JP4227010B2 - High strength steel for cold forming and steel strip or steel plate, method for manufacturing steel strip and method for manufacturing steel - Google Patents
High strength steel for cold forming and steel strip or steel plate, method for manufacturing steel strip and method for manufacturing steel Download PDFInfo
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- JP4227010B2 JP4227010B2 JP2003503854A JP2003503854A JP4227010B2 JP 4227010 B2 JP4227010 B2 JP 4227010B2 JP 2003503854 A JP2003503854 A JP 2003503854A JP 2003503854 A JP2003503854 A JP 2003503854A JP 4227010 B2 JP4227010 B2 JP 4227010B2
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
-
- 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
-
- 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
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
Abstract
Description
【０００１】
本発明は、冷間成形性に優れた高強度Ｆｅ−Ｍｎ−Ａｌ−Ｓｉ系軽量鋼および鋼帯（ストリップ）もしくは鋼板（シート）に関する。更に、本発明は、上記鋼から鋼帯を製造する方法および上記鋼の特に適した使用に関する。
【０００２】
車両ボディー部品製造用や低温用途に用いる軽量鋼がドイツ特許１９７２７７５９Ｃ２により知られている。この鋼は、Ｆｅの他に、１０％〜３０％のＭｎ、１％〜８％のＡｌ、および１％〜６％のＳｉを含有し、ＡｌとＳｉの合計含有量が１２％以下である。この公知鋼は、炭素含有量が、もし存在したとしても、不純物の範囲内である。
【０００３】
これに対して、ドイツ特許出願１９９００１９９Ａ１により知られる軽量構造用鋼では、炭素が任意成分として含有されている。この軽量鋼は、７％を超え２７％以下のＭｎ、１％を越え１０％以下のＡｌ、０．７％を超え４％以下のＳｉ、０．５％未満のＣ、１０％未満のＣｒ、１０％未満のＮｉ、および０．３％未満のＣｕを含有する。更に、この鋼は、Ｎ、Ｖ、Ｎｂ、ＴｉおよびＰを合計含有量２％以下含有し得る。
【０００４】
ヨーロッパ特許出願１０６７２０３Ａ１から知られる軽量鋼も０．００１〜１．６％の範囲の炭素を含有している。更に、この鋼は、Ｆｅ以外に、６〜３０％のＭｎ、６％以下のＡｌ、２．５％以下のＳｉ、１０％以下のＣｒ、１０％以下のＮｉ、および５％以下のＣｕを含有する。更に、この鋼は、Ｖ、Ｔｉ、Ｎｂ、Ｂ、Ｚｒおよび希土類元素を合計含有量３％以下含有し得る。この鋼は更に、Ｐ、Ｓｎ、ＳｂおよびＡｓを合計含有量０．２％以下含有し得る。
【０００５】
上記のような組成タイプの鋼は、炭素を含有しているにも関わらず、熱間圧延および冷間圧延ともに困難である。ストリップのエッジに不安定部分や亀裂が発生し易いため、鋼帯や鋼板の大量生産が困難である。更に、変形挙動の等方性が高く、Δｒ値が大きい。公知方法で製造した鋼板は成形性が低いため、更に成形を加えることが困難である。
【０００６】
歯あるいはそれに相当する形状を有する部材の製造には、強度が高くて成形性の良好な鋼も必要である。典型例としては、内歯あるいは外歯を備えた歯車部品がある。その製造は、コスト効率が良く寸法精度の高いフローフォーミングにより行なうことができる。
【０００７】
フローフォーミングにより歯車部品を製造する方法が、ドイツ特許１９７２４６６１Ｃ２により知られている。この方法によると、高強度構造用マイクロアロイ鋼から成り、下部降伏点が５００Ｎ／ｍｍ２以上である素形材を鋼板から製造する。そしてこの素形材をフローフォーミングして歯車に成形する。歯の成形の際に、鋼板はその成形能の限界まで再成形を受ける。その結果、歯を備えた被加工材の表面は温度を維持しつつ熱変形を伴わずに強化される。
【０００８】
本発明の目的は、上記従来技術を改良して、成形性に優れ強度が高く、また工業規模での製造が容易な軽量鋼および／またはそれから製造された鋼帯もしくは鋼を提供することである。更に、鋼帯もしくは鋼板の製造方法および鋼の望ましい使用についても示す。
【０００９】
この目的は、下記の組成（質量％）：
Ｃ：１．００％以下、
Ｍｎ：７．００〜３０．００％、
Ａｌ：１．００〜１０．００％、
Ｓｉ：２．５０％を超え８．００％以下、
Ａｌ＋Ｓｉ：３．５０％を超え１２．００％以下、
Ｂ：０．００％を超え、０．０１％未満、
および任意成分として、
Ｎｉ：８．００％未満、
Ｃｕ：３．００％未満、
Ｎ：０．６０％未満、
Ｎｂ：０．３０％未満、
Ｔｉ：０．３０％未満、
Ｖ：０．３０％未満、
Ｐ：０．０１％未満、
を有する軽量鋼によって達成される。
【００１０】
残部は、Ｆｅおよび不可避不純物である。この不純物としては、この場合は、硫黄と酸素がある。
【００１１】
特に、ボロンの添加により、本発明鋼は性質も製造性も著しく向上することが分かった。すなわち、本発明鋼中のボロン含有量は、降伏点を低下させ、それにより成形性を著しく高めるものである。本発明鋼においては、炭素含有量が０．１０〜１．００質量％、すなわち０．１０質量％以上の炭素が検出される状態であれば、本発明鋼の機械的性質および製造性に対する合金成分の作用効果は更に強化される。
【００１２】
この場合、合金成分の存在によって、機械的性質と製造性との組合せが特に良好になる。すなわち、本発明鋼および／または本発明鋼から製造した鋼帯もしくは鋼板は、上記従来の鋼に比べて、Δｒ値が著しく低い。
【００１３】
更に、本発明の組成を有する冷間圧延鋼帯および鋼の特徴は、降伏点が低下し、高い加工硬化指数（ｎ値）でのストレッチ成形性が向上し、深絞り性（ｒ値）が向上し、かつ面内異方性（Δｒ値）が低下していると同時に、降伏点と伸びとの積が大きくなっている。すなわち、本発明の鋼帯および鋼板の引張強さは６８０ＭＰａ以上である。引張強さと伸びとの積は４１，０００ＭＰａ以上である。本発明の鋼板および鋼帯の降伏点は５２０ＭＰａ以下である。同時に、本発明鋼および／または本発明鋼から製造した鋼板および鋼帯は、２０％から４５％を超える非常に大きな均一伸びを備えている。０．７に達するｎ値が得られる。
【００１４】
このように、高強度・低比重により自動車ボディー用部材の製造に特に適した冷間成形性の高い軽量鋼帯および鋼板が得られる。本発明により製造された鋼板は、重量に対する強度の比率が著しく高いので、下記の用途に適している。すなわち、車両特に動力車両用の車輪の製造、内部または外部からハイドロフォームされた部材の製造、カムシャフトやピストンロッドのような高強度エンジン部品の製造、爆撃のようなパルス状応力に対する保護を目的とした装甲板のような部材の製造、および、爆撃に対する人の保護を目的とした保護部材、といった用途に適している。特に、最後の用途では、本発明鋼が軽量であり同時に高強度であることが非常に有効である。
【００１５】
なお、本発明の鋼板はミクロ組織が完全にオーステナイトだけから成る場合には非磁性部材の製造にも適している。
【００１６】
更に、本発明鋼は極低温においても強度を維持する。そのため、低温技術用のコンテナーやパイプのような低温技術用部材の製造に特に適している。
【００１７】
本発明鋼におけるボロンの有用な効果は、ボロン含有量が０．００２質量％〜０．０１質量％、特に０．００３質量％〜０．００８質量％である場合に、特に顕著である。
【００１８】
Ｃ含有量は、０．１質量％〜１．０質量％であって、本発明の鋼板および鋼帯の製造性をも向上させる。本発明鋼は、炭素が存在することにより、金属間化合物相の生成が抑制される。従来鋼から製造されたストリップで発生するエッジ領域での亀裂や不安定性がこれにより大幅に低減され、特に炭素含有量の増加に伴って不安定性が低減される。ストリップエッジ品質は、ボロン添加により更に向上する。その結果、ストリップエッジの不安定性はＣとＢとの複合添加によりほぼ完全に防止される。
【００１９】
機械的性質および製造性に対する効果という面で、ボロンは合金元素であるＭｎの代替物として作用する。すなわち、２０％Ｍｎと０．００３％ボロンを含有する鋼は、２５％Ｍｎでボロンを含有しない鋼と同等の特性を有することが分かった。本発明の軽量構造用鋼はＭｎ含有量を低くしても高強度を維持することができる。これにより、合金元素コストが低減されると共に、本発明鋼の精錬制御が容易になる。
【００２０】
また、本発明のＣ含有量およびＢ含有量により、熱間圧延条件の選択の幅が広くなる。すなわち、本発明鋼は、熱間圧延最終温度および巻き取り温度が高いときに得られる特性と、熱間圧延最終温度および巻き取り温度が低いときに得られる特性とが、ほぼ同等である。このように熱間圧延条件に対して鈍感であるため、本発明の鋼板の製造も容易になる。
【００２１】
Ｓｉ含有量は２．５０質量％を超える、望ましくは２．７０質量％を超える、と規定したことにより、本発明の鋼帯および鋼板はＳｉ含有量の低い軽量鋼帯および鋼板に比べて冷間成形性が向上している。Ｓｉ含有量が高いことは、均一伸びでの降伏点および引張強度に現われており、破断伸びおよび均一伸びが大きくなっている。また、Ｓｉは本発明鋼のｒ値およびｎ値を高め、機械的性質の等方性を実現している。ＡｌとＳｉの合計含有量は、脆化の危険性を避けるために、１２％以下とする。
【００２２】
本発明の鋼帯および鋼板は望ましくは下記の方法により製造される。すなわち、上記組成を持つ本発明鋼から作られたスラブ、薄スラブまたはストリップのような出発材料を鋳造し、鋳造された出発材料を１１００℃に加熱するか又はこの温度で直接用い、上記予備加熱した出発材料を熱間圧延最終温度８００℃以上で熱間圧延して熱間圧延ストリップ（ホットストリップ）とし、仕上げ圧延されたホットストリップを巻き取り温度４５０℃〜７００℃で巻き取る。
【００２３】
本発明においては、ホットストリップを熱間圧延最終温度８００℃以上で熱間圧延し、低温で巻き取ることにより、炭素の有用な効果が、またボロンを用いた場合にはその有用な効果が、十分に活用される。すなわち、本発明の範囲内で熱間圧延したストリップの引張強さおよび降伏点はボロンおよび炭素の存在により高まり、同時に許容範囲内の破断伸びが確保される。熱間圧延最終温度が高くなるに伴い、引張強さおよび降伏点は低下し、一方、伸び値は増加する。本発明の規定範囲内で熱間圧延最終温度を変えることにより、鋼帯の所望特性を容易に制御できる。
【００２４】
巻き取り温度を７００℃以下に限定することにより、材料の脆化を安定して回避できる。巻き取り温度がこれより高いと脆性相が生成して、材料の剥離が発生し、その後の処理が困難または不可能になる場合があることが、これまでに分かっている。
【００２５】
本発明により製造したホットストリップは使用特性も優れている。薄い鋼板もしくは鋼帯を製造するには、巻き取り後にホットストリップを冷間圧延して冷間圧延ストリップとする。この冷間圧延は圧下率３０％〜７５％で行なうことが望ましい。
【００２６】
得られた冷間圧延ストリップは、６００℃〜１１０℃の焼鈍温度で焼鈍を施すことが望ましい。この焼鈍は、６００℃〜７５０℃の温度範囲でフード焼鈍により行なうか、７５０℃〜１１００℃の温度で焼鈍炉で連続焼鈍により行なうことができる。最後に、冷間成形性の観点からは、冷間圧延ストリップをドレッシングすることが望ましい。本発明の鋼および／または鋼帯もしくは鋼板の更に有利な特定の用途としては、フローフォーミングによる冷間成形部材の製造がある。その場合、本発明鋼から素形材を製造し、これをフローフォーミングにより仕上げる。本発明鋼および／または本発明鋼から製造した素形材は、その特性上、この用途に特に適している。
【００２７】
本発明鋼は、その組成に応じて、ミクロ組織が完全オーステナイト組織またはフェライト＋オーステナイトにマルテンサイトを含む混合組織になる。そのため本発明鋼は成形性が非常に高い。フローフォーミングによる製造に用いられていた従来公知の高強度マイクロアロイ鋼または高強度多相鋼に比べて、本発明鋼は冷間成形時により強力に緻密化する。そのため、冷間成形条件に応じて１４００Ｎ／ｍｍ２〜２２００Ｎ／ｍｍ２の部材強度が得られる。そのため、冷間成形後の付加的硬化は省略できる。歯付き歯車部材の製造のような特定の用途については、本発明鋼においてＳｉ、Ａｌのような軽量成分の含有量を多くすることにより比重を低下させることも望ましい。
【００２８】
本発明鋼を用いた場合、フローフォーミングした部材の熱処理または表面硬化処理を省略できる。使用時に局所的な大応力が負荷される歯付き部材を本発明鋼を用いて製造すれば、上記処理を行なっていた従来鋼で発生していた歪みや剥がれが発生することがない。このように、本発明鋼を用いることにより、軽量で過酷の使用条件向け、かつ寸法安定性の高い部材を、冷間成形特にフローフォーミングにより低コストで製造することができる。
【００２９】
以下に、本発明を実施例と比較例により更に詳細に説明する。
【００３０】
表１に示した鋼Ａ、Ｂ、Ｃ、Ｄ、Ｅのうち、鋼Ａ、Ｂ、Ｃは本発明の実施例であり、鋼Ｄ、Ｅは比較例である。
【００３１】
【表１】
上記組成の鋼Ａ〜Ｅを溶解し、スラブに鋳造した。次いで、スラブを１１５０℃に加熱した。加熱したスラブを熱間圧延し、次いで冷間圧延した。
【００３３】
表２に、上記で得られた各ホットストリップについて、熱間圧延最終温度：ＥＴ、巻き取り温度：ＨＴ、引張強さ：Ｒｍ、降伏点：Ｒｅ、Ａ５０伸び、均一伸びＡｇｌ、ｎ値を示す。
【００３４】
【表２】
比較例である鋼Ｄから製造したストリップは、冷間圧延が不可能であった。これ以外のストリップは、変形度約６５％で冷間圧延した後、９５０℃で連続焼鈍した。得られた各冷間圧延鋼板の機械的性質を表３に示す。
【００３６】
【表３】
鋼Ａ〜Ｃから製造した本発明の鋼帯は優れた冷間成形性を有することが分かった。そして、高強度および高破断伸びを備えていると共に、等方的な変形挙動を発揮した（ｒ≒１、Δｒ≒０）。鋼Ｃは本発明鋼ではあるが炭素を含有させずにボロンを含有させたものであるが、この鋼Ｃから製造したストリップでも、降伏点が低下すると共に、破断伸びおよび均一伸びが大きく、かつ変形挙動が等方的であった。
【００３８】
このように、本発明による全ての形態の鋼板は、車両ボディー部材、自動車ボディーの外装パネル、車両特に動力車両の車輪、内部または外部からハイドロフォームした部材、カムシャフトやピストンロッドのような高強度エンジン部品製造用の管、爆撃のようなパルス応力に対する保護を目的とする部材、装甲板のような保護部材、人や動物の装甲着などの製造に特に適している。また、本発明の鋼板からは、軽量で優れた使用特性を持つ過酷用途向け歯車部品を、付加的な熱処理を必要とせずに製造することができる。[0001]
The present invention relates to a high-strength Fe-Mn-Al-Si light steel and a steel strip (strip) or a steel plate (sheet) excellent in cold formability. Furthermore, the invention relates to a method for producing a steel strip from the steel and a particularly suitable use of the steel.
[0002]
A lightweight steel for use in the manufacture of vehicle body parts and for low temperature applications is known from German Patent 197277759C2. In addition to Fe, this steel contains 10% to 30% Mn, 1% to 8% Al, and 1% to 6% Si, and the total content of Al and Si is 12% or less. . This known steel has a carbon content within the range of impurities, if any.
[0003]
On the other hand, carbon is contained as an optional component in the lightweight structural steel known from German patent application 199100199A1. This lightweight steel has more than 7% and less than 27% Mn, more than 1% and less than 10% Al, more than 0.7% and less than 4% Si, less than 0.5% C, less than 10% Cr Contains less than 10% Ni and less than 0.3% Cu. Furthermore, this steel can contain N, V, Nb, Ti and P in a total content of 2% or less.
[0004]
The lightweight steel known from European patent application 10672203 A1 also contains carbon in the range of 0.001 to 1.6%. In addition to Fe, this steel contains 6-30% Mn, 6% or less Al, 2.5% or less Si, 10% or less Cr, 10% or less Ni, and 5% or less Cu. contains. Furthermore, this steel may contain V, Ti, Nb, B, Zr and rare earth elements in a total content of 3% or less. This steel may further contain P, Sn, Sb and As in a total content of 0.2% or less.
[0005]
Although the steel of the composition type as described above contains carbon, it is difficult to perform both hot rolling and cold rolling. Since unstable portions and cracks are likely to occur at the edge of the strip, mass production of steel strips and steel plates is difficult. Furthermore, the deformation behavior is highly isotropic and the Δr value is large. Steel sheets produced by a known method have low formability, so it is difficult to further form the steel sheet.
[0006]
For manufacturing a tooth or a member having a shape corresponding to it, steel having high strength and good formability is also required. A typical example is a gear component having internal teeth or external teeth. Its manufacture can be performed by flow forming with high cost efficiency and high dimensional accuracy.
[0007]
A method for producing gear parts by flow forming is known from German Patent 19724661C2. According to this method, a shaped material made of high-strength structural microalloy steel and having a lower yield point of 500 N / mm 2 or more is produced from a steel plate. Then, this raw material is flow-formed and formed into a gear. During tooth forming, the steel sheet undergoes re-forming to the limit of its forming ability. As a result, the surface of the workpiece with teeth is strengthened without thermal deformation while maintaining the temperature.
[0008]
An object of the present invention is to provide a lightweight steel and / or a steel strip or steel produced therefrom that is improved in the above prior art and has excellent formability and high strength and is easy to produce on an industrial scale. . In addition, the method of manufacturing the steel strip or steel plate and the preferred use of the steel are also presented.
[0009]
The purpose of this is as follows (mass%):
C: 1.00% or less,
Mn: 7.00 to 30.00%,
Al: 1.00 to 10.00%,
Si: more than 2.50% and 8.00% or less,
Al + Si: more than 3.50% and 12.00% or less,
B: more than 0.00%, less than 0.01%,
And as an optional ingredient
Ni: less than 8.00%,
Cu: less than 3.00%,
N: less than 0.60%,
Nb: less than 0.30%,
Ti: less than 0.30%,
V: less than 0.30%,
P: less than 0.01%,
Achieved by lightweight steel with.
[0010]
The balance is Fe and inevitable impurities. In this case, the impurities include sulfur and oxygen.
[0011]
In particular, it has been found that the addition of boron significantly improves the properties and manufacturability of the steel of the present invention. That is, the boron content in the steel of the present invention lowers the yield point, thereby significantly improving the formability. In the steel of the present invention, an alloy for the mechanical properties and manufacturability of the steel of the present invention as long as the carbon content is 0.10 to 1.00% by mass, that is, 0.10% by mass or more of carbon The effect of the component is further strengthened.
[0012]
In this case, the combination of mechanical properties and manufacturability is particularly good due to the presence of the alloy components. That is, the steel of the present invention and / or the steel strip or steel plate manufactured from the steel of the present invention has a significantly lower Δr value than the conventional steel.
[0013]
Furthermore, the features of the cold rolled steel strip and steel having the composition of the present invention are that the yield point is lowered, the stretch formability at a high work hardening index (n value) is improved, and the deep drawability (r value) is At the same time, the in-plane anisotropy (Δr value) decreases and the product of the yield point and the elongation increases. That is, the tensile strength of the steel strip and steel plate of the present invention is 680 MPa or more. The product of tensile strength and elongation is 41,000 MPa or more. The yield point of the steel plate and steel strip of the present invention is 520 MPa or less. At the same time, the steels according to the invention and / or steel plates and steel strips made from the steels according to the invention have a very large uniform elongation, exceeding 20% to 45%. An n value reaching 0.7 is obtained.
[0014]
In this way, a lightweight steel strip and a steel plate with high cold formability, which are particularly suitable for the manufacture of automobile body members, can be obtained with high strength and low specific gravity. The steel sheet produced according to the present invention has a remarkably high strength to weight ratio and is suitable for the following applications. In other words, the production of wheels for vehicles, particularly powered vehicles, the production of internally or externally hydroformed parts, the production of high-strength engine parts such as camshafts and piston rods, and the protection against pulsed stresses such as bombing It is suitable for use in the manufacture of members such as armor plates and protective members for the purpose of protecting people against bombing. In particular, in the last application, it is very effective that the steel of the present invention is lightweight and at the same time has high strength.
[0015]
The steel sheet of the present invention is also suitable for the production of nonmagnetic members when the microstructure is entirely composed of austenite.
[0016]
Furthermore, the steel of the present invention maintains strength even at extremely low temperatures. Therefore, it is particularly suitable for the production of low-temperature technology members such as containers and pipes for low-temperature technology.
[0017]
The useful effect of boron in the steel of the present invention is particularly remarkable when the boron content is 0.002% by mass to 0.01% by mass, particularly 0.003% by mass to 0.008% by mass.
[0018]
C content is 0.1 mass%-1.0 mass%, Comprising: The productivity of the steel plate and steel strip of this invention is also improved. In the steel of the present invention, the presence of carbon suppresses the formation of an intermetallic compound phase. This greatly reduces the cracks and instabilities in the edge regions that occur in strips made from conventional steel, especially with increasing carbon content. Strip edge quality is further improved by boron addition. As a result, strip edge instability is almost completely prevented by the combined addition of C and B.
[0019]
Boron acts as a substitute for the alloying element Mn in terms of its effects on mechanical properties and manufacturability. That is, it was found that steel containing 20% Mn and 0.003% boron has the same characteristics as steel containing 25% Mn and no boron. The lightweight structural steel of the present invention can maintain high strength even if the Mn content is lowered. This reduces the alloy element cost and facilitates refining control of the steel of the present invention.
[0020]
Moreover, the breadth of selection of hot rolling conditions becomes wide with C content and B content of this invention. That is, in the steel of the present invention, the characteristics obtained when the hot rolling final temperature and the coiling temperature are high are substantially the same as the characteristics obtained when the hot rolling final temperature and the coiling temperature are low. Thus, since it is insensitive with respect to hot rolling conditions, manufacture of the steel plate of the present invention becomes easy.
[0021]
By stipulating that the Si content exceeds 2.50% by mass, and desirably exceeds 2.70% by mass, the steel strip and steel sheet of the present invention are cooler than the lightweight steel strip and steel sheet having a low Si content. Interformability is improved. A high Si content appears in the yield point and tensile strength at uniform elongation, and the elongation at break and uniform elongation are large. Further, Si increases the r value and n value of the steel of the present invention, and realizes isotropy of mechanical properties. The total content of Al and Si is 12% or less in order to avoid the risk of embrittlement.
[0022]
The steel strip and steel plate of the present invention are desirably produced by the following method. That is, a starting material such as a slab, thin slab or strip made from the steel of the present invention having the above composition is cast, and the cast starting material is heated to 1100 ° C. or directly used at this temperature, and the preheating is performed. The obtained starting material is hot-rolled at a final hot rolling temperature of 800 ° C. or more to form a hot-rolled strip (hot strip), and the hot-rolled finish strip is wound at a winding temperature of 450 ° C. to 700 ° C.
[0023]
In the present invention, the hot strip is hot-rolled at a final temperature of 800 ° C. or higher, and wound at a low temperature, so that the useful effect of carbon is obtained, and when boron is used, the useful effect is Fully utilized. In other words, the tensile strength and yield point of the strip hot-rolled within the scope of the present invention are increased by the presence of boron and carbon, and at the same time, the elongation at break within the allowable range is ensured. As the hot rolling final temperature increases, the tensile strength and yield point decrease while the elongation value increases. By changing the hot rolling final temperature within the specified range of the present invention, the desired properties of the steel strip can be easily controlled.
[0024]
By limiting the winding temperature to 700 ° C. or lower, embrittlement of the material can be stably avoided. It has been previously found that at higher coiling temperatures, a brittle phase can form and material delamination can occur, making subsequent processing difficult or impossible.
[0025]
The hot strip produced according to the present invention has excellent service characteristics. To manufacture a thin steel plate or strip, the hot strip is cold rolled after winding to form a cold rolled strip. This cold rolling is desirably performed at a rolling reduction of 30% to 75%.
[0026]
The resulting cold-rolled strip is preferably annealed at an annealing temperature of 600 ° C to 110 ° C. This annealing can be performed by hood annealing at a temperature range of 600 ° C. to 750 ° C. or by continuous annealing in an annealing furnace at a temperature of 750 ° C. to 1100 ° C. Finally, it is desirable to dress the cold rolled strip from the standpoint of cold formability. A further advantageous specific application of the steel and / or steel strip or steel sheet according to the invention is the production of cold-formed parts by flow forming. In that case, a raw material is produced from the steel of the present invention, and this is finished by flow forming. The steel according to the present invention and / or the shape material produced from the steel according to the present invention is particularly suitable for this application because of its properties.
[0027]
According to the composition of the steel of the present invention, the microstructure becomes a complete austenite structure or a mixed structure containing martensite in ferrite + austenite. Therefore, the steel of the present invention has very high formability. Compared to the conventionally known high-strength microalloy steel or high-strength multiphase steel used for the production by flow forming, the steel of the present invention becomes more dense during cold forming. Therefore, members strength of 1400N / mm 2 ~2200N / mm 2 is obtained in accordance with the cold forming conditions. Therefore, additional curing after cold forming can be omitted. For specific applications such as the manufacture of toothed gear members, it is also desirable to reduce the specific gravity by increasing the content of lightweight components such as Si and Al in the steel of the present invention.
[0028]
When the steel of the present invention is used, heat treatment or surface hardening treatment of the flow-formed member can be omitted. If a toothed member to which a large local stress is applied at the time of use is manufactured using the steel of the present invention, the distortion and peeling that have occurred in the conventional steel that has been subjected to the above-described treatment will not occur. As described above, by using the steel of the present invention, it is possible to manufacture a lightweight, harsh use condition member having high dimensional stability at a low cost by cold forming, particularly flow forming.
[0029]
Hereinafter, the present invention will be described in more detail with reference to examples and comparative examples.
[0030]
Among the steels A, B, C, D, and E shown in Table 1, steels A, B, and C are examples of the present invention, and steels D and E are comparative examples.
[0031]
[Table 1]
Steels A to E having the above composition were melted and cast into slabs. The slab was then heated to 1150 ° C. The heated slab was hot rolled and then cold rolled.
[0033]
In Table 2, for each hot strip obtained above, hot rolling final temperature: ET, coiling temperature: HT, tensile strength: Rm, yield point: Re, A 50 elongation, uniform elongation A gl , n value Indicates.
[0034]
[Table 2]
The strip manufactured from steel D, which is a comparative example, could not be cold rolled. The other strips were cold-rolled at a degree of deformation of about 65% and then continuously annealed at 950 ° C. Table 3 shows the mechanical properties of the obtained cold-rolled steel sheets.
[0036]
[Table 3]
It has been found that the steel strip of the present invention produced from steels A to C has excellent cold formability. And while having high strength and high elongation at break, it exhibited an isotropic deformation behavior (r≈1, Δr≈0). Steel C is a steel of the present invention, but it contains boron without containing carbon. However, even with a strip manufactured from steel C, the yield point is lowered, the elongation at break and the uniform elongation are large, and The deformation behavior was isotropic.
[0038]
Thus, all forms of steel sheets according to the present invention are high strength such as vehicle body members, exterior panels of automobile bodies, wheels of vehicles, particularly powered vehicles, members hydroformed from inside or outside, camshafts and piston rods. It is particularly suitable for the production of pipes for manufacturing engine parts, members for the purpose of protecting against pulse stress such as bombing, protective members such as armor plates, and armor for humans and animals. Moreover, from the steel plate of this invention, the gear component for severe uses with the lightweight and the outstanding usage characteristic can be manufactured, without requiring additional heat processing.
Claims (29)
Ｍｎ：７．００〜３０．００％
Ａｌ：１．００〜１０．００％
Ｓｉ：２．５０％を超え８．００％以下
Ａｌ＋Ｓｉ：３．５０％を超え１２．００％以下
Ｂ：０．００２〜０．０１％
ならびに、残部の鉄および不可避的不純物
からなる、冷間成形性に優れた高強度軽量鋼。The following composition (mass%):
Mn: 7.00 to 30.00%
Al: 1.00 to 10.00%
Si: more than 2.50% and less than 8.00% Al + Si: more than 3.50% and less than 12.00% B: 0.002-0.01%
And the balance of iron and inevitable impurities
Consisting of high-strength lightweight steel excellent in cold formability.
請求項１から４のうちの１項記載の組成を有する鋼を鋳造する工程、
得られた鋳造材料を１１００℃以上まで加熱するかまたは該温度で直接用いる工程、
上記予備加熱された出発材料を、熱間圧延最終温度を８００℃以上として熱間圧延し、熱間圧延ストリップにする工程、および
仕上げ圧延された熱間圧延ストリップを４５０℃〜７００℃の巻き取り温度で巻き取る工程
を含む、冷間成形用高強度鋼帯又は鋼板の製造方法。 As the following of Engineering:
A casting step of steel having a composition according to 1, wherein one of the 請 Motomeko 1 4,
Heating the obtained casting material to 1100 ° C. or higher or directly using it at the temperature;
Hot-rolling the pre-heated starting material to a hot rolling final temperature of 800 ° C. or more to form a hot-rolled strip, and winding the finished-rolled hot-rolled strip at 450 ° C. to 700 ° C. A method for producing a high-strength steel strip for cold forming or a steel plate, comprising a step of winding at a temperature.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE10128544A DE10128544C2 (en) | 2001-06-13 | 2001-06-13 | High-strength, cold-workable sheet steel, process for its production and use of such a sheet |
| PCT/EP2002/006480 WO2002101109A1 (en) | 2001-06-13 | 2002-06-13 | Highly stable, steel and steel strips or steel sheets cold-formed, method for the production of steel strips and uses of said steel |
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| Publication Number | Publication Date |
|---|---|
| JP2004521192A JP2004521192A (en) | 2004-07-15 |
| JP4227010B2 true JP4227010B2 (en) | 2009-02-18 |
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| JP2003503854A Expired - Fee Related JP4227010B2 (en) | 2001-06-13 | 2002-06-13 | High strength steel for cold forming and steel strip or steel plate, method for manufacturing steel strip and method for manufacturing steel |
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| Country | Link |
|---|---|
| US (1) | US20030145911A1 (en) |
| EP (1) | EP1309734B2 (en) |
| JP (1) | JP4227010B2 (en) |
| KR (1) | KR100536645B1 (en) |
| CN (1) | CN1215188C (en) |
| AT (1) | ATE370258T1 (en) |
| CA (1) | CA2414138C (en) |
| DE (2) | DE10128544C2 (en) |
| DK (1) | DK1309734T3 (en) |
| ES (1) | ES2292762T5 (en) |
| PT (1) | PT1309734E (en) |
| WO (1) | WO2002101109A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006509912A (en) * | 2002-12-17 | 2006-03-23 | ティッセンクルップ シュタール アクチェンゲゼルシャフト | Steel product manufacturing method |
Families Citing this family (69)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2857980B1 (en) | 2003-07-22 | 2006-01-13 | Usinor | PROCESS FOR MANUFACTURING HIGH-STRENGTH FERRO-CARBON-MANGANESE AUSTENITIC STEEL SHEET, EXCELLENT TENACITY AND COLD SHAPINGABILITY, AND SHEETS THUS PRODUCED |
| DE102004028236B3 (en) * | 2004-06-11 | 2005-11-17 | Rolf-Josef Schwartz | Assembly for heating workpieces before shaping in a press, e.g. high tensile steel sheets for automobile bodywork components, has a kiln with a jet field and fans to give the workpieces a convective heating action |
| DE102004054444B3 (en) * | 2004-08-10 | 2006-01-19 | Daimlerchrysler Ag | Method for making steel articles with high rigidity and plasticity comprises mechanical shaping of steel in which twinning induce plasticity or shearband induced plasticity is produced, to give increase in rigidity of at least 30 percent |
| US20090010793A1 (en) * | 2004-11-03 | 2009-01-08 | Thyssenkrupp Steel Ag | Method For Producing High Strength Steel Strips or Sheets With Twip Properties, Method For Producing a Component and High-Strength Steel Strip or Sheet |
| DE102005010243A1 (en) * | 2005-03-05 | 2006-09-07 | Sms Demag Ag | Method and plant for producing a lightweight steel with a high manganese content |
| DE102005057599A1 (en) * | 2005-12-02 | 2007-06-06 | Volkswagen Ag | lightweight steel |
| DE202005021771U1 (en) | 2005-12-20 | 2010-02-18 | Salzgitter Flachstahl Gmbh | Formable lightweight steel |
| KR100742833B1 (en) * | 2005-12-24 | 2007-07-25 | 주식회사 포스코 | High Mn Steel Sheet for High Corrosion Resistance and Method of Manufacturing Galvanizing the Steel Sheet |
| KR100742823B1 (en) * | 2005-12-26 | 2007-07-25 | 주식회사 포스코 | High Manganese Steel Strips with Excellent Coatability and Superior Surface Property, Coated Steel Strips Using Steel Strips and Method for Manufacturing the Steel Strips |
| DE102006030699B4 (en) * | 2006-06-30 | 2014-10-02 | Daimler Ag | Cast steel piston for internal combustion engines |
| ES2325964T3 (en) * | 2006-10-30 | 2009-09-25 | Thyssenkrupp Steel Ag | PROCEDURE FOR MANUFACTURING STEEL FLAT PRODUCTS FROM A MULTIPHASIC STEEL ALLOYED WITH SILICON. |
| ATE432374T1 (en) * | 2006-10-30 | 2009-06-15 | Thyssenkrupp Steel Ag | METHOD FOR PRODUCING FLAT STEEL PRODUCTS FROM A MULTIPHASE STEEL ALLOYED WITH ALUMINUM |
| ATE432376T1 (en) * | 2006-10-30 | 2009-06-15 | Thyssenkrupp Steel Ag | METHOD FOR PRODUCING FLAT STEEL PRODUCTS FROM A MULTIPHASE STEEL MICRO-ALLOYED WITH BORON |
| PL1918403T3 (en) * | 2006-10-30 | 2009-10-30 | Thyssenkrupp Steel Ag | Process for manufacturing steel flat products from a steel forming martensitic structure |
| EP1918402B1 (en) * | 2006-10-30 | 2009-05-27 | ThyssenKrupp Steel AG | Process for manufacturing steel flat products from a steel forming a complex phase structure |
| KR100851158B1 (en) * | 2006-12-27 | 2008-08-08 | 주식회사 포스코 | High Manganese High Strength Steel Sheets With Excellent Crashworthiness, And Method For Manufacturing Of It |
| US8444776B1 (en) * | 2007-08-01 | 2013-05-21 | Ati Properties, Inc. | High hardness, high toughness iron-base alloys and methods for making same |
| CN101809181B (en) | 2007-08-01 | 2013-11-13 | Ati资产公司 | H hardness, high toughness iron-base alloys and methods for making same |
| JP5487543B2 (en) * | 2008-01-25 | 2014-05-07 | Ｊｆｅスチール株式会社 | Oil well steel pipe with excellent pipe expansion |
| EP2090668A1 (en) * | 2008-01-30 | 2009-08-19 | Corus Staal BV | Method of producing a high strength steel and high strength steel produced thereby |
| EP2208803A1 (en) | 2009-01-06 | 2010-07-21 | ThyssenKrupp Steel Europe AG | High-tensile, cold formable steel, steel flat product, method for producing a steel flat product and use of a steel flat product |
| WO2010126268A2 (en) * | 2009-04-28 | 2010-11-04 | 연세대학교 산학협력단 | High manganese nitrogen-containing steel sheet having high strength and high ductility, and method for manufacturing same |
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| ATE554190T1 (en) * | 2009-08-25 | 2012-05-15 | Thyssenkrupp Steel Europe Ag | METHOD FOR PRODUCING A STEEL COMPONENT AND STEEL COMPONENT PROVIDED WITH A METALLIC COATING TO PROTECT AGAINST CORROSION |
| CA2785318C (en) * | 2009-12-28 | 2014-06-10 | Posco | Austenite steel material having superior ductility |
| DE102010034161B4 (en) * | 2010-03-16 | 2014-01-02 | Salzgitter Flachstahl Gmbh | Method for producing workpieces made of lightweight steel with material properties that can be adjusted via the wall thickness |
| JP5003785B2 (en) | 2010-03-30 | 2012-08-15 | Ｊｆｅスチール株式会社 | High tensile steel plate with excellent ductility and method for producing the same |
| KR20120026249A (en) * | 2010-09-09 | 2012-03-19 | 연세대학교 산학협력단 | Steel having high strength and large ductility and method for manufacturing the same |
| US9182196B2 (en) | 2011-01-07 | 2015-11-10 | Ati Properties, Inc. | Dual hardness steel article |
| US9657363B2 (en) | 2011-06-15 | 2017-05-23 | Ati Properties Llc | Air hardenable shock-resistant steel alloys, methods of making the alloys, and articles including the alloys |
| KR101329925B1 (en) | 2011-08-26 | 2013-11-14 | 주식회사 포스코 | High manganese steel having good adhesiveness of coating layer and method for manufacturing galvanized steel therefrom |
| CN102409227B (en) * | 2011-10-26 | 2013-04-17 | 东北大学 | Hot rolled strip steel with low relative magnetic permeability and preparation method thereof |
| KR101428151B1 (en) | 2011-12-27 | 2014-08-08 | 주식회사 포스코 | Zn-coated hot rolled steel sheet having high mn and method for manufacturing the same |
| KR101449119B1 (en) * | 2012-09-04 | 2014-10-08 | 주식회사 포스코 | Ferritic lightweight high strength steel sheet having excellent rigidity and ductility and method for manufacturing the same |
| KR101490560B1 (en) | 2012-12-20 | 2015-02-05 | 주식회사 포스코 | Low gravity steel material having excellent ductility and method for manufacturing the same |
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Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE899508C (en) * | 1944-02-27 | 1953-12-14 | Administration Sequestre Des R | Heat-resistant aluminum-manganese-silicon steel |
| DE1182844B (en) * | 1959-06-23 | 1964-12-03 | Ford Werke Ag | Austenitic steel alloy |
| CH680267A4 (en) * | 1967-05-13 | 1969-11-14 | Straumann Inst Ag | Component with a temperature coefficient only slightly deviating from zero for a timing device |
| USH326H (en) * | 1984-05-22 | 1987-09-01 | The United States Of America As Represented By The United States Department Of Energy | Mn-Fe base and Mn-Cr-Fe base austenitic alloys |
| US4975335A (en) * | 1988-07-08 | 1990-12-04 | Fancy Steel Corporation | Fe-Mn-Al-C based alloy articles and parts and their treatments |
| JP3614869B2 (en) * | 1992-12-18 | 2005-01-26 | 財団法人電気磁気材料研究所 | High strength non-magnetic low thermal expansion alloy |
| DE19724661C2 (en) * | 1997-06-11 | 1999-10-28 | Leico Werkzeugmaschb Gmbh & Co | Process for producing a toothed gear part |
| DE19727759C2 (en) * | 1997-07-01 | 2000-05-18 | Max Planck Inst Eisenforschung | Use of a lightweight steel |
| DE19900199A1 (en) | 1999-01-06 | 2000-07-13 | Ralf Uebachs | High strength light constructional steel for pre-stressed concrete reinforcements or automobile body components has high manganese and aluminum contents |
| FR2796083B1 (en) * | 1999-07-07 | 2001-08-31 | Usinor | PROCESS FOR MANUFACTURING IRON-CARBON-MANGANESE ALLOY STRIPS, AND STRIPS THUS PRODUCED |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006509912A (en) * | 2002-12-17 | 2006-03-23 | ティッセンクルップ シュタール アクチェンゲゼルシャフト | Steel product manufacturing method |
Also Published As
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|---|---|
| PT1309734E (en) | 2007-11-28 |
| DE50210689D1 (en) | 2007-09-27 |
| ES2292762T3 (en) | 2008-03-16 |
| ES2292762T5 (en) | 2012-10-29 |
| WO2002101109A1 (en) | 2002-12-19 |
| CN1463297A (en) | 2003-12-24 |
| JP2004521192A (en) | 2004-07-15 |
| EP1309734B2 (en) | 2012-06-20 |
| CN1215188C (en) | 2005-08-17 |
| DE10128544A1 (en) | 2003-01-02 |
| EP1309734B1 (en) | 2007-08-15 |
| DE10128544C2 (en) | 2003-06-05 |
| US20030145911A1 (en) | 2003-08-07 |
| DK1309734T3 (en) | 2007-12-27 |
| EP1309734A1 (en) | 2003-05-14 |
| KR20030019908A (en) | 2003-03-07 |
| CA2414138A1 (en) | 2002-12-02 |
| ATE370258T1 (en) | 2007-09-15 |
| KR100536645B1 (en) | 2005-12-14 |
| CA2414138C (en) | 2012-12-11 |
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