JP2012157872A - Casting mold for continuous casting of steel and continuous casting method of steel - Google Patents
Casting mold for continuous casting of steel and continuous casting method of steel Download PDFInfo
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- 238000005266 casting Methods 0.000 title claims abstract description 50
- 238000009749 continuous casting Methods 0.000 title claims abstract description 35
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 31
- 239000010959 steel Substances 0.000 title claims abstract description 31
- 238000000034 method Methods 0.000 title claims description 5
- 239000002344 surface layer Substances 0.000 abstract description 6
- 238000007711 solidification Methods 0.000 description 24
- 230000008023 solidification Effects 0.000 description 24
- 238000001816 cooling Methods 0.000 description 5
- 238000010586 diagram Methods 0.000 description 5
- 239000000843 powder Substances 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 239000000498 cooling water Substances 0.000 description 4
- 238000000605 extraction Methods 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910000796 S alloy Inorganic materials 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000015271 coagulation Effects 0.000 description 1
- 238000005345 coagulation Methods 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
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- 238000010583 slow cooling Methods 0.000 description 1
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- 238000012546 transfer Methods 0.000 description 1
- 238000004017 vitrification Methods 0.000 description 1
- 239000011800 void material Substances 0.000 description 1
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Abstract
【課題】 鋳片の長辺長さと短辺長さとの比が１〜２である鋼鋳片を連続鋳造するための鋳型において、鋳造速度を２倍程度の範囲で変更した場合でも、鋳型と凝固シェルとの間に生成するエアーギャップ生成を効果的に抑制し、これにより、鋳片コーナー部の表層下の内部割れやそれに起因する縦割れを効果的に防止することのできる、鋳造速度依存性が小さく操業柔軟性に優れる連続鋳造用鋳型を提供する。
【解決手段】 鋳片の長辺長さと短辺長さとの比が１〜２である鋼鋳片用の鋳型であり、鋳型の内面に鋳片引き抜き方向に向かって対面間隔が狭まる傾斜面を有する鋳型において、鋳型の短辺３の内面は、上部側の第１傾斜面８と下部側の第２傾斜面９との２つの傾斜面で形成され、鋳型の長辺内面は１つの傾斜面で形成されていて、第１傾斜面のテーパ値が第２傾斜面のテーパ値よりも大きく、且つ、長辺内面のテーパ値が第１傾斜面のテーパ値よりも小さい。
【選択図】 図３PROBLEM TO BE SOLVED: To provide a mold for continuously casting a steel slab having a ratio of a long side length to a short side length of 1 to 2, even when the casting speed is changed in a range of about 2 times. Depends on casting speed, which effectively suppresses air gap generation between the solidified shell and effectively prevents internal cracks under the surface layer of the slab corner and vertical cracks resulting from it. The present invention provides a continuous casting mold which is small in performance and excellent in operational flexibility.
A steel slab mold having a ratio of a long side length to a short side length of a slab of 1 to 2, and an inclined surface with a facing distance narrowing toward the slab drawing direction on the inner surface of the mold. In the mold having, the inner surface of the short side 3 of the mold is formed by two inclined surfaces of the first inclined surface 8 on the upper side and the second inclined surface 9 on the lower side, and the inner surface of the long side of the mold is one inclined surface. The taper value of the first inclined surface is larger than the taper value of the second inclined surface, and the taper value of the long side inner surface is smaller than the taper value of the first inclined surface.
[Selection] Figure 3
Description
本発明は、鋼鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２であるブルーム鋳片或いはビレット鋳片を連続鋳造するための鋳型及び該鋳型を使用した連続鋳造方法に関する。 The present invention is for continuously casting a bloom slab or billet slab in which the ratio (W / N) of the long side length (W) to the short side length (N) of the steel slab is 1-2. The present invention relates to a mold and a continuous casting method using the mold.
鋼の連続鋳造における鋳型内での凝固シェルの二次元的な熱収縮の概念図を図１に示す。図１において、符号１は連続鋳造用の鋳型、２は鋳型長辺、３は鋳型短辺、４は長辺面凝固シェル、５は短辺面凝固シェル、６は溶鋼、７はエアーギャップ（空隙）である。凝固の進行に伴い、凝固シェル４、５の温度が低下して凝固シェル４、５が収縮し、鋳型１の内壁面と凝固シェル４、５との間にエアーギャップ７が形成される。エアーギャップ７が形成されると鋳型１による凝固シェル４、５の抜熱が阻害されるので、このエアーギャップ７を補償するべく、連続鋳造用鋳型は、その内壁面が、鋳片引き抜き方向に向かって対面間隔が徐々に狭くなった傾斜面で構成されている。この傾斜面は、従来、直線的な勾配（以下、「テーパ」と記す）を設けて凝固シェルの熱収縮量を補償する例が一般的であったが、最近では、例えば、特許文献１に示すように、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１．０〜２．０であるブルーム鋳片或いはビレット鋳片を連続鋳造する鋳型においては、鋳型の短辺面及び長辺面を多段勾配状に形成する鋳型、所謂、２段テーパを鋳型の長辺面及び短辺面に付与した連続鋳造用鋳型が提案されている。
FIG. 1 shows a conceptual diagram of two-dimensional heat shrinkage of a solidified shell in a mold in continuous casting of steel. In FIG. 1,
この２段テーパの鋳型は、凝固初期の大きな寸法収縮を補償し、これにより、鋳型と凝固シェルとの間に形成されるエアーギャップを小さくして、エアーギャップ生成による凝固シェルの復熱や不均一凝固を抑制し、特に、鋳片コーナー部の表層下に発生する内部割れやそれに起因する縦割れを防止することを目的とした鋳型である。ブルーム鋳片やビレット鋳片の場合には、鋳片の長辺長さが１２０〜６００ｍｍであり、スラブ鋳片のそれ（９００〜３４００ｍｍ）と比較して短く、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が小さいことから、鋳型内での凝固シェルのバルジング現象（溶鋼静圧により膨らむ現象）は無視できるので、特許文献１に提案されるように、鋳型の長辺面と短辺面のテーパを等しくし、且つ２段勾配状に設定することが行われていた。 This two-step taper mold compensates for the large dimensional shrinkage at the initial stage of solidification, thereby reducing the air gap formed between the mold and the solidified shell, thereby recuperating the heat of the solidified shell due to the generation of the air gap. It is a mold intended to suppress uniform solidification and in particular to prevent internal cracks that occur below the surface layer of the slab corner and vertical cracks resulting therefrom. In the case of a bloom slab or billet slab, the long side length of the slab is 120 to 600 mm, which is shorter than that of the slab slab (900 to 3400 mm), and the long side length of the slab ( Since the ratio (W / N) of W) to the short side length (N) is small, the bulging phenomenon of the solidified shell in the mold (a phenomenon that swells due to the static pressure of the molten steel) can be ignored. As described above, the taper of the long side surface and the short side surface of the mold is made equal, and the two-step gradient is set.
しかし、特許文献１のような鋳型テーパの場合、同一連続鋳造機で鋳造速度が大きく異なる操業形態を採る際には好適なテーパ値が変化することから、スラブ鋳片用の連続鋳造用鋳型のように幅変更できない構造であるブルーム鋳片用やビレット鋳片用の鋳型では、鋳造速度に対応したテーパの鋳型を複数台設ける必要がある。例えば、特許文献１において、鋳造速度が０．６ｍ／ｍｉｎ及び１．５ｍ／ｍｉｎの場合を例としてテーパ値を算出すると、鋳造速度と好適テーパ値（％／ｍ）は、下記の表１のようになる。
However, in the case of a mold taper as in
つまり、好適な鋳型テーパ値は鋳造速度の依存性が大きく、同一組成の連続鋳造用モールドパウダーを使用しても、鋳造速度が２倍以上異なる操業を行う場合には、テーパの異なる鋳型を少なくとも２セット設ける必要があり、鋳型準備やメンテナンスの費用を考えると大きな負担となる。特許文献１では、これを解決するために、テーパの小さい鋳型を優先使用して操業するとしている。従って、特許文献１においては、好適なテーパ値が使用する鋳型のテーパ値よりも大きい鋳造条件では、前述した鋳片欠陥の効率的防止に限界が生じるという問題があった。
In other words, the preferred mold taper value is highly dependent on the casting speed. Even when mold powder for continuous casting having the same composition is used, when casting operations are performed more than twice as different, at least molds having different tapers are used. It is necessary to provide two sets, which is a heavy burden considering the cost of mold preparation and maintenance. In
本発明は上記事情に鑑みてなされたもので、その目的とするところは、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２であるブルーム鋳片或いはビレット鋳片を連続鋳造するための鋳型において、鋳造速度を２倍程度の範囲で変更した場合でも、鋳型と凝固シェルとの間に生成するエアーギャップ生成を抑制し、これにより、鋳片コーナー部の表層下の内部割れやそれに起因する縦割れを効果的に防止することのできる、鋳造速度依存性が小さく操業柔軟性に優れた連続鋳造用鋳型を提供することであり、また、この連続鋳造用鋳型を使用した鋼の連続鋳造方法を提供することである。 The present invention has been made in view of the above circumstances, and its object is that the ratio (W / N) of the long side length (W) to the short side length (N) of the slab is 1-2. Even when the casting speed is changed in the range of about 2 times in the mold for continuous casting of the bloom slab or billet slab, the generation of the air gap generated between the mold and the solidified shell is suppressed. Is to provide a continuous casting mold that can effectively prevent internal cracks under the surface of the slab corners and vertical cracks resulting from it, and has low casting speed dependency and excellent operational flexibility. Another object of the present invention is to provide a continuous casting method of steel using this continuous casting mold.
上記課題を解決するための本発明の要旨は以下のとおりである。
（１） 鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２である鋼鋳片を連続鋳造する鋳型であり、該鋳型の内面に鋳片引き抜き方向に向かって対面間隔が狭まる傾斜面を有する連続鋳造用鋳型において、鋳型の短辺内面は、上部側の第１傾斜面と下部側の第２傾斜面との２つの傾斜面で形成され、鋳型の長辺内面は１つの傾斜面で形成されていて、前記第１傾斜面のテーパ値が前記第２傾斜面のテーパ値よりも大きく、且つ、前記長辺内面のテーパ値が前記第１傾斜面のテーパ値よりも小さいことを特徴とする、鋼の連続鋳造用鋳型。
（２） 前記短辺内面の第１傾斜面のテーパ値θnuと前記長辺内面の傾斜面のテーパ値θwとの比（θnu／θw）が２．０〜３．５であり、前記短辺内面の第１傾斜面のテーパ値θnuが１．５〜４．０％／ｍ、前記短辺内面の第２傾斜面のテーパ値θndが０．７〜１．０％／ｍであることを特徴とする、上記（１）に記載の鋼の連続鋳造用鋳型。
（３） 上記（１）または上記（２）に記載の鋼の連続鋳造用鋳型を用いて、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２である鋼鋳片を連続鋳造することを特徴とする、鋼の連続鋳造方法。
The gist of the present invention for solving the above problems is as follows.
(1) A mold for continuously casting a steel slab having a ratio (W / N) of the long side length (W) to the short side length (N) of the slab of 1 to 2, and the inner surface of the mold In the continuous casting mold having an inclined surface whose facing distance narrows toward the slab drawing direction, the inner surface of the short side of the mold is two inclined surfaces of a first inclined surface on the upper side and a second inclined surface on the lower side The inner surface of the long side of the mold is formed by one inclined surface, the taper value of the first inclined surface is larger than the taper value of the second inclined surface, and the taper value of the inner surface of the long side Is a mold for continuous casting of steel, wherein the taper value of the first inclined surface is smaller.
(2) The ratio (θnu / θw) between the taper value θnu of the first inclined surface of the inner surface of the short side and the taper value θw of the inclined surface of the inner surface of the long side is 2.0 to 3.5, and the short side The taper value θnu of the first inclined surface of the inner surface is 1.5 to 4.0% / m, and the taper value θnd of the second inclined surface of the inner surface of the short side is 0.7 to 1.0% / m. The continuous casting mold for steel according to (1), characterized in that it is characterized in that
(3) Using the steel continuous casting mold described in (1) or (2) above, the ratio of the long side length (W) to the short side length (N) of the slab (W / N) ) Is a continuous casting method of steel, characterized by continuously casting a steel slab of 1 to 2.
本発明によれば、鋳型長辺のテーパ値が鋳型短辺のテーパ値に比較して小さいことから、鋳造速度依存性が小さく、鋳造速度を２倍程度の範囲で変更した場合でも、鋳型と凝固シェルとの間に生成するエアーギャップ生成を効果的に抑制し、これにより、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２であるブルーム鋳片或いはビレット鋳片のコーナー部の表層下の内部割れやそれに起因する縦割れを効果的に防止することが実現される。 According to the present invention, since the taper value on the long side of the mold is smaller than the taper value on the short side of the mold, the casting speed dependency is small, and even when the casting speed is changed in the range of about twice, The air gap generated between the solidified shell is effectively suppressed, and the ratio (W / N) of the long side length (W) to the short side length (N) of the slab is 1 to 1. Therefore, it is possible to effectively prevent internal cracks under the surface layer of the corners of the bloom slab or billet slab and vertical cracks resulting therefrom.
以下、本発明を具体的に説明する。凝固初期における凝固シェルの体積収縮に起因する凝固シェルと鋳型内面との間でのエアーギャップ（空隙）の生成は、凝固シェルの冷却速度つまり鋳型抜熱量に大きく影響するのは公知の事実であり、従って、鋼の連続鋳造においては、凝固シェルの温度低下に伴う体積収縮に応じたテーパを鋳型内壁面に設け、凝固シェルと鋳型内壁との間にエアーギャップが形成されることを防止している。特に、ブルーム鋳片及びビレット鋳片は、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２であり、スラブ鋳片のように鋳型内における長辺側凝固シェルのバルジングが発生しずらいため、鋳型の長辺内面及び短辺内面にテーパを設けることが一般的である。 Hereinafter, the present invention will be specifically described. It is a well-known fact that the formation of an air gap (void) between the solidified shell and the inner surface of the mold due to the volume shrinkage of the solidified shell in the initial stage of solidification greatly affects the cooling rate of the solidified shell, that is, the amount of heat removed from the mold. Therefore, in continuous casting of steel, a taper corresponding to the volume shrinkage accompanying the temperature drop of the solidified shell is provided on the inner wall surface of the mold to prevent an air gap from being formed between the solidified shell and the inner wall of the mold. Yes. In particular, the bloom slab and billet slab have a ratio (W / N) of the long side length (W) to the short side length (N) of the slab of 1 to 2, as in a slab slab. Since bulging of the long-side solidified shell in the mold is difficult to occur, it is common to provide a taper on the long-side inner surface and the short-side inner surface of the mold.
発明者らは、特許文献１の効果を検証するために、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２であるブルーム鋳片及びビレット鋳片の連続鋳造において、特許文献１に開示された好適テーパ値による鋳造実験を実施した。しかしながら、期待に反して、鋳片コーナー部の表層下の内部割れやそれに起因する縦割れが軽減するどころか、逆に増える場合が発生することを経験した。また、このような場合、鋳片の断面形状が平行四辺形（ブルーム鋳片の場合）や菱形（ビレット鋳片の場合）に変形することもあった。この場合には、鋳型の４つの面での抜熱量がアンバランスになっていることを確認した。
In order to verify the effect of
この現象の原因を調査した結果、生成するエアーギャップの厚みを鋳型の長辺面及び短辺面ともにテーパで補償し過ぎると、凝固シェルから鋳型への熱移動が促進されて凝固初期の凝固シェルの冷却速度がより一層大きくなり、これによって不均一凝固を招くことが主たる原因であることを突き止めた。 As a result of investigating the cause of this phenomenon, if the thickness of the air gap to be generated is too much compensated by the taper on both the long and short sides of the mold, heat transfer from the solidified shell to the mold is promoted, and the solidified shell in the initial stage of solidification It has been found that the main cause of this is that the cooling rate of the steel is further increased, thereby causing uneven solidification.
この問題を解決するためには、鋳型短辺の内壁面は、鋳片短辺面の冷却を促進させるために上部側のテーパ値が下部側のテーパ値よりも大きい２段の傾斜面とした上で、鋳型長辺側のテーパ値をエアーギャップの生成量よりも少なく補償して鋳型長辺面での抜熱量の増加を緩和させ、鋳片長辺面の凝固シェルの幅方向熱収縮を抑制することが必要であり、その結果として、鋳片短辺凝固シェルと鋳型短辺との間に生成するエアーギャップが抑制できることに思い至り、本発明に繋がった。即ち、鋳型長辺面のテーパ値を鋳型短辺面のテーパ値よりも相対的に小さくして鋳片長辺面の冷却速度を鋳片短辺面の冷却速度に比較して遅くする必要があり、また、このためには鋳型長辺面のテーパは１段とすべきであることを知見した。 In order to solve this problem, the inner wall surface of the mold short side is a two-step inclined surface in which the taper value on the upper side is larger than the taper value on the lower side in order to promote cooling of the short side surface of the slab. Above, the taper value on the long side of the mold is compensated less than the amount of air gap generated to mitigate the increase in heat removal on the long side of the mold and suppress the heat shrinkage in the width direction of the solidified shell on the long side of the slab As a result, it was conceived that the air gap generated between the slab short side solidified shell and the mold short side can be suppressed, which led to the present invention. That is, the taper value of the mold long side surface should be relatively smaller than the taper value of the mold short side surface, and the cooling rate of the slab long side surface must be slower than the cooling rate of the slab short side surface. Also, for this purpose, it has been found that the taper of the long side surface of the mold should be one step.
本発明は、上記知見に基づくものであり、本発明に係る連続鋳造用鋳型は、鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２である鋼鋳片を連続鋳造する鋳型であって、鋳型の短辺内面は、上部側の第１傾斜面と下部側の第２傾斜面との２つの傾斜面で形成され、鋳型の長辺内面は１つの傾斜面で形成されていて、前記第１傾斜面のテーパ値が前記第２傾斜面のテーパ値よりも大きく、且つ、前記長辺内面のテーパ値が前記第１傾斜面のテーパ値よりも小さいことを特徴とする。 The present invention is based on the above knowledge, and the continuous casting mold according to the present invention has a ratio (W / N) of the long side length (W) to the short side length (N) of the slab of 1. A casting mold for continuously casting a steel slab of ˜2, wherein the inner surface of the mold is formed by two inclined surfaces of a first inclined surface on the upper side and a second inclined surface on the lower side, The inner surface of the long side is formed by one inclined surface, the taper value of the first inclined surface is larger than the taper value of the second inclined surface, and the taper value of the inner surface of the long side is the first inclined surface. It is characterized by being smaller than the taper value.
図２に、本発明に係る連続鋳造用鋳型の長辺断面及び短辺断面の模式図を示す。図２（Ａ）が鋳型長辺断面であり、図２（Ｂ）が鋳型短辺断面の模式図であり、図２は片側の鋳型長辺及び鋳型短辺のみを表示し、相対する鋳型長辺及び鋳型短辺は省略している。尚、図２において、符号２は鋳型長辺、３は鋳型短辺、４は長辺面凝固シェル、５は短辺面凝固シェル、６は溶鋼、７はエアーギャップ、８は第１傾斜面、９は第２傾斜面である。
In FIG. 2, the schematic diagram of the long side cross section and short side cross section of the casting mold for continuous casting according to the present invention is shown. 2A is a mold long-side cross section, FIG. 2B is a schematic diagram of a mold short-side cross section, and FIG. 2 shows only one mold long side and mold short side, and the opposite mold lengths. Sides and mold short sides are omitted. In FIG. 2,
鋳型長辺２の内壁面は、図２（Ａ）に示すように、テーパ値がθwの１つの面で形成され、鋳型短辺３の内壁面は、図２（Ｂ）に示すように、テーパ値がθnuの第１傾斜面８とテーパ値がθndの第２傾斜面９とで形成されている。
The inner wall surface of the mold
ここでテーパ値の定義を説明する。図３は、本発明に係る連続鋳造用鋳型を鋳片長辺面に平行な面で切断したときの断面図である。鋳型短辺３の第１傾斜面８のテーパ値θnuは下記の（１）式で求められ、鋳型短辺３の第２傾斜面９のテーパ値θndは下記の（２）式で求められる。
θnu=[(Wu-Wm)/Wm]×100/H1 …(1)
θnd=[(Wm-Wd)/Wd]×100/H2 …(2)
但し、（１）式及び（２）式において、Ｗuは鋳型上端での鋳型幅（ｍｍ）、Ｗmは第１傾斜面と第２傾斜面との境界での鋳型幅（ｍｍ）、Ｗdは鋳型下端での鋳型幅（ｍｍ）、Ｈ1は鋳型上端から第１傾斜面と第２傾斜面との境界までの鉛直方向距離（ｍ）、Ｈ2は第１傾斜面と第２傾斜面との境界から鋳型下端までの鉛直方向距離（ｍ）である。（１）式、（２）式から明らかなようにテーパ値の単位は「％／ｍ」となる。
Here, the definition of the taper value will be described. FIG. 3 is a cross-sectional view of the continuous casting mold according to the present invention cut along a plane parallel to the long side surface of the slab. The taper value θnu of the first
θnu = [(Wu-Wm) / Wm] × 100 / H 1 … (1)
θnd = [(Wm-Wd) / Wd] × 100 / H 2 (2)
In the equations (1) and (2), Wu is the mold width (mm) at the upper end of the mold, Wm is the mold width (mm) at the boundary between the first inclined surface and the second inclined surface, and Wd is the mold. The mold width (mm) at the lower end, H 1 is the vertical distance (m) from the upper end of the mold to the boundary between the first inclined surface and the second inclined surface, and H 2 is the distance between the first inclined surface and the second inclined surface. The vertical distance (m) from the boundary to the lower end of the mold. As apparent from the equations (1) and (2), the unit of the taper value is “% / m”.
図示はしないが、同様に、鋳型長辺のテーパ値θwは下記の（３）式で求められる。
θw=[(Nu-Nd)/Nd]×100/L …(3)
但し、（３）式において、Ｎuは鋳型上端での鋳型厚み（ｍｍ）、Ｎdは鋳型下端での鋳型厚み（ｍｍ）、Ｌは鋳型の鉛直方向長さ（ｍ）である。
Although not shown, similarly, the taper value θw of the mold long side can be obtained by the following equation (3).
θw = [(Nu-Nd) / Nd] × 100 / L (3)
In equation (3), Nu is the mold thickness (mm) at the upper end of the mold, Nd is the mold thickness (mm) at the lower end of the mold, and L is the vertical length (m) of the mold.
本発明者らは、鋳型短辺の第１傾斜面のテーパ値θnu、鋳型短辺の第２傾斜面のテーパ値θnd、及び、鋳型長辺のテーパ値θwの好適条件を検討した。その結果、鋳型短辺内面の第１傾斜面のテーパ値θnuと鋳型長辺内面の傾斜面のテーパ値θwとの比（θnu／θw）が下記の（４）式を満たし、鋳型短辺内面の第１傾斜面のテーパ値θnuが下記の（５）式を満たし、且つ鋳型短辺内面の第２傾斜面のテーパ値θndが下記の（６）式を満たす鋳型を用いることで、鋳造速度を０．５〜２．０ｍ／ｍｉｎの範囲で変更しても、鋳片コーナー部の表層下の内部割れやそれに起因する縦割れを効果的に防止することができ、表面品質及び内部品質に優れた鋳片を安定して製造できることを確認した。 The present inventors examined suitable conditions for the taper value θnu of the first inclined surface of the mold short side, the taper value θnd of the second inclined surface of the mold short side, and the taper value θw of the mold long side. As a result, the ratio (θnu / θw) between the taper value θnu of the first inclined surface on the inner surface of the mold short side and the taper value θw of the inclined surface on the inner surface of the mold long side satisfies the following equation (4), By using a mold in which the taper value θnu of the first inclined surface satisfies the following expression (5) and the taper value θnd of the second inclined surface of the inner surface of the mold short side satisfies the following expression (6), the casting speed is Even if it is changed within the range of 0.5 to 2.0 m / min, it is possible to effectively prevent internal cracks under the surface layer of the slab corners and vertical cracks resulting from the cracks. It was confirmed that excellent slabs could be manufactured stably.
2.0≦θnu/θw≦3.5 …(4)
1.5≦θnu≦4.0 …(5)
0.7≦θnd≦1.0 …(6)
以下、比（θnu／θw）、第１傾斜面のテーパ値θnu（以下、単に「θnu」とも記す）及び第２傾斜面のテーパ値θnd（以下、単に「θnd」とも記す）が上記の（４）式〜（６）式の範囲に限定される理由を説明する。尚、鋳型長辺のテーパ値θw（以下、単に「θw」とも記す）の範囲は（４）式及び（５）式から自ずと求められ、θwは０．４３〜２．０％／ｍとなる。
2.0 ≦ θnu / θw ≦ 3.5 (4)
1.5 ≦ θnu ≦ 4.0 (5)
0.7 ≦ θnd ≦ 1.0 (6)
Hereinafter, the ratio (θnu / θw), the taper value θnu of the first inclined surface (hereinafter simply referred to as “θnu”), and the taper value θnd of the second inclined surface (hereinafter also simply referred to as “θnd”) are The reason for being limited to the range of 4) Formula-(6) Formula is demonstrated. The range of the taper value θw (hereinafter also simply referred to as “θw”) of the long side of the mold is naturally obtained from the equations (4) and (5), and θw is 0.43 to 2.0% / m. .
本発明者らは、θnu＝０．９〜５．０％／ｍ、θnd＝０．５〜１．３％／ｍ、θw＝０．２３〜５．０％／ｍ、比（θnu／θw）＝１．０〜４．０の範囲の鋳型を準備し、鋳造速度を０．６ｍ／ｍｉｎ（鋳片サイズ：長辺長さ５６０ｍｍ、短辺長さ４００ｍｍ）、１．０ｍ／ｍｉｎ（鋳片サイズ：長辺長さ４００ｍｍ、短辺長さ３００ｍｍ）、２．０ｍ／ｍｉｎ（鋳片サイズ：長辺長さ２３０ｍｍ、短辺長さ１９０ｍｍ）の３水準として鋳造試験を実施した。 We have θnu = 0.9 to 5.0% / m, θnd = 0.5 to 1.3% / m, θw = 0.23 to 5.0% / m, ratio (θnu / θw ) = 1.0 to 4.0, and casting speed is 0.6 m / min (slab size: long side length 560 mm, short side length 400 mm), 1.0 m / min (casting) The casting test was carried out with three levels of one size: long side length 400 mm, short side length 300 mm) and 2.0 m / min (cast piece size: long side length 230 mm, short side length 190 mm).
鋳造中、鉄板に包んだＦｅ−Ｓ合金粉末を鋳型内に浸漬・投入し、鋳片断面から採取したサルファープリントによって鋳型内における凝固シェル厚（測定箇所：鋳型内溶鋼湯面から１００ｍｍ下方の位置）を測定し、下記の（７）式で定義する凝固不均一度を求め、鋳型テーパと凝固不均一度との関係を調査した。また鋳造中、鋳型長辺及び鋳型短辺での鋳型抜熱量を鋳型冷却水の入出温度差と冷却水流量とから計算し、下記の（８）式で定義する抜熱量偏差を求め、鋳型テーパと抜熱量偏差との関係を調査した。 During casting, the Fe-S alloy powder wrapped in an iron plate is immersed in the mold, and the thickness of the solidified shell in the mold is measured by sulfur printing taken from the cross section of the slab (measurement location: 100 mm below the molten steel surface in the mold) ) Was measured, the solidification nonuniformity defined by the following equation (7) was determined, and the relationship between the mold taper and the solidification nonuniformity was investigated. Also, during casting, the amount of heat removed from the mold at the long side and the short side of the mold is calculated from the difference in temperature of the mold cooling water and the flow rate of the cooling water, and the deviation of the heat removal amount defined by the following equation (8) is obtained. And the relationship between the amount of heat removal and the deviation.
凝固不均一度=(dmax-dmin)×100/dmax …(7)
但し、（７）式において、ｄmax：鋳片長辺面または短辺面の凝固シェル厚の最大値（ｍｍ）、ｄmin：鋳片長辺面または短辺面の凝固シェル厚の最小値（ｍｍ）である。
Solidification non-uniformity = (dmax-dmin) x 100 / dmax (7)
However, in the formula (7), dmax is the maximum value (mm) of the solidified shell thickness on the long side or short side of the slab, and dmin is the minimum value (mm) of the solidified shell thickness on the long or short side of the slab. is there.
抜熱量偏差=|Hw-Hn|×100/max(Hw,Hn) …(8)
但し、（８）式において、Ｈw：鋳型長辺の平均抜熱量、Ｈn：鋳型短辺の平均抜熱量、max(Ｈw,Ｈn)：ＨwまたはＨnのいずれかの最大値である。
Heat removal deviation = | Hw-Hn | × 100 / max (Hw, Hn)… (8)
However, in the equation (8), Hw is the average heat removal amount at the long side of the mold, Hn is the average heat removal amount at the short side of the mold, and max (Hw, Hn) is the maximum value of either Hw or Hn.
その結果、鋳造速度が０．６〜２．０ｍ／ｍｉｎと広範囲においても、比（θnu／θw）を２．０〜３．５とし、θnuを１．５〜４．０％／ｍ、且つ、θndを０．７〜１．０％／ｍとすることで、凝固不均一度は、鋳片表面の縦割れ限界の凝固不均一度とされる１０％を下回り、且つ、抜熱量偏差も鋳片断面形状劣化を防止する１５％未満にできることを突き止めた。 As a result, the ratio (θnu / θw) is set to 2.0 to 3.5, θnu is set to 1.5 to 4.0% / m, and the casting speed is 0.6 to 2.0 m / min over a wide range. , Θnd is set to 0.7 to 1.0% / m, the solidification non-uniformity is less than 10%, which is the solidification non-uniformity of the vertical crack limit of the slab surface, and the heat removal amount deviation is also It was ascertained that the cross-sectional shape deterioration of the slab can be reduced to less than 15%.
比（θnu／θw）に範囲が存在する理由：
比（θnu／θw）が小さ過ぎると相対的に鋳片短辺面の凝固シェルの成長が抑制され、同様に、比（θnu／θw）が大き過ぎると相対的に鋳片長辺面の凝固シェルの成長が抑制される。いずれのケースにおいても、鋳片短辺面と長辺面との凝固シェル厚に差が生じて凝固不均一度が大きくなることから、凝固不均一度を１０％以下とするためには比（θnu／θw）に或る範囲を設ける必要があり、２．０〜３．５が好適である。
Reasons why there is a range in the ratio (θnu / θw):
If the ratio (θnu / θw) is too small, the growth of the solidified shell on the short side of the slab is relatively suppressed. Similarly, if the ratio (θnu / θw) is too large, the solidified shell on the long side of the slab is relatively small. Growth is suppressed. In any case, since the solidification shell thickness between the slab short side surface and the long side surface is different and the solidification nonuniformity is increased, the ratio ( It is necessary to provide a certain range for θnu / θw), and 2.0 to 3.5 is preferable.
θnuに好適な範囲が存在する理由：
比（θnu／θw）が好適な２．０〜３．５の範囲において、θnuが小さ過ぎると抜熱量偏差が大きくなり、且つ鋳型短辺の抜熱量が低下して凝固シェル成長低下によるブレークアウトの危険があることから、これを回避するためにθnuに下限を設けている。一方、θnuが大き過ぎると、抜熱量偏差は小さくなるが、鋳型抜熱量絶対値の増加による縦割れや鋳型／凝固シェル間の摩擦力増大による拘束性ブレークアウトの危険があり、これを回避するためにθnuに上限を設けている。つまり、θnuにも好適な範囲が存在し、その値は上記理由から１．５〜４．０％／ｍとなる。
Reason why there is a suitable range for θnu:
When the ratio (θnu / θw) is in the preferred range of 2.0 to 3.5, if θnu is too small, the deviation in heat removal becomes large, and the heat removal at the short side of the mold is reduced, resulting in a breakout due to reduced solidified shell growth. In order to avoid this, a lower limit is set for θnu. On the other hand, if θnu is too large, the deviation in heat removal becomes small, but there is a risk of a vertical break due to an increase in the absolute value of the heat removal from the mold and a constraining breakout due to an increase in the frictional force between the mold and the solidified shell. Therefore, an upper limit is set for θnu. That is, there is a preferable range for θnu, and the value is 1.5 to 4.0% / m for the above reason.
θndに好適な範囲が存在する理由：
初期凝固シェルの成長や鋳型抜熱量は鋳型上部で大略決定される。換言すれば、鋳型下部のテーパθndは、上部のテーパθnuに比べると、初期凝固シェルの成長や鋳型抜熱挙動に及ぼす影響が小さくなる。しかし、その影響が小さいながらも初期凝固シェル成長や鋳型抜熱に影響し、θndの変化は、θnuと比（θnu／θw）との関係において、凝固不均一度１０％以下、抜熱量偏差１５％以下の領域を変化させる。
Reasons why there is a suitable range for θnd:
The growth of the initial solidified shell and the amount of heat removed from the mold are largely determined at the upper part of the mold. In other words, the taper θnd at the bottom of the mold has less influence on the growth of the initial solidified shell and the heat removal behavior of the mold than the taper θnu at the top. However, although the influence is small, it affects the initial solidification shell growth and mold heat removal. The change of θnd is a solidification nonuniformity of 10% or less and a heat removal deviation of 15 in the relationship between θnu and the ratio (θnu / θw). Change the area below%.
定性的にはθndが小さすぎると凝固シェル成長が遅れるので、その遅れを補うために、比（θnu／θw）を大きく設定する必要がある。従って、θndが小さい場合には、θnuと比（θnu／θw）との関係における凝固不均一度１０％以下、抜熱量偏差１５％以下の好適領域は、比（θnu／θw）の大きい側にシフトする。θndが大きい場合には、その逆に、好適領域は比（θnu／θw）の小さい側にシフトする。これらの結果から、θndの好適領域に或る範囲が存在することが分る。 Qualitatively, if θnd is too small, the growth of the solidified shell is delayed. Therefore, in order to compensate for the delay, the ratio (θnu / θw) needs to be set large. Therefore, when θnd is small, the preferred region where the solidification nonuniformity is 10% or less and the heat removal deviation is 15% or less in the relationship between θnu and the ratio (θnu / θw) is on the larger side of the ratio (θnu / θw). shift. Conversely, when θnd is large, the preferred region is shifted to the side where the ratio (θnu / θw) is small. From these results, it can be seen that a certain range exists in the preferred region of θnd.
θndの好適範囲０．７〜１．０％／ｍは、鋳造速度が大きく変化しても、θnuと比（θnu／θw）の関係において、凝固不均一度が１０％以下、抜熱量偏差が１５％以下である領域が広く、且つその領域の変化が少ない範囲として定められる。 A preferable range of θnd of 0.7 to 1.0% / m is a solidification non-uniformity of 10% or less and a heat removal amount deviation in the relationship between θnu and a ratio (θnu / θw) even if the casting speed changes greatly. The region that is 15% or less is defined as a wide range and a change in the region is small.
尚、鋳型短辺における第１傾斜面と第２傾斜面との境界の位置は、一般的に鋳型銅板温度変動の大きい鋳型内溶鋼湯面から１００〜３００ｍｍ下方の位置（鋳型上端から約１５０〜３５０ｍｍ下方の位置）とすればよい。 In addition, the position of the boundary between the first inclined surface and the second inclined surface on the short side of the mold is generally a position 100 to 300 mm below the molten steel surface in the mold where the temperature fluctuation of the mold copper plate is large (about 150 to about 150 to the upper end of the mold). (Position below 350 mm).
このような構成の本発明に係る連続鋳造用鋳型を用いて、鋼鋳片の長辺長さ（Ｗ）と短辺長さ（Ｎ）との比（Ｗ／Ｎ）が１〜２であるブルーム鋳片或いはビレット鋳片を連続鋳造することで、鋳型長辺のテーパ値は鋳型短辺のテーパ値に比較して小さいことから、鋳造速度依存性が小さく、鋳造速度を２倍程度の範囲で変更した場合でも、鋳型と凝固シェルとの間に生成するエアーギャップ生成を効果的に抑制し、これにより、鋳片コーナー部の表層下の内部割れやそれに起因する縦割れを効果的に防止することが実現される。 Using the continuous casting mold according to the present invention having such a configuration, the ratio (W / N) of the long side length (W) to the short side length (N) of the steel slab is 1-2. By continuously casting bloom or billet slabs, the taper value on the long side of the mold is smaller than the taper value on the short side of the mold, so the dependence on the casting speed is small, and the casting speed is about twice the range. Even if it is changed, the air gap generated between the mold and the solidified shell is effectively suppressed, which effectively prevents internal cracks under the surface layer of the slab corner and vertical cracks caused by it. Is realized.
Ｃ：０．１０〜０．１３質量％、Ｓｉ：０．１５〜０．３０質量％、Ｍｎ：０．１０〜０．２５質量％、Ｐ：０．０１５〜０．０２５質量％、Ｓ：０．０１０〜０．０２０質量％、Ａｌ：０．０１０〜０．０３５質量％の溶鋼を、鋳型短辺の第１傾斜面のテーパ値θnuが０．９〜５．０％／ｍ、鋳型短辺の第２傾斜面のテーパ値θndが０．５〜１．３％／ｍ、鋳型長辺のテーパ値θwが０．２３〜５．０％／ｍ、比（θnu／θw）が１．０〜４．０％／ｍである鋳型を準備し、鋳造速度を０．６ｍ／ｍｉｎ（鋳片サイズ：長辺長さ（Ｗ）＝５６０ｍｍ、短辺長さ（Ｎ）＝４００ｍｍ、比（Ｗ／Ｎ）＝１．４０）、１．０ｍ／ｍｉｎ（鋳片サイズ：長辺長さ４００ｍｍ、短辺長さ３００ｍｍ、比（Ｗ／Ｎ）＝１．３３）、２．０ｍ／ｍｉｎ（鋳片サイズ：長辺長さ２３０ｍｍ、短辺長さ１９０ｍｍ、比（Ｗ／Ｎ）＝１．２１）の３水準で連続鋳造する試験を実施した。鋳型短辺の第１傾斜面と第２傾斜面との境界は、鋳型内湯面から１５０ｍｍ下方の位置（鋳型上端から約２００ｍｍ下方の位置）とした。 C: 0.10 to 0.13 mass%, Si: 0.15 to 0.30 mass%, Mn: 0.10 to 0.25 mass%, P: 0.015 to 0.025 mass%, S: A molten steel of 0.010 to 0.020 mass%, Al: 0.010 to 0.035 mass%, a mold having a taper value θnu of 0.9 to 5.0% / m of the first inclined surface on the short side of the mold, and a mold The taper value θnd of the second inclined surface of the short side is 0.5 to 1.3% / m, the taper value θw of the mold long side is 0.23 to 5.0% / m, and the ratio (θnu / θw) is 1. A mold having a thickness of 0.0 to 4.0% / m was prepared, and the casting speed was 0.6 m / min (slab size: long side length (W) = 560 mm, short side length (N) = 400 mm, ratio (W / N) = 1.40), 1.0 m / min (slab size: long side length 400 mm, short side length 300 mm, ratio (W / N) = 1.33), 2.0 m / min (Slab size Long side length 230 mm, the short side length 190 mm, a continuous casting test in three levels of the ratio (W / N) = 1.21) was performed. The boundary between the first inclined surface and the second inclined surface on the short side of the mold was set to a position 150 mm below the molten metal surface in the mold (a position about 200 mm below the upper end of the mold).
尚、使用したモールドパウダーは、一般的に使用されている緩冷却（低抜熱）を志向した市販品（塩基度０．６７、ガラス化温度１１３５℃）を使用し、鋳造速度に依らず同一のモールドパウダーを使用した。 The mold powder used is a commercially available product (basicity 0.67, vitrification temperature 1135 ° C) that is generally used for slow cooling (low heat removal), and is the same regardless of casting speed. The mold powder was used.
鋳造中、鉄板に包んだＦｅ−Ｓ合金粉末を鋳型内に浸漬・投入し、鋳片断面から採取したサルファープリントによって鋳型内における凝固シェル厚（測定箇所：鋳型内溶鋼湯面から１００ｍｍ下方の位置）を測定し、（７）式を用いて凝固不均一度を算出した。また鋳造中、鋳型長辺と鋳型短辺の鋳型抜熱量を鋳型冷却水の入出温度差と冷却水流量とから計算し、（８）式を用いて抜熱量偏差を求め、鋳型テーパとこれら凝固不均一度、抜熱量偏差との関係を調査した。鋳造した鋳片表面の縦割れ発生の有無も調査した。 During casting, the Fe-S alloy powder wrapped in an iron plate is immersed in the mold, and the thickness of the solidified shell in the mold is measured by sulfur printing taken from the cross section of the slab (measurement location: 100 mm below the molten steel surface in the mold) ) Was measured, and the coagulation nonuniformity was calculated using equation (7). Also, during casting, the amount of heat removed from the mold long side and the short side of the mold is calculated from the difference in the temperature of the mold cooling water and the flow rate of the cooling water, and the deviation of the heat removal is calculated using equation (8). The relationship between the non-uniformity and the heat extraction deviation was investigated. The presence or absence of vertical cracks on the cast slab surface was also investigated.
図４に、比（θnu／θw）とθnuとの関係において、鋳造速度が０．６〜２．０ｍ／ｍｉｎで鋳型内凝固不均一度が１０％以下となる領域を、θnd別に示す。図中には、凝固不均一度が１０％超えるθnuの上限と下限とをθnd別に線引きした。θnd別に上限及び下限として示した線で挟まれ、その内部に存在する領域が凝固不均一度１０％以下となる。 FIG. 4 shows, by θnd, regions where the casting speed is 0.6 to 2.0 m / min and the in-mold solidification nonuniformity is 10% or less in the relationship between the ratio (θnu / θw) and θnu. In the figure, the upper limit and lower limit of θnu at which solidification nonuniformity exceeds 10% are drawn by θnd. It is sandwiched by lines shown as the upper and lower limits for each θnd, and the region existing inside thereof is solidification nonuniformity of 10% or less.
同様のことを鋳型内抜熱量偏差についても整理し、図５にその結果を示す。図中、鋳型内抜熱量偏差が１５％超えるθnuの上限と下限とを線引きした。θnd別に上限及び下限として示した線で挟まれ、その内部に存在する領域が鋳型内抜熱量偏差１５％以下となる。 The same thing is arranged for the heat extraction deviation in the mold, and the result is shown in FIG. In the figure, the upper limit and the lower limit of θnu, in which the deviation of heat extraction from the mold exceeds 15%, are drawn. It is sandwiched by the lines shown as the upper and lower limits for each θnd, and the region existing in the inside is 15% or less of the heat removal amount in the mold.
図４及び図５から、比（θnu／θw）が２．０〜３．５で、θnuが１．５〜４．０％／ｍ、且つ、θndが０．７〜１．０％／ｍである場合に、凝固不均一度が１０％以下で且つ鋳型内抜熱量偏差が１５％以下を同時に満足することが分る。 4 and 5, the ratio (θnu / θw) is 2.0 to 3.5, θnu is 1.5 to 4.0% / m, and θnd is 0.7 to 1.0% / m. In this case, it can be seen that the non-uniformity of solidification is 10% or less and the heat extraction deviation in the mold satisfies 15% or less at the same time.
また、図６には、比（θnu／θw）とθnuとの関係において、鋳造速度０．６〜２．０ｍ／ｍｉｎで縦割れ或いは内部割れの発生有無を調査した結果を示す。この時、θndは０．７〜１．０％／ｍとした。図６において、○印は、縦割れ或いは内部割れが発生しないことを表し、●印は、縦割れ或いは内部割れが発生したことを表している。 FIG. 6 shows the results of investigating whether vertical cracks or internal cracks occurred at a casting speed of 0.6 to 2.0 m / min in the relationship between the ratio (θnu / θw) and θnu. At this time, θnd was set to 0.7 to 1.0% / m. In FIG. 6, ◯ indicates that no vertical crack or internal crack occurs, and ● indicates that a vertical crack or internal crack has occurred.
図７には、比（θnu／θw）とθnuとの関係において、鋳造速度１．０〜２．０ｍ／ｍｉｎでブレークアウト或いは鋳型と凝固シェルとの焼き付きの発生有無を調査した結果を示す。この時、θndは０．７〜１．０％／ｍとした。図７において、○印は、ブレークアウト或いは焼き付きが発生しないことを表し、●印は、ブレークアウト或いは焼き付きが発生したことを表している。 FIG. 7 shows the result of investigating the occurrence of breakout or seizure between the mold and the solidified shell at a casting speed of 1.0 to 2.0 m / min in the relationship between the ratio (θnu / θw) and θnu. At this time, θnd was set to 0.7 to 1.0% / m. In FIG. 7, ◯ indicates that breakout or burn-in does not occur, and ● indicates that breakout or burn-in has occurred.
図６及び図７から明らかなように、本発明の範囲の鋳型（2.0≦比(θnu／θw)≦3.5、1.5≦θnu≦4.0、0.7≦θnd≦1.0）においては、鋳片欠陥（縦割れ或いは内部割れ）や操業トラブル（ブレークアウト或いは焼き付き）を抑止できることが確認できた。 As apparent from FIGS. 6 and 7, in the mold within the scope of the present invention (2.0 ≦ ratio (θnu / θw) ≦ 3.5, 1.5 ≦ θnu ≦ 4.0, 0.7 ≦ θnd ≦ 1.0), slab defects (longitudinal cracks) It was also confirmed that internal cracks) and operational troubles (breakout or seizure) could be suppressed.
図６及び図７では、比較のために、特許文献１の実施例における比（θnu／θw）（＝０．３〜１．５）とθnu（＝０．３〜５％／ｍ)との範囲を破線で示す。図６及び図７に示すように、特許文献１の実施例に示す鋳型は、本発明の鋳型に比べて鋳片品質及び操業ともに不安定であることが確認できた。
6 and 7, for comparison, the ratio (θnu / θw) (= 0.3 to 1.5) and θnu (= 0.3 to 5% / m) in the example of
１ 鋳型
２ 鋳型長辺
３ 鋳型短辺
４ 長辺面凝固シェル
５ 短辺面凝固シェル
６ 溶鋼
７ エアーギャップ
８ 第１傾斜面
９ 第２傾斜面
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| CN103264147A (en) * | 2013-06-13 | 2013-08-28 | 钢铁研究总院 | Method for inhibiting surface longitudinal cracks of continuous casting sheet billet and crystallizer |
| JP2018130742A (en) * | 2017-02-15 | 2018-08-23 | 新日鐵住金株式会社 | Continuous casting mold for steel and method for continuous casting of steel slab |
| JP2019147178A (en) * | 2018-02-28 | 2019-09-05 | 日本製鉄株式会社 | Continuous casting machine |
| JP2020171932A (en) * | 2019-04-09 | 2020-10-22 | 日本製鉄株式会社 | Continuous casting method |
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| JP2018130742A (en) * | 2017-02-15 | 2018-08-23 | 新日鐵住金株式会社 | Continuous casting mold for steel and method for continuous casting of steel slab |
| JP2019147178A (en) * | 2018-02-28 | 2019-09-05 | 日本製鉄株式会社 | Continuous casting machine |
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| JP2020171932A (en) * | 2019-04-09 | 2020-10-22 | 日本製鉄株式会社 | Continuous casting method |
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