JP2004515362A - Method for producing hot strip from steel with high manganese content - Google Patents

Method for producing hot strip from steel with high manganese content Download PDF

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JP2004515362A
JP2004515362A JP2002548196A JP2002548196A JP2004515362A JP 2004515362 A JP2004515362 A JP 2004515362A JP 2002548196 A JP2002548196 A JP 2002548196A JP 2002548196 A JP2002548196 A JP 2002548196A JP 2004515362 A JP2004515362 A JP 2004515362A
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strip
hot strip
hot
weight
casting
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JP3836793B2 (en
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ベルンハルト エルグル
ディーター ゼンク
シュミッツ ヨハン ヴィルヘルム
アンドレーアス オッフェアゲルト
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp Steel AG
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    • 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
    • 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
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • 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
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • B21B1/463—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 continuous process, i.e. the cast not 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
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B9/00—Measures for carrying out rolling operations under special conditions, e.g. in vacuum or inert atmosphere to prevent oxidation of work; Special measures for removing fumes from rolling mills

Abstract

A steel strip can be produced which in spite of its high manganese content has good deformation behaviour in that, according to the invention, from a steel which comprises more than 12 to 30 weight % of manganese, a roughed strip (V) is cast close to the final dimensions in a double-roller casting machine ( 2 ), said roughed strip comprising a thickness of up to 6 mm. Following casting, this roughed strip is further processed to form a continuous hot strip by preferably being rolled in a single hot roll pass.

Description

【０００１】
本発明は、１２重量％より多く３０重量％以下の高いマンガン含有量を有する鋼から熱間ストリップを製造する方法に関する。このタイプの鋼は、特に高い強度により特徴付けられている。
【０００２】
マンガン含有量がこのように高い鋼を製造及び処理する場合には、その凝固挙動が、深絞り加工用途に通常用いられる鋼、例えば、ＩＦ鋼又は低炭素鋼の凝固挙動と異なるという問題がある。従って、高いマンガン含有量を有する問題としているタイプの鋼であって、通常の連続スラブキャスティングにおいてキャスティングされた鋼は、変形挙動が乏しいことが示されている。
【０００３】
ＤＥ１９９００１９９Ａ１から公知の方法に従って、薄ストリップキャスティングを実施して最終寸法に近いストリップを形成することにより、他の合金要素以外にＭｎ７％〜２７％を含有する鋼を製造することができ、そして処理して熱間ストリップにすることができる。この方法により得られた材料は、自動車のボディー構造の分野における用途に特に適している。
【０００４】
本発明の課題は、高いマンガン含有量にもかかわらず、変形挙動が良好な鋼ストリップを製造することを可能にする方法を提供することである。
【０００５】
この課題は、マンガンを１２重量％より多く３０重量％以下の量で含有する鋼からＴＷＩＰ及びＴＲＩＰ特性を持った熱間ストリップを製造する方法であって、メルトをダブルローラーキャスティングマシンにおいて最終寸法に近い寸法にキャスティングして粗ストリップを形成し、ここで前記粗ストリップの厚さは６ｍｍ以下であり、そしてキャスティングの後に前記粗ストリップをシングル熱間圧延パスにおいて熱間ストリップの最終厚さまで圧延することにより連続的に更に処理して熱間ストリップを形成する方法により解決される。
【０００６】
本発明の方法では、高マンガン含有の鋼をキャスティングして、寸法が熱間ストリップの最終寸法に近い原材料を形成する。この方法においては、既に前記キャスティング処理の間に、製造された材料は、その全横断面にわたり本質的に均一な凝固が保証されるほどに薄い。驚くべきことに、最終寸法に近くなるようにキャスティングされた原材料のミクロ組織は、常法で製造された比較的マンガン含有量の高い鋼ストリップの場合よりも、本質的により微細な結晶粒からなると共に、より均一であることが示された。この原材料から製造された熱間ストリップは、ＴＲＩＰ（変態誘起塑性［Ｔｒａｎｓｆｏｒｍａｔｉｏｎ Ｉｎｄｕｃｅｄ Ｐｌａｓｔｉｃｉｔｙ］）特性及びＴＷＩＰ（双晶変形誘起塑性［Ｔｗｉｎｎｉｎｇ Ｉｎｄｕｃｅｄ Ｐｌａｓｔｉｃｉｔｙ］）特性を有しており、そしてその結果として、その高い強度と相俟って自動車のボディー構造における用途に極めて適するようにする良好な変形能を有している。
【０００７】
本発明では、製造された材料はできるだけ薄いことが好ましい。キャスト原材料が薄ければ薄いほど、凝固ミクロ組織はより微細となり、そして熱間ストリップを形成すべき更なる処理を妨害する凝固による欠陥の範囲はより少なくなる。それと同時に、薄いキャスト原材料において、前記凝固処理は、目標の方法によって容易に制御することができる。従って、制御された処理は、とりわけ本明細書において述べている鋼の場合に、凝固速度がマイクロ偏析の範囲及び分布に直接的な影響を与えるという事実を考慮に入れることができる。凝固速度は、次いで、凝固の間に起こる、例えば、ＭｎＳ、ＡｌＮ、及びＴｉ（Ｃ、Ｎ）の析出の状態及び粒子の成長に影響を与える。従って、キャスト原材料のミクロ組織パラメータの目標の制御の結果として、更なる処理に対する能力及び最終製品の使用特性に決定的な影響を与える基本的な設定を選択することが可能である。
【０００８】
本発明では、ダブルローラーキャスティングマシンにおいて鋼をキャスティングする。このタイプのキャスティングマシンは、それ自体は公知であり、特に、結果として最適なキャスト組織及びそれに関連した最適な変形能を生じる原材料の凝固挙動（特に凝固速度及び凝固の均一性）を有する熱間ストリップの最終寸法に極めて近い薄い原材料を製造することが可能である。
【０００９】
驚くべきことに、粗ストリップから、熱間ストリップをその最終厚さまで圧延する際に、わずか１回のパスでとりわけ良好な加工結果を達成することができることが見出された。前記キャスティング処理と熱間圧延（一回のパス）との、即座に連続する配列は、キャスティング処理の熱を圧延処理に持ち込むことを可能にする。その結果として、熱間圧延前の再加熱の工程であって、通常のスラブキャスティングにおいて常に必要とされる工程を回避することができる。キャスティング熱を「持ち込む」ことは、過剰の結晶成長をも阻止し、従って、更に、原材料における微細なミクロ組織の形成を支持する。
【００１０】
最終製品の特性における凝固処理の特別な影響のため、原材料の熱間ストリップを形成するための更なる処理が、キャスティングの直後に実施される制御された冷却を含むと好都合である。このことは、更なる処理に対して最適化されるミクロ組織を得るように、鋳型から出てくる原材料を、目標の方法によって冷却することを可能にする。通常、冷却は、周囲空気への暴露による冷却に比較して加速された速度で行う。
【００１１】
最終製品の所望な特性及び組成に応じて、原材料がロールスタンドに挿入する平均初期圧延温度が、１１００℃〜７５０℃の範囲内であることができることが、実験により示された。
【００１２】
原材料を熱間圧延する場合、圧延された熱間ストリップを熱間圧延後に制御された方法で冷却する目標の方法によって、熱間圧延されたストリップの特性に更に影響を与えることができる。
【００１３】
原則として、本発明に従って得られた熱間ストリップを「インライン」でさらに処理して、例えば、冷間ストリップを形成することを想定することができる。しかしながら、可能性のある続きの処理工程又は準備される熱間ストリップの特性を考慮して、更なる処理の一部として前記ストリップをコイリングすることが、多くの場合に好都合であろう。
【００１４】
保護ガス雰囲気において少なくとも断続的（ａｂｓｃｈｎｉｔｔｓｗｅｉｓｅ）に実施し、原材料の熱間ストリップを形成するための更なる処理の結果として、ストリップ表面の酸化、及びそれに関連した過剰なスケール形成を回避することができる。この関係において、原材料を、少なくとも原材料がロールスタンドに挿入するまで保護ガス雰囲気中に維持することが特に好ましい。
【００１５】
更なる合金要素とは別に、本発明において用いられる鋼は、ケイ素を３．５重量％以下、特には３重量％以下の量で含有することができる。更に、前記鋼は、アルミニウムを３．５重量％以下、特には３重量％以下の量で含有することができる。本発明により処理されるタイプの鋼において、鉄及びアルミニウム又は鉄及びケイ素は、熱間形成温度より低い温度で生じ、且つ室温に対して安定である合金相（ｉｎｔｅｒｍｅｔａｌｌｉｓｃｈ ｐｈａｓｅｎ）を形成する。
【００１６】
以下に、一つの実施態様によって本発明を更に詳細に説明する。
図面は、熱間ストリップを製造する装置のデザインの模式的側面図であり；
グラフは、図１の装置における粗ストリップ及び熱間ストリップの処理時間の間の温度コースを示し；
写真１は、図１の装置により製造された熱間ストリップの端部の拡大断面を示し；そして
写真２は、図１の装置により製造された熱間ストリップの中央部の拡大断面を示す。
【００１７】
前記図面は、熱間ストリップＷを製造するための装置１のデザインを模式的に示しており、前記装置は、キャスティング装置２、第一冷却セクション３、ロールスタンド４、第二冷却セクション５、及びコイリング装置６を含む。
【００１８】
公知の原理によって設計されたダブルローラーキャスティングマシンにおいて、タンディッシュ７中に含まれるメルトＳ（そのメルト組成は、詳細に後述する）を、２つのキャスティングローラー８，９の間に形成されたキャスティングギャップ１０中に注いで、粗ストリップＶを形成する。前記キャスト粗ストリップＶは、１ｍｍ〜６ｍｍよりも狭い範囲で変化することができる厚さで、連続運搬処理によって前記キャスティングギャップ１０を出る。
【００１９】
前記粗ストリップＶは、ロールスタンド４へ向かう途中で、キャスティングギャップ１０の出口の下流であってキャスティングギャップ１０に密接して配置されている第一冷却セクション３において、前記粗ストリップＶの表面に適用された冷却媒体により、制御された方法で冷却される。
【００２０】
コンベヤーセクション（これに沿って、薄ストリップＶがキャスティングギャップ１０の出口とロールスタンド４との間を通過する）は、内部に保護ガス雰囲気が維持されているドッグハウス１１により囲まれている。この方法では、前記ストリップの表面と周囲空気との間の接触が回避される。
【００２１】
薄ストリップＶは、初期圧延温度ＡＴでロールスタンド４に入り、そして前記ロールスタンドにおいて１回のパスで最終厚さまで圧延される。
その直後に、最終圧延温度ＥＴでロールスタンド４を出る熱間ストリップＷは、第二冷却セクション５を通過する。この冷却セクション５において、熱間ストリップＷは、制御された方法で適切な冷却媒体によりコイリング温度ＨＴまで再び導かれた後に、コイリング装置６においてコイリングされて、コイルＣを形成する。
【００２２】
添付のグラフは、初期圧延温度ＡＴ、最終圧延温度ＥＴ、及びストリップ幅にキャスティングした後の処理時間の間のコイリング温度ＨＴ（これは、製造されるべき熱間ストリップの組成及び所望の特性に応じており、図１に従って設計された装置において設定することができる）を示している。引き続きの等温保持、圧延、及び急冷を伴う特定の制限曲線に沿った適切な温度制御管理によって、熱間ストリップの良好な用途特性が熱間圧延後に残存するように、熱間ストリップがロールスタンドから出た後に、熱間ストリップの微細粒化ミクロ組織を固定（ｅｉｎｆｒｉｅｒｅｎ）することができる。この効果は、とりわけ、前記粗ストリップ及び前記熱間ストリップの温度経過がグラフに示す下限曲線に近い場合に、達成されることができる。
【００２３】
通常の不可避な不純物を除き、前記実施態様において注がれたメルトＳは、Ｍｎ（含有量２０重量％）、Ｃ（含有量０．００３重量％）、硫黄（含有量０．００７重量％）、Ｓｉ（含有量３．０重量％）、Ａｌ（含有量３．０重量％）、及び鉄（その残部）を含んでいた。
【００２４】
写真１は、端部の拡大断面を示しており、一方、写真２は、図１に示した装置により製造された熱間ストリップから製造された鋼の中央部の等倍の拡大断面を示している。このストリップが、オーステナイト及び第二の相〔これは、おそらく含炭素相であろう〕を含むデンドライトミクロ組織を含んでいることは明らかである。このミクロ組織は、ストリップのコアに対して有意に、より微細になる。
【図面の簡単な説明】
【図１】
熱間ストリップを製造する装置のデザインを表す模式的側面図である。
【図２】
図１の装置における粗ストリップ及び熱間ストリップの処理時間の間の温度経過を示すグラフである。
【図３】
写真１は、図１の装置により製造された熱間ストリップの端部の拡大断面を示し、そして
写真２は、図１の装置により製造された熱間ストリップの中央部の拡大断面を示す。
【符号の説明】
１・・・装置；
２・・・ダブルローラーキャスティングマシン；
３・・・第一冷却セクション；
４・・・ローラースタンド；
５・・・第二冷却セクション；
６・・・コイリング装置；
７・・・タンディッシュ；
８，９・・・キャスティングローラー；
１０・・・キャスティングギャップ；
１１・・・ドッグハウス；
ＡＴ・・・初期圧延温度；
Ｃ・・・コイル；
ＥＴ・・・最終圧延温度；
Ｓ・・・メルト；
Ｖ・・・薄ストリップ；
Ｗ・・・熱間ストリップ。[0001]
The present invention relates to a method for producing hot strip from steel having a high manganese content of more than 12% by weight and not more than 30% by weight. This type of steel is characterized by a particularly high strength.
[0002]
The problem with producing and processing steels with such high manganese content is that their solidification behavior differs from the solidification behavior of steels commonly used for deep drawing applications, such as IF steels or low carbon steels. . Thus, steels of the type in question having a high manganese content, cast in conventional continuous slab casting, have been shown to have poor deformation behavior.
[0003]
According to the method known from DE 199 00 199 A1, thin strip casting can be carried out to form strips close to the final dimensions, whereby steels containing 7% to 27% Mn besides other alloy elements can be produced and processed. Hot strip. The material obtained by this method is particularly suitable for applications in the field of automotive body structures.
[0004]
The object of the present invention is to provide a method which makes it possible to produce a steel strip with good deformation behavior, despite a high manganese content.
[0005]
The object is to produce a hot strip with TWIP and TRIP properties from steel containing manganese in an amount of more than 12% by weight and not more than 30% by weight, wherein the melt is brought to its final dimensions in a double roller casting machine. Casting to a close dimension to form a coarse strip, wherein the thickness of the coarse strip is not more than 6 mm, and after casting, rolling the coarse strip in a single hot rolling pass to the final thickness of the hot strip. The method is further solved by a method of continuously processing to form a hot strip.
[0006]
In the method of the present invention, high manganese content steel is cast to form a raw material whose dimensions are close to the final dimensions of the hot strip. In this way, already during the casting process, the material produced is thin enough to ensure essentially uniform solidification over its entire cross section. Surprisingly, the microstructure of the raw material, cast to near final dimensions, consists essentially of finer grains than in the case of relatively manufactured manganese-rich steel strip. , And was shown to be more uniform. The hot strip produced from this raw material has TRIP (Transformation Induced Plasticity) properties and TWIP (Twinning Induced Plasticity) properties, and consequently, its properties. Combined with high strength, it has good deformability which makes it very suitable for use in automotive body structures.
[0007]
According to the invention, it is preferred that the material produced is as thin as possible. The thinner the cast material, the finer the solidification microstructure and the less the extent of solidification defects that will interfere with further processing to form a hot strip. At the same time, in thin cast raw materials, the solidification process can be easily controlled by the targeted method. Thus, the controlled treatment can take into account the fact that the solidification rate has a direct effect on the extent and distribution of microsegregation, especially in the case of the steels mentioned herein. The solidification rate then affects the state of precipitation and particle growth of, for example, MnS, AlN, and Ti (C, N) that occur during solidification. Thus, as a result of controlling the target of the microstructure parameters of the cast raw material, it is possible to select basic settings which have a decisive influence on the capacity for further processing and the use properties of the final product.
[0008]
In the present invention, steel is cast in a double roller casting machine. Casting machines of this type are known per se and are, in particular, hot working with the solidification behavior of the raw materials (especially the solidification rate and uniformity of solidification) resulting in an optimal cast structure and the associated optimal deformability. It is possible to produce thin raw materials very close to the final dimensions of the strip.
[0009]
Surprisingly, it has been found that particularly good processing results can be achieved with only one pass when rolling a hot strip to its final thickness from a coarse strip. The immediate, continuous arrangement of the casting process and hot rolling (single pass) allows the heat of the casting process to be brought into the rolling process. As a result, the step of reheating before hot rolling, which is always required in normal slab casting, can be avoided. "Carrying in" the casting heat also prevents excessive crystal growth, and thus further supports the formation of a fine microstructure in the raw material.
[0010]
Because of the special effects of the solidification process on the properties of the final product, it is advantageous that further processing to form a hot strip of raw material includes controlled cooling performed immediately after casting. This allows the raw material coming out of the mold to be cooled in a targeted manner, so as to obtain a microstructure that is optimized for further processing. Typically, cooling is at an accelerated rate compared to cooling by exposure to ambient air.
[0011]
Experiments have shown that, depending on the desired properties and composition of the final product, the average initial rolling temperature at which the raw materials enter the roll stand can be in the range of 1100C to 750C.
[0012]
When hot rolling raw materials, the properties of the hot rolled strip can be further affected by the targeted method of cooling the rolled hot strip in a controlled manner after hot rolling.
[0013]
In principle, it can be envisaged that the hot strip obtained according to the invention is further processed "in-line", for example to form a cold strip. However, in view of possible subsequent processing steps or the properties of the hot strip to be prepared, it will often be advantageous to coil said strip as part of further processing.
[0014]
It can be performed at least intermittently in a protective gas atmosphere to avoid oxidation of the strip surface and associated excessive scale formation as a result of further processing to form a hot strip of raw material. . In this connection, it is particularly preferred that the raw material is maintained in a protective gas atmosphere at least until the raw material is inserted into the roll stand.
[0015]
Apart from the further alloying elements, the steels used according to the invention can contain up to 3.5% by weight of silicon, in particular up to 3% by weight. Furthermore, the steel may contain up to 3.5% by weight of aluminum, especially up to 3% by weight. In steels of the type treated according to the invention, iron and aluminum or iron and silicon form at lower temperatures than the hot forming temperature and form an alloy phase that is stable to room temperature.
[0016]
Hereinafter, the present invention will be described in more detail with reference to one embodiment.
The drawings are schematic side views of a design of an apparatus for manufacturing a hot strip;
The graph shows the temperature course during the processing time of the coarse and hot strips in the apparatus of FIG. 1;
Photo 1 shows an enlarged cross section of an end of a hot strip manufactured by the apparatus of FIG. 1; and Photo 2 shows an enlarged cross section of a central portion of a hot strip manufactured by the apparatus of FIG.
[0017]
The figure schematically shows the design of an apparatus 1 for producing a hot strip W, said apparatus comprising a casting device 2, a first cooling section 3, a roll stand 4, a second cooling section 5, and It includes a coiling device 6.
[0018]
In a double-roller casting machine designed according to a known principle, the melt S contained in the tundish 7 (the melt composition of which will be described in detail later) is removed by a casting gap formed between two casting rollers 8 and 9. Pour into 10 to form coarse strip V. The coarse cast strip V exits the casting gap 10 by a continuous transport process, with a thickness that can vary in a range less than 1 mm to 6 mm.
[0019]
The coarse strip V is applied to the surface of the coarse strip V on the way to the roll stand 4 in the first cooling section 3 downstream of the exit of the casting gap 10 and arranged in close proximity to the casting gap 10. The cooling medium is cooled in a controlled manner.
[0020]
The conveyor section (along which the thin strip V passes between the exit of the casting gap 10 and the roll stand 4) is surrounded by a doghouse 11 in which a protective gas atmosphere is maintained. In this way, contact between the surface of the strip and the surrounding air is avoided.
[0021]
The thin strip V enters the roll stand 4 at the initial rolling temperature AT and is rolled in said roll stand to a final thickness in one pass.
Immediately thereafter, the hot strip W leaving the roll stand 4 at the final rolling temperature ET passes through the second cooling section 5. In this cooling section 5, the hot strip W is coiled in a coiling device 6 to form a coil C after being re-directed to the coiling temperature HT by a suitable cooling medium in a controlled manner.
[0022]
The accompanying graph shows the initial rolling temperature AT, the final rolling temperature ET, and the coiling temperature HT during the processing time after casting to strip width (this depends on the composition and the desired properties of the hot strip to be produced). And can be set in a device designed according to FIG. 1). With appropriate temperature control management along specific limiting curves with subsequent isothermal holding, rolling, and quenching, the hot strip is removed from the roll stand so that good application properties of the hot strip remain after hot rolling. After exiting, the fine-grained microstructure of the hot strip can be einfrieren. This effect can be achieved, inter alia, if the temperature course of the coarse strip and of the hot strip is close to the lower curve shown in the graph.
[0023]
Except for usual unavoidable impurities, the melt S poured in the above embodiment is Mn (content 20% by weight), C (content 0.003% by weight), sulfur (content 0.007% by weight) , Si (content 3.0% by weight), Al (content 3.0% by weight), and iron (the balance).
[0024]
Photo 1 shows an enlarged cross section of the end, while Photo 2 shows a 1: 1 enlarged cross section of the center of steel made from a hot strip made by the apparatus shown in FIG. I have. It is clear that this strip contains a dendrite microstructure comprising austenite and a second phase, which is probably a carbonaceous phase. This microstructure becomes significantly finer with respect to the core of the strip.
[Brief description of the drawings]
FIG.
FIG. 2 is a schematic side view illustrating a design of an apparatus for manufacturing a hot strip.
FIG. 2
2 is a graph showing the temperature profile during the processing time of the coarse strip and the hot strip in the apparatus of FIG. 1.
FIG. 3
Photo 1 shows an enlarged cross section of an end of a hot strip manufactured by the apparatus of FIG. 1, and Photo 2 shows an enlarged cross section of a central portion of a hot strip manufactured by the apparatus of FIG.
[Explanation of symbols]
1 ... device;
2 ... double roller casting machine;
3 ... first cooling section;
4 ... roller stand;
5 ... second cooling section;
6 ... coiling device;
7 ... tundish;
8, 9 ... casting roller;
10: casting gap;
11 ... dog house;
AT: initial rolling temperature;
C: coil;
ET: Final rolling temperature;
S: melt;
V: thin strip;
W: Hot strip.

Claims (11)

マンガンを１２重量％より多く３０重量％以下の量で含有する鋼からＴＷＩＰ及びＴＲＩＰ特性を有する熱間ストリップ（Ｗ）を製造する方法であって、メルト（Ｓ）をダブルローラーキャスティングマシン（２）において最終寸法に近い寸法にキャスティングして粗ストリップ（Ｖ）を形成し、ここで前記粗ストリップ（Ｖ）の厚さは６ｍｍ以下であり、そしてキャスティングの後に前記粗ストリップ（Ｖ）をシングル熱間圧延パスにおいて熱間ストリップ（Ｗ）の最終厚さまで圧延することにより連続的に更に処理して、熱間ストリップ（Ｗ）を形成する、前記製造方法。A method for producing a hot strip (W) having TWIP and TRIP properties from a steel containing manganese in an amount of more than 12% by weight and not more than 30% by weight, wherein a melt (S) is cast on a double roller casting machine (2). Casting to a size close to the final dimension to form a coarse strip (V), wherein the thickness of the coarse strip (V) is less than or equal to 6 mm, and after casting, the coarse strip (V) is subjected to a single hot strip. The above method wherein the hot strip (W) is continuously processed by rolling to a final thickness of the hot strip (W) in a rolling pass to form the hot strip (W). 前記粗ストリップの厚さが４ｍｍ以下、特には２．５ｍｍ以下であることを特徴とする、請求項１に記載の方法。2. The method according to claim 1, wherein the thickness of the coarse strip is less than 4 mm, in particular less than 2.5 mm. 前記熱間ストリップを形成するための粗ストリップの更なる処理が、キャスティングの直後に実施する制御された冷却を含むことを特徴とする、請求項１又は２に記載の方法。The method according to claim 1 or 2, wherein the further processing of the coarse strip to form the hot strip comprises controlled cooling performed immediately after casting. 前記冷却を、周囲空気への暴露による冷却よりも速い速度で行うことを特徴とする、請求項３に記載の方法。4. The method of claim 3, wherein the cooling is performed at a faster rate than cooling by exposure to ambient air. 前記粗ストリップがロールスタンド（４）に挿入される際の平均初期圧延温度（ＡＴ）が、１１００℃〜７５０℃の範囲にあることを特徴とする、請求項１〜４のいずれか一項に記載の方法。The average initial rolling temperature (AT) when the coarse strip is inserted into the roll stand (4) is in the range of 1100C to 750C, according to any one of the preceding claims. The described method. 熱間圧延の後に、圧延された前記熱間ストリップ（Ｗ）を、制御された方法で冷却することを特徴とする、請求項１〜５のいずれか一項に記載の方法。6. The method according to claim 1, wherein after hot rolling, the rolled hot strip (W) is cooled in a controlled manner. 更なる処理の最後で、前記熱間ストリップ（Ｗ）をコイリングしてコイル（Ｃ）を形成することを特徴とする、請求項１〜６のいずれか一項に記載の方法。7. The method according to claim 1, wherein at the end of further processing, the hot strip (W) is coiled to form a coil (C). 熱間ストリップ（Ｗ）を形成するための粗ストリップの更なる処理を、保護ガス雰囲気中で、少なくとも断続的に実施することを特徴とする、請求項１〜７のいずれか一項に記載の方法。8. The method according to claim 1, wherein the further processing of the crude strip to form a hot strip is performed at least intermittently in a protective gas atmosphere. 9. Method. 少なくともロールスタンド（４）に挿入されるまで、前記粗ストリップ（Ｖ）を保護ガス雰囲気中に維持することを特徴とする、請求項８に記載の方法。Method according to claim 8, characterized in that the crude strip (V) is maintained in a protective gas atmosphere at least until it is inserted into a roll stand (4). 前記鋼が、ケイ素３．５重量％以下、特には３重量％以下を含むことを特徴とする、請求項１〜９のいずれか一項に記載の方法。The method according to claim 1, wherein the steel comprises at most 3.5% by weight of silicon, in particular at most 3% by weight. 前記鋼が、アルミニウム３．５重量％以下、特には３重量％以下を含むことを特徴とする、請求項１〜１０のいずれか一項に記載の方法。Method according to any of the preceding claims, characterized in that the steel comprises not more than 3.5% by weight of aluminum, especially not more than 3% by weight.
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