JP2008531292A - Method and equipment for producing lightweight steel with high manganese content - Google Patents

Method and equipment for producing lightweight steel with high manganese content Download PDF

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JP2008531292A
JP2008531292A JP2007557433A JP2007557433A JP2008531292A JP 2008531292 A JP2008531292 A JP 2008531292A JP 2007557433 A JP2007557433 A JP 2007557433A JP 2007557433 A JP2007557433 A JP 2007557433A JP 2008531292 A JP2008531292 A JP 2008531292A
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ケンプケン・イェンス
ライフェルシャイト・マルクス
ギルゲンゾーン・アルブレヒト
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エス・エム・エス・デマーク・アクチエンゲゼルシャフト
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/466—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a non-continuous process, i.e. the cast being cut before rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/111—Treating the molten metal by using protecting powders
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1213—Accessories for subsequent treating or working cast stock in situ for heating or insulating strands
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/14—Plants for continuous casting
    • B22D11/142—Plants for continuous casting for curved casting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting

Abstract

従来技術では、様々な理由から、連続鋳造法によってマンガン（Ｍｎ）、アルミニウム（Ａｌ）及びケイ素（Ｓｉ）の含有量が多く、ＴＷＩＰ（双晶誘起塑性）特性を持つ鋼鉄を製造することは難しい、或いは不可能と考えられている。その理由は、Ｍｎの強いミクロ偏析に対して、凝固時におけるストランド凝固殻の強度が小さい、低い温度での大きな強度、鋼鉄内のアルミニウムと鋳造用粉末との反応、マクロ偏析、周縁領域での合金元素の密度低下、及びあと押し炉でブルームを再加熱する際の粒界の酸化等である。そのため、この発明では、１５〜２７％のＭｎ、１〜６％のＡｌ、１〜６％のＳｉ、０．８％以下の炭素及び残りを鉄と微量元素とする所定の化学的な組成を持つ軽量鋼を、順番に配置した工程にもとづき、薄いブルーム（ｄ≦１２０ｍｍ）の鋳造機（１）で、好適な鋳造用粉末を用いて鋳造し、凝固に続いて直ぐに、連続したストランド（２）からブルーム（３）を分割し、作業過程内の中間炉（４）で温度の均等化を行い、その次に、その後冷却すること無く直ぐにブルーム（３）を熱間圧延することを提案する。  In the prior art, for various reasons, it is difficult to produce steel having a high content of manganese (Mn), aluminum (Al), and silicon (Si) and having TWIP (twinning induced plasticity) characteristics by a continuous casting method. Or is considered impossible. The reason for this is that the strength of the strand solidification shell during solidification is small compared to the strong microsegregation of Mn, the strength is high at low temperatures, the reaction between aluminum in the steel and the powder for casting, macrosegregation, These include a decrease in the density of alloy elements and oxidation of grain boundaries when bloom is reheated in a boost furnace. Therefore, in the present invention, a predetermined chemical composition having 15 to 27% Mn, 1 to 6% Al, 1 to 6% Si, 0.8% or less of carbon, and the balance of iron and trace elements is used. The lightweight steel is cast in a thin bloom (d ≦ 120 mm) casting machine (1) using a suitable casting powder based on the sequence of steps, and immediately after solidification, a continuous strand (2 ) To divide the bloom (3), equalize the temperature in the intermediate furnace (4) in the work process, and then propose to hot-roll the bloom (3) immediately without cooling thereafter .

Description

この発明は、鋼鉄を先ずは連続鋳造設備で連続したストランドとして鋳造して、ブルームに分割し、その次に最終的な厚さに圧延する形で、マンガン（Ｍｎ）、アルミニウム（Ａｌ）及びケイ素（Ｓｉ）の含有量の多い、ＴＷＩＰ（双晶誘起塑性）特性を持つ良好に冷間成形可能な高強度オーステナイト軽量鋼から成る熱間圧延ストリップを製造するための方法及び設備に関する。   The present invention relates to manganese (Mn), aluminum (Al) and silicon in which steel is first cast as continuous strands in a continuous casting facility, divided into blooms and then rolled to final thickness. The present invention relates to a method and equipment for producing a hot-rolled strip of high strength austenitic lightweight steel with high (Si) content and good cold formability with TWIP (twinning induced plasticity) properties.

例えば、車体用シート綱、車体補強部材並びに低温用容器及びパイプに使用されるＴＷＩＰ特性を持つオーステナイト軽量鋼は、例えば、特許文献１によると、１０〜３０％のＭｎ、１〜６％のＳｉ、１〜８％のＡｌ（但し、Ｓｉ＋Ａｌ≦１２％）、残りのＦｅを有する。   For example, according to Patent Document 1, for example, austenitic lightweight steel having TWIP characteristics used for a vehicle body sheet rope, a vehicle body reinforcing member, a low temperature container and a pipe is 10-30% Mn, 1-6% Si. 1-8% Al (however, Si + Al ≦ 12%) and the remaining Fe.

特許文献２には、良好な機械的特性の他に、腐食及び応力腐食割れに対する良好な耐性を有する、７〜３０％のＭｎ、１〜１０％のＡｌ、０．７〜４％のＳｉ、１０％以下のＣｒ、１０％以下のＮｉ、３％以下のＣｕ及び０．５％以下のＣ、並びに任意選択として合金元素Ｎ、Ｖａ、Ｎｂ、Ｔｉ、Ｐを更に有する高強度軽量鋼が記載されている。この鋼鉄は、連続鋳造法で鋳造されて、熱間圧延されるか、或いは薄板鋳造法によって、最終的なサイズに近い形で鋳造されている。   Patent Document 2 includes 7-30% Mn, 1-10% Al, 0.7-4% Si, which has good resistance to corrosion and stress corrosion cracking in addition to good mechanical properties. High strength lightweight steel further comprising 10% or less of Cr, 10% or less of Ni, 3% or less of Cu and 0.5% or less of C, and optionally further alloying elements N, Va, Nb, Ti, P Has been. This steel is cast by a continuous casting method, hot-rolled, or cast to a shape close to the final size by a thin plate casting method.

従来技術では、様々な理由から、連続鋳造法によってマンガン含有量の多い鋼鉄を製造することは難しい、或いは不可能と考えられている。その理由は、Ｍｎの強いミクロ偏析に対して、凝固時におけるストランド凝固殻の強度が小さい（Ｍｎ＞１５％の場合に突破される虞が有る）、低い温度での大きな強度（設備による過負荷、ひび割れの問題）、鋼鉄内のアルミニウムと鋳造用粉末との反応（機能の制限）、マクロ偏析、散水冷却による水素及び／又は酸素の吸収、非金属含有物の混入増大、周縁領域での合金元素の密度低下、及びあと押し炉でブルームを再加熱する際の粒界の酸化である。   In the prior art, it is considered difficult or impossible to produce steel with a high manganese content by continuous casting for various reasons. The reason for this is that the strength of the strand solidification shell at the time of solidification is small against strong microsegregation of Mn (there is a possibility of breaking through when Mn> 15%), and high strength at low temperature (overload by equipment , Cracking problems), reaction of aluminum in steel with casting powder (restriction of function), macrosegregation, absorption of hydrogen and / or oxygen by sprinkling cooling, increased incorporation of non-metallic inclusions, alloys in the peripheral region This is a decrease in element density and oxidation of grain boundaries when bloom is reheated in a boost furnace.

それに関して、非特許文献１では、マンガン含有量が増大すると、鋼鉄が益々鋳造し難くなることが示されている。一方において、マンガンは、含有量が多い場合、残留溶融物内で大きく濃縮されて、樹枝状晶間領域において融点を低下させるので、凝固後の温度の高い時に鋼鉄の強度が小さくなる。それによって、殻が突破される傾向が増大して、現在の推定によるとマンガン含有量が１５％以上の場合連続鋳造は不可能である。他方において、温度が低い場合、鋼鉄は大きな強度を有し、その結果ストランドを曲げる際に設備による過負荷が生じて、ひび割れの発生を覚悟しなければならない。更に、このような鋼鉄の場合、密度を低下させるなどのためにアルミニウムが混入されるように、アルミニウムの含有量が数パーセントとなると、鋳造用粉末との反応が起こり、その機能に大きな影響を与えることとなる。   In that regard, Non-Patent Document 1 shows that steel becomes more difficult to cast as the manganese content increases. On the other hand, when the manganese content is large, the manganese is greatly concentrated in the residual melt and lowers the melting point in the interdendritic region, so that the strength of the steel decreases when the temperature after solidification is high. This increases the tendency of the shell to break through, and according to current estimates, continuous casting is not possible when the manganese content is 15% or more. On the other hand, when the temperature is low, the steel has great strength, so that when the strand is bent, the equipment is overloaded and must be prepared to crack. Furthermore, in the case of such steel, when the aluminum content reaches several percent, the reaction with the casting powder occurs so that the aluminum is mixed in to reduce the density and the like, and this greatly affects the function. Will give.

それに関して、非特許文献２により、要約すると、鋳造用粉末を用いた方法に関して、ＴＷＩＰ綱を作るためには、想定されている合金構成で鋳造することは有利でないことが確認されている。   In that regard, Non-Patent Document 2 summarizes that, for the method using casting powder, it is confirmed that it is not advantageous to cast with the assumed alloy configuration to make a TWIP rope.

Ａｌ含有量の多い（１％を超える）鋼鉄を鋳造する際の主要な問題は、鋼鉄内のアルミニウムが鋳造用粉末の酸化物成分と反応することである。スラグ内のＳｉＯ2 と鋼鉄内のアルミニウムとの反応によって、Ａｌ2 Ｏ3 が生じて、スラグ内に取り込まれ、それによって、スラグの塩基度（ＣａＯ／ＳｉＯ2 の比率）が増大する。その結果、鋳型内における粘性及び潤滑性が非常に大きく変化することとなる。 A major problem in casting steel with high Al content (greater than 1%) is that the aluminum in the steel reacts with the oxide component of the casting powder. The reaction between SiO 2 in the slag and aluminum in the steel produces Al 2 O 3 and is incorporated into the slag, thereby increasing the basicity of the slag (CaO / SiO 2 ratio). As a result, the viscosity and lubricity in the mold change greatly.

このような難しさの理由から、過去において、ＴＷＩＰ綱を製造するための様々な方法が記載されている。   Because of this difficulty, various methods for manufacturing TWIP ropes have been described in the past.

特許文献３により、可能な炭素含有量（Ｃ≦１％）の増大と更なる元素（ここでは特にＢであるが、Ｎｉ、Ｃｕ、Ｎ、Ｎｂ、Ｔｉ、Ｖ、Ｐも可能）の添加とによって、弾性限界の明らかな低下とそれによる熱間及び冷間圧延時の可塑性の改善を達成する方法が周知である。この鋼鉄を製造するために、投入材料（ブルーム、薄いブルーム又はストリップ）を加熱して、所定の温度限界に注意しつつ熱間圧延し、巻き取っている。   According to Patent Document 3, an increase in possible carbon content (C ≦ 1%) and addition of further elements (here in particular B, but Ni, Cu, N, Nb, Ti, V, P are also possible) Thus, it is well known how to achieve an apparent reduction in the elastic limit and thereby an improvement in plasticity during hot and cold rolling. In order to produce this steel, the input material (bloom, thin bloom or strip) is heated, hot rolled and wound while paying attention to predetermined temperature limits.

特許文献４には、２ロール式鋳造機を用いて、１２〜３０％のマンガンを含有する鋼鉄を１ｍｍ〜６ｍｍ未満の厚さの薄い中間ストリップとして鋳造し、圧延ロールの隙間から垂直に出て来る中間ストリップを、その表面に塗布する冷却剤によって冷却し、その次に一回の熱間圧延パスで最終的な厚さに圧延する方法が記載されている。圧延ロールの隙間からの出力から圧延機への入力までの間の全体的な時間間隔は、約８秒である。   In Patent Document 4, a steel containing 12 to 30% manganese is cast as a thin intermediate strip having a thickness of 1 mm to less than 6 mm using a two-roll type casting machine, and the steel roll is vertically exited from the gap between the rolling rolls. A method is described in which the incoming intermediate strip is cooled by a coolant applied to its surface and then rolled to a final thickness in one hot rolling pass. The overall time interval between the output from the mill roll gap and the input to the mill is about 8 seconds.

特許文献５により、Ｆｅ−Ｃ−Ｍｎ合金から成るストリップを製造する方法が周知であり、その方法では、先ずは、６〜３０％のＭｎ、０．００１〜１．６％のＣ、２．５％以下のＳｉ、６％以下のＡｌ、１０％以下のＣｒ及び更なる元素から成る組成の１．５〜１０ｍｍの厚さの薄い鋼板を２ロール式鋳造機で作り、その次にそれを１０〜６０％の低減度を持つ一つ以上の工程により熱間圧延している。
欧州特許第０８８９１４４号明細書 ドイツ特許公開第１９９００１９９号明細書 国際特許公開第０２／１０１１０９号明細書 欧州特許第１３４１９３７号明細書 欧州特許第１０６７２０３号明細書 Spitzer et al.:"Innovative Stahlprodukte - Herausforderung fuer die Prozessentwicklung"; Konferenz-Einzelbericht: Barbara 2001, S.71-84 Gigacher et al.:"Eigenschaften hochmanganhaltiger Staehle unter stranggiessaehnlichen Bedingungen"; BHM149 (2004), Heft 3, S.112-117 According to US Pat. No. 6,057,049, a method for producing a strip made of Fe—C—Mn alloy is known, in which first, 6-30% Mn, 0.001-1.6% C, 2. A thin steel sheet having a thickness of 1.5 to 10 mm having a composition of 5% or less of Si, 6% or less of Al, 10% or less of Cr and further elements is produced by a two-roll casting machine, and then Hot rolling is performed by one or more processes having a reduction degree of 10 to 60%.
EP 0 899 144 German Patent Publication No. 19900199 International Patent Publication No. 02/101109 Specification EP 1341937 European Patent No. 10672203 Spitzer et al.:"Innovative Stahlprodukte-Herausforderung fuer die Prozessentwicklung "; Konferenz-Einzelbericht: Barbara 2001, S.71-84 Gigacher et al.:"Eigenschaften hochmanganhaltiger Staehle unter stranggiessaehnlichen Bedingungen "; BHM149 (2004), Heft 3, S.112-117

この発明の課題は、前述した従来技術を出発点として、所定の化学的組成を持つマンガン含有量の多い鋼鉄を連続鋳造法により製造することを可能とする出来る限り簡単に実現される方法及び設備を提示することである。   The object of the present invention is to provide a method and equipment that can be realized as simply as possible, making it possible to produce a manganese-rich steel having a predetermined chemical composition with a predetermined chemical composition by a continuous casting method. Is to present.

この設定した課題は、方法に関して、請求項１に挙げた特徴にもとづき、１５〜２７％のＭｎ、１〜６％のＡｌ、１〜６％のＳｉ、０．８％以下の炭素及び残りを鉄と微量元素とする所定の化学的な組成を持つ軽量鋼を、順番に配置した工程にもとづき、
・薄いブルーム（ｄ≦１２０ｍｍ）の鋳造機（１）で、非常に高速に平衡状態を達成して、その次にその潤滑性をもはや変化させない好適な鋳造用粉末を用いて鋳造して、ブルームに分割し、
・凝固と分割に続いて直ぐに、作業過程内の中間炉（４）でブルーム（３）の温度の均等化を行い、その次に、
・その後冷却すること無く直ぐにブルーム（３）を熱間圧延する、
ことによって解決される。 This set task is based on the features listed in claim 1 with respect to the method, including 15-27% Mn, 1-6% Al, 1-6% Si, 0.8% carbon or less and the rest. Based on a process in which lightweight steel with a predetermined chemical composition of iron and trace elements is placed in order,
Casting in a thin bloom (d ≦ 120 mm) casting machine (1) with a suitable casting powder that achieves equilibrium at very high speed and then no longer changes its lubricity; Divided into
-Immediately following solidification and division, the temperature of the bloom (3) is equalized in the intermediate furnace (4) in the work process, and then
-Hot-roll the bloom (3) immediately without cooling after that,
It is solved by.

この方法を実施するための設備は、請求項７の特徴によって特徴付けられる。   An installation for carrying out this method is characterized by the features of claim 7.

例えば、ＣＳＰ鋳造機（ＣＳＰ：コンパクトストリップ製造）で薄いブルームを製造する場合、ストランドは、垂直に引き出されて、凝固に続いて水平方向に曲げられ、その次にブルームに分割される。そのため、この場合内部のひび割れに関する問題は起こらない。高強度のオーステナイト鋼を製造することは、設備による過負荷を加えること無しに実施可能であり、この限りにおいて従来技術である。   For example, when producing thin blooms on a CSP caster (CSP: compact strip manufacture), the strands are drawn vertically, bent horizontally following solidification, and then divided into blooms. Therefore, in this case, there is no problem with internal cracks. The production of high strength austenitic steel can be carried out without overloading by equipment, and as far as this is the prior art.

凝固後直ぐのストランド内にも存在するミクロ偏析は、中間炉、例えば、ローラーハース炉による作業過程において、その後の圧延成形の前に、拡散によって大部分が又もや消滅する。その場合、ブルーム中心のマクロ偏析は、オーステナイト特殊鋼の場合と同様に、熱間圧延設備での大きな成形によって十分に均等化される。   Most of the microsegregation existing in the strands immediately after solidification disappears again by diffusion in the course of work in an intermediate furnace, for example, a roller hearth furnace, before subsequent rolling. In that case, the macrosegregation at the center of the bloom is sufficiently equalized by the large forming in the hot rolling equipment, as in the case of the austenitic special steel.

この発明にもとづきＣＳＰ設備においてローラーハース炉を使用することによって、有利には、その短い通過時間のために、例えば、従来技術による伝統的な幅広ストランド用熱間圧延ラインのあと押し炉での長い加熱フェーズにより障害となる可能性の有る合金元素の大きな密度低下又は粒界の酸化が防止される。   By using a roller hearth furnace in a CSP facility according to the invention, it is advantageous because of its short transit time, for example, in the booster furnace of a traditional wide strand hot rolling line according to the prior art. A large decrease in density or oxidation of the grain boundaries of the alloying elements that can be an obstacle due to the heating phase is prevented.

この発明にもとづき薄いブルーム鋳造機でマンガン及びアルミニウム含有量の多いＴＷＩＰ軽量鋼を鋳造する技術を利用することができるためには、好適な鋳造用粉末を使用する必要がある。そのような好適な鋳造用粉末は、この発明によると、平衡状態を非常に高速に達成するとともに、その後その潤滑性をもはや変化させないという特性を有するものである。   In order to be able to utilize the technique of casting TWIP lightweight steel with high manganese and aluminum contents in a thin bloom caster based on this invention, it is necessary to use a suitable casting powder. Such a suitable casting powder has, according to the invention, the property of achieving an equilibrium state very fast and subsequently no longer changing its lubricity.

この発明では、例えば、鋼鉄内のアルミニウムによるＳｉＯ2 を低下させる反応速度を遅くするために、鋳造用粉末は、１０％を超える多くのＡｌ2 Ｏ3 成分を含有する。平衡状態においてより多くのＳｉＯ2 を利用可能とするためには、それに代わって、或いはそれに追加して、鋳造用粉末のＳｉＯ2 成分を増加させ、その場合増加は、０．５〜０．７までの塩基度（ＣａＯ／ＳｉＯ2 の比率）で行われる。 In this invention, for example, the casting powder contains more than 10% Al 2 O 3 component to slow down the reaction rate of lowering SiO 2 by aluminum in the steel. In order to make more SiO 2 available in equilibrium, instead or in addition, the SiO 2 component of the casting powder is increased, in which case the increase is between 0.5 and 0.7. Up to basicity (CaO / SiO 2 ratio).

ＭｎＯ2 が、鋼鉄内のＡｌによって容易にＳｉＯ2 として還元され、それによってＳｉＯ2 の減少（燃焼）が防止されるので、この発明の追加的な手法として、鋳造用粉末にＭｎＯ2 を添加することが可能である。 MnO 2 is easily reduced as SiO 2 by Al in the steel, because it by a reduction in SiO 2 (combustion) is prevented, as an additional method of the present invention, the addition of MnO 2 to the casting powder It is possible.

この発明では、ＳｉＯ2 のようにガスを形成する形で作用するが、鋼鉄内のアルミニウムによって浸食（還元）されないＴｉＯ2 によってＳｉＯ2 の一部を置き換えて、鋳造用粉末に混合することも可能である。 In this invention, it works in the form of gas like SiO 2 , but it is also possible to replace a part of SiO 2 with TiO 2 that is not eroded (reduced) by aluminum in the steel and to mix it with the casting powder. It is.

最後に、鋳型内における鋳造用粉末の粘性を低下させる手法も有る。そうすることによって、鋳造用粉末の使用量が増大して、生成するＡｌ2 Ｏ3 がより多く取り去られ、その結果Ａｌ2 Ｏ3 の含有量が少ない形で平衡状態が設定される。この粘性の低減は、鋳造用粉末にＢ2 Ｏ3 （ボラート）、Ｎａ2 Ｏ及び／又はＬｉＯ2 を添加することによって達成される。 Finally, there is a technique for reducing the viscosity of the casting powder in the mold. By doing so, the amount of casting powder used is increased, and a larger amount of Al 2 O 3 is removed, and as a result, an equilibrium state is set with a lower content of Al 2 O 3 . This reduction in viscosity is achieved by adding B 2 O 3 (borate), Na 2 O and / or LiO 2 to the casting powder.

以下において、この発明により熱間圧延ストリップを製造するための設備を模式図に図示して、方法の構成を詳しく説明する。   In the following, the equipment for producing a hot-rolled strip according to the present invention is illustrated in a schematic diagram, and the configuration of the method will be described in detail.

基本的に、使用する設備は、周知のＣＳＰ設備であり、この発明では、個々の設備構成部分間の間隔を変更して、凝固に続いて直ぐに作業過程内の中間炉で温度の均等化を実行し、その次にその後冷却すること無く直ぐにブルームを熱間圧延するとの要件を果たす形で、この発明による方法を実施することが可能となっている。   Basically, the equipment used is a well-known CSP equipment. In the present invention, the interval between the individual equipment components is changed, and immediately after solidification, the temperature is equalized in the intermediate furnace in the work process. It is possible to carry out the method according to the invention in such a way that it fulfills the requirement that it is carried out and then immediately hot-rolled without subsequent cooling.

それに対応して、図面に図示した設備は、薄いブルームの鋳造機１とその後に配置された中間炉４から構成されており、中間炉には、凝固後の連続したストランド２から分割されたブルーム３が運び込まれる。この中間炉４には、更に圧延設備５が後置されており、そこでは、中間炉４で温度の均等化が行われた後のブルーム３が、直ぐに、即ち、その後冷却されずに、熱間圧延ストリップ６として圧延される。   Correspondingly, the equipment shown in the drawing consists of a thin bloom casting machine 1 and an intermediate furnace 4 arranged thereafter, in which the bloom is divided from the continuous strand 2 after solidification. 3 is brought in. This intermediate furnace 4 is further provided with a rolling facility 5 in which the bloom 3 after the temperature equalization in the intermediate furnace 4 is heated immediately, i.e. without cooling thereafter. It is rolled as an intermediate rolled strip 6.

この発明による熱間圧延ストリップを製造するための設備の模式図Schematic diagram of equipment for producing hot rolled strips according to this invention

Claims (7)

軽量鋼を先ずは連続鋳造設備（１）で連続したストランド（２）として鋳造して、ブルーム（２）に分割し、その次に最終的な厚さに圧延する形で、マンガン（Ｍｎ）、アルミニウム（Ａｌ）及びケイ素（Ｓｉ）の含有量の多い、ＴＷＩＰ（双晶誘起塑性）特性を持つ良好に冷間成形可能な高強度オーステナイト軽量鋼から成る熱間圧延ストリップ（６）を製造するための方法において、
１５〜２７％のＭｎ、１〜６％のＡｌ、１〜６％のＳｉ、０．８％以下の炭素及び残りを鉄と微量元素とする所定の化学的な組成を持つ軽量鋼を、順番に配置した工程にもとづき、
・薄いブルーム（ｄ≦１２０ｍｍ）の鋳造機（１）で、非常に高速に平衡状態を達成して、その次にその潤滑性をもはや変化させない鋳造用粉末を用いて鋳造して、ブルーム（３）に分割し、
・凝固と分割に続いて直ぐに、作業過程内の中間炉（４）でブルーム（３）の温度の均等化を行い、その次に、
・その後冷却すること無く直ぐにブルーム（３）を熱間圧延する、
ことを特徴とする方法。 Lightweight steel is first cast as a continuous strand (2) in a continuous casting facility (1), divided into blooms (2), then rolled to final thickness, manganese (Mn), To produce a hot-rolled strip (6) made of high-strength austenitic lightweight steel with good TWIP (twinning-induced plasticity) properties with high aluminum (Al) and silicon (Si) content and good cold formability In the method of
15 to 27% Mn, 1 to 6% Al, 1 to 6% Si, 0.8% or less of carbon, and light weight steel having a predetermined chemical composition with the remainder being iron and trace elements, in order Based on the process placed in
Casting in a thin bloom (d ≦ 120 mm) casting machine (1) with a casting powder that achieves equilibrium at very high speed and then no longer changes its lubricity; )
-Immediately following solidification and division, the temperature of the bloom (3) is equalized in the intermediate furnace (4) in the work process, and then
-Hot-roll the bloom (3) immediately without cooling after that,
A method characterized by that. 当該の鋳造用粉末が、１０％を超えるまでに含有量を増大させたＡｌ2 Ｏ3 を有することを特徴とする請求項１に記載の方法。 The method according to claim 1, characterized in that the casting powder has Al 2 O 3 whose content is increased by more than 10%. 当該の鋳造用粉末が、０．５〜０．７の粘性（ＣａＯ／ＳｉＯ2 の比率）を持つまでに含有量を増大させたＳｉＯ2 を有することを特徴とする請求項１又は２に記載の方法。 Casting powder in question, according to claim 1 or 2, characterized in that it has a SiO 2 with increased content before having viscosity (CaO / SiO 2 ratio) of 0.5 to 0.7 the method of. 当該の鋳造用粉末が、ＭｎＯ2 及び／又はＴｉＯ2 を含有することを特徴とする請求項１から３までのいずれか一つに記載の方法。 The method according to any one of claims 1 to 3, wherein the casting powder contains MnO 2 and / or TiO 2 . 鋳型内における鋳造用粉末の粘性を低減するために、当該の鋳造用粉末が、Ｂ2 Ｏ3 （ボラート）、Ｎａ2 Ｏ及び／又はＬｉＯ2 の成分を含有することを特徴とする請求項１から４までのいずれか一つに記載の方法。 To reduce the viscosity of the casting powder in the mold, the casting powder contains B 2 O 3 (borate), Na 2 O and / or LiO 2 components. 5. The method according to any one of 4 to 4. 中間炉（４）が、ローラーハース炉であることを特徴とする請求項１から５までのいずれか一つに記載の方法。   6. The method as claimed in claim 1, wherein the intermediate furnace (4) is a roller hearth furnace. 請求項１から６までのいずれか一つに記載の方法を実施するための、マンガン（Ｍｎ）、アルミニウム（Ａｌ）及びケイ素（Ｓｉ）の含有量の多い、ＴＷＩＰ（双晶誘起塑性）特性を持つ良好に冷間成形可能な高強度オーステナイト軽量鋼から成る熱間圧延ストリップの製造設備において、
この設備の構成部分である薄いブルームの鋳造機（１）、中間炉（４）及び熱間圧延設備（５）が、直接連続する形で配置されていることを特徴とする設備。 A TWIP (twinning induced plasticity) characteristic with a high content of manganese (Mn), aluminum (Al) and silicon (Si) for carrying out the method according to any one of claims 1 to 6. In the production facility of hot-rolled strip made of high-strength austenitic lightweight steel with good cold forming
A facility characterized in that a thin bloom casting machine (1), an intermediate furnace (4), and a hot rolling facility (5), which are components of this facility, are arranged in a directly continuous form.
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