JP2003033849A - Mold powder for continuous casting - Google Patents
Mold powder for continuous castingInfo
- Publication number
- JP2003033849A JP2003033849A JP2001219460A JP2001219460A JP2003033849A JP 2003033849 A JP2003033849 A JP 2003033849A JP 2001219460 A JP2001219460 A JP 2001219460A JP 2001219460 A JP2001219460 A JP 2001219460A JP 2003033849 A JP2003033849 A JP 2003033849A
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- powder
- mass
- molten steel
- continuous casting
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Abstract
Description
【発明の詳細な説明】
【０００１】
【発明の属する技術分野】本発明は、連続鋳造用モール
ドパウダーを用いて連続鋳造を行なうにあたって潤滑性
を安定して維持することによって、潤滑不良に起因する
ブレークアウトや鋳片表面品質の劣化の防止に優れた効
果を有する連続鋳造用モールドパウダー（以下、パウダ
ーという）に関する。
【０００２】
【従来の技術】一般に、溶鋼の連続鋳造を行なう際に、
鋳型と鋳片との潤滑，鋳型内の溶鋼の保温，溶鋼浴面の
酸化防止を目的として、鋳型内の溶鋼浴面にパウダーを
投入する。溶鋼には、その精錬工程で施される脱酸処理
等によって生成した Al2Ｏ3 が残留しているので、鋳型
内に溶鋼を注入したときに Al2Ｏ3 が溶鋼内を浮上して
パウダーに取り込まれる。
【０００３】特に、Alを 0.010質量％以上含有する溶鋼
の連続鋳造を行なう場合は、溶鋼に含有されるAlが、下
記の (1)式および (2)式で表わされるように、パウダー
に含有されるSiＯ2 やMnＯと反応して Al2Ｏ3 を生成す
る。 この反応によって生成した Al2Ｏ3 もパウダーに取
り込まれる。
４［Al］＋３（SiＯ2 ）→２（ Al2Ｏ3 ）＋３［Si］ ・・・ (1)
２［Al］＋３（MnＯ） → （ Al2Ｏ3 ）＋３［Mn］ ・・・ (2)
［Al］ ：溶鋼中のAl
［Si］ ：溶鋼中のSi
［Mn］ ：溶鋼中のMn
（SiＯ2 ） ：パウダー中のSiＯ2
（MnＯ） ：パウダー中のMnＯ
（ Al2Ｏ3 ）：パウダー中の Al2Ｏ3
したがって、Alを 0.010質量％以上含有する溶鋼の連続
鋳造を行なう場合は、パウダー中の Al2Ｏ3 量が増加す
る。その結果、パウダー内に高融点の２CaＯ・Al2Ｏ3
・SiＯ2 （すなわちゲーレナイト）を生成しやすくな
り、潤滑性が劣化する原因になる。
【０００４】そこで連続鋳造を行なう際に、パウダー中
の Al2Ｏ3 量が増加しても安定した潤滑性を維持し、ブ
レークアウトや鋳片の表面欠陥を抑制して優れた表面品
質を有する鋳片を得るために、種々の技術が提案されて
いる。たとえば特開昭61-186155 号公報には、BaＯや L
i2Ｏを含有し、かつBaＯ＋CaＯ＋SiＯ2 およびCaＯ／Si
Ｏ2 を好適範囲に調整したパウダーが開示されている。
また特開昭61-10052号公報には、融点，粘度およびCaＯ
／SiＯ2 を好適範囲に調整したパウダーが開示されてい
る。さらに特開平3-77753 号公報には、SiＯ2と Al2Ｏ
3 の含有量を好適範囲に調整したパウダーが開示されて
いる。
【０００５】しかしながら、これらのパウダーは、いず
れもSiＯ2 を10〜40質量％含有している。そのため (1)
式および (2)式によるテルミット反応（すなわち発熱反
応）が生じるので、さらに下記の問題が発生する可能性
がある。
メニスカス部において凝固遅れが生じるので、オシレ
ーションマークに沿った凝固シェルの小規模な破断（以
下、ブリードという）が発生する。
還元されたSiが溶鋼中に溶け込むので、溶鋼のSi含有
量が増大する。一方、溶鋼中のAlが酸化されて Al2Ｏ3
が生成する。その結果、溶鋼成分が変動する。
テルミット反応により火炎が発生するので、設備故障
や操業停止を引き起こす原因になる。
【０００６】このようなSiＯ2 に起因する問題点を解消
するために、特開昭63-56019号公報には、SiＯ2 を極力
添加せずに (1)式の反応を抑制するパウダーが開示され
ている。しかしこの技術では、塩基度（すなわちCaＯ／
SiＯ2 ）の調整が困難であるから、パウダーの粘度が不
安定となる。その結果、鋳型と鋳片との間に流入するパ
ウダー量が不均一となり、潤滑不良が発生する。
【０００７】そこで特開平5-185195号公報には、CaＯ，
Al2Ｏ3 ，TiＯ2 ， Li2Ｏ，BaＯ，MgＯおよび Na2Ｏを
主成分とし、SiＯ2 を殆ど含有せず、しかも潤滑不良が
発生しないパウダーが開示されている。しかしこの技術
では、Al含有量の高い溶鋼の連続鋳造を行なう場合に、
鋳造速度を増速すると、鋳型と鋳片との間に流入するパ
ウダー量が不均一となり、潤滑不良が発生する。 したが
って連続鋳造の生産性向上の観点から、さらなる改善の
余地があった。
【０００８】
【発明が解決しようとする課題】本発明は上記のような
問題を解消し、スラグ還元性金属（たとえばAl，Ti，希
土類元素等）の含有量の高い溶鋼の連続鋳造を行なうに
あたって、鋳造速度の高い領域においても潤滑性を安定
して維持できるパウダーを提供することを目的とする。
【０００９】
【課題を解決するための手段】本発明は、Ｃを 0.5〜4.
0 質量％，CaＯを10〜40質量％， Al2Ｏ3 を10〜40質量
％， Li2Ｏを３〜20質量％，BaＯを５〜40質量％，Ｆ化
合物をＦ換算で15質量％以下含有し、残部が不可避的不
純物からなる組成を有する連続鋳造用モールドパウダー
である。
【００１０】
【発明の実施の形態】本発明者らの実験によると、前記
のような問題は、CaＯ− Al2Ｏ3 系を基本組成とし、こ
れに融点降下作用の大きい Li2Ｏを添加したパウダーを
使用することによって解決できることが分かった。 すな
わち本発明のパウダーは、CaＯを10〜40質量％， Al2Ｏ
3 を10〜40質量％， Li2Ｏを３〜20質量％，BaＯを５〜
40質量％，Ｆ化合物をＦ換算で15質量％以下含有し、さ
らに骨材としてＣを 0.5〜4.0質量％含有する。
【００１１】従来は、パウダーの低融点化とガラス化の
促進を目的として、SiＯ2 をパウダーに添加していた。
しかしスラグ還元性金属（たとえばAl，Ti，希土類元素
等）を含有する溶鋼の連続鋳造を行なう際に、SiＯ2 を
多量に含有するパウダーを使用すると、 (1)式の反応に
よって Al2Ｏ3 が生成される。この Al2Ｏ3 は、溶鋼浴
面のパウダーに取り込まれるので、パウダー中の Al2Ｏ
3 量が増加する。その結果、パウダー内に高融点の２Ca
Ｏ・ Al2Ｏ3 ・SiＯ2 （すなわちゲーレナイト）が生成
する。
【００１２】これに対して、パウダーにSiＯ2 を添加せ
ず、 Li2Ｏを３〜20質量％添加すると、パウダーの融点
が低下するという効果がある。また、 Li2Ｏは、 Al2Ｏ
3 の活量を高めて、溶鋼中のAlの酸化を抑制する効果も
ある。 Li2Ｏ含有量が３質量％未満では、このような効
果は発揮されない。一方、 Li2Ｏ含有量が20質量％を超
えると、 Li2Ｏが還元されやすくなり、かえって Al2Ｏ
3 の生成を促進して融点を高める結果となる。したがっ
て、 Li2Ｏは３〜20質量％の範囲内を満足する必要があ
る。なお、 Li2Ｏの還元反応は下記の (3)式で表わされ
る。
【００１３】
ｎ［Ｍ］＋ｍ（ Li2Ｏ）→２ｍ［Li］＋（Ｍn Ｏm ） ・・・ (3)
Ｍ ：スラグ還元性金属（たとえばAl）
［Ｍ］ ：溶鋼中のＭ
［Li］ ：溶鋼中のLi
（ Li2Ｏ） ：パウダー中のLiＯ2
（Ｍn Ｏm ）：パウダー中のＭn Ｏm （Ｍの酸化物）
ｍ，ｎ ：係数
CaＯは、 Al2Ｏ3 とともに、溶鋼浴面でパウダーを溶融
状態に保って溶鋼の保温や酸化防止、あるいは鋳型と鋳
片との潤滑というパウダーの機能を発揮するために必要
な成分である。CaＯと Al2Ｏ3 の含有量は、それぞれ10
〜40％が適量である。 すなわち、融点，粘度を上昇させ
てパウダーとしての潤滑機能を損なうことのないように
上限値を制限する必要がある。また、CaＯ， Al2Ｏ3 が
外来性介在物として混入した場合でも大きな物性変化を
起こさせないことも必要である。このような観点から、
他の成分との関係を考えると、CaＯ， Al2Ｏ3 ともに40
％が上限値である。 一方、10％未満になると、他の成分
の配合比率が増大して、前述した各成分の上限値を超え
ることになる。したがって下限値を10％とした。
【００１４】BaＯは、結晶の析出を防止し、かつパウダ
ーの粘度を低下させるために添加する。しかもスラグ還
元性金属（たとえばAl）と反応しない（還元されない）
ので、BaＯの添加による効果が安定して発揮される。Ba
Ｏ含有量が５質量％未満では、結晶の析出を防止する効
果が得られない。 一方、BaＯ含有量が40質量％を超える
と、パウダーの粘度を低下させる効果が飽和する。した
がって、BaＯは５〜40質量％の範囲内を満足する必要が
ある。
【００１５】Ｆ化合物は、パウダーの融点および粘度を
調整するために添加する。Ｆ化合物の含有量がＦ換算で
15質量％を超えると、融点や粘度を調整する効果が飽和
するばかりでなく、パウダー中の他の成分と反応して弗
化物を生成する。その弗化物がガス化して白煙を生じる
ので、連続鋳造の操業に支障をきたす。 したがって、Ｆ
化合物はＦ換算で15質量％以下とした。なお、好ましく
は５〜10質量％である。
【００１６】Ｆ化合物としては特に限定するものではな
く、パウダーの媒溶剤として通常使用されるLiＦやNaＦ
等が使用できる。Ｃは、骨材として添加する。Ｃ含有量
が 0.5質量％未満では、骨材としての効果が得られな
い。 一方、Ｃ含有量が 4.0質量％を超えると、 (1)式，
(2) 式あるいは (3)式の発熱反応が生じたときに、Ｃが
燃焼して火炎が発生して、設備故障や操業停止を引き起
こす原因になる。したがって、Ｃは 0.5〜4.0 質量％の
範囲内を満足する必要がある。
【００１７】
【実施例】表１に示す２種類の成分の溶鋼を溶製し、次
いで断面サイズ 200mm×1000mmのスラブの連続鋳造を行
なった。 パウダーは表２に示す５種類の成分のものを使
用し、鋳造速度は 0.5〜0.8 ｍ／min とした。パウダー
Ｂ，Ｃ，Ｄ，Ｅは本発明のパウダーの例であり、パウダ
ーＡは従来のTiＯ2 ， Na2Ｏを含有するパウダーの例で
ある。
【００１８】
【表１】
【００１９】
【表２】【００２０】こうして連続鋳造を行ないながら、煙や炎
の発生状況を調査した。 また、得られた鋳片を観察し
て、ブリード発生数（個／ｍ2 ）およびパウダー噛み込
み数（個／ｍ2 ）を調査した。 さらに、これらの表面欠
陥の手入れを行ない、手入れ歩留りを調査した。その結
果は、表３に示す通りである。なお、手入れ歩留りは、
下記の (4)式で算出される値である。
【００２１】
手入れ歩留り（％）＝
100×（手入れ後の重量）／（手入れ前の重量） ・・・ (4)
【００２２】
【表３】
【００２３】表３から明らかなように、Al，Ti，希土類
元素等のスラグ還元性金属を含有する溶鋼の連続鋳造を
行なう場合に、鋳造速度で比較すると、本発明のパウダ
ーを使用することによって、操業時に煙や炎の発生が抑
えられた。 しかも本発明のパウダーを使用することによ
って、同一鋳造速度において鋳片の表面欠陥が減少し、
手入れ歩留りが向上した。特に、鋳造速度が高い場合に
おいて、その効果は顕著であった。
【００２４】
【発明の効果】本発明では、スラグ還元性金属（たとえ
ばAl，Ti，希土類元素等）の含有量の高い溶鋼の連続鋳
造を行なうにあたって、鋳造速度の高い領域においても
潤滑性を安定して維持することによって、潤滑不良に起
因するブレークアウトや鋳片表面品質の劣化を防止でき
る。Description: BACKGROUND OF THE INVENTION [0001] 1. Field of the Invention [0002] The present invention relates to poor lubrication by maintaining stable lubricity when performing continuous casting using a mold powder for continuous casting. The present invention relates to a continuous casting mold powder (hereinafter, referred to as powder) having an excellent effect of preventing breakout and deterioration of cast slab surface quality. [0002] Generally, when performing continuous casting of molten steel,
Powder is poured into the molten steel bath surface in the mold for the purpose of lubricating the mold and the slab, keeping the molten steel in the mold warm, and preventing oxidation of the molten steel bath surface. Since Al 2 O 3 generated by the deoxidation treatment etc. in the refining process remains in the molten steel, when the molten steel is poured into the mold, the Al 2 O 3 floats in the molten steel and the powder It is taken in. [0003] In particular, when performing continuous casting of molten steel containing 0.010 mass% or more of Al, the Al contained in the molten steel is contained in the powder as represented by the following equations (1) and (2). Reacts with the SiO 2 or MnO to form Al 2 O 3 . Al 2 O 3 generated by this reaction is also taken into the powder. 4 [Al] +3 (SiO 2 ) → 2 (Al 2 O 3 ) +3 [Si] (1) 2 [Al] +3 (MnO) → (Al 2 O 3 ) +3 [Mn] (( 2) [Al]: Al in the molten steel [Si]: Si in the molten steel [Mn]: Mn in the molten steel (SiO 2): SiO 2 in powder (MnO): MnO in powder (Al 2 O 3) : Al 2 O 3 in powder Therefore, when continuous casting of molten steel containing 0.010% by mass or more of Al is performed, the amount of Al 2 O 3 in the powder increases. As a result, high melting point 2CaO.Al 2 O 3
· SiO 2 (i.e. gehlenite) likely to generate, cause the lubricity is deteriorated. Therefore, when continuous casting is performed, even if the amount of Al 2 O 3 in the powder is increased, stable lubricity is maintained, and breakout and surface defects of the slab are suppressed to provide excellent surface quality. Various techniques have been proposed for obtaining cast slabs. For example, JP-A-61-186155 discloses BaO and L
containing i 2 O, and BaO + CaO + SiO 2 and CaO / Si
A powder in which O 2 is adjusted to a suitable range is disclosed.
Japanese Patent Application Laid-Open No. 61-10052 discloses melting point, viscosity and CaO.
/ Powder adjusted for SiO 2 in the preferable range is disclosed. Further, JP-A-3-77753 discloses that SiO 2 and Al 2 O
3 powder was adjusted to the preferred range the content of is disclosed. However, all of these powders contain 10 to 40% by mass of SiO 2 . Therefore (1)
Since a thermite reaction (that is, an exothermic reaction) according to the formula and the formula (2) occurs, the following problem may further occur. Since a solidification delay occurs in the meniscus portion, a small-scale fracture (hereinafter, referred to as bleed) of the solidified shell occurs along the oscillation mark. Since the reduced Si melts into the molten steel, the Si content of the molten steel increases. On the other hand, Al in the molten steel is oxidized to Al 2 O 3
Is generated. As a result, the molten steel component fluctuates. A flame is generated by the thermite reaction, which may cause equipment failure or operation shutdown. In order to solve such problems caused by SiO 2 , JP-A-63-56019 discloses a powder which suppresses the reaction of the formula (1) without adding SiO 2 as much as possible. Have been. However, in this technique, the basicity (ie, CaO /
Since the adjustment of SiO 2 ) is difficult, the viscosity of the powder becomes unstable. As a result, the amount of powder flowing between the mold and the slab becomes uneven, and poor lubrication occurs. [0007] Japanese Patent Application Laid-Open No. 5-185195 discloses CaO,
A powder containing Al 2 O 3 , TiO 2 , Li 2 O, BaO, MgO and Na 2 O as main components, containing almost no SiO 2 , and causing no poor lubrication is disclosed. However, in this technology, when performing continuous casting of molten steel with a high Al content,
When the casting speed is increased, the amount of powder flowing between the mold and the slab becomes uneven, resulting in poor lubrication. Therefore, there is room for further improvement from the viewpoint of improving the productivity of continuous casting. SUMMARY OF THE INVENTION [0008] The present invention solves the above-mentioned problems, and is used for continuous casting of molten steel having a high content of slag reducing metals (eg, Al, Ti, rare earth elements, etc.). It is another object of the present invention to provide a powder capable of stably maintaining lubricity even in a high casting speed region. According to the present invention, C is set to 0.5 to 4.
0 wt%, 10 to 40 wt% of CaO, the Al 2 O 3 10 to 40 wt%, the Li 2 O 3 to 20 wt%, a BaO 5 to 40 wt%, 15 wt% of compound F in terms of F It is a mold powder for continuous casting which contains the following and has the balance of inevitable impurities. DETAILED DESCRIPTION OF THE INVENTION According to experiments conducted by the present inventors, the above-described problem is caused by the fact that a basic composition of a CaO--Al 2 O 3 system is used, and Li 2 O having a large melting point lowering action is added thereto. It has been found that the problem can be solved by using powder. That powder of the present invention, 10 to 40 wt% of CaO, Al 2 O
3 10 to 40 wt%, 3 to 20 wt% of Li 2 O,. 5 to the BaO
It contains 40% by mass and 15% by mass or less of an F compound in terms of F, and further contains 0.5 to 4.0% by mass of C as an aggregate. Conventionally, SiO 2 has been added to powder for the purpose of lowering the melting point of the powder and promoting vitrification.
However, when performing continuous casting of molten steel containing a slag-reducing metal (eg, Al, Ti, rare earth element, etc.), if a powder containing a large amount of SiO 2 is used, Al 2 O 3 is obtained by the reaction of equation (1). Is generated. The Al 2 O 3, since incorporated into powder of the molten steel bath surface, Al 2 O in the powder
3 amount increases. As a result, high melting point 2Ca
O · Al 2 O 3 · SiO 2 ( i.e. gehlenite) is produced. On the other hand, if 3 to 20% by mass of Li 2 O is added without adding SiO 2 to the powder, there is an effect that the melting point of the powder is lowered. Li 2 O is Al 2 O
It also has the effect of increasing the activity of 3 and suppressing the oxidation of Al in the molten steel. If the Li 2 O content is less than 3% by mass, such an effect is not exhibited. On the other hand, when the content of Li 2 O exceeds 20 mass%, the Li 2 O is easily reduced, rather Al 2 O
As a result, the formation of 3 is promoted and the melting point is increased. Therefore, Li 2 O needs to satisfy the range of 3 to 20% by mass. The reduction reaction of Li 2 O is represented by the following equation (3). N [M] + m (Li 2 O) → 2 m [Li] + (M n O m ) (3) M: slag reducing metal (for example, Al) [M]: M in molten steel li]: in the molten steel Li (Li 2 O): LiO in powder 2 (M n O m): ( oxides of M) M n O m in powder m, n: coefficients CaO is, Al 2 O 3 At the same time, it is a component necessary for maintaining the powder in a molten state on the surface of the molten steel bath to maintain the temperature and prevent oxidation of the molten steel, or to exert the function of the powder of lubricating the mold and the slab. The contents of CaO and Al 2 O 3 were 10
~ 40% is appropriate. That is, it is necessary to limit the upper limit so that the melting point and the viscosity are not increased and the lubrication function as the powder is not impaired. In addition, it is necessary to prevent large changes in physical properties even when CaO and Al 2 O 3 are mixed as exogenous inclusions. From this perspective,
Considering the relationship with other components, both CaO and Al 2 O 3
% Is the upper limit. On the other hand, if it is less than 10%, the mixing ratio of other components increases, and exceeds the upper limit of each component described above. Therefore, the lower limit was set to 10%. BaO is added to prevent precipitation of crystals and reduce the viscosity of the powder. Moreover, it does not react with slag reducing metal (for example, Al) (it is not reduced)
Therefore, the effect of adding BaO is stably exhibited. Ba
If the O content is less than 5% by mass, the effect of preventing the precipitation of crystals cannot be obtained. On the other hand, if the BaO content exceeds 40% by mass, the effect of reducing the viscosity of the powder is saturated. Therefore, BaO needs to satisfy the range of 5 to 40% by mass. The F compound is added to adjust the melting point and viscosity of the powder. When the content of F compound is converted to F
If it exceeds 15% by mass, the effect of adjusting the melting point and viscosity is not only saturated, but also reacts with other components in the powder to produce fluoride. The fluoride gasifies and produces white smoke, which hinders the operation of continuous casting. Therefore, F
The compound was 15% by mass or less in terms of F. In addition, it is preferably 5 to 10% by mass. The F compound is not particularly limited, and LiF and NaF which are commonly used as a solvent for the powder are used.
Etc. can be used. C is added as an aggregate. If the C content is less than 0.5% by mass, the effect as an aggregate cannot be obtained. On the other hand, when the C content exceeds 4.0% by mass, the equation (1),
When the exothermic reaction of the formula (2) or (3) occurs, C is burned to generate a flame, which may cause equipment failure or operation stop. Therefore, C needs to satisfy the range of 0.5 to 4.0% by mass. EXAMPLES Molten steel having two components shown in Table 1 was smelted, and then a slab having a cross section of 200 mm × 1000 mm was continuously cast. The powder used had five components as shown in Table 2, and the casting speed was 0.5 to 0.8 m / min. Powders B, C, D, and E are examples of the powder of the present invention, and powder A is an example of a conventional powder containing TiO 2 and Na 2 O. [Table 1] [Table 2] While performing continuous casting in this way, the state of generation of smoke and flame was investigated. In addition, the obtained slab was observed, and the number of bleeds generated (pieces / m 2 ) and the number of powder bites (pieces / m 2 ) were examined. Furthermore, these surface defects were repaired and the repair yield was investigated. The results are as shown in Table 3. In addition, the care yield
This is a value calculated by the following equation (4). Maintenance yield (%) = 100 × (weight after maintenance) / (weight before maintenance) (4) As is apparent from Table 3, when performing continuous casting of molten steel containing slag reducing metals such as Al, Ti, and rare earth elements, when the casting speed is compared, the use of the powder of the present invention shows that During operation, the generation of smoke and flame was reduced. Moreover, by using the powder of the present invention, surface defects of the slab are reduced at the same casting speed,
The maintenance yield has improved. In particular, when the casting speed was high, the effect was remarkable. According to the present invention, when performing continuous casting of molten steel having a high content of slag reducing metals (eg, Al, Ti, rare earth elements, etc.), lubricity is stabilized even in a high casting speed region. By maintaining this, breakout and deterioration of the surface quality of the slab due to poor lubrication can be prevented.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 糸山 誓司 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 (72)発明者 柏 孝幸 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社千葉製鉄所内 (72)発明者 吉田 孝行 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社千葉製鉄所内 (72)発明者 光宗 隆裕 兵庫県神戸市須磨区大池町３−１−26 坂 井化学工業株式会社神戸工場内 Ｆターム(参考） 4E004 JA00 NC01 ────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Soji Itoyama 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Iron Research Institute (72) Inventor Takayuki Kashiwa 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Inside the Iron Corporation Chiba Works (72) Inventor Takayuki Yoshida 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Inside the Iron Corporation Chiba Works (72) Inventor Takahiro Mitsumune Saka Ward, Kobe City, Hyogo Prefecture Inside the Kobe factory of Ii Chemical Industry Co., Ltd. F-term (reference) 4E004 JA00 NC01
Claims (1)
量％、 Al2Ｏ3 を10〜40質量％、 Li2Ｏを３〜20質量
％、BaＯを５〜40質量％、Ｆ化合物をＦ換算で15質量％
以下含有し、残部が不可避的不純物からなる組成を有す
ることを特徴とする連続鋳造用モールドパウダー。Claims We claim: 1. A C to 0.5 to 4.0 mass%, the CaO 10 to 40 wt%, the Al 2 O 3 10 to 40 wt%, 3 to 20 wt% of Li 2 O, BaO, 5 to 40% by mass, F compound 15% by mass in terms of F
A mold powder for continuous casting, characterized in that it contains the following and the balance consists of unavoidable impurities.
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| JP2001219460A JP4554120B2 (en) | 2001-07-19 | 2001-07-19 | Mold powder for continuous casting |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006110578A (en) * | 2004-10-13 | 2006-04-27 | Sanyo Special Steel Co Ltd | Mold powder for continuously casting high aluminum-containing steel and method for continuously casting high aluminum-containing steel using the powder |
| JP2006247712A (en) * | 2005-03-11 | 2006-09-21 | Jfe Steel Kk | Mold powder for continuous casting of steel |
| KR100992925B1 (en) | 2003-12-17 | 2010-11-08 | 주식회사 포스코 | Mold flux used in continuos casting of isotropic electromagnetic steel slab |
| CN104107890A (en) * | 2013-04-19 | 2014-10-22 | 宝山钢铁股份有限公司 | Continuously-cast mold powder for cold-rolled sheet steel and production method thereof |
| US10486227B2 (en) * | 2014-06-24 | 2019-11-26 | Thyssenkrupp Steel Europe Ag | Casting powder, casting slag and method for casting steel |
| CN111331093A (en) * | 2020-02-12 | 2020-06-26 | 钢铁研究总院 | Casting powder for rare earth microalloyed steel bar crystallizer and preparation and application methods thereof |
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| JPH05185195A (en) * | 1991-09-05 | 1993-07-27 | Kawasaki Steel Corp | Mold powder for continuous casting |
| JPH0985404A (en) * | 1995-09-19 | 1997-03-31 | Nippon Yakin Kogyo Co Ltd | Flux for continuously casting a1-containing molten steel and continuous casting method |
| JP2000000646A (en) * | 1998-06-17 | 2000-01-07 | Nippon Steel Metal Prod Co Ltd | Mold flux for continuous casting |
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2001
- 2001-07-19 JP JP2001219460A patent/JP4554120B2/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05185195A (en) * | 1991-09-05 | 1993-07-27 | Kawasaki Steel Corp | Mold powder for continuous casting |
| JPH0985404A (en) * | 1995-09-19 | 1997-03-31 | Nippon Yakin Kogyo Co Ltd | Flux for continuously casting a1-containing molten steel and continuous casting method |
| JP2000000646A (en) * | 1998-06-17 | 2000-01-07 | Nippon Steel Metal Prod Co Ltd | Mold flux for continuous casting |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100992925B1 (en) | 2003-12-17 | 2010-11-08 | 주식회사 포스코 | Mold flux used in continuos casting of isotropic electromagnetic steel slab |
| JP2006110578A (en) * | 2004-10-13 | 2006-04-27 | Sanyo Special Steel Co Ltd | Mold powder for continuously casting high aluminum-containing steel and method for continuously casting high aluminum-containing steel using the powder |
| JP4610290B2 (en) * | 2004-10-13 | 2011-01-12 | 山陽特殊製鋼株式会社 | Mold powder for continuous casting of high aluminum content steel and method for continuous casting of high aluminum content steel using this powder |
| JP2006247712A (en) * | 2005-03-11 | 2006-09-21 | Jfe Steel Kk | Mold powder for continuous casting of steel |
| JP4708055B2 (en) * | 2005-03-11 | 2011-06-22 | Ｊｆｅスチール株式会社 | Mold powder for continuous casting of steel |
| CN104107890A (en) * | 2013-04-19 | 2014-10-22 | 宝山钢铁股份有限公司 | Continuously-cast mold powder for cold-rolled sheet steel and production method thereof |
| CN104107890B (en) * | 2013-04-19 | 2016-06-01 | 宝山钢铁股份有限公司 | A kind of cold rolled sheet steel continuous casting covering slag and manufacture method thereof |
| US10486227B2 (en) * | 2014-06-24 | 2019-11-26 | Thyssenkrupp Steel Europe Ag | Casting powder, casting slag and method for casting steel |
| CN111331093A (en) * | 2020-02-12 | 2020-06-26 | 钢铁研究总院 | Casting powder for rare earth microalloyed steel bar crystallizer and preparation and application methods thereof |
| CN111331093B (en) * | 2020-02-12 | 2021-06-04 | 钢铁研究总院 | Casting powder for rare earth microalloyed steel bar crystallizer and preparation and application methods thereof |
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| JP4554120B2 (en) | 2010-09-29 |
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