JPH11100640A - High strength hot rolled steel sheet having high dynamic deformation resistance and its production - Google Patents
High strength hot rolled steel sheet having high dynamic deformation resistance and its productionInfo
- Publication number
- JPH11100640A JPH11100640A JP25888797A JP25888797A JPH11100640A JP H11100640 A JPH11100640 A JP H11100640A JP 25888797 A JP25888797 A JP 25888797A JP 25888797 A JP25888797 A JP 25888797A JP H11100640 A JPH11100640 A JP H11100640A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- less
- rolled steel
- hot
- deformation resistance
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車部材等に使
用され、衝突時の衝撃エネルギーを効率よく吸収するこ
とによって乗員の安全性確保に寄与することの出来る高
い動的変形抵抗を示す高強度熱延鋼板とその製造方法に
関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength steel having a high dynamic deformation resistance which can be used for automobile parts and the like and which can contribute to ensuring the safety of occupants by efficiently absorbing impact energy at the time of collision. The present invention relates to a hot-rolled steel sheet and a method for manufacturing the same.
【０００２】[0002]
【従来の技術】近年、自動車衝突時の乗員保護が自動車
の最重要性能として認識され、それに対応するための高
い高速変形抵抗を示す材料への期待が高まっている。例
えば乗用車の前面衝突においては、フロントサイドメン
バーと呼ばれる部材にこの様な材料を適用すれば、該部
材が圧潰することで衝撃のエネルギーが吸収され、乗員
にかかる衝撃を和らげることが出来る。2. Description of the Related Art In recent years, occupant protection in the event of an automobile collision has been recognized as the most important performance of an automobile, and there has been an increasing expectation for a material exhibiting high high-speed deformation resistance in order to cope with it. For example, in the case of a frontal collision of a passenger car, if such a material is applied to a member called a front side member, the member is crushed, so that the energy of the impact is absorbed and the impact on the occupant can be reduced.
【０００３】自動車の衝突時に各部位が受ける変形の歪
み速度は１０3 （１／ｓ）程度まで達するため、材料の
衝撃吸収性能を考える場合には、この様な高歪み速度領
域での動的変形特性の解明が必要である。また同時に、
省エネルギー、ＣＯ2 排出削減を目指して自動車車体の
軽量化を同時に達成することが必須と考えられ、このた
めに有効な高強度鋼板へのニーズが高まっている。[0003] Since the strain rate of deformation applied to each part at the time of an automobile collision reaches up to about 10 3 (1 / s), when considering the shock absorbing performance of a material, dynamic deformation in such a high strain rate region is considered. It is necessary to clarify the deformation characteristics. At the same time,
It is considered essential to simultaneously reduce the weight of automobile bodies with the aim of conserving energy and reducing CO 2 emissions, and for this purpose there is a growing need for effective high-strength steel sheets.
【０００４】例えば本発明者らは、CAMP-ISIJ Vol.9 (1
996) p.1112 〜1115に、高強度薄鋼板の高速変形特性と
衝撃エネルギー吸収能について報告し、その中で、１０
3 （１／ｓ）程度の高歪み速度領域での動的強度は、１
０-3（１／ｓ）の低歪み速度での静的強度と比較して大
きく上昇すること、材料の強化機構によって変形抵抗の
歪み速度依存性が変化すること、この中で、ＴＲＩＰ
（変態誘起塑性）型の鋼やＤＰ（フェライト／マルテン
サイト２相）型の鋼が他の高強度鋼板に比べて優れた成
形性と衝撃吸収能を兼ね備えていることを報告してい
る。[0004] For example, the present inventors have proposed CAMP-ISIJ Vol.
996) pp. 1112 to 1115 report on the high-speed deformation characteristics and impact energy absorption capacity of high-strength thin steel sheets.
The dynamic strength in a high strain rate region of about 3 (1 / s) is 1
0 -3 (1 / s) of the greatly increased as compared to the static strength at a low strain rate, the strain rate dependence of deformation resistance by strengthening mechanism of the material changes, in this, TRIP
It is reported that (transformation-induced plasticity) type steel and DP (ferrite / martensite two-phase) type steel have both excellent formability and shock absorbing ability as compared with other high-strength steel sheets.
【０００５】また、残留オーステナイトを含む耐衝撃特
性に優れた高強度鋼板とその製造方法を提供するものと
して、特開平７−１８３７２号公報には、衝撃吸収能を
変形速度の上昇に伴う降伏応力の上昇のみで解決できる
ことを開示しているが衝撃吸収能を向上させるために、
残留オーステナイトの量以外に残留オーステナイトの性
質をどのように制御すべきかは依然として明確にされて
いない。Japanese Patent Application Laid-Open No. 7-18372 discloses a high-strength steel sheet containing retained austenite and having excellent impact resistance and a method of manufacturing the same. It is disclosed that it can be solved only by the rise of, but in order to improve the shock absorption capacity,
How to control the properties of retained austenite other than the amount of retained austenite remains unclear.
【０００６】[0006]
【発明が解決しようとする課題】このように、自動車衝
突時の衝撃エネルギーの吸収に及ぼす部材構成材料の動
的変形特性は少しづつ解明されつつあるものの、衝撃エ
ネルギー吸収能に優れた自動車部品用鋼材としてどのよ
うな特性に注目し、どのような基準に従って材料選定を
行うべきかは未だ明らかにされていない。また、自動車
用部品は、鋼材をプレス成形によって要求された部品形
状に成形され、その後、一般的には塗装焼き付けされた
後に自動車に組み込まれ、実際の衝突現象に直面する。
しかしながら、このような予変形＋焼き付け処理を行っ
た後の鋼材の衝突時の衝突エネルギー吸収能の向上にど
のような鋼材強化機構が適しているかも未だ明らかにさ
れていない。As described above, although the dynamic deformation characteristics of the constituent materials affecting the absorption of the impact energy at the time of the collision of the automobile are gradually being elucidated, the automotive parts having excellent impact energy absorption capability are being elucidated. It has not yet been clarified what properties to focus on and what criteria should be used for material selection as steel. In addition, automotive parts are formed by pressing steel into the required part shape and then, after being generally painted and baked, are assembled into the automobile and face an actual collision phenomenon.
However, it has not yet been clarified which steel material strengthening mechanism is suitable for improving the collision energy absorbing ability at the time of collision of the steel material after performing such pre-deformation and baking treatment.
【０００７】[0007]
【課題を解決するための手段】本発明は、フロントサイ
ドメンバー等の衝突時の衝撃エネルギー吸収を担う部品
に成形加工されて使用される鋼材で、高い衝撃エネルギ
ー吸収能を示す高強度鋼板とその製造方法を提供するこ
とを目的としている。その要旨は次のとおりである。SUMMARY OF THE INVENTION The present invention relates to a high-strength steel sheet having high impact energy absorbing ability, which is a steel material formed into a part for absorbing impact energy at the time of collision such as a front side member and used. It is intended to provide a manufacturing method. The summary is as follows.
【０００８】（１）重量％で、Ｃ：０．０４％以上０．
３％以下、ＳｉとＡｌの一方または双方を合計で０．５
％以上３．０％以下、Ｍｎ，Ｎｉ，Ｃｒ，Ｃｕ，Ｍｏの
１種または２種以上を合計で０．５％以上３．５％以下
含み、残部がＦｅ及び不可避的不純物からなり、最終的
に得られる圧延鋼板のミクロ組織がフェライトおよびベ
イナイトを含み、このいずれかを主相とし、体積分率で
３％以上の残留オーステナイトを含む第３相との複合組
織であり、前記残留オーステナイト中の固溶〔Ｃ〕と鋼
材の平均Ｍｎ等量｛Ｍｎｅｑ＝Ｍｎ＋（Ｎｉ＋Ｃｒ＋Ｃ
ｕ＋Ｍｏ）／２｝によって決まる値（Ｍ＝６７８−４２
８×〔Ｃ〕−３３×Ｍｎｅｑ）が７０以上２５０以下
で、前記熱延鋼板に相当歪みで０％超１０％以下の予変
形を与えた後、５×１０2 〜５×１０3 （１／ｓ）の歪
み速度範囲で変形した時の３〜１０％の相当歪み範囲に
おける変形応力の平均値：σdyn (MPa) が予変形を与え
る前の５×１０-4〜５×１０-3（１／ｓ）の歪み速度範
囲で測定された静的な引張り試験における最大応力ＴＳ
(MPa) によって表現される式：σdyn ≧０．７６６×Ｔ
Ｓ＋２５０を満足することを特徴とする高い動的変形抵
抗を有する高強度熱延鋼板。(1) By weight%, C: 0.04% or more.
3% or less, one or both of Si and Al in total of 0.5
% Or more and 3.0% or less, one or more of Mn, Ni, Cr, Cu and Mo are contained in a total of 0.5% or more and 3.5% or less, with the balance being Fe and inevitable impurities. The microstructure of the rolled steel sheet obtained in a typical manner contains ferrite and bainite, and has a composite phase with a third phase containing any one of them as a main phase and having a volume fraction of 3% or more of retained austenite. [C] and average Mn equivalent of steel material 等 Mneq = Mn + (Ni + Cr + C
u + Mo) / 2} (M = 678−42)
8 × [C] −33 × Mneq) is 70 or more and 250 or less, and after giving a pre-deformation of more than 0% and 10% or less with considerable strain to the hot-rolled steel sheet, 5 × 10 2 to 5 × 10 3 (1 / S) average value of the deformation stress in the equivalent strain range of 3 to 10% when deformed in the strain rate range of 5 × 10 −4 to 5 × 10 −3 before σdyn (MPa) gives the pre-deformation. 1 / s) maximum stress TS in a static tensile test measured in the strain rate range
Expression expressed by (MPa): σdyn ≧ 0.766 × T
A high-strength hot-rolled steel sheet having high dynamic deformation resistance, satisfying S + 250.
【０００９】（２）Ｎｂ，Ｔｉ，Ｖの１種又は２種以上
を合計で０．３重量％以下更に含むことを特徴とする
（１）に記載の高い動的変形抵抗を有する高強度熱延鋼
板。 （３）Ｐを０．２重量％以下更に含むことを特徴とする
（１）または（２）に記載の高い動的変形抵抗を有する
高強度熱延鋼板。 （４）Ｂを０．０１重量％以下更に含むことを特徴とす
る（１）〜（３）のいずれか１に記載の高い動的変形抵
抗を有する高強度熱延鋼板。(2) A high-strength heat having high dynamic deformation resistance according to (1), further comprising one or more of Nb, Ti and V in a total amount of 0.3% by weight or less. Rolled steel sheet. (3) The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to (1) or (2), further comprising P in an amount of 0.2% by weight or less. (4) The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to any one of (1) to (3), further comprising 0.01% by weight or less of B.
【００１０】（５）０％超１０％以下の予変形を与えた
後の鋼材の残留オーステナイト体積分率が２．５％超で
あり、かつ、予変形前の残留オーステナイト体積分率と
予変形後の残留オーステナイト体積分率の比が０．３以
上であることを特徴とする（１）〜（４）のいずれか１
に記載の高い動的変形抵抗を有する高強度熱延鋼板。 （６）最終的に得られた熱延鋼板のミクロ組織中の残留
オーステナイトの平均粒径と、主相であるフェライトも
しくはベイナイトの平均粒径の比が０．６以下であるこ
とを特徴とする（１）〜（５）のいずれか１に記載の高
い動的変形抵抗を有する高強度熱延鋼板。(5) The residual austenite volume fraction of the steel after the pre-deformation of more than 0% and 10% or less is more than 2.5%, and the residual austenite volume fraction and pre-deformation before the pre-deformation Any one of (1) to (4), wherein the ratio of the remaining retained austenite volume fraction is 0.3 or more
A high-strength hot-rolled steel sheet having high dynamic deformation resistance according to 1. (6) The ratio of the average grain size of retained austenite in the microstructure of the finally obtained hot-rolled steel sheet to the average grain size of ferrite or bainite as a main phase is 0.6 or less. The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to any one of (1) to (5).
【００１１】（７）重量％で、Ｃ：０．０４％以上０．
３％以下、ＳｉとＡｌの一方または双方を合計で０．５
％以上３．０％以下、Ｍｎ，Ｎｉ，Ｃｒ，Ｃｕ，Ｍｏの
１種または２種以上を合計で０．５％以上３．５％以下
含み、残部がＦｅ及び不可避的不純物からなる鋳造スラ
ブを、鋳造ままで熱延工程へ直送し、もしくは一旦冷却
した後に１０００℃〜１３００℃の範囲に再度加熱した
後、熱延をＡｒ3 変態温度−１０℃以上Ａｒ3 変態温度
＋１２０℃未満の温度（熱延仕上げ温度ＦＴ）で完了
し、その後５℃／秒以上１００℃／秒以下の冷却速度で
冷却し、巻き取る際に、前記熱延仕上げ温度がＡｒ3 変
態温度＋５０℃以上の場合には２５０℃以上３８０℃未
満の温度で巻き取り、前記熱延仕上げ温度がＡｒ3 変態
温度＋５０℃未満の場合には２５０℃以上４２０℃未満
で巻き取ることを特徴とする、最終的に得られる熱延鋼
板のミクロ組織がフェライトおよびベイナイトを含み、
このいずれかを主相とし、体積分率で３％以上の残留オ
ーステナイトを含む第３相との複合組織であり、残留オ
ーステナイト中の固溶〔Ｃ〕とスラブの平均Ｍｎ等量
｛Ｍｎｅｑ＝Ｍｎ＋（Ｎｉ＋Ｃｒ＋Ｃｕ＋Ｍｏ）／２｝
によって決まる値（Ｍ＝６７８−４２８×〔Ｃ〕−３３
×Ｍｎｅｑ）が７０以上２５０以下で、その鋼材に相当
歪みで０％超１０％以下の予変形を与えた後、５×１０
2 〜５×１０3 （１／ｓ）の歪み速度範囲で変形した時
の３〜１０％の相当歪み範囲における変形応力の平均
値：σdyn (MPa) が予変形を与える前の５×１０-4〜５
×１０-3（１／ｓ）の歪み速度範囲で測定された静的な
引張り試験における最大応力ＴＳ(MPa) によって表現さ
れる式：σdyn ≧０．７６６×ＴＳ＋２５０を満足する
高い動的変形抵抗を有する高強度熱延鋼板の製造方法。(7) By weight%, C: 0.04% or more.
3% or less, one or both of Si and Al in total of 0.5
% Or more and 3.0% or less, and one or more of Mn, Ni, Cr, Cu and Mo in total of 0.5% or more and 3.5% or less, with the balance being Fe and unavoidable impurities. Is directly sent to the hot rolling process as cast, or once cooled and then heated again in the range of 1000 ° C. to 1300 ° C., and then the hot rolled is heated to a temperature of Ar 3 transformation temperature−10 ° C. or more and less than Ar 3 transformation temperature + 120 ° C. (Hot-rolling finishing temperature FT), then cooling at a cooling rate of 5 ° C / sec or more and 100 ° C / sec or less, and when winding, when the hot-rolling finishing temperature is Ar 3 transformation temperature + 50 ° C or more, the wound at a temperature below 250 ° C. or higher 380 ° C., wherein the wound is less than 420 ° C. 250 ° C. or higher in the case where the hot-rolling finishing temperature is lower than Ar 3 transformation temperature + 50 ° C., the finally obtained The microstructure of hot rolled steel sheet Including the intent and bainite,
A composite structure of any one of the main phases and a third phase containing retained austenite in a volume fraction of 3% or more, wherein the solid solution [C] in the retained austenite and the average Mn equivalent of the slab ｛Mneq = Mn + (Ni + Cr + Cu + Mo) / 2｝
(M = 678-428 × [C] -33)
× Mneq) is 70 or more and 250 or less, and after giving a predeformation of more than 0% and 10% or less with considerable strain to the steel material, 5 × 10
The average value of the deformation stress in the equivalent strain range of 3 to 10% when deformed at the strain rate range of 2 to 5 × 10 3 (1 / s): 5 × 10 − before σdyn (MPa) gives the pre-deformation. 4 to 5
High dynamic deformation resistance that satisfies the equation expressed by the maximum stress TS (MPa) in a static tensile test measured in a strain rate range of × 10 −3 (1 / s): σdyn ≧ 0.766 × TS + 250 A method for producing a high-strength hot-rolled steel sheet having:
【００１２】（８）Ｎｂ，Ｔｉ，Ｖの１種又は２種以上
を合計で０．３％以下更に含むことを特徴とする（７）
に記載の高い動的変形抵抗を有する高強度熱延鋼板の製
造方法。 （９）Ｐを０．２重量％以下更に含むことを特徴とする
（７）または（８）に記載の高い動的変形抵抗を有する
高強度熱延鋼板の製造方法。(8) One or more of Nb, Ti and V are further contained in a total of 0.3% or less. (7)
3. A method for producing a high-strength hot-rolled steel sheet having high dynamic deformation resistance according to item 1. (9) The method for producing a high-strength hot-rolled steel sheet having high dynamic deformation resistance according to (7) or (8), further comprising 0.2% by weight or less of P.
【００１３】（１０）Ｂを０．０１重量％以下更に含む
ことを特徴とする（７）〜（９）のいずれか１に記載の
高い動的変形抵抗を有する高強度熱延鋼板の製造方法。(10) The method for producing a high-strength hot-rolled steel sheet having high dynamic deformation resistance according to any one of (7) to (9), further comprising 0.01% by weight or less of B. .
【００１４】[0014]
【発明の実施の形態】自動車のフロントサイドメンバー
等の衝突時の衝撃吸収用部材は、鋼板に曲げ加工やプレ
ス成形加工によって製造される。自動車の衝突時の衝撃
は、この様にして加工されて後に一般的には塗装焼き付
けされた後に加えられる。従って、この様に部材への加
工、処理が行われたのちに高い衝撃エネルギーの吸収能
を示す鋼板が必要となる。DESCRIPTION OF THE PREFERRED EMBODIMENTS A member for absorbing a shock such as a front side member of an automobile at the time of a collision is manufactured by bending or pressing a steel plate. The impact of an automobile collision is applied after it has been worked in this way, and generally after it has been baked. Therefore, a steel sheet that exhibits high impact energy absorption capacity after such processing and processing into members is required.
【００１５】本発明者らの研究の結果、このような成形
加工された実部材において、鋼板に適量の残留オーステ
ナイトを含むことが優れた衝撃吸収特性を示す高強度鋼
板を提供できることが判明した。すなわち、最終的に得
られる熱延鋼板中に存在する最適なミクロ組織は、種々
の置換型元素によって容易に固溶強化されるフェライト
およびベイナイトを含み、このいずれかを主相として、
塑性変形中に硬質のマルテンサイトに変態する残留オー
ステナイトを体積分率で３％以上含む場合に、高い動的
変形抵抗を示すことが判明した。また、初期ミクロ組織
の第３相にマルテンサイト粒子を含む場合にも、他の条
件が満足されれば、本発明の目的とする高い衝撃エネル
ギー吸収能を示す高強度鋼板の製造が可能となる。As a result of the study of the present inventors, it has been found that a high strength steel sheet exhibiting excellent shock absorption characteristics can be provided by including an appropriate amount of retained austenite in the steel sheet in such a molded real member. That is, the optimal microstructure present in the finally obtained hot-rolled steel sheet includes ferrite and bainite which are easily solid-solution strengthened by various substitution elements, and any one of these as a main phase,
It was found that high dynamic deformation resistance was exhibited when residual austenite, which transforms into hard martensite during plastic deformation, is contained in a volume fraction of 3% or more. Further, even when the third phase of the initial microstructure contains martensite particles, if the other conditions are satisfied, it is possible to produce a high-strength steel sheet exhibiting a high impact energy absorbing ability, which is the object of the present invention. .
【００１６】本発明で規定する熱延鋼板の各成分の限定
理由は下記のとおりである。 Ｃ：Ｃはオーステナイトを室温で安定化させて残留させ
るために必要なオーステナイトの安定化に貢献する最も
安価な元素であるために、本発明において最も重要な元
素といえる。鋼材の平均Ｃ量は、室温で確保できる残留
オーステナイト体積分率に影響を及ぼすのみならず、製
造の加工熱処理中に未変態オーステナイト中に濃化する
ことで、残留オーステナイトの加工に対する安定性を向
上させることが出来る。しかしながら、この添加量が
０．０４重量％未満の場合には、最終的に得られる残留
オーステナイト体積分率が３％以上を確保することが出
来ないので０．０４％を下限とした。一方、鋼材の平均
Ｃ量が増加するに従って確保可能な残留オーステナイト
体積分率は増加し、残留オーステナイト体積率を確保し
つつ残留オーステナイトの安定性を確保することが可能
となる。しかしながら、鋼材のＣ添加量が過大になる
と、必要以上に鋼材の強度を上昇させ、プレス加工等の
成形性を阻害するのみならず、静的な強度上昇に比して
動的な応力上昇が阻害されると共に、溶接性を低下させ
ることによって成形された部品としての鋼材の利用が制
限されるようになる。従って鋼材のＣ重量％の上限を
０．３％とした。The reasons for limiting each component of the hot-rolled steel sheet specified in the present invention are as follows. C: C is the most important element in the present invention because it is the cheapest element that contributes to the stabilization of austenite, which is necessary for stabilizing austenite at room temperature to remain. The average C content of the steel material not only affects the retained austenite volume fraction that can be secured at room temperature, but also increases the stability of the retained austenite to processing by enriching in untransformed austenite during the thermomechanical heat treatment during production. Can be done. However, if the addition amount is less than 0.04% by weight, the residual austenite volume fraction finally obtained cannot be 3% or more, so the lower limit was made 0.04%. On the other hand, the retained austenite volume fraction that can be secured increases as the average C content of the steel material increases, and it becomes possible to secure the stability of retained austenite while securing the retained austenite volume fraction. However, when the amount of C added to the steel material is excessive, the strength of the steel material is increased more than necessary, not only impairing the formability such as press working, but also increasing the dynamic stress as compared with the static strength increase. In addition to being hindered, the use of steel as a molded part is restricted by reducing the weldability. Therefore, the upper limit of C weight% of the steel material is set to 0.3%.
【００１７】Ａｌ，Ｓｉ：ＡｌとＳｉは共にフェライト
の安定化元素であり、フェライト体積率を増加させるこ
とによって鋼材の加工性を向上させる働きがある。ま
た、Ａｌ，Ｓｉ共にセメンタイトの生成を抑制すること
から、効果的にオーステナイト中へのＣを濃化させるこ
とを可能とすることから、室温で適当な体積分率のオー
ステナイトを残留させるためには不可避的な添加元素で
ある。このようなセメンタイト生成抑制機能を持つ添加
元素としては、Ａｌ，Ｓｉ以外に、ＰやＣｕ，Ｃｒ，Ｍ
ｏ等が挙げられ、このような元素を適切に添加すること
も同様な効果が期待される。しかしながら、ＡｌとＳｉ
の一種もしくは双方の合計が０．５重量％未満の場合に
は、セメンタイト生成抑制の効果が十分でなく、オース
テナイトの安定化に最も効果的な添加されたＣの多くが
炭化物の形で浪費され、本発明に必要な残留オーステナ
イト体積率を確保することが出来ないか、もしくは残留
オーステナイトの確保に必要な製造条件が大量生産工程
の条件に適しないため下限を０．５重量％とした。ま
た、ＡｌとＳｉの一種もしくは双方の合計が３．０％を
越える場合には、母相であるフェライトもしくはベイナ
イトの硬質化や脆化を招き、歪み速度上昇による変形抵
抗の増加を阻害するばかりでなく、鋼材の加工性の低
下、靱性の低下、さらには鋼材コストの上昇を招き、ま
た化成処理性等の表面処理特性が著しく劣化するため
に、３．０重量％を上限値とした。Al, Si: Al and Si are both ferrite stabilizing elements, and have a function of improving the workability of steel by increasing the volume ratio of ferrite. In addition, since both Al and Si suppress the generation of cementite, it is possible to effectively enrich C in austenite. Therefore, it is necessary to leave austenite having an appropriate volume fraction at room temperature. It is an inevitable additional element. Examples of the additive element having such a cementite generation suppressing function include P, Cu, Cr, and M in addition to Al and Si.
and the like, and the same effect can be expected by appropriately adding such an element. However, Al and Si
If the total amount of one or both of them is less than 0.5% by weight, the effect of suppressing the formation of cementite is not sufficient, and most of the added C most effective for stabilizing austenite is wasted in the form of carbide. Since the volume ratio of retained austenite required for the present invention cannot be secured, or the manufacturing conditions required for securing the retained austenite are not suitable for the conditions of the mass production process, the lower limit was set to 0.5% by weight. On the other hand, if the sum of one or both of Al and Si exceeds 3.0%, hardening or embrittlement of the ferrite or bainite as the mother phase is caused, and the increase in deformation resistance due to an increase in strain rate is hindered. On the other hand, the upper limit was set to 3.0% by weight because the workability and toughness of the steel material were lowered, the cost of the steel material was increased, and the surface treatment properties such as chemical conversion property were significantly deteriorated.
【００１８】Ｍｎ，Ｎｉ，Ｃｒ，Ｃｕ，Ｍｏ：Ｍｎ，Ｎ
ｉ，Ｃｒ，Ｃｕ，Ｍｏは全てオーステナイト安定化元素
であり、室温でオーステナイトを安定化させるためには
有効な元素である。特に、溶接性の観点からＣの添加量
が制限される場合には、この様なオーステナイト安定化
元素を適量添加することによって効果的にオーステナイ
トを残留させることが可能となる。また、これらの元素
はＡｌやＳｉ程ではないがセメンタイトの生成を抑制す
る効果があり、オーステナイトへのＣの濃化を助ける働
きもする。更に、これらの元素はＡｌ，Ｓｉと共にマト
リックスであるフェライトやベイナイトを固溶強化させ
ることによって、高速での動的変形抵抗を高める働きも
持つ。しかしながら、これらの元素の１種もしくは２種
以上の添加の合計が０．５重量％未満の場合には、必要
な残留オーステナイトの確保が出来なくなるとともに、
鋼材の強度が低くなり、有効な車体軽量化が達成できな
くなることから、下限を０．５重量％とした。一方、こ
れらの合計が３．５重量％を越える場合には、母相であ
るフェライトもしくはベイナイトの硬質化を招き、歪み
速度上昇による変形抵抗の増加を阻害するばかりでな
く、鋼材の加工性の低下、靱性の低下、さらには鋼材コ
ストの上昇を招くために、上限を３．５重量％とした。Mn, Ni, Cr, Cu, Mo: Mn, N
i, Cr, Cu, and Mo are all austenite stabilizing elements, and are effective elements for stabilizing austenite at room temperature. In particular, when the addition amount of C is restricted from the viewpoint of weldability, it is possible to effectively retain austenite by adding an appropriate amount of such an austenite stabilizing element. In addition, these elements are not as effective as Al and Si, but have the effect of suppressing the generation of cementite, and also work to assist the enrichment of C in austenite. Further, these elements have a function of increasing the dynamic deformation resistance at high speed by solid-solution strengthening the matrix ferrite and bainite together with Al and Si. However, if the total of the addition of one or more of these elements is less than 0.5% by weight, the necessary retained austenite cannot be secured, and
The lower limit was set to 0.5% by weight because the strength of the steel material was reduced and an effective vehicle weight reduction could not be achieved. On the other hand, if the sum of them exceeds 3.5% by weight, hardening of the ferrite or bainite which is the parent phase is caused, and not only the increase in deformation resistance due to the increase in strain rate is inhibited, but also the workability of the steel material is reduced. The upper limit is set at 3.5% by weight in order to cause a decrease in the toughness, a decrease in the toughness, and an increase in the cost of the steel material.
【００１９】Ｎｂ，Ｔｉ，Ｖ：また、必要に応じて添加
するＮｂ，Ｔｉ，Ｖは、炭化物、窒化物もしくは炭窒化
物を形成することによって鋼材を高強度化することが出
来るが、その合計が０．３％を越えた場合には母相であ
るフェライトやベイナイト粒内もしくは粒界に多量の炭
化物、窒化物もしくは炭窒化物として析出し、高速変形
時の可動転位発生源となって、高い動的変形抵抗を得る
ことが出来なくなる。また、炭化物の生成は、本発明に
とって最も重要な残留オーステナイト中へのＣの濃化を
阻害し、Ｃを浪費することから上限を０．３重量％とし
た。Nb, Ti, V: Nb, Ti, V added as necessary can increase the strength of steel by forming carbide, nitride or carbonitride. If it exceeds 0.3%, it precipitates as a large amount of carbide, nitride or carbonitride in the ferrite or bainite grains, which are the parent phase, or at the grain boundaries, and becomes a mobile dislocation generating source during high-speed deformation. High dynamic deformation resistance cannot be obtained. The formation of carbides inhibits the concentration of C in retained austenite, which is the most important for the present invention, and wastes C. Therefore, the upper limit is set to 0.3% by weight.
【００２０】Ｐ：更に、必要に応じて添加するＰは、鋼
材の高強度化や前述のように残留オーステナイトの確保
に有効ではあるが、０．２重量％を越えて添加された場
合には鋼材のコストの上昇を招くばかりでなく、主相で
あるフェライトやベイナイトの変形抵抗を必要以上に高
め、かつ高速変形時の変形抵抗の上昇を阻害する。更
に、耐置き割れ性の劣化や疲労特性、靱性の劣化を招く
ことから、０．２重量％をその上限とした。P: P added as necessary is effective in increasing the strength of the steel material and securing the retained austenite as described above. However, when added in excess of 0.2% by weight, Not only does the cost of the steel material rise, but also the deformation resistance of the main phase, ferrite and bainite, is unnecessarily increased, and the deformation resistance during high-speed deformation is hindered. In addition, 0.2% by weight was set as the upper limit because deterioration of storage crack resistance and deterioration of fatigue characteristics and toughness are caused.
【００２１】Ｂ：また、必要に応じて添加するＢは、粒
界の強化や鋼材の高強度化に有効ではあるが、その添加
量が０．０１重量％を越えるとその効果が飽和するばか
りでなく、必要以上に鋼板強度を上昇させ、高速変形時
の変形抵抗の上昇を阻害すると共に、成形部品への加工
性も低下させることから、上限を０．０１重量％とし
た。B: B, which is added as required, is effective for strengthening grain boundaries and increasing the strength of steel materials. However, if the added amount exceeds 0.01% by weight, the effect is only saturated. Rather, the upper limit is set to 0.01% by weight because the steel sheet strength is unnecessarily increased, the increase in deformation resistance during high-speed deformation is inhibited, and the workability of a molded part is also reduced.
【００２２】次に、本発明者らの実験・検討の結果、フ
ロントサイドメンバー等の衝撃吸収用部材の成形加工に
相当する予変形の量は、部材中の部位によっては最大２
０％以上に達する場合もあるが、相当歪みとして０％超
１０％以下の部位が大半であり、また、この範囲の予変
形の効果を把握することで、部材全体としての予変形後
の挙動を推定することが可能であることを見いだした。
従って、本発明においては、部材への加工時に与えられ
る予変形量として相当歪みにして０％超１０％以下の変
形を選択した。Next, as a result of experiments and studies conducted by the present inventors, the amount of pre-deformation corresponding to the forming process of a shock absorbing member such as a front side member may be up to 2 depending on a part in the member.
Although it may reach 0% or more, most of the parts have an equivalent strain of more than 0% to 10%, and by grasping the effect of the pre-deformation in this range, the behavior of the member as a whole after the pre-deformation It was found that it was possible to estimate
Therefore, in the present invention, a deformation of more than 0% and 10% or less is selected as a substantial strain as a pre-deformation amount given at the time of processing the member.
【００２３】また、フロントサイドメンバー等の衝撃吸
収用部材は、特徴的にハット型の断面形状をしており、
このような部材の高速での衝突圧潰時の変形を本発明者
らが解析した結果、最大では４０％以上の高い歪みまで
変形が進んでいるものの、吸収エネルギー全体の約７０
％以上が、高速の応力−歪み線図の１０％以下の歪み範
囲で吸収されていることを見いだした。従って、高速で
の衝突エネルギーの吸収能の指標として、１０％以下で
の高速変形時の動的変形抵抗を採用した。特に、歪み量
として３％〜１０％の範囲が最も重要であることから、
高速引張り変形時の相当歪みで３％〜１０％の範囲の平
均応力：σdyn をもって衝撃エネルギー吸収能の指標と
した。The shock absorbing member such as the front side member has a characteristic hat-shaped cross section.
As a result of analyzing the deformation of such a member at the time of collision crush at high speed, the deformation has progressed up to a high strain of 40% or more at the maximum, but about 70% of the total absorbed energy.
% Was absorbed in the strain range of 10% or less of the high-speed stress-strain diagram. Therefore, the dynamic deformation resistance at the time of high-speed deformation of 10% or less was adopted as an index of the absorption capacity of the collision energy at high speed. In particular, since the range of 3% to 10% is most important as the amount of distortion,
The equivalent energy at the time of high-speed tensile deformation was 3% to 10% and the average stress: σdyn was used as an index of the impact energy absorbing ability.
【００２４】この高速変形時の３％〜１０％の平均応
力：σdyn (MPa) は、予変形や焼き付け処理が行われる
前の鋼材の静的な引張り強度（５×１０-4〜５×１０-3
（１／ｓ）の歪み速度範囲で測定された静的な引張り試
験における最大応力ＴＳの上昇に伴って大きくなること
が一般的である。従って鋼材の静的な引張り強度を増加
させることは部材の衝撃エネルギー吸収能の向上に直接
寄与する。しかしながら、鋼材の強度が上昇すると部材
への成形性が劣化し、必要な部材形状を得ることが困難
となる。従って、同一の最大応力で高いσdyn を持つ鋼
材が望ましい。この関係で、特にσdyn ≧０．７６６×
ＴＳ＋２５０の関係を満足する鋼材は、実部材としての
衝撃エネルギー吸収能が他の鋼材に比べて高く、部材の
総重量を増加させることなく衝撃エネルギー吸収能を向
上させることができることを見いだした。The average stress of 3% to 10% during high-speed deformation: σdyn (MPa) is the static tensile strength (5 × 10 −4 to 5 × 10 −4 ) of the steel material before the pre-deformation or baking treatment is performed. -3
It generally increases with an increase in the maximum stress TS in a static tensile test measured in a strain rate range of (1 / s). Therefore, increasing the static tensile strength of the steel directly contributes to the improvement of the impact energy absorbing ability of the member. However, when the strength of the steel material increases, the formability of the member deteriorates, and it becomes difficult to obtain a required member shape. Therefore, a steel material having the same maximum stress and a high σdyn is desirable. In this relation, in particular, σdyn ≧ 0.766 ×
It has been found that a steel material that satisfies the relationship of TS + 250 has a higher impact energy absorbing ability as an actual member than other steel materials, and can improve the impact energy absorbing ability without increasing the total weight of the member.
【００２５】本発明者らの実験・検討の結果、同一レベ
ルの最大応力に対して、σdyn は部材への加工が行われ
る以前の鋼板中に含まれる残留オーステナイト中の固溶
炭素量〔Ｃ〕（重量％）と鋼材の平均Ｍｎ等量（Ｍｎｅ
ｑ：重量％）｛Ｍｎｅｑ＝Ｍｎ＋（Ｎｉ＋Ｃｒ＋Ｃｕ＋
Ｍｏ）／２｝によって変化することが見いだされた。残
留オーステナイト中の炭素濃度は、Ｘ線解析やメスバウ
アー分光により実験的に求めることが出来、例えばＭｏ
のＫα線を用いたＸ線解析によりフェライトの（２０
０）面、（２１１）面及びオーステナイトの（２００）
面、（２２０）面、（３１１）面の積分反射強度をもち
いて、Journal of The Iron and Steel Institute, 206
(1968) p.60に示された方法にて算出できる。本発明者
らが行った実験結果から、この様にして得られた残留オ
ーステナイト中の固溶〔Ｃ〕と鋼材に添加されている置
換型合金元素から求められるＭｎｅｑを用いて計算され
る値（Ｍ＝６７８−４２８×〔Ｃ〕−３３×Ｍｎｅｑ）
が７０以上２５０以下の場合に、同一の静的な引張り強
度（ＴＳ）に対して大きなσdyn を示すことが見いださ
れた。このときＭ＞２５０では、実質的に変形中の残留
オーステナイトの変態による強度上昇の効果が極めて低
い歪み領域にのみ限られるために、部材への予変形時に
ほぼ全ての残留オーステナイトが浪費され、高速変形時
のσdyn の上昇に寄与しなくなることから、Ｍの上限を
２５０とした。また、Ｍが７０未満の場合には、変形途
中での残留オーステナイトの変態は進行するものの、変
態の進行が低歪み領域では十分に起こらないことから、
相当歪みで３％〜１０％の範囲での平均応力σdyn が低
いままに保たれ、静的な引張り強度（ＴＳ）に対してσ
dyn ≧０．７６６×ＴＳ＋２５０の関係を満足しなくな
るので、Ｍの下限を７０とした。As a result of experiments and studies conducted by the present inventors, for the same level of maximum stress, σdyn is the amount of dissolved carbon [C] in the retained austenite contained in the steel sheet before the member is processed. (% By weight) and average Mn equivalent of steel (Mne
q: wt%) ｛Mneq = Mn + (Ni + Cr + Cu +
Mo) / 2}. The carbon concentration in the retained austenite can be determined experimentally by X-ray analysis or Mossbauer spectroscopy.
X-ray analysis using Kα ray of
0) plane, (211) plane and austenite (200)
Using the integrated reflection intensity of the (220) and (311) planes, Journal of The Iron and Steel Institute, 206
(1968) It can be calculated by the method shown on p.60. From the experimental results performed by the present inventors, a value calculated using the solid solution [C] in the residual austenite thus obtained and Mneq obtained from the substitutional alloy element added to the steel material ( M = 678-428 × [C] −33 × Mneq)
Is greater than or equal to 70 and less than or equal to 250, it has been found to exhibit a large σdyn for the same static tensile strength (TS). At this time, when M> 250, substantially all of the retained austenite is wasted at the time of pre-deformation of the member because the effect of increasing the strength due to the transformation of the retained austenite during deformation is substantially limited only to a very low strain region. The upper limit of M is set to 250 because it does not contribute to the increase in σdyn during deformation. When M is less than 70, the transformation of the retained austenite during the deformation progresses, but the progress of the transformation does not sufficiently occur in the low strain region.
The average stress σdyn in the range of 3% to 10% at equivalent strain is kept low and the σdyn for static tensile strength (TS)
Since the relationship of dyn ≧ 0.766 × TS + 250 is no longer satisfied, the lower limit of M was set to 70.
【００２６】熱延条件：熱延ままで本発明の鋼板を製造
する場合には、所定の成分に調整されたスラブを、鋳造
ままで熱延工程へ直送し、もしくは一旦冷却した後に１
０００℃〜１３００℃の範囲に再度加熱した後、熱間圧
延を行う。再加熱温度を１０００℃未満とする場合に
は、スラブの均一加熱が困難となり、表面キズ発生等の
問題を生じるので、再加熱温度の下限を１０００℃とし
た。また、再加熱温度が１３００℃超では、スラブの変
形が激しくなると同時にコスト高となることから、１３
００℃を上限とした。また、熱延仕上げ温度（ＦＴ）が
Ａｒ3 変態温度−１０℃未満である場合には、鋼板の表
層部及びその近傍に加工フェライト層が生成し、加工性
を著しく劣化させると同時に、動的な変形抵抗を下げ
る。従って、熱延仕上げ温度の下限値をＡｒ3 変態温度
−１０℃とする。また熱延仕上げ温度がＡｒ3 ＋１２０
℃以上の場合には、必要以上に鋼板の強度が上昇するの
みならず、組織の粗大化が起こり、鋼板動的変形抵抗の
上昇を阻害する。またこのような高温で熱延が完了され
た場合には鋼板の表面粗度が大きくなり、表面品位を落
とす。従って、熱延仕上げ温度の上限値をＡｒ3 ＋１２
０℃未満とする。Hot-rolling conditions: In the case of producing the steel sheet of the present invention as hot-rolled, a slab adjusted to a predetermined component is directly sent to a hot-rolling process as cast, or is cooled once and then cooled.
After reheating to the range of 000 ° C to 1300 ° C, hot rolling is performed. If the reheating temperature is lower than 1000 ° C., it becomes difficult to uniformly heat the slab, causing problems such as surface flaws. Therefore, the lower limit of the reheating temperature was set to 1000 ° C. On the other hand, if the reheating temperature is higher than 1300 ° C., the cost of the slab becomes high at the same time as the deformation of the slab becomes severe.
The upper limit was 00 ° C. When the hot-rolling finishing temperature (FT) is lower than the Ar 3 transformation temperature −10 ° C., a processed ferrite layer is formed on the surface layer of the steel sheet and in the vicinity thereof, thereby significantly deteriorating the workability and simultaneously reducing the dynamic workability. Low deformation resistance. Therefore, the lower limit of the hot rolling finish temperature is set to the Ar 3 transformation temperature −10 ° C. The hot rolling finish temperature is Ar 3 +120.
When the temperature is higher than ° C., not only the strength of the steel sheet is unnecessarily increased, but also the structure is coarsened, which hinders an increase in the dynamic deformation resistance of the steel sheet. Further, when the hot rolling is completed at such a high temperature, the surface roughness of the steel sheet increases, and the surface quality deteriorates. Therefore, the upper limit of the hot rolling finish temperature is set to Ar 3 +12.
It should be less than 0 ° C.
【００２７】熱延完了後に鋼板は冷却されるが、このと
きの冷却速度を５℃／秒未満もしくは１００℃／秒超と
することは、大量生産の工程条件上困難であることか
ら、これを下限、上限とした。また冷却の方法は一定の
冷却速度で行っても、途中で低冷却速度の領域を含むよ
うな複数種類の冷却速度の組み合わせであってもよい。
冷却後鋼板は巻き取り処理が行われるが、この時の巻き
取り温度が２５０℃未満ではマルテンサイトの生成が過
多となって加工性を損なうので下限を２５０℃とした。
また、熱延仕上げ温度（ＦＴ）がＡｒ3 ＋５０℃以上の
場合には、３８０℃以上で巻き取ると静的強度（ＴＳ）
に対する動的な変形抵抗（σdyn ）の値が小さくなるこ
とから、熱延仕上げ温度（ＦＴ）がＡｒ3 ＋５０℃以上
の場合には巻き取り温度を３８０℃未満とした。また、
熱延仕上げ温度（ＦＴ）がＡｒ3＋５０℃未満の場合に
は、動的変形抵抗σdyn が低くなる巻き取り温度が４２
０℃以上であったため、熱延仕上げ温度（ＦＴ）がＡｒ
3 ＋５０℃未満の場合には巻き取り温度を４２０℃未満
とした。最終的な鋼板の動的変形抵抗をより高めるため
には巻き取り温度の下限を３００℃とすることが望まし
い。After the completion of hot rolling, the steel sheet is cooled. However, it is difficult to set the cooling rate at this time to less than 5 ° C./sec or more than 100 ° C./sec because of mass production process conditions. The lower and upper limits were set. The cooling method may be performed at a constant cooling rate, or may be a combination of a plurality of types of cooling rates including a low cooling rate area on the way.
After cooling, the steel sheet is subjected to a winding process. If the winding temperature at this time is lower than 250 ° C., the formation of martensite becomes excessive and the workability is impaired, so the lower limit was set to 250 ° C.
When the hot rolling finish temperature (FT) is Ar 3 + 50 ° C. or higher, the static strength (TS) can be obtained by winding at 380 ° C. or higher.
When the hot-rolling finishing temperature (FT) is higher than Ar 3 + 50 ° C., the winding temperature is set to less than 380 ° C. because the value of the dynamic deformation resistance (σdyn) becomes smaller. Also,
When the hot rolling finishing temperature (FT) is lower than Ar 3 + 50 ° C., the winding temperature at which the dynamic deformation resistance σdyn becomes low is 42
0 ° C. or higher, the hot rolling finish temperature (FT) is Ar
3 When the temperature was lower than + 50 ° C., the winding temperature was lower than 420 ° C. In order to further increase the dynamic deformation resistance of the final steel sheet, it is desirable to set the lower limit of the winding temperature to 300 ° C.
【００２８】[0028]
＜実施例１＞表１に示す２５種類の鋼板を１２００℃に
加熱し、各鋼の成分からＡｒ3 ＝９０１−３２５×％Ｃ
＋３３×％Ｓｉ−９２×％Ｍｎｅｑの式（％Ｍｎｅｑ＝
％Ｍｎ＋％Ｎｉ／２＋％Ｃｒ／２＋％Ｃｕ／２＋％Ｍｏ
／２）で計算されるＡｒ3 変態温度＋５０℃〜Ａｒ3 変
態温度＋１００℃の範囲内で熱延を完了し、４５℃／秒
の冷却速度で冷却し、３５０℃〜３７０℃の範囲で巻き
取った。なお圧延完了後の板厚は３．０mmであった。こ
のようにして得られた熱延鋼板の熱延方向（Ｌ方向）と
これに直行する方向（Ｃ方向）に単軸引張りにより５％
の予変形を付加し、焼き付け処理を模擬するために１７
０℃×２０分の熱処理を行った後に鋼材の動的な特性を
調査し、予変形する前の静的な特性と比較した結果を表
２に示した。鋼の成分が本発明の範囲内のものについて
は表中の＊１の欄に示した値が正すなわち、目的通りσ
dyn が（０．７６６×ＴＳ＋２５０）以上であることが
わかる。 ＜実施例２＞表１に示した本発明の成分範囲内である鋼
Ｐ２を用いて、熱延条件、予変形条件及び熱処理条件、
を変化させた場合の特性を調査した結果を表３および表
４に示す。Ｐ２鋼のＡｒ3 変態温度は上記の式から７６
４℃と計算された。加熱温度は１２００℃一定とした。
熱延仕上げ温度（ＦＴ）がＡｒ3 ＋５０℃以上の８３０
℃の場合には、Ｎｏ．１，４，５では巻き取り温度が本
発明の範囲外であるために所定の動的変形抵抗σdyn が
得られていない。また、Ｎｏ．６では、熱延仕上げ温度
（ＦＴ）が本発明の範囲外であるために結果的に残留オ
ーステナイト粒径とフェライト粒径の比が０．６よりも
大きくなり、所定の動的変形抵抗σdynが得られていな
い。他の例はすべて本発明の例であり、熱延仕上げ温
度、巻き取り温度、予変形量が本発明の範囲内であれ
ば、予変形付与の形態や予変形後の加工硬化処理（ＢＨ
処理：１７０℃×２０分の熱処理）の有無に関わらず表
３の＊１の欄の値が正、すなわち、所定の動的変形抵抗
σdyn が得られることがわかる。ここで、Ｌ方向とは熱
延と同一の方向を指し、Ｃ方向はこれと直行する方向を
指す。<Example 1> 25 kinds of steel sheets shown in Table 1 were heated to 1200 ° C, and Ar 3 = 901-325 ×% C was determined from the components of each steel.
+ 33 ×% Si−92 ×% Mneq (% Mneq =
% Mn +% Ni / 2 +% Cr / 2 +% Cu / 2 +% Mo
/ 2) The hot rolling is completed within the range of the Ar 3 transformation temperature + 50 ° C. to the Ar 3 transformation temperature + 100 ° C., cooled at a cooling rate of 45 ° C./sec, and wound in the range of 350 ° C. to 370 ° C. I took it. The thickness after rolling was 3.0 mm. In the hot-rolled steel sheet thus obtained, 5% by uniaxial tension in the hot-rolling direction (L direction) and the direction perpendicular thereto (C direction).
17 to add the pre-deformation of
After heat treatment at 0 ° C. for 20 minutes, the dynamic characteristics of the steel material were investigated, and the results of comparison with the static characteristics before pre-deformation are shown in Table 2. When the steel composition is within the range of the present invention, the value shown in the column of * 1 in the table is positive, that is, σ
It can be seen that dyn is (0.766 × TS + 250) or more. <Example 2> Using steel P2 within the component range of the present invention shown in Table 1, hot rolling conditions, pre-deformation conditions and heat treatment conditions,
Tables 3 and 4 show the results of investigating the characteristics in the case where is changed. The Ar 3 transformation temperature of the P2 steel is 76 from the above equation.
Calculated as 4 ° C. The heating temperature was constant at 1200 ° C.
830 with hot rolling finishing temperature (FT) of Ar 3 + 50 ° C. or more
° C. In Examples 1, 4, and 5, the predetermined dynamic deformation resistance σdyn was not obtained because the winding temperature was outside the range of the present invention. In addition, No. In No. 6, since the hot-rolling finishing temperature (FT) is out of the range of the present invention, the ratio between the retained austenite grain size and the ferrite grain size becomes larger than 0.6, and the predetermined dynamic deformation resistance σdyn becomes smaller. Not obtained. All other examples are examples of the present invention. If the hot-rolling finishing temperature, the winding temperature, and the amount of pre-deformation are within the range of the present invention, the form of pre-deformation imparting and the work hardening treatment after pre-deformation (BH
Regardless of the presence or absence of (treatment: heat treatment at 170 ° C. × 20 minutes), the value in the column of * 1 in Table 3 is positive, that is, a predetermined dynamic deformation resistance σdyn can be obtained. Here, the L direction indicates the same direction as that of hot rolling, and the C direction indicates a direction perpendicular to the direction.
【００２９】[0029]
【表１】 [Table 1]
【００３０】[0030]
【表２】 [Table 2]
【００３１】[0031]
【表３】 [Table 3]
【００３２】[0032]
【表４】 [Table 4]
【００３３】[0033]
【発明の効果】本発明により、自動車の軽量化と衝突安
全性の確保の要求に応えることのできる高い動的変形抵
抗を有する高強度熱延鋼板を確実に提供することができ
る。According to the present invention, it is possible to reliably provide a high-strength hot-rolled steel sheet having high dynamic deformation resistance and capable of meeting the demands for reducing the weight of an automobile and ensuring collision safety.
【図面の簡単な説明】[Brief description of the drawings]
【図１】本発明における、衝突時の衝撃エネルギー吸収
能の指標である、５×１０2 〜５×１０3 （１／ｓ）の
歪み速度範囲で変形した時の３〜１０％の相当歪み範囲
における変形応力の平均値σdyn と静的な素材強度との
関係を示す図である。FIG. 1 is an equivalent strain of 3 to 10% when deformed in a strain rate range of 5 × 10 2 to 5 × 10 3 (1 / s), which is an index of impact energy absorption capacity at the time of collision in the present invention. FIG. 9 is a diagram showing a relationship between an average value σdyn of deformation stress in a range and static material strength.
Claims (10)
以下、ＳｉとＡｌの一方または双方を合計で０．５％以
上３．０％以下、Ｍｎ，Ｎｉ，Ｃｒ，Ｃｕ，Ｍｏの１種
または２種以上を合計で０．５％以上３．５％以下含
み、残部がＦｅ及び不可避的不純物からなり、最終的に
得られる熱延鋼板のミクロ組織がフェライトおよびベイ
ナイトを含み、このいずれかを主相とし、体積分率で３
％以上の残留オーステナイトを含む第３相との複合組織
であり、前記残留オーステナイト中の固溶〔Ｃ〕と鋼材
の平均Ｍｎ等量｛Ｍｎｅｑ＝Ｍｎ＋（Ｎｉ＋Ｃｒ＋Ｃｕ
＋Ｍｏ）／２｝によって決まる値（Ｍ＝６７８−４２８
×〔Ｃ〕−３３×Ｍｎｅｑ）が７０以上２５０以下で、
前記熱延鋼板に相当歪みで０％超１０％以下の予変形を
与えた後、５×１０2 〜５×１０3 （１／ｓ）の歪み速
度範囲で変形した時の３〜１０％の相当歪み範囲におけ
る変形応力の平均値：σdyn (MPa) が予変形を与える前
の５×１０-4〜５×１０-3（１／ｓ）の歪み速度範囲で
測定された静的な引張り試験における最大応力ＴＳ(MP
a) によって表現される式：σdyn ≧０．７６６×ＴＳ
＋２５０を満足することを特徴とする高い動的変形抵抗
を有する高強度熱延鋼板。C: 0.04% to 0.3% by weight
Hereinafter, one or both of Si and Al are 0.5% or more and 3.0% or less in total, and one or two or more of Mn, Ni, Cr, Cu, and Mo are 0.5% or more and 3.5 in total. %, The balance being Fe and unavoidable impurities, and the microstructure of the finally obtained hot-rolled steel sheet contains ferrite and bainite.
% Or more of the third phase containing retained austenite, and the solid solution [C] in the retained austenite and the average Mn equivalent of steel material 材 Mneq = Mn + (Ni + Cr + Cu)
+ Mo) / 2} (M = 678-428)
× [C] −33 × Mneq) is 70 or more and 250 or less,
After giving a pre-deformation of more than 0% and not more than 10% with a considerable strain to the hot-rolled steel sheet, 3-10% when deformed in a strain rate range of 5 × 10 2 to 5 × 10 3 (1 / s). Mean value of deformation stress in equivalent strain range: Static tensile test measured in a strain rate range of 5 × 10 −4 to 5 × 10 −3 (1 / s) before σdyn (MPa) gives pre-deformation. Stress TS (MP
Expression represented by a): σdyn ≧ 0.766 × TS
A high-strength hot-rolled steel sheet having high dynamic deformation resistance, which satisfies +250.
計で０．３重量％以下更に含むことを特徴とする請求項
１に記載の高い動的変形抵抗を有する高強度熱延鋼板。2. The high-strength hot-rolled steel having high dynamic deformation resistance according to claim 1, further comprising one or more of Nb, Ti, and V in a total amount of 0.3% by weight or less. steel sheet.
徴とする請求項１または２記載の高い動的変形抵抗を有
する高強度熱延鋼板。3. The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to claim 1, further comprising 0.2% by weight or less of P.
特徴とする請求項１〜３のいずれか１項に記載の高い動
的変形抵抗を有する高強度熱延鋼板。4. The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to claim 1, further comprising B in an amount of 0.01% by weight or less.
鋼材の残留オーステナイト体積分率が２．５％超であ
り、かつ、予変形前の残留オーステナイト体積分率と予
変形後の残留オーステナイト体積分率の比が０．３以上
であることを特徴とする請求項１〜４のいずれか１項に
記載の高い動的変形抵抗を有する高強度熱延鋼板。5. A steel material after a predeformation of more than 0% and 10% or less has a retained austenite volume fraction of more than 2.5%, and a residual austenite volume fraction before predeformation and after predeformation. The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to any one of claims 1 to 4, wherein a ratio of a retained austenite volume fraction of the steel sheet is 0.3 or more.
中の残留オーステナイトの平均粒径と、主相であるフェ
ライトもしくはベイナイトの平均粒径の比が０．６以下
であることを特徴とする請求項１〜５のいずれか１項に
記載の高い動的変形抵抗を有する高強度熱延鋼板。6. The ratio of the average grain size of retained austenite in the microstructure of the finally obtained hot rolled steel sheet to the average grain size of ferrite or bainite as a main phase is 0.6 or less. The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to any one of claims 1 to 5.
以下、ＳｉとＡｌの一方または双方を合計で０．５％以
上３．０％以下、Ｍｎ，Ｎｉ，Ｃｒ，Ｃｕ，Ｍｏの１種
または２種以上を合計で０．５％以上３．５％以下含
み、残部がＦｅ及び不可避的不純物からなる鋳造スラブ
を、鋳造ままで熱延工程へ直送し、もしくは一旦冷却し
た後に１０００℃〜１３００℃の範囲に再度加熱した
後、熱延をＡｒ3 変態温度−１０℃以上Ａｒ3 変態温度
＋１２０℃未満の温度（熱延仕上げ温度ＦＴ）で完了
し、その後５℃／秒以上１００℃／秒以下の冷却速度で
冷却し、巻き取る際に、前記熱延仕上げ温度がＡｒ3 変
態温度＋５０℃以上の場合には２５０℃以上３８０℃未
満の温度で巻き取り、前記熱延仕上げ温度がＡｒ3 変態
温度＋５０℃未満の場合には２５０℃以上４２０℃未満
で巻き取ることを特徴とする、最終的に得られる熱延鋼
板のミクロ組織がフェライトおよびベイナイトを含み、
このいずれかを主相とし、体積分率で３％以上の残留オ
ーステナイトを含む第３相との複合組織であり、残留オ
ーステナイト中の固溶〔Ｃ〕とスラブの平均Ｍｎ等量
｛Ｍｎｅｑ＝Ｍｎ＋（Ｎｉ＋Ｃｒ＋Ｃｕ＋Ｍｏ）／２｝
によって決まる値（Ｍ＝６７８−４２８×〔Ｃ〕−３３
×Ｍｎｅｑ）が７０以上２５０以下で、その鋼材に相当
歪みで０％超１０％以下の予変形を与えた後、５×１０
2 〜５×１０3 （１／ｓ）の歪み速度範囲で変形した時
の３〜１０％の相当歪み範囲における変形応力の平均
値：σdyn (MPa) が予変形を与える前の５×１０-4〜５
×１０-3（１／ｓ）の歪み速度範囲で測定された静的な
引張り試験における最大応力ＴＳによって表現される
式：σdyn ≧０．７６６×ＴＳ＋２５０を満足する高い
動的変形抵抗を有する高強度熱延鋼板の製造方法。7. C: 0.04% to 0.3% by weight
Hereinafter, one or both of Si and Al are 0.5% or more and 3.0% or less in total, and one or two or more of Mn, Ni, Cr, Cu, and Mo are 0.5% or more and 3.5 in total. % or less includes, after the balance was heated cast slab consisting of Fe and unavoidable impurities, and direct the hot rolling step while casting, or once again to the range of 1000 ° C. to 1300 ° C. after cooling, the hot rolled Ar 3 Transformation temperature: Completed at a temperature of −10 ° C. or more and an Ar 3 transformation temperature of less than + 120 ° C. (hot rolling finishing temperature FT), and then cooled at a cooling rate of 5 ° C./sec to 100 ° C./sec. hot rolling finishing temperature is wound at a temperature of 380 lower than ° C. 250 ° C. or higher in the case of more than Ar 3 transformation temperature + 50 ℃, 420 ° C. 250 ° C. or higher in the case where the hot-rolling finishing temperature is lower than Ar 3 transformation temperature + 50 ℃ Characterized by winding up with , The microstructure of the finally obtained hot-rolled steel sheet comprises a ferrite and bainite,
A composite structure of any one of the main phases and a third phase containing retained austenite in a volume fraction of 3% or more, wherein the solid solution [C] in the retained austenite and the average Mn equivalent of the slab ｛Mneq = Mn + (Ni + Cr + Cu + Mo) / 2｝
(M = 678-428 × [C] -33)
× Mneq) is 70 or more and 250 or less, and after giving a predeformation of more than 0% and 10% or less with considerable strain to the steel material, 5 × 10
The average value of the deformation stress in the equivalent strain range of 3 to 10% when deformed at the strain rate range of 2 to 5 × 10 3 (1 / s): 5 × 10 − before σdyn (MPa) gives the pre-deformation. 4 to 5
A formula having a high dynamic deformation resistance that satisfies σdyn ≧ 0.766 × TS + 250, which is expressed by a maximum stress TS in a static tensile test measured in a strain rate range of × 10 −3 (1 / s). Manufacturing method of high strength hot rolled steel sheet.
計で０．３％以下更に含むことを特徴とする請求項７に
記載の高い動的変形抵抗を有する高強度熱延鋼板の製造
方法。8. The high-strength hot-rolled steel sheet having high dynamic deformation resistance according to claim 7, further comprising 0.3% or less in total of one or more of Nb, Ti, and V. Manufacturing method.
徴とする請求項７または８に記載の高い動的変形抵抗を
有する高強度熱延鋼板の製造方法。9. The method for producing a high-strength hot-rolled steel sheet having high dynamic deformation resistance according to claim 7, further comprising 0.2% by weight or less of P.
を特徴とする請求項７〜９のいずれか１項に記載の高い
動的変形抵抗を有する高強度熱延鋼板の製造方法。10. The method for producing a high-strength hot-rolled steel sheet having high dynamic deformation resistance according to any one of claims 7 to 9, further comprising B in an amount of 0.01% by weight or less.
Priority Applications (17)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25888797A JP3530355B2 (en) | 1997-09-24 | 1997-09-24 | High-strength hot-rolled steel sheet with high dynamic deformation resistance for impact absorption at the time of collision and manufacturing method thereof |
| CA002273334A CA2273334C (en) | 1996-11-28 | 1997-11-28 | High strength steels having high impact energy absorption properties and a method for producing the same |
| KR1019997004657A KR100318213B1 (en) | 1996-11-28 | 1997-11-28 | High-strength steel plate having high dynamic deformation resistance and method of manufacturing the same |
| EP97913471.5A EP0952235B2 (en) | 1996-11-28 | 1997-11-28 | Method for producing high-strength steels having high impact energy absorption properties |
| CN97180921A CN1078623C (en) | 1996-11-28 | 1997-11-28 | High-strength steel having high impact energy absorption power and method for mfg. same |
| PCT/JP1997/004359 WO1998023785A1 (en) | 1996-11-28 | 1997-11-28 | High-strength steel plate having high dynamic deformation resistance and method of manufacturing the same |
| AU50679/98A AU711873B2 (en) | 1996-11-28 | 1997-11-28 | High-strength steels having high impact energy absorption properties and a method for producing the same |
| TW086117962A TW384313B (en) | 1996-11-28 | 1997-11-28 | High strength steels having high impact energy absorption properties and a method for producing the same |
| EP10181458A EP2314730B1 (en) | 1996-11-28 | 1997-11-28 | High-strength steels having high impact energy absorption properties. |
| PCT/JP1998/000272 WO1998032889A1 (en) | 1997-01-29 | 1998-01-23 | High-strength steel sheet highly resistant to dynamic deformation and excellent in workability and process for the production thereof |
| AU55767/98A AU716203B2 (en) | 1997-01-29 | 1998-01-23 | High strength steels having excellent formability and high impact energy absorption properties, and a method for production the same |
| US09/355,435 US6544354B1 (en) | 1997-01-29 | 1998-01-23 | High-strength steel sheet highly resistant to dynamic deformation and excellent in workability and process for the production thereof |
| CA002278841A CA2278841C (en) | 1997-01-29 | 1998-01-23 | High strength steels having excellent formability and high impact energy absorption properties, and a method for producing the same |
| KR1019997006826A KR100334948B1 (en) | 1997-01-29 | 1998-01-23 | High-strength steel sheet highly resistant to dynamic deformation and excellent in workability and process for the production thereof |
| EP98900718.2A EP0974677B2 (en) | 1997-01-29 | 1998-01-23 | A method for producing high strength steels having excellent formability and high impact energy absorption properties |
| EP10181439A EP2312008B1 (en) | 1997-01-29 | 1998-01-23 | High-strength steels having high impact energy absorption properties. |
| CN98802157A CN1072272C (en) | 1997-01-29 | 1998-01-23 | High-strength steel sheet highly resistant to dynamic deformation and excellent in workability and process for production thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25888797A JP3530355B2 (en) | 1997-09-24 | 1997-09-24 | High-strength hot-rolled steel sheet with high dynamic deformation resistance for impact absorption at the time of collision and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11100640A true JPH11100640A (en) | 1999-04-13 |
| JP3530355B2 JP3530355B2 (en) | 2004-05-24 |
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| JP25888797A Expired - Fee Related JP3530355B2 (en) | 1996-11-28 | 1997-09-24 | High-strength hot-rolled steel sheet with high dynamic deformation resistance for impact absorption at the time of collision and manufacturing method thereof |
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| JP (1) | JP3530355B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2060646A1 (en) * | 2006-12-27 | 2009-05-20 | Nippon Steel & Sumikin Stainless Steel Corporation | Stainless steel sheet for structural members excellent in impact -absorbing characteristics |
| WO2014073084A1 (en) * | 2012-11-08 | 2014-05-15 | Ｊｆｅスチール株式会社 | Impact absorbing member |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3619357B2 (en) * | 1997-12-26 | 2005-02-09 | 新日本製鐵株式会社 | High strength steel sheet having high dynamic deformation resistance and manufacturing method thereof |
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| JPS6479345A (en) * | 1987-06-03 | 1989-03-24 | Nippon Steel Corp | High-strength hot rolled steel plate excellent in workability and its production |
| JPH01184226A (en) * | 1988-01-14 | 1989-07-21 | Kobe Steel Ltd | Production of steel sheet having high-ductility high-strength multiple structure |
| JPH0762485A (en) * | 1993-08-25 | 1995-03-07 | Nippon Steel Corp | High strength steel plate excellent in workability and fatigue property and its production method |
| JPH07207413A (en) * | 1994-01-12 | 1995-08-08 | Nippon Steel Corp | Cold rolled steel sheet of high-strength composite structure having excellent workability and tensile strength of 45 to 65kgf/mm2 and its production |
| JPH07252592A (en) * | 1994-03-15 | 1995-10-03 | Nippon Steel Corp | Hot rolled high strength steel sheet excellent in formability, low temperature toughness and fatigue property |
| WO1995029268A1 (en) * | 1994-04-26 | 1995-11-02 | Nippon Steel Corporation | High-strength steel sheet adapted for deep drawing and process for producing the same |
| JPH09241788A (en) * | 1996-03-04 | 1997-09-16 | Kawasaki Steel Corp | High tensile strength steel plate excellent in impact resistance and its production |
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- 1997-09-24 JP JP25888797A patent/JP3530355B2/en not_active Expired - Fee Related
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6479345A (en) * | 1987-06-03 | 1989-03-24 | Nippon Steel Corp | High-strength hot rolled steel plate excellent in workability and its production |
| JPH01184226A (en) * | 1988-01-14 | 1989-07-21 | Kobe Steel Ltd | Production of steel sheet having high-ductility high-strength multiple structure |
| JPH0762485A (en) * | 1993-08-25 | 1995-03-07 | Nippon Steel Corp | High strength steel plate excellent in workability and fatigue property and its production method |
| JPH07207413A (en) * | 1994-01-12 | 1995-08-08 | Nippon Steel Corp | Cold rolled steel sheet of high-strength composite structure having excellent workability and tensile strength of 45 to 65kgf/mm2 and its production |
| JPH07252592A (en) * | 1994-03-15 | 1995-10-03 | Nippon Steel Corp | Hot rolled high strength steel sheet excellent in formability, low temperature toughness and fatigue property |
| WO1995029268A1 (en) * | 1994-04-26 | 1995-11-02 | Nippon Steel Corporation | High-strength steel sheet adapted for deep drawing and process for producing the same |
| JPH09241788A (en) * | 1996-03-04 | 1997-09-16 | Kawasaki Steel Corp | High tensile strength steel plate excellent in impact resistance and its production |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2060646A1 (en) * | 2006-12-27 | 2009-05-20 | Nippon Steel & Sumikin Stainless Steel Corporation | Stainless steel sheet for structural members excellent in impact -absorbing characteristics |
| EP2060646A4 (en) * | 2006-12-27 | 2014-01-01 | Nippon Steel & Sumikin Sst | Stainless steel sheet for structural members excellent in impact -absorbing characteristics |
| WO2014073084A1 (en) * | 2012-11-08 | 2014-05-15 | Ｊｆｅスチール株式会社 | Impact absorbing member |
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| Publication number | Publication date |
|---|---|
| JP3530355B2 (en) | 2004-05-24 |
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