JP4688890B2 - 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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JP4688890B2
JP4688890B2 JP2007557433A JP2007557433A JP4688890B2 JP 4688890 B2 JP4688890 B2 JP 4688890B2 JP 2007557433 A JP2007557433 A JP 2007557433A JP 2007557433 A JP2007557433 A JP 2007557433A JP 4688890 B2 JP4688890 B2 JP 4688890B2
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casting powder
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ギルゲンゾーン・アルブレヒト
ケンプケン・イェンス
ライフェルシャイト・マルクス
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エス・エム・エス・ジーマーク・アクチエンゲゼルシャフト
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    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21BROLLING OF METAL
    • B21B1/00Metal-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
    • B21B1/46Metal-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
    • B21B1/466Metal-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
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21BROLLING OF METAL
    • B21B3/00Rolling 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
    • B21B3/02Rolling special iron alloys, e.g. stainless steel
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/10Supplying or treating molten metal
    • B22D11/11Treating the molten metal
    • B22D11/111Treating the molten metal by using protecting powders
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12Accessories for subsequent treating or working cast stock in situ
    • B22D11/1213Accessories for subsequent treating or working cast stock in situ for heating or insulating strands
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/14Plants for continuous casting
    • B22D11/142Plants for continuous casting for curved casting
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D6/00Heat treatment of ferrous alloys
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D6/00Heat treatment of ferrous alloys
    • C21D6/005Heat treatment of ferrous alloys containing Mn
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021Modifying 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
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021Modifying 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
    • C21D8/0215Rapid solidification; Thin strip casting

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 due to 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 3 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 caster, and the steel roll exits vertically 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) caster (1) with a suitable casting powder that achieves equilibrium at very high speed and then no longer changes its lubricity; Divided into
-Immediately after 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 3 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 3 がより多く取り去られ、その結果Al2 3 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 3 (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 (6)

  1. 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(3)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)含有する、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、
    全体の重量に対する重量百分率に関して、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不純物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)で鋳造用粉末を用いて鋳造して、ブルーム(3)に分割し、その場合、鋼鉄内のアルミニウムによるSiOの還元反応速度を遅くさせるか、或いは鋳型内における粘性を低下させることによりAl含有量を減少させるか、或いはその両方を実現するのに適した成分を鋳造用粉末に添加し、
    ・連続したストランド(2)の凝固とブルーム(3)への分割に続いて直ぐに、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、
    ことと、
    この鋳造用粉末が、0.5〜0.7の粘性(CaO/SiO の比率)を持つまでに含有量を増大させたSiO を有することと、
    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 (3), then rolled to final thickness, manganese (Mn), methods for containing aluminum (Al) and silicon (Si), for producing a TWIP hot-rolled strip of (twinning induced plasticity) good cold formable high-strength austenitic lightweight steel having a characteristic (6) In
    Predetermined chemical composition with 15 to 27% Mn, 1 to 6% Al, 1 to 6% Si, less than or equal to 0.8% carbon and the balance iron and impurities with respect to the weight percentage of the total weight Based on the process of arranging lightweight steel with
    Casting with casting powder (1) in a thin bloom (d ≦ 120 mm) casting powder and dividing into bloom (3), in which case the reduction reaction rate of SiO 2 by the aluminum in the steel is slowed Or by reducing the Al 2 O 3 content by reducing the viscosity in the mold, or by adding ingredients suitable for realizing both to the casting powder,
    -Immediately following solidification of the continuous strand (2) and division into bloom (3), the temperature is equalized in the intermediate furnace (4) in the working process, then
    -Hot-roll the bloom (3) immediately without cooling after that,
    And
    The casting powder, and having a SiO 2 with increased content before having viscosity (CaO / SiO 2 ratio) of 0.5 to 0.7,
    A method characterized by.
  2. 当該の鋳造用粉末が、全体の重量に対する重量百分率に関して、10%を超えるまでに含有量を増大させたAlを有することを特徴とする請求項1に記載の方法。The process according to claim 1, characterized in that the casting powder has Al 2 O 3 with an increased content by more than 10% in terms of weight percentage with respect to the total weight.
  3. 当該の鋳造用粉末が、MnO及び/又はTiOを含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, the method according to claim 1 or 2, characterized in that it contains MnO 2 and / or TiO 2.
  4. 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、B(ボラート)、NaO及び/又はLi の成分を含有することを特徴とする請求項1から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, according to claim casting powder in question, B 2 O 3 to (borate), characterized in that it contains Na 2 O and / or Li 2 O component The method according to any one of 1 to 3 .
  5. 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からまでのいずれか一つに記載の方法。Intermediate furnace (4) The method according to any one of claims 1 to 4, characterized in that the roller hearth furnace.
  6. 請求項1からまでのいずれか一つに記載の方法を実施するための、CSP(コンパクトストリップ製造)設備と、その後に配置された設備構成部分である薄いブルームの鋳造機(1)、中間炉(4)及び圧延設備(5)とから構成された、全体の重量に対する重量百分率に関して、15〜27%のマンガン(Mn)、1〜6%のアルミニウム(Al)及び1〜6%のケイ素(Si)を含有する、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、
    薄いブルームの鋳造機(1)で、鋳造用粉末を用いて鋳造して、ブルーム(3)に分割し、連続したストランド(2)の凝固に続いて直ぐに作業過程内の中間炉で、分割したブルーム(3)の温度の均等化を行い、次にその後冷却させること無く直ぐに、そのブルーム(3)を熱間圧延するように、これらの設備構成部分間の間隔を変化させることと、
    この鋳造用粉末が、0.5〜0.7の粘性(CaO/SiO の比率)を持つまでに含有量を増大させたSiO を有することと、
    を特徴とする設備。
    A CSP (Compact Strip Manufacturing) facility, followed by a thin-bloom caster (1), an intermediate component, for carrying out the method according to any one of claims 1-5 , intermediate Composed of a furnace (4) and rolling equipment (5), with respect to the weight percentage of the total weight, 15 to 27% manganese (Mn), 1 to 6% aluminum (Al) and 1 to 6% silicon In a production facility for hot-rolled strips made of high-strength austenitic lightweight steel containing (Si) and well cold-formable with TWIP (twinning induced plasticity) properties,
    Cast in thin bloom casting machine (1) with casting powder, split into bloom (3), and immediately after solidification of continuous strand (2), split in intermediate furnace in process Changing the spacing between these equipment components so that the temperature of the bloom (3) is equalized and then immediately hot rolled without subsequent cooling ;
    The casting powder, and having a SiO 2 with increased content before having viscosity (CaO / SiO 2 ratio) of 0.5 to 0.7,
    Equipment characterized by.
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