JP5076518B2 - Method for producing galvannealed steel sheet - Google Patents
Method for producing galvannealed steel sheet Download PDFInfo
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- JP5076518B2 JP5076518B2 JP2007020883A JP2007020883A JP5076518B2 JP 5076518 B2 JP5076518 B2 JP 5076518B2 JP 2007020883 A JP2007020883 A JP 2007020883A JP 2007020883 A JP2007020883 A JP 2007020883A JP 5076518 B2 JP5076518 B2 JP 5076518B2
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本発明は、合金化溶融亜鉛めっき鋼板の製造方法に係り、特に、自動車外板に用いられる合金化溶融亜鉛めっき鋼板を製造する際に用いるのに好適な、磁界印加による鋳型内溶鋼流動の改善に関する。 The present invention relates to a method for producing an alloyed hot-dip galvanized steel sheet, and particularly, to improve the flow of molten steel in a mold by applying a magnetic field, which is suitable for use in producing an alloyed hot-dip galvanized steel sheet used for an automobile outer plate. About.
合金化溶融亜鉛めっき鋼板は、溶接性、塗装性、塗装後耐食性に優れ、自動車車体や家電製品、建材等、幅広く用いられている。この合金化亜鉛溶融めっき鋼板は、自動車外板にも用いられるが、そのめっきむらは、外観不良につながり、製品価値を損ねる原因となって問題となっていた。 Alloyed hot-dip galvanized steel sheets are excellent in weldability, paintability, and corrosion resistance after painting, and are widely used in automobile bodies, home appliances, building materials, and the like. This alloyed galvannealed steel sheet is also used for an automobile outer plate, but the plating unevenness leads to a poor appearance and causes a problem of deteriorating the product value.
合金化溶融亜鉛めっき鋼板は、溶融めっき後、加熱して母板の鉄成分を亜鉛めっき層に拡散させたものであり、母板の表面状態により合金化溶融亜鉛めっき層が変化する。従って、めっき不良の原因は種々考えられるが、圧延後の集合組織に着目し、集合組織を調整する技術等が、例えば特許文献1に開示されている。 The alloyed hot dip galvanized steel sheet is obtained by heating and hot diffusing the iron component of the base plate into the galvanized layer, and the galvannealed layer changes depending on the surface state of the base plate. Therefore, although various causes of plating defects are conceivable, for example, Patent Document 1 discloses a technique for adjusting the texture by paying attention to the texture after rolling.
しかしながら、圧延前の鋳片製造段階から根本的に改善する方法は提案されていなかった。 However, a method for fundamental improvement from the slab manufacturing stage before rolling has not been proposed.
本発明は、前記従来の問題点を解決するべくなされたもので、圧延前の鋳片製造段階からめっき不良を根本的に改善することを課題とする。 The present invention has been made to solve the above-mentioned conventional problems, and an object of the present invention is to fundamentally improve plating defects from the slab manufacturing stage before rolling.
本発明は、合金化溶融亜鉛めっき鋼板の製造に際して、図1(鉛直断面図)及び図2(水平断面図)に例示する如く、長辺10aと短辺10bを有する矩形鋳型10の長辺10aの対向側壁の背面に配設した磁極12で磁界を発生させ、該磁界により浸漬ノズル6から鋳型10内に供給される溶鋼8の流動を制御する鋼の連続鋳造方法であって、浸漬ノズル6の上部に配置した磁極12により、浸漬ノズル吐出孔6aより上部の位置の鋳型幅中央で且つ鋳型厚み中央の位置で、0.03T〜0.15Tの直流磁場を印加し、且つ、凝固シェル(14a)滞在時間0〜10秒の間は、熱流束150万〜300万W/m 2 で鋳型10を介して鋳片14を冷却する鋼の連続鋳造方法で製造した鋳片14を用いるようにして、前記課題を解決したものである。
In the production of the galvannealed steel sheet according to the present invention, as illustrated in FIG. 1 (vertical sectional view) and FIG. 2 (horizontal sectional view), the
前記凝固シェル滞在時間は、鋳型10の高さDを鋳造速度Vcで割ることによって、D/Vcとして得られる。
The solidified shell residence time is obtained as D / Vc by dividing the height D of the
ここで、浸漬ノズル吐出孔より上部の位置の鋳型幅中央で且つ鋳型厚み中央の位置での直流磁界としたのは、モールドフラックスの巻き込みは鋳型厚み中央の溶鋼流の渦生成に起因するので、直流磁界で、この渦を抑制する目的から適切と考えられたからである。 Here, the DC magnetic field at the center of the mold width at the position above the immersion nozzle discharge hole and at the center of the mold thickness is because the entrainment of the mold flux is caused by the vortex generation of the molten steel flow at the center of the mold thickness, This is because it was considered appropriate for the purpose of suppressing this eddy with a DC magnetic field.
又、直流磁場の磁界強度の下限を0.03Tとするのは、磁界強度が0.03T未満であると、直流磁場による制動効果が不充分で、湯面変動が大きく、モールドフラックス16を巻き込んで欠陥が発生するからである。
Moreover, the lower limit of the magnetic field strength of the DC magnetic field is set to 0.03T. If the magnetic field strength is less than 0.03T, the braking effect by the DC magnetic field is insufficient, the molten metal surface fluctuation is large, and the
一方、磁界強度の上限を0.15Tとするのは、磁界強度が0.15Tを超えると、直流磁場による制動がかかり過ぎて溶鋼流速が遅くなり、温度が不均一となって、低流速域の部分が早く凝固し、偏析によりMn、C、P等の成分が集中して、成分が不均一となり、凝固組織が不均一となって、筋状模様を発生するためである。 On the other hand, the upper limit of the magnetic field strength is set to 0.15 T. When the magnetic field strength exceeds 0.15 T, braking by the DC magnetic field is excessively applied, the molten steel flow velocity becomes slow, the temperature becomes uneven, and the low flow velocity region This is because the portion solidifies rapidly, components such as Mn, C, and P are concentrated due to segregation, the components become non-uniform, the solidified structure becomes non-uniform, and a streak pattern is generated.
又、冷却の熱流束の下限を150万W/m2とするのは、熱流束が150万W/m2未満であると、溶鋼8の熱流束が低過ぎて、図3(A)に例示する如く、凝固シェル14aの成長が遅れ、薄くなる部分が生じるためである。
Moreover, the lower limit of the heat flux of cooling is 1.5 million W / m 2 because if the heat flux is less than 1.5 million W / m 2 , the heat flux of the
一方、熱流束の上限を300万W/m2とするのは、熱流束が300万W/m2を越えると、溶鋼8の熱流束が高過ぎて、図3(B)に例示する如く、凝固シェル厚が異常成長するところが生じるからである。
On the other hand, the upper limit of the heat flux is set to 3 million W / m 2 because when the heat flux exceeds 3 million W / m 2 , the heat flux of the
熱流束とシェル厚みのばらつきの関係の一例を図4に示す。 An example of the relationship between the heat flux and the shell thickness variation is shown in FIG.
本発明によれば、凝固組織、特に表層の凝固組織を均一化して、合金化溶融亜鉛めっき鋼板の外観不良を防ぐことが可能となる。 According to the present invention, it is possible to uniformize the solidified structure, particularly the solidified structure of the surface layer, and prevent the appearance defect of the galvannealed steel sheet.
以下図面を参照して、本発明の実施形態を詳細に説明する。 Hereinafter, embodiments of the present invention will be described in detail with reference to the drawings.
本発明の第1実施形態は、図1及び図2に示した如く、長辺10aと短辺10bを有する矩形鋳型10の長辺10aの対向側壁の背面に配設した磁極12で磁界を発生させ、該磁界により浸漬ノズル6から鋳型10内に供給される溶鋼8の流動を制御する際に、浸漬ノズル6の上部に配置した磁極12により、浸漬ノズル吐出孔6aより上部の位置の鋳型幅中央で且つ鋳型厚み中央の位置で、0.03T〜0.15Tの直流磁場を印加し、且つ、凝固シェル滞在時間0〜10秒の間で、熱流束150万〜300万W/m2の熱流束で鋳型10を介して鋳片14を冷却するようにしたものである。
In the first embodiment of the present invention, as shown in FIGS. 1 and 2, a magnetic field is generated by the
本発明は、C:0.001〜0.005重量%、Si:0.034重量%以下、Mn:0.03〜0.3重量%、P:0.01〜0.08重量%の鋼組成を有する溶融亜鉛めっき鋼板の製造において、めっきむら等の欠陥発生の対策として特に良好な効果を奏する。 The present invention is a steel of C: 0.001 to 0.005 wt%, Si: 0.034 wt% or less, Mn: 0.03 to 0.3 wt%, P: 0.01 to 0.08 wt% In the production of a hot dip galvanized steel sheet having a composition, it has a particularly good effect as a countermeasure against the occurrence of defects such as uneven plating.
そこで、実施例では、C:0.002重量%、Si:0.02重量%、Mn:0.1重量%、P:0.05重量%の成分を含む溶鋼で試験を行なった。結果を次の表に示す。 Therefore, in the examples, the test was performed with molten steel containing components of C: 0.002 wt%, Si: 0.02 wt%, Mn: 0.1 wt%, and P: 0.05 wt%. The results are shown in the following table.
ここで、「スリーパー状欠陥指数」は、スラブを溶融亜鉛めっき鋼板に仕上げた後、コイルの外表面を目視で検査し、スリーパー状欠陥発生状況を指数化したもので、指数化は、コイルの長手方向に延びたスリーパー状の欠陥の長さを計測し、その総和を検査したコイルの全長で割算することにより求め、最大指数を10として指数化した。 Here, the “Sleeper-like defect index” is obtained by visually inspecting the outer surface of the coil after finishing the slab into a hot-dip galvanized steel sheet and indexing the occurrence of the sleeper-like defect. The length of the sleeper-like defect extending in the longitudinal direction was measured, and the sum was divided by the total length of the inspected coil.
又、「めっきむら評価指数」は、スラブを溶融亜鉛めっき鋼板に仕上げた後、コイルの外表面を目視で検査し、めっきむらに起因した欠陥発生状況を指数化したもので、指数化は、コイルの長手方向に延びためっきむらに起因した筋状欠陥の長さを計測し、その総和を検査したコイルの全長で割算することにより求め、最大指数を10として指数化した。 Also, the “Plating unevenness evaluation index” is obtained by visually inspecting the outer surface of the coil after finishing the slab into a hot dip galvanized steel sheet, and indexing the occurrence of defects caused by uneven plating. The length of the streak defect due to the plating unevenness extending in the longitudinal direction of the coil was measured, and the total sum was divided by the total length of the inspected coil.
実施例では、幅1500mm、厚さ220mmの鋳片幅方向に4箇所をサンプリングし、断面をEDX解析し、硫黄分布を調査し、凝固シェル厚を評価した。 In the examples, four locations were sampled in the width direction of a slab having a width of 1500 mm and a thickness of 220 mm, a cross section was subjected to EDX analysis, a sulfur distribution was investigated, and a solidified shell thickness was evaluated.
ここで、凝固シェル厚の確認は、硫黄プリント法(Sプリント法)で行なった。即ち、凝固中のある時点で、鋳型内に硫黄を添加し、鋳片を解体し、硫黄の分布状態を鋳片の断面観察により確認し、凝固シェルの成長状態を確認した。 Here, the thickness of the solidified shell was confirmed by a sulfur printing method (S printing method). That is, at a certain point during solidification, sulfur was added into the mold, the slab was disassembled, the distribution state of sulfur was confirmed by observing the cross section of the slab, and the growth state of the solidified shell was confirmed.
その結果、図4に示したように、熱流束150万〜300万W/m2では、シェル厚10mmに対し、±2mmの範囲内でのばらつきで良好であった。これに対して、150万W/m2以下や300万W/m2以上では、ばらつきが±4mmとなり、不良であった。
As a result, as shown in FIG. 4, the heat flux from 1,500,000 to 3,000,000 W / m 2, relative to the
なお、第1実施形態では、浸漬ノズル6の上部に配置した磁極14のみにより直流磁界を印加していたが、図5に示す第2実施形態のように、浸漬ノズル6の下側にも磁極16を配置し、この磁極16により、上部磁界と同じ磁場条件の磁界を印加しても良い。
In the first embodiment, the DC magnetic field is applied only by the
6…浸漬ノズル
6a…ノズル吐出孔
8…溶鋼
10…鋳型
10a…長辺
10b…短辺
12、16…磁極
14…鋳片
14a…凝固シェル
6 ... Submerged
Claims (1)
浸漬ノズルの上部に配置した磁極により、浸漬ノズル吐出孔より上部の位置の鋳型幅中央で且つ鋳型厚み中央の位置で、0.03T〜0.15Tの直流磁場を印加し、且つ、
凝固シェル滞在時間0〜10秒の間は、熱流束150万〜300万W/m 2 で鋳型を介して鋳片を冷却する鋼の連続鋳造方法で製造した鋳片を用いることを特徴とする合金化溶融亜鉛めっき鋼板の製造方法。 Continuous casting of steel that generates a magnetic field with magnetic poles arranged on the back side of the opposing side wall of the long side of a rectangular mold having a long side and a short side, and controls the flow of molten steel supplied from the immersion nozzle into the mold by the magnetic field A method,
Applying a DC magnetic field of 0.03T to 0.15T at the center of the mold width at the position above the immersion nozzle discharge hole and at the center of the mold thickness by the magnetic pole disposed on the top of the immersion nozzle; and
Between solidified shells residence time 0-10 seconds, characterized by using a cast slab produced by continuous casting method of steel to cool a heat flux from 1.5 to 3 million cast piece through a mold in W / m 2 A method for producing a galvannealed steel sheet.
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