JP3488093B2 - Continuous casting method of molten steel - Google Patents
Continuous casting method of molten steelInfo
- Publication number
- JP3488093B2 JP3488093B2 JP23508498A JP23508498A JP3488093B2 JP 3488093 B2 JP3488093 B2 JP 3488093B2 JP 23508498 A JP23508498 A JP 23508498A JP 23508498 A JP23508498 A JP 23508498A JP 3488093 B2 JP3488093 B2 JP 3488093B2
- Authority
- JP
- Japan
- Prior art keywords
- molten steel
- equiaxed
- slab
- electromagnetic stirring
- mold
- 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.)
- Expired - Lifetime
Links
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Continuous Casting (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Description
【発明の詳細な説明】
【０００１】
【発明の属する技術分野】通常の連続鋳造鋳片の横断面
には、中心にポロシティを伴う最終凝固部を取り囲むよ
うに配された中心近傍の粗い粒状晶部と、粗い粒状晶部
を取り囲む粗い柱状晶部とが観察される。この粗い粒状
晶と粗い柱状晶とを微細な等軸晶にすることができれ
ば、例えばスラブを薄板にした際には成形加工性が顕著
に優れた薄板になり、また例えば厚板にした際には低温
靱性に優れた厚板となる。本発明は、この粗い粒状晶と
柱状晶を微細な等軸晶にできる溶鋼の連続鋳造方法およ
びそれを用いて鋳造した微細な凝固組織を有する連続鋳
造鋳片に関するものである。
【０００２】
【従来の技術】「鉄鋼便覧」第３版、II 製銑・製鋼、
ｐ．６５３には、等軸晶は溶鋼過熱度が低いと増加する
ことから、等軸晶化には低温鋳造が有効であることが示
されている。また、特開昭５０−２３３３８号公報に
は、誘導電磁攪拌装置を用いて、凝固界面近傍の溶鋼に
一方向の旋回流を与え、柱状デンドライトを分断するこ
とにより柱状晶を等軸晶にする技術が記載されている。
現状、凝固組織の等軸晶化には上記２つの技術が最も効
果的であるとされており、これら技術は単独で、又は、
組み合わせて使用することにより凝固組織をある程度等
軸晶化し、鋳片の中心偏析低減に効果を発揮している。
【０００３】
【発明が解決しようとする課題】しかしながら、低温鋳
造では、溶融金属の過熱度を液相線に近い温度にし、こ
れを浸漬ノズルから鋳型内に注入する必要があるため、
浸漬ノズルの閉塞や鋳型内でのディッケル生成等の凝固
異常を招く場合がある。このため、現状の連続鋳造では
注入する溶融金属の過熱度は２０〜３０Ｋ程度を採用し
ており、このような温度条件では薄板の成形加工性や厚
板の低温靱性を改善できる程の微細等軸晶化は達成され
ていない。また、誘導電磁攪拌を用いる方法について
も、材質が改善できるまでの十分な微細等軸晶が安定し
て得られているわけではなく、例えば等軸晶が生成し難
いＣ含有率が０．１％以下の溶鋼に対しては、柱状晶を
十分に等軸晶化することは難しい。
【０００４】本発明は、このような現状を鑑み、中心近
傍の粗い粒状晶とそれを取り囲む粗い柱状晶を、共に微
細な等軸晶にできる連続鋳造方法およびそれを用いて鋳
造した微細な凝固組織を有する連続鋳造鋳片の提供を課
題としている。
【０００５】
【課題を解決するための手段】本発明は、（１）鋳型内
メニスカス〜鋳型下１０ｍの間に誘導電磁攪拌装置を有
する連続鋳造装置を用いて、Ａｌ濃度が０．０５％以下
の溶鋼に、取鍋、タンディッシュあるいは鋳型で溶鋼中
にＭｇを０．０００２〜０．０１％になるように含有せ
しめ、該誘導電磁攪拌装置により水平面内で溶鋼を旋回
流速が３０〜１００ｃｍ／ｓで旋回させながら鋳造する
ことを特徴とする連続鋳造方法である。本発明における
％表示は、すべて重量％を意味する。
【０００６】
【発明の実施の形態】本発明の基本思想は、微細な酸化
物を溶鋼中に分散させ、これに電磁攪拌を加え溶鋼の過
熱度を低下させることにより、微細に分散させた酸化物
を等軸晶生成の核として効率的に活用し、鋳片内に微細
な等軸晶を生成させることにある。この基本思想を実現
するためには、鋳片内で等軸晶の核となり得る微細な
酸化物を生成させる方法と、微細な酸化物を起点に生
成した等軸晶核の再溶解を防止できるように溶鋼過熱度
を低減させた上で、微細に分散させた酸化物が凝集・合
体しない電磁攪拌条件を明らかにすることが重要であ
る。
【０００７】まず、の方法について述べる。Ａｌ脱酸
溶鋼には多数のＡｌ2 Ｏ3 系介在物が存在するが、この
介在物は極めて凝集・合体し易く粗大な酸化物となるた
め、等軸晶の核として有効に作用しない。これに対し、
本発明者らは、溶鋼中にＭｇを添加し、Ａｌ2 Ｏ3 系介
在物をＭｇＯ、或いはＭｇＯ・Ａｌ2 Ｏ3 に改質するこ
とにより、微細な酸化物を溶鋼中に均一に分散できるこ
と、さらにこれら酸化物が等軸晶生成の核になり易いこ
とを見いだした。これは、Ａｌ2 Ｏ3 と比較して、Ｍｇ
ＯやＭｇＯ・Ａｌ2 Ｏ3 は溶鋼と濡れ易いためだと考え
られる。本発明では、溶鋼中のＡｌ濃度は０．０５％以
下であり、これを超えるＡｌ濃度ではＭｇを添加しても
Ａｌ2 Ｏ3 系介在物をＭｇＯ、或いはＭｇＯ・Ａｌ2 Ｏ
3 に改質できず、微細な酸化物を溶鋼中に分散できな
い。また、Ｍｇの添加量は０．０００２〜０．０１％に
規定した。これは、Ｍｇ濃度が０．０００２％未満では
微細な酸化物の量が少なくなることにより、Ｍｇ濃度が
０．０１％を超えると酸化物が粗大化し易くなることに
より、何れも鋳片内の凝固組織を微細な等軸晶にする効
果が失われるためである。
【０００８】次に、について述べる。一般に、電磁攪
拌では、凝固界面の溶鋼に旋回流を付与するため、この
旋回流が柱状デンドライトを分断し、等軸晶化を促進す
ると考えられている。しかし、本発明者等の知見では、
電磁攪拌は柱状デンドライトを流れの上流側に傾ける効
果を有するものの、従来から言われている柱状デンドラ
イトを分断する効果は比較的小さく、むしろ電磁攪拌に
より凝固シェルと溶鋼間の熱伝達が促進され、溶鋼の過
熱度を低下させる効果が高いことを見いだした。本発明
では、この電磁攪拌の溶鋼過熱度を低下させる効果を活
用しており、電磁攪拌により微細な酸化物を起点に生成
した等軸晶核の再溶解を防止している。しかしながら、
電磁攪拌による溶鋼過熱度の低減効果を高めていくため
には、旋回流速を速くする必要があり、その場合微細な
酸化物が凝集・合体により粗大化し、等軸晶の核として
有効に機能しなくなる。そこで、Ｍｇを添加した溶鋼の
連続鋳造実験により等軸晶粒径に及ぼす電磁攪拌の旋回
流速の影響を調査した。なお、柱状晶の場合の粒径も同
時に評価できるように等軸晶粒径は２（ａ・ｂ）0.5 と
定義した（ａは結晶粒の長径、ｂは結晶粒の短径であ
る。）。鋳片横断面の平均等軸晶粒径と電磁攪拌の旋回
流速との関係を図１に示す。図１から分かるように、Ｍ
ｇを添加した鋳片の平均等軸晶粒径は溶鋼の旋回流速が
３０ｃｍ／ｓ以上になると小さくなるが、１００ｃｍ／
ｓを超えると反対に鋳片の平均等軸晶粒径は大きくなり
始める。この原因は、電磁攪拌の旋回流速が３０ｃｍ／
ｓ以上になると微細酸化物を起点に生成した等軸晶核の
再溶鋼が抑制されるのに対し、旋回流速が１００ｃｍ／
ｓを超えるとＭｇＯやＭｇＯ・Ａｌ2 Ｏ3 でも、凝集・
合体による粗大化が進行し、等軸晶の核として機能しな
くなるためだと考えられる。したがって、鋳片の凝固組
織を微細な等軸晶にするためには、電磁攪拌の旋回流速
を３０〜１００ｃｍ／ｓに制御する必要がある。また、
鋳型下１０ｍよりも更に下方では、既に鋳片表層の凝固
はほぼ完了しているため、誘導電磁攪拌は凝固の始まる
鋳型内メニスカスから鋳型下１０ｍの位置に設置すれば
良い。
【０００９】本発明は、上記説明からも分かるように、
スラブへの適用に限られたものではなく、ブルームやビ
レットに適用しても、十分な凝固組織の微細化効果が得
られる。
【００１０】
【実施例】以下に、実施例及び比較例を挙げて、本発明
について説明する。
（実施例１）炭素濃度０．１％、Ａｌ濃度０．０３８％
の取鍋内の溶鋼に１０％Ｍｇ−Ｎｉ合金を添加し、Ｍｇ
濃度を０．００２％に調整した。タンディッシュ内で溶
鋼温度を１５５０℃とし、厚み２５０ｍｍ×幅１５００
ｍｍの鋳片を鋳造速度１．８ｍ／ｍｉｎで鋳造した。誘
導電磁攪拌は鋳型内メニスカスに設置されており、鋳造
中はこの電磁攪拌装置に５００Ａ、周波数２Ｈｚの電流
を流して凝固界面の溶鋼を５０ｃｍ／ｓの旋回流速で攪
拌した。本発明の方法で得られた鋳片を調査したとこ
ろ、鋳片横断面の凝固組織は全て等軸晶化し、その平均
等軸晶粒径は２．３ｍｍであり、鋳片全面の凝固組織は
微細化していた。
【００１１】（比較例１）炭素濃度０．１％、Ａｌ濃度
０．０３８％の取鍋内の溶鋼に１０％Ｍｇ−Ｎｉ合金を
添加し、Ｍｇ濃度を０．００２％に調整した。タンディ
ッシュ内で溶鋼温度を１５５０℃とし、厚み２５０ｍｍ
×幅１５００ｍｍの鋳片を鋳造速度１．８ｍ／ｍｉｎで
鋳造した。鋳造中は電磁攪拌を使用しなかった。本鋳造
で得られた鋳片を調査したところ、鋳片横断面には比較
的長い柱状晶が残留しており、そのため平均等軸晶粒径
も５．０ｍｍで、凝固組織は微細化されていなかった。
【００１２】（比較例２）炭素濃度０．１％、Ａｌ濃度
０．０３８％、溶鋼温度１５５０℃の溶鋼をタンディッ
シュから鋳型内に注入し、厚み２５０ｍｍ×幅１５００
ｍｍの鋳片を鋳造速度１．８ｍ／ｍｉｎで鋳造した。溶
鋼へのＭｇ添加は実施しなかった。誘導電磁攪拌は鋳型
内メニスカスに設置されており、鋳造中はこの電磁攪拌
装置に５００Ａ、周波数２Ｈｚの電流を流して凝固界面
の溶鋼を５０ｃｍ／ｓの旋回流速で攪拌した。本鋳造で
得られた鋳片を調査したところ、鋳片横断面には比較的
長い柱状晶が残留しており、そのため平均等軸晶粒径も
４．１ｍｍで、凝固組織は微細化されていなかった。
【００１３】
【発明の効果】以上に説明したように、本発明による
と、鋳片表層と鋳片内部の凝固組織を、共に微細に等軸
晶化した連続鋳造鋳片を製造することができるため、薄
板では成形加工性に、厚板では低温靱性に優れた材料を
製造することが可能となる。Description: BACKGROUND OF THE INVENTION [0001] The cross section of a normal continuous cast slab has a coarse grain near its center arranged around a final solidified part with porosity in the center. Parts and coarse columnar parts surrounding the coarse granular parts are observed. If this coarse granular crystal and coarse columnar crystal can be made into fine equiaxed crystals, for example, when a slab is made into a thin plate, the formability becomes remarkably excellent, and when, for example, a thick plate is formed, Becomes a thick plate having excellent low-temperature toughness. The present invention relates to a continuous casting method of molten steel capable of converting the coarse granular crystals and columnar crystals into fine equiaxed crystals, and a continuous cast slab having a fine solidified structure cast using the method. [0002] Iron and Steel Handbook, 3rd edition, II Iron and steel making,
p. 653 shows that low-temperature casting is effective for equiaxed crystallization because the equiaxed crystal increases when the degree of superheat of molten steel is low. Japanese Patent Application Laid-Open No. 50-23338 discloses that an induction electromagnetic stirrer is used to apply a unidirectional swirling flow to molten steel near a solidification interface to break columnar dendrites to make columnar crystals equiaxed. The technology is described.
At present, the above two techniques are considered to be the most effective for equiaxed crystallization of the solidified structure, and these techniques are used alone or
When used in combination, the solidification structure is made equiaxed to some extent, which is effective in reducing the center segregation of the slab. [0003] However, in low-temperature casting, it is necessary to set the degree of superheating of the molten metal to a temperature close to the liquidus line and to inject the molten metal into the mold from a dipping nozzle.
Solidification abnormalities such as clogging of the immersion nozzle and deckle formation in the mold may be caused. For this reason, in the current continuous casting, the degree of superheat of the molten metal to be injected is about 20 to 30K. No axial crystallization has been achieved. Also, in the method using induction electromagnetic stirring, a sufficient fine equiaxed crystal is not obtained stably until the material can be improved. For example, the C content at which an equiaxed crystal is hardly generated is 0.1%. % Or less, it is difficult to make columnar crystals sufficiently equiaxed. [0004] In view of the above situation, the present invention provides a continuous casting method capable of forming a coarse granular crystal near the center and a coarse columnar crystal surrounding it into fine equiaxed crystals, and a fine solidification cast using the same. It is an object to provide a continuous cast slab having a structure. [0005] The present invention provides: (1) In a mold
Induction electromagnetic stirrer between meniscus and 10m below mold
Al concentration is 0.05% or less using a continuous casting machine
In a ladle, tundish or mold
Containing 0.0002 to 0.01% of Mg
The molten steel is cast while swirling at a swirling flow rate of 30 to 100 cm / s in a horizontal plane by the induction electromagnetic stirring device.
A continuous casting method characterized by the following. All percentages in the present invention mean% by weight. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS The basic idea of the present invention is to disperse fine oxides in molten steel and to reduce the superheat degree of the molten steel by applying electromagnetic stirring to the finely divided oxides. The object is to efficiently utilize the material as a nucleus for generating an equiaxed crystal and to generate a fine equiaxed crystal in a slab. In order to realize this basic idea, a method of generating a fine oxide that can be a nucleus of an equiaxed crystal in a slab and a re-dissolution of an equiaxed nucleus generated from the fine oxide can be prevented. After reducing the degree of superheat of the molten steel, it is important to clarify the electromagnetic stirring conditions under which the finely dispersed oxides do not agglomerate and coalesce. First, the method will be described. Although a large number of Al 2 O 3 -based inclusions are present in Al deoxidized molten steel, these inclusions are very easy to aggregate and coalesce and become coarse oxides, and thus do not effectively act as nuclei of equiaxed crystals. In contrast,
The present inventors are able to uniformly disperse fine oxides in molten steel by adding Mg to molten steel and modifying Al 2 O 3 -based inclusions to MgO or MgO · Al 2 O 3. Further, they have found that these oxides are likely to become nuclei for the formation of equiaxed crystals. This is because compared to Al 2 O 3 , Mg
It is considered that O and MgO.Al 2 O 3 are easily wetted by molten steel. In the present invention, the Al concentration in the molten steel is 0.05% or less, and at an Al concentration higher than this, even if Mg is added, the Al 2 O 3 -based inclusions are changed to MgO or MgO · Al 2 O.
3 cannot be modified and fine oxides cannot be dispersed in molten steel. Further, the addition amount of Mg was specified to be 0.0002 to 0.01%. This is because when the Mg concentration is less than 0.0002%, the amount of fine oxides decreases, and when the Mg concentration exceeds 0.01%, the oxides are liable to be coarsened. This is because the effect of making the solidified structure a fine equiaxed crystal is lost. Next, will be described. Generally, it is considered that in the electromagnetic stirring, a swirl flow is given to molten steel at a solidification interface, and this swirl flow breaks columnar dendrites and promotes equiaxed crystallization. However, according to the findings of the present inventors,
Although the electromagnetic stirring has the effect of tilting the columnar dendrite to the upstream side of the flow, the effect of dividing the columnar dendrite, which has been conventionally called, is relatively small, and rather, the electromagnetic stirring promotes the heat transfer between the solidified shell and the molten steel, It has been found that the effect of reducing the degree of superheat of molten steel is high. In the present invention, the effect of lowering the degree of superheat of molten steel by electromagnetic stirring is utilized to prevent the re-dissolution of equiaxed nuclei generated from fine oxides as a starting point by electromagnetic stirring. However,
In order to increase the effect of reducing the degree of superheat of molten steel by electromagnetic stirring, it is necessary to increase the swirl flow velocity, in which case fine oxides are coarsened by aggregation and coalescence, and function effectively as nuclei of equiaxed crystals. Disappears. Therefore, the influence of the swirling flow rate of the electromagnetic stirring on the equiaxed grain size was investigated by a continuous casting experiment of molten steel containing Mg. The equiaxed crystal grain size is defined as 2 (a · b) 0.5 so that the grain size in the case of columnar crystals can be evaluated at the same time (a is the major axis of the crystal grains, and b is the minor axis of the crystal grains). . FIG. 1 shows the relationship between the average equiaxed grain size of the cross section of the slab and the swirling flow rate of electromagnetic stirring. As can be seen from FIG.
The average equiaxed grain size of the slab to which g was added becomes smaller when the swirling flow rate of the molten steel is 30 cm / s or more,
On the other hand, if it exceeds s, the average equiaxed grain size of the slab starts to increase. The cause is that the swirling flow rate of the electromagnetic stirring is 30 cm /
s or more, the re-melting of equiaxed nuclei generated from the fine oxide as a starting point is suppressed, while the swirling flow rate is 100 cm /
If it exceeds s, even with MgO or MgO.Al 2 O 3 ,
This is considered to be because coarsening due to coalescence progresses and stops functioning as nuclei of equiaxed crystals. Therefore, in order to make the solidified structure of the slab a fine equiaxed crystal, it is necessary to control the swirling flow rate of the electromagnetic stirring to 30 to 100 cm / s. Also,
Below 10 m below the mold, the solidification of the surface layer of the slab has already been almost completed, so induction electromagnetic stirring may be set at a position 10 m below the mold from the meniscus in the mold where solidification starts. As can be seen from the above description, the present invention
The present invention is not limited to application to slabs, and even when applied to blooms and billets, a sufficient effect of refining a solidified structure can be obtained. The present invention will be described below with reference to examples and comparative examples. (Example 1) Carbon concentration 0.1%, Al concentration 0.038%
Add 10% Mg-Ni alloy to molten steel in ladle
The concentration was adjusted to 0.002%. The temperature of molten steel is set at 1550 ° C in a tundish, and the thickness is 250 mm x 1500
mm was cast at a casting speed of 1.8 m / min. The induction electromagnetic stirring was provided on the meniscus in the mold. During casting, a current of 500 A and a frequency of 2 Hz was passed through the electromagnetic stirring device to stir the molten steel at the solidification interface at a swirling flow rate of 50 cm / s. Investigation of the slab obtained by the method of the present invention revealed that the solidification structure of the slab cross section was all equiaxed, the average equiaxed grain size was 2.3 mm, and the solidification structure of the entire slab was It was finer. Comparative Example 1 A 10% Mg-Ni alloy was added to molten steel in a ladle having a carbon concentration of 0.1% and an Al concentration of 0.038% to adjust the Mg concentration to 0.002%. The temperature of molten steel is set at 1550 ° C in a tundish and the thickness is 250mm.
× A slab having a width of 1500 mm was cast at a casting speed of 1.8 m / min. No electromagnetic stirring was used during casting. Examination of the slab obtained by this casting revealed that relatively long columnar crystals remained in the cross section of the slab, the average equiaxed grain size was 5.0 mm, and the solidification structure was refined. Did not. Comparative Example 2 Molten steel having a carbon concentration of 0.1%, an Al concentration of 0.038% and a molten steel temperature of 1550 ° C. was poured into a mold from a tundish, and had a thickness of 250 mm and a width of 1500.
mm was cast at a casting speed of 1.8 m / min. Mg was not added to the molten steel. The induction electromagnetic stirring was provided on the meniscus in the mold. During casting, a current of 500 A and a frequency of 2 Hz was passed through the electromagnetic stirring device to stir the molten steel at the solidification interface at a swirling flow rate of 50 cm / s. Examination of the slab obtained by this casting revealed that relatively long columnar crystals remained in the cross section of the slab, the average equiaxed crystal grain size was 4.1 mm, and the solidification structure was refined. Did not. As described above, according to the present invention, it is possible to manufacture a continuous cast slab in which both the surface layer of the slab and the solidification structure inside the slab are finely equiaxed. Therefore, it becomes possible to produce a material having excellent formability in a thin plate and excellent low-temperature toughness in a thick plate.
【図面の簡単な説明】
【図１】鋳片横断面の平均等軸晶粒径と電磁攪拌の旋回
流速との関係を示す図。BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a diagram showing the relationship between the average equiaxed crystal grain size in the cross section of a slab and the swirling flow rate of electromagnetic stirring.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平10−168539（ＪＰ，Ａ) 特開 昭57−75267（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B22D 11/108 B22D 11/115 ────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-10-168539 (JP, A) JP-A-57-75267 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) B22D 11/108 B22D 11/115
Claims (1)
誘導電磁攪拌装置を有する連続鋳造装置を用いて、Ａｌ
濃度が０．０５％以下の溶鋼に、取鍋、タンディッシュ
あるいは鋳型で溶鋼中にＭｇを０．０００２〜０．０１
％になるように含有せしめ、該誘導電磁攪拌装置により
水平面内で溶鋼を旋回流速が３０〜１００ｃｍ／ｓで旋
回させながら鋳造することを特徴とする連続鋳造方法。 (57) [Claims] [Claim 1] Between the meniscus in the mold and 10 m below the mold
Using a continuous casting device with an induction electromagnetic stirrer,
Ladle and tundish on molten steel with a concentration of 0.05% or less
Alternatively, 0.0002 to 0.01 Mg is added to molten steel in a mold.
%, And by the induction electromagnetic stirrer
Handed the molten steel in a horizontal plane in turning the flow rate is 30~100cm / s
A continuous casting method characterized by casting while rotating.
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| JP23508498A JP3488093B2 (en) | 1998-08-21 | 1998-08-21 | Continuous casting method of molten steel |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23508498A JP3488093B2 (en) | 1998-08-21 | 1998-08-21 | Continuous casting method of molten steel |
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| JP2000061598A JP2000061598A (en) | 2000-02-29 |
| JP3488093B2 true JP3488093B2 (en) | 2004-01-19 |
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| EP2308617B1 (en) | 1999-04-08 | 2018-02-21 | Nippon Steel & Sumitomo Metal Corporation | Method for processing molten steel |
| JP4501223B2 (en) * | 2000-05-17 | 2010-07-14 | Ｊｆｅスチール株式会社 | Continuous casting method |
| JP3760144B2 (en) * | 2001-08-07 | 2006-03-29 | 新日本製鐵株式会社 | Ultra-low carbon steel sheet, ultra-low carbon steel slab and method for producing the same |
| JP4660038B2 (en) * | 2001-09-27 | 2011-03-30 | 新日本製鐵株式会社 | Method for melting steel sheet for thin plate and cast piece thereof |
| JP5308857B2 (en) * | 2009-02-12 | 2013-10-09 | 日新製鋼株式会社 | Martensitic stainless steel continuous casting slab and manufacturing method thereof |
| JP6500630B2 (en) * | 2014-10-27 | 2019-04-17 | 日本製鉄株式会社 | Continuous casting method for molten steel and continuous cast slab |
| JP6488931B2 (en) * | 2015-07-21 | 2019-03-27 | 新日鐵住金株式会社 | Continuous casting method for molten steel |
| JP6728933B2 (en) * | 2016-04-25 | 2020-07-22 | 日本製鉄株式会社 | Continuous casting method for molten steel |
| JP6728934B2 (en) * | 2016-04-25 | 2020-07-22 | 日本製鉄株式会社 | Continuous casting method for molten steel |
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