JP 6101629 A JP6101629 A JP 6101629A JP 10162994 A JP10162994 A JP 10162994A JP H07291714 A JPH07291714 A JP H07291714A
- Authority
- JP
- Japan
- Prior art keywords
- refractory
- zro
- basic refractory
- tio
- basic
- 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.)
- Withdrawn
Links
- 239000011822 basic refractory Substances 0.000 title claims abstract description 16
- 239000000843 powder Substances 0.000 claims abstract description 28
- 229910010413 TiO 2 Inorganic materials 0.000 claims abstract description 15
- 239000002994 raw material Substances 0.000 claims abstract description 14
- 238000002844 melting Methods 0.000 claims abstract description 11
- 230000008018 melting Effects 0.000 claims abstract description 10
- 239000000463 material Substances 0.000 claims abstract description 8
- 239000002245 particle Substances 0.000 claims abstract description 6
- 238000010304 firing Methods 0.000 claims abstract description 5
- 239000011362 coarse particle Substances 0.000 claims abstract description 3
- 239000011819 refractory material Substances 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 7
- 239000011230 binding agent Substances 0.000 claims description 4
- 239000002893 slag Substances 0.000 abstract description 38
- 230000008595 infiltration Effects 0.000 abstract description 27
- 238000001764 infiltration Methods 0.000 abstract description 27
- 230000007797 corrosion Effects 0.000 abstract description 23
- 238000005260 corrosion Methods 0.000 abstract description 23
- 238000007670 refining Methods 0.000 abstract description 7
- 238000000034 method Methods 0.000 abstract description 6
- 238000009849 vacuum degassing Methods 0.000 abstract description 6
- 229910052751 metal Inorganic materials 0.000 abstract description 5
- 239000002184 metal Substances 0.000 abstract description 5
- 239000002699 waste material Substances 0.000 abstract description 2
- 239000011449 brick Substances 0.000 description 44
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 16
- 238000004901 spalling Methods 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- ODINCKMPIJJUCX-UHFFFAOYSA-N Calcium oxide Chemical compound [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 description 8
- 239000000292 calcium oxide Substances 0.000 description 8
- 235000012255 calcium oxide Nutrition 0.000 description 8
- 239000000395 magnesium oxide Substances 0.000 description 8
- 238000011156 evaluation Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 5
- 229910052596 spinel Inorganic materials 0.000 description 5
- 239000011029 spinel Substances 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 4
- 238000000280 densification Methods 0.000 description 4
- 230000003628 erosive effect Effects 0.000 description 4
- 229910004298 SiO 2 Inorganic materials 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 239000010459 dolomite Substances 0.000 description 3
- 229910000514 dolomite Inorganic materials 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 1
- 239000003610 charcoal Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910000423 chromium oxide Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical group O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000010436 fluorite Substances 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 238000004898 kneading Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Abstract
(57)【要約】
【目的】 常圧下および高真空下でも高耐食性ならびに
耐スラグ浸潤性を持つ塩基性耐火物を提供する。
【構成】 ５００μｍ以上の粗粒：６０〜９０ｗｔ％
と、残部５００μｍ以下の微粉部で構成された、１７０
０℃以上の高融点を有する塩基性耐火物原料の１種また
は２種以上からなる、耐火物骨材に、０．５〜５０μｍ
の粒度範囲にある、ＺｒＯ2：５０〜９９ｗｔ％、およ
びＴｉＯ2：１〜５０ｗｔ％の酸化物粉を、前記耐火物
骨材の総量外掛けで１０〜５０ｗｔ％配合したのち、焼
成して得られる塩基性耐火物である。
【効果】 本発明によって得られた耐火物は、公害発生
防止のために行われる廃棄処理工程を省略し、溶融金属
精錬容器、特に真空脱ガス容器の耐用性を大幅に延長し
て、製鉄の二次精錬プロセスにおけるコストを大幅に下
げることができる。(57) [Abstract] [Purpose] To provide a basic refractory having high corrosion resistance and slag infiltration resistance under normal pressure and high vacuum. [Structure] Coarse particles of 500 μm or more: 60 to 90 wt%
And a fine powder part having a balance of 500 μm or less, 170
0.5 to 50 μm for a refractory aggregate composed of one or more basic refractory raw materials having a high melting point of 0 ° C. or higher.
ZrO 2 : 50 to 99 wt% and TiO 2 : 1 to 50 wt% of oxide powders in the particle size range of 10 to 50 wt% are added to the total amount of the refractory aggregates, and then obtained by firing. It is a basic refractory material. [Effect] The refractory obtained by the present invention omits the waste treatment step performed to prevent the occurrence of pollution, greatly extends the durability of the molten metal refining vessel, especially the vacuum degassing vessel, and The cost of the secondary refining process can be significantly reduced.
Description
【０００１】[0001]
【産業上の利用分野】本発明は、溶融金属精錬容器、特
に真空脱ガス容器に用いられる塩基性耐火物に関する。TECHNICAL FIELD The present invention relates to a basic refractory used for a molten metal refining vessel, particularly a vacuum degassing vessel.
【０００２】[0002]
【従来の技術】現状の溶融金属精錬プロセスにおいて、
真空脱ガス容器は高級鋼製造に不可欠な設備となってい
る。2. Description of the Related Art In the current molten metal refining process,
The vacuum degassing vessel is an indispensable facility for high-grade steel production.
【０００３】精錬中の真空脱ガス容器には、溶鋼と共に
高塩基度のスラグが存在する。このスラグが容器の内張
耐火物れんがと接触して、れんが表面が侵食される。In the vacuum degassing vessel during refining, high basicity slag exists together with molten steel. The slag comes into contact with the refractory brick lining the container and erodes the brick surface.
【０００４】そのため、現状の操業では、このような問
題に対応するために、マグクロ質れんがが使用されてき
た。Therefore, in the current operation, maguro bricks have been used to cope with such problems.
【０００５】ところが、近年、マグクロ質れんがに含ま
れるＣｒ化合物、特にＣｒ6+イオンの人体に与える影響
が問題とされており、このような化合物（特に金属Ｃｒ
や酸化クロム）を一切使用しないクロムフリーれんがが
製造され、マグクロ質れんがに代わるクロムフリーれん
がとして、マグネシア―スピネル質れんがやマグネシア
―ドロマイト（カルシア）質れんがが使用されている。However, in recent years, the influence of Cr compounds contained in magchromatic bricks, especially Cr 6+ ions, on the human body has become a problem, and such compounds (especially metal Cr
Chrome-free bricks that do not use chrome and chromium oxide) are used, and magnesia-spinel bricks and magnesia-dolomite (calcia) bricks are used as chrome-free bricks that replace magchromatic bricks.
【０００６】これらのれんがは、ＣａＯ濃度の高い高塩
基性スラグに対して、高耐食性を示し、特開平４―２３
８８５５号公報には、ＴｉＯ2成分を含有するスピネル
クリンカー（原料）からなる骨材を含んだマグネシア―
ドロマイト質れんがが、また、特開平５―４３３０５号
公報には、ＺｒＯ2成分を含有するマグネシアクリンカ
ー（原料）からなる骨材を含んだマグネシア―ドロマイ
ト質れんがが、従来のクロムフリーれんがより高耐食性
であることが開示されている。These bricks show high corrosion resistance against highly basic slag having a high CaO concentration, and are disclosed in Japanese Patent Laid-Open No. 4-23.
No. 8855 discloses a magnesia-containing aggregate made of spinel clinker (raw material) containing a TiO 2 component.
Dolomite bricks, and in JP-A-5-43305, magnesia-domite bricks containing an aggregate composed of a magnesia clinker (raw material) containing a ZrO 2 component have higher corrosion resistance than conventional chromium-free bricks. Is disclosed.
【０００７】[0007]
【発明が解決しようとする課題】しかしながら、極低炭
鋼量産と超高純度鋼の要求に対して、処理容器中に、脱
Ｐのためにホタル石（Ｃａ Ｆ2）等の添加が行われ、ス
ラグ中のＣａ成分は増加し、スラグは更に高塩基性化し
ている。[Problems to be Solved by the Invention] However, extra low charcoal
To meet the demand for mass production of steel and ultra-high-purity steel, de-gassing in the processing container
Fluorite (Ca for P F2) Etc. are added,
The Ca content in the lag increases and the slag becomes more basic.
ing.
【０００８】このためにこれらのれんが中の不純物であ
るＳｉＯ2やＡｌ2Ｏ3等とＣａＯスラグが低融点化合物
を作り易くなり、高塩基性スラグは、これら不純物が含
まれるれんが微粉部を通して、れんが内部へ浸潤し、処
理容器の温度変動による熱衝撃により構造スポーリング
を発生する問題がある。[0008] The SiO 2, Al 2 O 3 or the like and the CaO slag, which is an impurity in these bricks in order tends to make a low-melting compound, highly basic slag, through brick fines portion contains these impurities, There is a problem that the bricks infiltrate into the interior of the brick and structural spalling occurs due to thermal shock due to temperature fluctuation of the processing container.
【０００９】この損耗は、微粉部の高塩基性スラグに対
する耐スラグ浸潤性、耐食性の不足が、原因となってい
る。This wear is caused by insufficient slag infiltration resistance and corrosion resistance of the finely powdered portion with respect to the highly basic slag.
【００１０】そこで、微粉部中からＳｉＯ2、Ａｌ2Ｏ3
等の不純物を減少させ、ＺｒＯ2等を含有したクリンカ
ーを添加した耐火物を製造したとしても、微粉部は開気
孔を多く有しているため、スラグ浸潤の原因となり、こ
のようなれんがの耐用性の低下を解消することはできな
い。Therefore, from the fine powder portion, SiO 2 , Al 2 O 3
Even if a refractory material containing clinker containing ZrO 2 etc. is produced by reducing impurities such as slag, it will cause slag infiltration because the fine powder part has many open pores, and the durability of such bricks will be improved. It is not possible to eliminate the decline in sex.
【００１１】本発明の目的は、常圧下はもちろん、高真
空下でも高耐食性、ならびに高耐スラグ浸潤性を持つ塩
基性耐火物を提供することにある。An object of the present invention is to provide a basic refractory which has high corrosion resistance under high pressure as well as under normal pressure and high slag infiltration resistance.
【００１２】[0012]
【課題を解決するための手段】上記課題を解決する手段
として、以下の事柄が必須である。[Means for Solving the Problems] As means for solving the above problems, the following matters are essential.
【００１３】５００μｍ以上の粗粒：６０〜９０ｗｔ％
と、残部５００μｍ以下の微粉部で構成された、１７０
０℃以上の高融点を有する塩基性耐火物原料の１種また
は２種以上からなる、耐火物骨材に、０．５〜５０μｍ
の粒度範囲にある、ＺｒＯ2：５０〜９９ｗｔ％、およ
びＴｉＯ：１〜５０ｗｔ％の酸化物粉を、前記耐火物の
総量外掛けで１０〜５０ｗｔ％共に配合したのち、焼成
して得られる耐火物でなければならない。Coarse particles of 500 μm or more: 60 to 90 wt%
And a fine powder part having a balance of 500 μm or less, 170
0.5 to 50 μm for a refractory aggregate composed of one or more basic refractory raw materials having a high melting point of 0 ° C. or higher.
A fire resistance obtained by blending ZrO 2 : 50 to 99 wt% and TiO: 1 to 50 wt% oxide powder in the particle size range of 10 Must be a thing.
【００１４】特に、１７００℃以上の高融点を有する塩
基性耐火物原料が、ＭｇＯ成分および／またはＣａＯ成
分を含み、ＺｒＯ2成分およびＴｉＯ2成分として不純物
またはバインダー起源のもの以外を含まないものでなけ
ればならない。In particular, the basic refractory raw material having a high melting point of 1700 ° C. or higher contains MgO component and / or CaO component, and does not contain impurities or binder origin other than ZrO 2 component and TiO 2 component. There must be.
【００１５】[0015]
【作用】したがって、真空脱ガス容器で、クロムフリー
れんがの耐用性を延ばす為には、微粉部に、ＺｒＯ2と
共にＴｉＯ2を適用して、微粉部自体を緻密化し、耐食
性、耐スラグ浸潤性を向上させる必要がある。Therefore, in a vacuum degassing container, in order to extend the durability of chromium-free bricks, TiO 2 is applied to the fine powder portion together with ZrO 2 to make the fine powder portion itself dense, and to have corrosion resistance and slag infiltration resistance. Need to improve.
【００１６】以下、本発明を、詳細に説明する。The present invention will be described in detail below.
【００１７】本発明において、塩基性耐火物の微粉部に
添加されたＴｉＯ2は、れんが焼成時に、焼結助材とな
り、れんが組織、特に微粉部の緻密化を促進し、スラグ
浸潤の原因となるれんが内部の連結気孔を減少させる。In the present invention, TiO 2 added to the fine powder portion of the basic refractory material serves as a sintering aid when the brick is fired, accelerates the densification of the brick structure, particularly the fine powder portion, and causes slag infiltration. Narrow brick reduces connected porosity inside.
【００１８】同時に、れんが中に存在する過剰なＴｉＯ
2は、スラグ中のＡｌ2Ｏ3ならびにＣａＯ成分と、高融
点化合物Ａｌ2ＴｉＯ5およびＣａＴｉＯ3を作り、耐ス
ラグ浸潤性を向上させる。At the same time, excess TiO present in the brick is present.
2 forms Al 2 O 3 and CaO components in the slag and high melting point compounds Al 2 TiO 5 and CaTiO 3 to improve slag infiltration resistance.
【００１９】また、ＺｒＯ2が存在することにより、微
粉部の耐食性を向上させ、同時に、れんが内部に浸潤し
たスラグ中のＣａＯ成分と高融点化合物ＣａＺｒＯ3を
作り、耐スラグ浸潤を向上させる。Further, the presence of ZrO 2 improves the corrosion resistance of the fine powder portion, and at the same time, forms the CaO component in the slag infiltrated into the brick and the high melting point compound CaZrO 3 to improve the slag infiltration resistance.
【００２０】本発明において、ＴｉＯ2およびＺｒＯ2を
微粉部に存在させることにより高耐食性、高耐スラグ浸
潤性のれんがを作ることができる。In the present invention, the presence of TiO 2 and ZrO 2 in the fine powder portion makes it possible to produce a brick having high corrosion resistance and high slag infiltration resistance.
【００２１】しかし、これらの酸化物の内、どちらか一
方しか存在しなかった場合、高耐食性と耐スラグ浸潤性
を合わせ持つことは出来ない。However, when only one of these oxides is present, it is not possible to have both high corrosion resistance and slag infiltration resistance.
【００２２】もし、ＴｉＯ2だけが存在した場合、緻密
化は図れるものの、スラグ浸潤を十分に抑制することは
できない。If only TiO 2 is present, densification can be achieved, but slag infiltration cannot be sufficiently suppressed.
【００２３】また、ＺｒＯ2だけが存在した場合、スラ
グ浸潤は抑制できるが、緻密化ができない。そこで本発
明では、微粉部に、ＴｉＯ2およびＺｒＯ2を添加する。When only ZrO 2 is present, slag infiltration can be suppressed, but densification cannot be achieved. Therefore, in the present invention, TiO 2 and ZrO 2 are added to the fine powder portion.
【００２４】本発明の耐火物原料としては、１７００℃
以上の高融点を有する耐火物原料の１種または２種以上
を使用し、好ましくは、マグネシアクリンカー、マグド
ロクリンカー、スピネルクリンカー等とする。The refractory raw material of the present invention is 1700 ° C.
One or more of the above refractory raw materials having a high melting point are used, preferably magnesia clinker, magdro clinker, spinel clinker and the like.
【００２５】脱ガス槽での溶鋼の処理によっては、槽内
温度が１６００℃以上となることがあり、このような操
業での溶損に耐えるためには、本発明の耐火物原料とし
ては、１７００℃以上の高融点を有する耐火物原料が必
要である。Depending on the treatment of molten steel in the degassing tank, the temperature inside the tank may reach 1600 ° C. or higher. In order to withstand the melting damage in such an operation, the refractory raw material of the present invention is A refractory raw material having a high melting point of 1700 ° C. or higher is required.
【００２６】具体的には、ＭｇＯ成分および／またはＣ
ａＯ成分を含有する塩基性耐火物で、ＺｒＯ2成分やＴ
ｉＯ2成分は、不純物としてあるいはバインダーに基づ
くもの以外は含まないものである必要がある。Specifically, the MgO component and / or C
Basic refractory material containing aO component, ZrO 2 component and T
The iO 2 component must be free of impurities other than those based on the binder.
【００２７】不純物起源としては、高々２ｗｔ％以下で
あり、バインダー起源としては、例えば１ｗｔ％位の場
合があるが、その範囲については前後の値を含む。The source of impurities is 2 wt% or less at most, and the source of binder may be, for example, about 1 wt%, but the range includes the values before and after.
【００２８】本発明の耐火物は、５００μｍ以上の骨
材：６０〜９０ｗｔ％と、残部を５００μｍ以下の微粉
部より構成する。The refractory material of the present invention comprises aggregates of 500 μm or more: 60 to 90% by weight, and the balance of fine powder portions of 500 μm or less.
【００２９】本発明者らの実験によれば、５００μｍ以
上の骨材：６０〜９０ｗｔ％と、残部を５００μｍ以下
の微粉部から耐火物を製造した場合、れんが原料の充填
性がよく、さらに、焼成後、微粉部が充分に緻密化が図
られ、良好な耐食性と耐スラグ浸潤性が得られた。According to the experiments conducted by the present inventors, when a refractory material is manufactured from an aggregate having a size of 500 μm or more: 60 to 90 wt% and the balance of a fine powder part having a size of 500 μm or less, the brick raw material has a good filling property. After firing, the fine powder portion was sufficiently densified, and good corrosion resistance and slag infiltration resistance were obtained.
【００３０】骨材が５００μｍ未満の場合、および、骨
材量が全体の６０ｗｔ％未満の場合、れんがが非常に緻
密化し、良好な耐熱スポーリング性が得られず、一方、
９０ｗｔ％超の場合、焼成時に十分な緻密化ができず良
好な耐食性が得られなかった。When the aggregate is less than 500 μm and when the amount of the aggregate is less than 60 wt% of the whole, the brick becomes very dense and good heat spalling resistance cannot be obtained.
If it exceeds 90 wt%, sufficient densification cannot be achieved during firing and good corrosion resistance cannot be obtained.
【００３１】また、残部の微粉部が５００μｍ超の場
合、耐火性原料間への充填性が悪く、微粉部も充分に緻
密化が図られず、良好な耐食性と耐スラグ浸潤性が得ら
れなかった。When the balance of the fine powder portion is more than 500 μm, the filling property between the refractory raw materials is poor, the fine powder portion cannot be sufficiently densified, and good corrosion resistance and slag infiltration resistance cannot be obtained. It was
【００３２】本発明の耐火物に添加される、ＺｒＯ2と
ＴｉＯ2の酸化物粉の粒度は、０．５μｍ以上、５０μ
ｍ以下の粒度分布とし、好ましくは１μｍ以上、１０μ
ｍ以下とし、その酸化物粉の組成はＺｒＯ2：５０〜９
９ｗｔ％、および、ＴｉＯ2：１〜５０ｗｔ％とし、好
ましくは、ＺｒＯ2：８０〜９９ｗｔ％、および、Ｔｉ
Ｏ2：１〜２０ｗｔ％の組成とする。The particle size of the oxide powder of ZrO 2 and TiO 2 added to the refractory material of the present invention is 0.5 μm or more and 50 μm or more.
The particle size distribution is m or less, preferably 1 μm or more and 10 μm
m or less, and the composition of the oxide powder is ZrO 2 : 50-9
9 wt% and TiO 2 : 1 to 50 wt%, preferably ZrO 2 : 80 to 99 wt%, and Ti
O 2 : 1 to 20 wt% composition.
【００３３】粒度分布が０．５μｍ未満の場合、酸化物
粉の分散性が悪くなり、緻密なれんがは得られるが、耐
食性、耐スラグ浸潤性が劣化する。When the particle size distribution is less than 0.5 μm, the dispersibility of the oxide powder is deteriorated and a dense brick is obtained, but the corrosion resistance and the slag infiltration resistance are deteriorated.
【００３４】５０μｍを超えた場合、微粉部への充填性
が悪くなり、緻密なれんが組織が得られない。そのため
に良好な耐スラグ浸潤性が得られなくなる。When it exceeds 50 μm, the filling property into the fine powder portion is deteriorated and a dense brick structure cannot be obtained. Therefore, good slag infiltration resistance cannot be obtained.
【００３５】さらに、ＺｒＯ2が５０ｗｔ％未満、また
はＴｉＯ2が５０ｗｔ％を超える場合、ＺｒＯ2の添加量
が少なくなり、良好な耐食性、耐スラグ浸潤性が得られ
なくなる。Further, when ZrO 2 is less than 50 wt% or TiO 2 exceeds 50 wt%, the added amount of ZrO 2 is small and good corrosion resistance and slag infiltration resistance cannot be obtained.
【００３６】一方、ＺｒＯ2が９９ｗｔ％超、または、
ＴｉＯ2が１ｗｔ％未満の場合、ＴｉＯ2の添加量が少な
くなり、緻密なれんが組織が得られず、耐スラグ浸潤性
の低下を招く。On the other hand, ZrO 2 exceeds 99 wt%, or
If the amount of TiO 2 is less than 1 wt%, the amount of TiO 2 added is small, a dense brick structure cannot be obtained, and the slag infiltration resistance deteriorates.
【００３７】また、前述の酸化物粉は、耐火物の総量外
掛けで１０ｗｔ％以上、５０ｗｔ％以下配合する。The above-mentioned oxide powder is blended in an amount of 10 wt% or more and 50 wt% or less based on the total amount of refractory.
【００３８】１０ｗｔ％未満の場合、れんが中に存在す
るＺｒＯ2が少ないため、良好な耐食性が得られない。If it is less than 10 wt%, good corrosion resistance cannot be obtained because the amount of ZrO 2 present in the brick is small.
【００３９】一方、５０ｗｔ％部超の場合、微粉部中の
ＺｒＯ2が多くなり、耐食性の向上は図られる。On the other hand, if it exceeds 50 wt%, the amount of ZrO 2 in the fine powder portion increases, and the corrosion resistance is improved.
【００４０】しかし、れんが焼成時に、ＺｒＯ2の周辺
のＭｇＯやＣａＯと反応して安定化されていないＺｒＯ
2量が増え、異常膨張が生じ、微粉部に亀裂が生じ、れ
んが自体の緻密化が図られなくなる。However, when the brick is fired, it reacts with MgO and CaO around ZrO 2 and is not stabilized.
2 The amount increases, abnormal expansion occurs, cracks occur in the fine powder part, and the brick itself cannot be densified.
【００４１】本発明のれんが作成に際して、前述の条件
に従い原料を配合し、混練、加圧成形後、焼成すること
により、本発明の塩基性耐火物を得ることができる。In producing the brick of the present invention, the basic refractory material of the present invention can be obtained by blending the raw materials according to the above-mentioned conditions, kneading, press-molding and firing.
【００４２】[0042]
【実施例】以下、本発明の実施例を表１に示し、その明
細を説明する。EXAMPLES Examples of the present invention are shown in Table 1 below, and the specifications thereof will be described.
【００４３】表１に本発明において製造した耐火物
（１）〜（７）および比較品（８）〜（１７）の微粉部
と骨材を各種重量比に組み合わせ、混錬・成形後、焼成
した耐火物の耐食性、耐スラグ浸潤性および耐スポーリ
ング性を示す。Table 1 shows the refractory materials (1) to (7) and the comparative products (8) to (17) produced in the present invention, which are combined in various weight ratios with the fine powder portion, kneaded and molded, and then fired. It exhibits corrosion resistance, slag infiltration resistance and spalling resistance of the refractory.
【００４４】なお、表２に比較品（８）のマグネシア―
クロミア質れんが、比較品（９）のマグネシア―スピネ
ル質れんが、および、比較品（１０）のマグネシア―ド
ロマイト質れんがの化学組成を示す。これらのれんが
は、それぞれ、１８００℃で６時間焼成を実施した製品
である。Table 2 shows the magnesia of the comparative product (8).
The chemical composition of the chromia brick, the magnesia-spinel brick of the comparative product (9), and the magnesia-dromite brick of the comparative product (10) are shown. Each of these bricks is a product fired at 1800 ° C. for 6 hours.
【００４５】表１における耐食性指数および耐スラグ浸
潤性指数は、１６００℃で、組成ＳｉＯ2＝１０ｗｔ
％、ＣａＯ＝５５ｗｔ％、Ａｌ2Ｏ3＝１５ｗｔ％、Ｆｅ
Ｏ＝１０ｗｔ％、ＭｇＯ＝１０ｗｔ％のスラグを侵食剤
とする回転侵食試験における各材料の侵食量とスラグ浸
潤量を、比較品（８）のマグネシア―クロミア質れんが
の侵食量、耐スラグ浸潤性を１００とする指数で示した
もので、それぞれの数値が小さいほど、耐食性、耐スラ
グ浸潤性に優れることを示している。In Table 1, the corrosion resistance index and the slag infiltration resistance index are 1600 ° C. and the composition SiO 2 = 10 wt.
%, CaO = 55 wt%, Al 2 O 3 = 15 wt%, Fe
The erosion amount and slag infiltration amount of each material in the rotary erosion test using O = 10 wt% and MgO = 10 wt% slag as an erosion agent are compared with the erosion amount of the magnesia-chromia brick of the comparative product (8) and the slag infiltration resistance. Is shown as an index, and the smaller each value is, the better the corrosion resistance and the slag infiltration resistance are.
【００４６】表１において、耐食性、耐スラグ浸潤性評
価とは、耐食性、耐スラグ浸潤性が１００未満の優れる
ものを○、１００以上を×とした。In Table 1, the corrosion resistance and the slag infiltration resistance are evaluated as ◯ when the corrosion resistance and slag infiltration resistance are less than 100 and x when 100 or more.
【００４７】また、耐熱スポーリング性耐用回数は、１
５００℃での空冷スポーリング試験における各材料の耐
用回数を示したもので、それぞれの数値が大きいほど、
耐熱スポーリング性に優れることを示している。The number of times the heat-resistant spalling resistance is used is 1
The number of times each material was used in the air cooling spalling test at 500 ° C. is shown.
It shows that it has excellent heat spalling resistance.
【００４８】耐熱スポーリング性評価とは、比較品
（８）のマグクロ質ダイレクトボンドれんがの耐熱スポ
ーリング性耐用回数１０回を基準として、１０回を超え
た場合を○、１０回以下を×とした。The heat-resistant spalling property evaluation means that the heat-resistant spalling property of the comparative product (8), magrophilic direct-bonded brick, is 10 when it is more than 10 times, and X is 10 times or less. did.
【００４９】さらに、総合評価とは、耐スラグ浸潤性評
価、耐食性評価および耐熱スポーリング性評価のいずれ
もが○の場合に○、評価の内、１つでも×がある場合
か、あるいはいずれもが×の場合には、×とした。ま
た、組成番号とは、表２において化学組成を示す番号で
ある。Further, the comprehensive evaluation means that when all of the slag infiltration resistance evaluation, the corrosion resistance evaluation and the heat resistant spalling resistance evaluation are ◯, the evaluation is ◯, and at least one of the evaluations is ×, or both. When was x, it was marked as x. Further, the composition number is a number indicating the chemical composition in Table 2.
【００５０】表１において、（１）〜（７）に示す本発
明の耐火物は、比較品（８）のマグネシア―クロミア質
れんが、比較品（９）のマグネシア―スピネル質れん
が、比較品（１０）のマグネシア―ドロマイト質れんが
ならびに、比較品（１１）〜（１７）と比べて、良好な
耐食性、耐スラグ浸潤性および耐熱スポーリング性が得
られた。In Table 1, the refractories of the present invention shown in (1) to (7) are the magnesia-chromia bricks of the comparative product (8) and the magnesia-spinel bricks of the comparative product (9). Good corrosion resistance, slag infiltration resistance, and heat resistant spalling resistance were obtained as compared with the magnesia-dolomite brick of 10) and the comparative products (11) to (17).
【００５１】[0051]
【表１】 [Table 1]
【００５２】[0052]
【表２】 [Table 2]
【００５３】[0053]
【発明の効果】本発明によって得られた耐火物は、マグ
クロ質れんがのように、公害発生防止のために行われる
廃棄処理工程を省略することができるだけでなく、溶融
金属精錬容器、特にＤＨ法、ＲＨ法、ＶＯＤ法などの真
空脱ガス容器の耐用性を大幅に延長することができ、さ
らには、製鉄の二次精錬プロセスにおけるコストを大幅
に下げることができる。INDUSTRIAL APPLICABILITY The refractory material obtained according to the present invention can not only omit the waste treatment step for preventing the occurrence of pollution, such as magric brick, but can also melt metal refining vessels, especially the DH method. , The RH method, the VOD method and the like can significantly extend the durability of the vacuum degassing vessel, and further, can significantly reduce the cost in the secondary refining process of iron making.
Claims (2)
％と、残部５００μｍ以下の微粉部で構成された、１７
００℃以上の高融点を有する塩基性耐火物原料の１種ま
たは２種以上からなる、耐火物骨材に、０．５〜５０μ
ｍの粒度範囲にある、ＺｒＯ2：５０〜９９ｗｔ％、お
よびＴｉＯ2：１〜５０ｗｔ％の酸化物粉を、前記耐火
物の総量外掛けで１０〜５０ｗｔ％同時に配合したの
ち、焼成して得られる塩基性耐火物。1. Coarse particles of 500 μm or more: 60 to 90 wt
%, And the balance consisting of a fine powder portion of 500 μm or less, 17
A refractory aggregate composed of one or more basic refractory raw materials having a high melting point of 00 ° C. or higher has 0.5 to 50 μm.
The oxide powders of ZrO 2 : 50 to 99 wt% and TiO 2 : 1 to 50 wt% in the particle size range of m were simultaneously mixed with the total amount of the refractory material in an amount of 10 to 50 wt%, and then obtained by firing. Basic refractory used.
耐火物原料が、ＭｇＯ成分および／またはＣａＯ成分を
含み、ＺｒＯ2成分およびＴｉＯ2成分として不純物また
はバインダー起源のもの以外を含まないものであること
を特徴とする請求項１記載の塩基性耐火物。2. A basic refractory raw material having a high melting point of 1700 ° C. or higher contains a MgO component and / or a CaO component, and does not contain impurities or a binder origin other than ZrO 2 component and TiO 2 component. The basic refractory material according to claim 1, wherein the basic refractory material is present.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6101629A JPH07291714A (en) | 1994-04-15 | 1994-04-15 | Basic refractory |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6101629A JPH07291714A (en) | 1994-04-15 | 1994-04-15 | Basic refractory |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07291714A true JPH07291714A (en) | 1995-11-07 |
Family
ID=14305698
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6101629A Withdrawn JPH07291714A (en) | 1994-04-15 | 1994-04-15 | Basic refractory |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07291714A (en) |
-
1994
- 1994-04-15 JP JP6101629A patent/JPH07291714A/en not_active Withdrawn
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