JPH073328A - Production of high strength hot rolled steel sheet excellent in processability - Google Patents
Production of high strength hot rolled steel sheet excellent in processabilityInfo
- Publication number
- JPH073328A JPH073328A JP17259993A JP17259993A JPH073328A JP H073328 A JPH073328 A JP H073328A JP 17259993 A JP17259993 A JP 17259993A JP 17259993 A JP17259993 A JP 17259993A JP H073328 A JPH073328 A JP H073328A
- Authority
- JP
- Japan
- Prior art keywords
- austenite
- mass
- steel sheet
- strength
- retained austenite
- 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.)
- Pending
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、残留オーステナイト
を１０ｖｏｌ％以上含有する複合組織からなる加工性に
優れた熱延鋼板、特に引張強さが８００Ｎ／ｍｍ２級の
高強度熱延鋼板の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention This invention relates to a hot rolled steel sheet having a composite structure containing 10% by volume or more of retained austenite and having excellent workability, and particularly to the production of a high strength hot rolled steel sheet having a tensile strength of 800 N / mm 2. Regarding the method.
【０００２】[0002]
【従来の技術】近年、自動車業界においては車体重量の
軽減ひいては燃費の向上をはかるために高強度鋼板の需
要が急速に増加しつつあるが、素材の薄鋼板はプレス加
工等の冷間成形工程を経るのが通常であり、したがって
その際優れた冷間加工性を具備していることが要求され
る。2. Description of the Related Art In recent years, in the automobile industry, the demand for high-strength steel sheets is rapidly increasing in order to reduce the weight of vehicle bodies and thus improve fuel efficiency. However, thin steel sheets are used for cold forming processes such as press working. Therefore, it is required to have excellent cold workability.
【０００３】加工性の良好な熱延鋼板としては、フェラ
イトーマルテンサイト組織からなる高強度熱延鋼板が知
られている。この鋼板はフェライト相とマルテンサイト
および残留オーステナイト相の複合した組織をもち、そ
の機械的特性値は降伏比（降伏強度／引張強さ）が低
く、同じ延性では強度が高い特徴をもっている。As a hot rolled steel sheet having good workability, a high strength hot rolled steel sheet having a ferrite-martensite structure is known. This steel sheet has a composite structure of a ferrite phase, martensite, and retained austenite phase, and its mechanical characteristic values are characterized by a low yield ratio (yield strength / tensile strength) and high strength at the same ductility.
【０００４】このような複合組織をもつ高強度熱延鋼板
の製造方法としては、従来各種の方法が提案されてい
る。例えば、特開昭５５−９４４４４号公報には、表面
にスケールが付着したままのＣ含有量０．４質量％以上
の高炭素熱延鋼帯を６５０〜Ａ１点の温度域で５〜４０
時間焼鈍し、さらに熱処理を行うことにより、中心部に
ベイナイト相を、表層部に脱炭層を有する高強度高加工
性鋼板を製造する方法が、特開昭６０−４３４２５号公
報には、Ｃ０．３０〜０．５５質量％、Ｓｉ０．７〜
２．０質量％、Ｍｎ０．５〜２．０質量％を含有する鋼
をＡｒ３〜Ａｒ３＋５０℃の温度で仕上圧延を行い、４
５０〜６５０℃の温度域に４〜２０秒間保持し、３５０
℃の温度域で巻取る方法が提案されている。Various methods have been conventionally proposed as a method for producing a high-strength hot-rolled steel sheet having such a composite structure. For example, in JP-A-55-94444, a high carbon hot-rolled steel strip having a C content of 0.4% by mass or more with a scale attached to the surface thereof is 5-40 at a temperature range of 650-A 1 point.
A method for producing a high-strength and high-workability steel sheet having a bainite phase in the central portion and a decarburized layer in the surface layer portion by annealing for a long time and further heat treatment is disclosed in JP-A-60-43425, C0. 30 to 0.55 mass%, Si 0.7 to
Steel containing 2.0 mass% and Mn 0.5 to 2.0 mass% is finish-rolled at a temperature of Ar 3 to Ar 3 + 50 ° C., and 4
Hold in the temperature range of 50 to 650 ° C. for 4 to 20 seconds, 350
A method of winding in a temperature range of ℃ has been proposed.
【０００５】また、特開昭６０−１８４６６４号公報に
は、Ｃ０．１５〜０．８０質量％、Ｓｉ１．０〜３．０
質量％、Ｍｎ０．５〜３．０質量％を含有し、残留オー
ステナイト量が５〜１０ｖｏｌ％の高延性高張力鋼が提
案されている。Further, JP-A-60-184664 discloses that C0.15 to 0.80 mass% and Si1.0 to 3.0.
A high ductility high tensile steel containing 0.5% to 3.0% by mass of Mn and having a residual austenite amount of 5 to 10% by volume has been proposed.
【０００６】[0006]
【発明が解決しようとする課題】しかし、前記の熱延後
焼鈍する方法により得られる高強度高加工性鋼板は、Ｃ
含有量が０．４質量％以上あるいは０．３０質量％以上
と多いために溶接性が不足し、例えば自動車のホイール
ディスク等の素材としては適さない。また、残留オース
テナイト量が５〜１０ｖｏｌ％の高延性高張力鋼の場
合、任意添加元素であるＣｒを含有しないと残留オース
テナイト量を１０ｖｏｌ％以上に高めることができず、
伸びが不足する。However, the high-strength and high-workability steel sheet obtained by the method of annealing after hot rolling is C
Since the content is as large as 0.4% by mass or more or 0.30% by mass or more, the weldability is insufficient and, for example, it is not suitable as a material for wheel discs of automobiles. Further, in the case of a high ductility high tensile steel having a residual austenite amount of 5 to 10 vol%, the residual austenite amount cannot be increased to 10 vol% or more unless Cr, which is an optional addition element, is contained,
Insufficient growth.
【０００７】このように、従来の技術では、残留オース
テナイトを１０ｖｏｌ％以上含有し、引張強度が８００
Ｎ／ｍｍ２級の複合組織からなる加工性に優れた熱延鋼
板を製造することはできなかった。そこで、この発明
は、従来技術で得られなかった高強度、高加工性を備
え、自動車のホイールディスク等の素材として好適な、
残留オーステナイトを１０ｖｏｌ％以上含有し、引張強
度が８００Ｎ／ｍｍ２級の複合組織鋼板の製造方法を提
案しようとするものである。As described above, in the conventional technique, the residual austenite is contained in an amount of 10 vol% or more, and the tensile strength is 800.
It was not possible to manufacture a hot-rolled steel sheet having an N / mm 2 grade composite structure and excellent in workability. Therefore, the present invention has high strength and high workability that cannot be obtained by the prior art, and is suitable as a material for automobile wheel discs,
The present invention is intended to propose a method for producing a composite structure steel sheet containing 10 vol% or more of retained austenite and having a tensile strength of 800 N / mm 2 grade.
【０００８】[0008]
【課題を解決するための手段】この発明は、残留オース
テナイトの変態誘起塑性（ＴＲＩＰ効果）を利用するこ
とにより延性の優れた高強度鋼板を得ようとするもので
あり、通常の熱間圧延後フェライト＋オーステナイト二
相域に加熱保持することにより、フェライトを生成させ
てオーステナイト中にＣを濃化し、オーステナイトを安
定化させることにより残留オーステナイトを１０ｖｏｌ
％以上含有する伸びー強度バランスが極めて良好な高強
度高延性の熱延鋼板の製造を可能としたもので、その要
旨とするところは、Ｃ０．１０〜０．２０質量％、Ｓｉ
０．５０質量％以下、Ｍｎ３．０〜６．０質量％、Ａｌ
０．５０〜２．０質量％を含有し、残部実質的にＦｅお
よび不可避的不純物からなる鋼を熱間圧延した後、Ａｃ
１〜Ａｃ１＋５０℃のフェライト＋オーステナイト二相
域温度で１〜２０時間保持し、その後炉冷することを特
徴とするものである。The present invention is intended to obtain a high-strength steel sheet having excellent ductility by utilizing the transformation-induced plasticity (TRIP effect) of retained austenite. By maintaining the ferrite + austenite in the two-phase region by heating, ferrite is generated and C is concentrated in the austenite, and the austenite is stabilized, so that the residual austenite is 10 vol.
%, Which enables the production of a high-strength and high-ductility hot-rolled steel sheet having an extremely good elongation-strength balance, the gist of which is C0.10 to 0.20 mass%, Si
0.50 mass% or less, Mn 3.0 to 6.0 mass%, Al
After hot-rolling a steel containing 0.50 to 2.0 mass% and the balance consisting essentially of Fe and inevitable impurities, Ac
1 to Ac 1 + 50 ° C. ferrite + austenite two-phase region temperature is maintained for 1 to 20 hours, and then the furnace is cooled.
【０００９】[0009]
【作用】この発明における対象鋼の成分限定理由として
は、次の通りである。 Ｃ：０．１０〜０．２０質量％ Ｃはオーステナイト中に濃化することにより残留オース
テナイトを安定化させる効果を有するとともに、鋼の強
度向上に寄与する作用を有するが、０．１０質量％未満
では必要な強度が得られず、さらにオーステナイト中へ
のＣの濃化が不十分となり、残留オーステナイトを１０
ｖｏｌ％以上確保することが困難となる。他方０．２０
質量％を超えると溶接性が劣化する。このため、０．１
０〜０．１５質量％とした。The reason for limiting the composition of the subject steel in the present invention is as follows. C: 0.10 to 0.20 mass% C has the effect of stabilizing retained austenite by concentrating in austenite, and has the effect of contributing to the improvement of the strength of the steel, but less than 0.10 mass%. However, the required strength cannot be obtained, and the concentration of C in the austenite becomes insufficient.
It will be difficult to secure at least vol%. On the other hand 0.20
If it exceeds the mass%, the weldability will deteriorate. Therefore, 0.1
It was set to 0 to 0.15 mass%.
【００１０】Ｓｉ：０．５０質量％以下 Ｓｉは焼鈍の際にフェライト生成を促進し、オーステナ
イト中へのＣ濃化を促進する効果があるが、０．５０質
量％を超えるとＡｌ含有量との関係でフェライト生成促
進の効果が飽和するため、０．５０質量％以下とした。Si: 0.50% by mass or less Si has the effect of promoting the formation of ferrite during annealing and promoting the concentration of C in austenite. Therefore, the effect of accelerating the generation of ferrite is saturated, so the content was made 0.50 mass% or less.
【００１１】Ｍｎ：３．０〜６．０質量％ Ｍｎはオーステナイトの安定化に寄与する元素である
が、３．０質量％未満では残留オーステナイトを１０ｖ
ｏｌ％以上確保するのが困難である。一方、Ｍｎは焼入
性向上元素であるため、６．０質量％を超えるとフェラ
イトの生成が困難となり、その結果得られる組織がベイ
ナイト主体となり伸び性の劣化を招く。このため、Ｍｎ
含有量を３．０〜６．０質量％とした。Mn: 3.0 to 6.0 mass% Mn is an element that contributes to the stabilization of austenite, but if it is less than 3.0 mass%, residual austenite is 10 v.
It is difficult to secure ol% or more. On the other hand, since Mn is a hardenability-improving element, if it exceeds 6.0 mass%, it becomes difficult to form ferrite, and the resulting structure mainly consists of bainite, leading to deterioration of elongation. Therefore, Mn
Content was 3.0-6.0 mass%.
【００１２】Ａｌ：０．５０〜２．０質量％ Ａｌは製鋼段階での脱酸元素として鋼中に含まれるが、
Ｓｉと同様フェライト生成を促進してオーステナイト中
へのＣ濃化を促進する。しかしながら、０．５０質量％
未満ではその作用は十分に得られず、他方２．０質量％
を超えるとフェライト生成の促進効果が飽和するため、
０．５０〜２．０質量％以下とした。Al: 0.50 to 2.0 mass% Al is contained in the steel as a deoxidizing element in the steelmaking stage.
Like Si, it promotes ferrite formation and promotes C concentration in austenite. However, 0.50 mass%
If less than 2.0%, the effect is not sufficiently obtained, while 2.0% by mass
If it exceeds, the effect of promoting ferrite generation will be saturated,
It was 0.50 to 2.0 mass% or less.
【００１３】残留オーステナイト：１０ｖｏｌ％以上 この発明では残留オーステナイトのＴＲＩＰ効果により
優れた延性を得るものであるが、残留オーステナイト量
が１０ｖｏｌ％未満ではその効果が十分でないために優
れた延性が得られない。このため、この発明では残留オ
ーステナイト量を１０ｖｏｌ％以上と限定したのであ
る。なお、上限は特に限定するものではないが、残留オ
ーステナイト量が多過すぎるとオーステナイト中へのＣ
濃化が不足し、オーステナイトが不安定となるため応力
誘起変態を起し易くなり、ＴＲＩＰ効果による高い伸び
が得られなくなるおそれがあることを考慮すると、残留
オーステナイト量は５０ｖｏｌ％以下とすることが望ま
しい。Retained austenite: 10 vol% or more In the present invention, excellent ductility is obtained due to the TRIP effect of retained austenite, but if the amount of retained austenite is less than 10 vol%, excellent ductility cannot be obtained. . Therefore, in the present invention, the amount of retained austenite is limited to 10 vol% or more. The upper limit is not particularly limited, but if the amount of retained austenite is too large, C in the austenite is increased.
Considering that stress-induced transformation is likely to occur due to insufficient enrichment and instability of austenite, and high elongation due to the TRIP effect may not be obtained, the amount of retained austenite may be 50 vol% or less. desirable.
【００１４】次に、この発明では上記成分の鋼を熱間圧
延した後、焼鈍炉でＡｃ１〜Ａｃ１＋５０℃の温度範囲
にて１〜２０時間保持し、その後炉冷するが、焼鈍温度
をＡｃ１〜Ａｃ１＋５０℃としたのは、オーステナイト
を生成させるためにはＡｃ１以上の温度にすることが必
要であり、他方Ａｃ１＋５０℃を超えると生成するフェ
ライト量が少なくなり、オーステナイト量が多くなるた
めにオーステナイト中に濃化するＣ量が不足して残留オ
ーステナイトが安定せず、上記のＴＲＩＰ効果による高
い伸びが得られない。このため、焼鈍温度をＡｃ１〜Ａ
ｃ１＋５０℃に限定した。Next, in the present invention, after hot rolling the steel having the above-mentioned components, the steel is held in an annealing furnace in the temperature range of Ac 1 to Ac 1 + 50 ° C. for 1 to 20 hours and then cooled in the furnace. the was the Ac 1 ~Ac 1 + 50 ℃, in order to produce austenite is required to be in Ac 1 temperature above the other Ac 1 + 50 exceeds ° C. and ferrite amount is reduced to produce austenite Since the amount is large, the amount of C concentrated in austenite is insufficient, the retained austenite is not stable, and high elongation due to the TRIP effect cannot be obtained. Therefore, the annealing temperature is set to Ac 1 to A.
It was limited to c 1 + 50 ° C.
【００１５】また、焼鈍時間が１時間未満ではオーステ
ナイト中へのＣ濃化が不十分となり、残留オーステナイ
ト量を１０ｖｏｌ％以上とすることが困難であり、他
方、２０時間以上でも目的の鋼板を得ることはできる
が、エネルギーの効率が悪くなるため通常の焼鈍時間
（８〜２０時間）を考慮して２０時間を上限とした。If the annealing time is less than 1 hour, the concentration of C in austenite will be insufficient, and it will be difficult to make the residual austenite amount 10 vol% or more. On the other hand, even if it is 20 hours or more, the desired steel sheet will be obtained. However, since the energy efficiency deteriorates, the upper limit was 20 hours in consideration of the normal annealing time (8 to 20 hours).
【００１６】[0016]
【実施例】表１に示す化学成分を有する連続鋳造スラブ
（厚さ２２０〜３００ｍｍ）を通常の圧延条件（仕上温
度７５０〜９３０℃、巻取温度４００〜６００℃）で熱
間圧延した後、該熱延コイルを焼鈍炉でＡｃ１〜Ａｃ１
＋５０℃の温度範囲にて１〜２０時間保持し、その後炉
冷した。得られた鋼板の焼鈍条件とＸ線回析により測定
した残留オーステナイト量および機械的特性を表２に、
焼鈍温度と残留オーステナイト量およびＴＳ×Ｅｌの関
係を図１に、それぞれ示す。なお、鋼種Ｄ、Ｅ、Ｆ、
Ｇ、供試Ｎｏ．２５〜２８は、化学成分が本発明範囲外
のもの、供試Ｎｏ．６、１４、２２は、焼鈍温度をＡｃ
１未満とした例、供試Ｎｏ．８、１６、２４は焼鈍温度
をＡｃ１＋５０℃超えとした例、供試Ｎｏ．７、１５、
２３は焼鈍時間を１時間未満とした例をそれぞれ示す。EXAMPLE A continuous casting slab (thickness 220 to 300 mm) having the chemical composition shown in Table 1 was hot rolled under normal rolling conditions (finishing temperature 750 to 930 ° C., winding temperature 400 to 600 ° C.), Ac 1 to Ac 1 the heat-rolled coil annealing furnace
It was kept in the temperature range of + 50 ° C. for 1 to 20 hours and then cooled in the furnace. Table 2 shows the amount of retained austenite and the mechanical properties measured by X-ray diffraction, and the annealing conditions of the obtained steel sheet.
The relationship between the annealing temperature, the amount of retained austenite, and TS × El is shown in FIG. 1, respectively. Steel types D, E, F,
G, sample No. Nos. 25 to 28 have chemical components outside the scope of the present invention, and sample No. Nos. 6, 14, and 22 have an annealing temperature of Ac.
Example of less than 1 , test sample No. Nos. 8, 16, and 24 are examples in which the annealing temperature exceeded Ac 1 + 50 ° C., and sample No. 7, 15,
23 shows the example which made the annealing time less than 1 hour, respectively.
【００１７】表２に示す結果より明らかなごとく、化学
成分が本発明範囲の鋼でも焼鈍温度がＡｃ１未満の供試
Ｎｏ．６、１４、２２は、焼鈍温度がフェライトーオー
ステナイト二相域に入っていないためオーステナイト生
成量が少なく、そのため残留オーステナイト量も少な
く、その結果十分な伸びが得られずＴＳ×Ｅｌも低い値
となっている。また、同じく焼鈍時間が１時間未満の供
試Ｎｏ．７、１５、２３は、オーステナイト中へのＣ濃
化が不十分なため、残留オーステナイト量が低く、上記
のものと同様十分な伸びが得られずＴＳ×Ｅｌも低い値
となっている。さらに、焼鈍温度がＡｃ１＋５０℃超え
の供試Ｎｏ．８、１６、２４は、焼鈍温度が高すぎるこ
とによりフェライト生成量が少なくなり、オーステナイ
ト生成量が多くなるため、オーステナイト中へのＣの濃
化が不十分となり、オーステナイトが安定しない。その
結果、残留オーステナイト量は１３〜１５ｖｏｌ％程度
にとどまり、残留オーステナイトの安定度も低くなるた
め上記と同じく十分な伸びが得られずＴＳ×Ｅｌも低い
値となっている。As is clear from the results shown in Table 2, even in the steel having the chemical composition within the range of the present invention, the sample No. having the annealing temperature of less than Ac 1 was tested. In Nos. 6, 14, and 22, since the annealing temperature was not within the ferrite-austenite two-phase region, the amount of austenite formed was small, and therefore the amount of retained austenite was small, and as a result, sufficient elongation was not obtained and TS × El was low. Has become. Similarly, the sample No. with an annealing time of less than 1 hour was used. In Nos. 7, 15, and 23, the amount of retained austenite was low because the C concentration in austenite was insufficient, and similar to the above, sufficient elongation was not obtained and TS × El was also a low value. Further, the sample No. with the annealing temperature exceeding Ac 1 + 50 ° C. In Nos. 8, 16 and 24, since the amount of ferrite produced is reduced and the amount of austenite produced is increased due to the excessively high annealing temperature, the concentration of C in austenite is insufficient and austenite is not stable. As a result, the amount of retained austenite remains at about 13 to 15 vol%, and the stability of retained austenite is also low, so that sufficient elongation cannot be obtained and TS × El is also a low value as above.
【００１８】これに対し、本発明法はいずれも、残留オ
ーステナイトが１５〜２７ｖｏｌ％含まれ、ＴＳ×Ｅｌ
の値が２００００以上の強度ー伸びバランスの極めて良
好な高強度高延性の鋼板が得られた。On the other hand, in all the methods of the present invention, the residual austenite is contained in an amount of 15 to 27 vol%, and TS × El is contained.
A steel sheet with a high strength and a high ductility having a very good balance of strength and elongation was obtained.
【００１９】なお、図１より明らかなごとく、焼鈍温度
がＡｃ１未満では残留オーステナイト量が１０ｖｏｌ未
満となり、優れた伸びが得られない。また、焼鈍温度が
Ａｃ１＋５０℃を超えると、強度が上昇するとともに伸
びも低下し、優れた強度ー伸びバランスが得られない。As is clear from FIG. 1, when the annealing temperature is less than Ac 1 , the amount of retained austenite is less than 10 vol, and excellent elongation cannot be obtained. Further, when the annealing temperature exceeds Ac 1 + 50 ° C., the strength is increased and the elongation is decreased, and an excellent strength-elongation balance cannot be obtained.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】[0022]
【発明の効果】以上説明したごとく、この発明方法によ
れば、残留オーステナイトを１０ｖｏｌ％以上含有し、
強度×伸びが２００００以上の強度ー伸びバランスの優
れた熱延薄鋼板を、複雑な制御圧延を行うことなしに焼
鈍条件を限定することにより簡単に製造することができ
るという、優れた効果を奏する。As described above, according to the method of the present invention, the content of retained austenite is 10 vol% or more,
A hot rolled thin steel sheet having an excellent strength-elongation balance of strength and elongation of 20,000 or more can be easily manufactured by limiting the annealing conditions without performing complicated controlled rolling, which is an excellent effect. .
【図１】この発明の実施例における焼鈍温度と残留オー
ステナイト量およびＴＳ×Ｅｌの関係を示す図である。FIG. 1 is a diagram showing a relationship among an annealing temperature, an amount of retained austenite, and TS × El in an example of the present invention.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 38/00 ３０２ Ａ 38/06 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Office reference number FI technical display location C22C 38/00 302 A 38/06
Claims (1)
５０質量％以下、Ｍｎ３．０〜６．０質量％、Ａｌ０．
５０〜２．０質量％を含有し、残部実質的にＦｅおよび
不可避的不純物からなる鋼を熱間圧延した後、Ａｃ１〜
Ａｃ１＋５０℃のフェライト＋オーステナイト二相域温
度で１〜２０時間保持し、その後炉冷することを特徴と
する加工性に優れた高強度熱延鋼板の製造方法。1. C0.10 to 0.20 mass%, Si0.
50 mass% or less, Mn 3.0 to 6.0 mass%, Al0.
After hot-rolling a steel containing 50 to 2.0 mass% and the balance consisting essentially of Fe and inevitable impurities, Ac 1 to
A method for producing a high-strength hot-rolled steel sheet having excellent workability, which is characterized by holding the temperature of the ferrite + austenite two-phase region of Ac 1 + 50 ° C for 1 to 20 hours and then cooling the furnace.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17259993A JPH073328A (en) | 1993-06-18 | 1993-06-18 | Production of high strength hot rolled steel sheet excellent in processability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17259993A JPH073328A (en) | 1993-06-18 | 1993-06-18 | Production of high strength hot rolled steel sheet excellent in processability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH073328A true JPH073328A (en) | 1995-01-06 |
Family
ID=15944845
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17259993A Pending JPH073328A (en) | 1993-06-18 | 1993-06-18 | Production of high strength hot rolled steel sheet excellent in processability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH073328A (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0922777A1 (en) * | 1997-11-19 | 1999-06-16 | RECHERCHE ET DEVELOPPEMENT DU GROUPE COCKERILL SAMBRE, en abrégé: RD-CS | Flat product, such as sheet, made from ductile high-yield steel and process for manufacturing the same |
| WO2000003041A1 (en) * | 1998-07-08 | 2000-01-20 | Recherche Et Developpement Du Groupe Cockerill Sambre, Rd-Cs | Flat product, such as sheet metal, made of steel with high yield strength having good ductility and method for making same |
| US6395108B2 (en) | 1998-07-08 | 2002-05-28 | Recherche Et Developpement Du Groupe Cockerill Sambre | Flat product, such as sheet, made of steel having a high yield strength and exhibiting good ductility and process for manufacturing this product |
| US7381372B2 (en) | 2000-07-06 | 2008-06-03 | Sysmex Corporation | Sample suction apparatus |
| JP2014025091A (en) * | 2012-07-25 | 2014-02-06 | Nippon Steel & Sumitomo Metal | Steel material and manufacturing method therefor |
| WO2015102050A1 (en) * | 2014-01-06 | 2015-07-09 | 新日鐵住金株式会社 | Steel material and process for producing same |
| CN107354385A (en) * | 2017-07-11 | 2017-11-17 | 北京科技大学 | A kind of preparation method of automobile using superhigh-strength hot forming steel |
| US10266911B2 (en) | 2014-01-06 | 2019-04-23 | Nippon Steel & Sumitomo Metal Corporation | Hot-formed member and manufacturing method of same |
| CN112063931A (en) * | 2020-09-07 | 2020-12-11 | 清华大学 | Low-carbon medium-manganese high-residual-austenite high-toughness steel and heat treatment method thereof |
| JP2021518489A (en) * | 2018-03-30 | 2021-08-02 | エーケー スティール プロパティ−ズ、インク． | Low alloy 3rd generation advanced high-strength steel and manufacturing process |
-
1993
- 1993-06-18 JP JP17259993A patent/JPH073328A/en active Pending
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0922777A1 (en) * | 1997-11-19 | 1999-06-16 | RECHERCHE ET DEVELOPPEMENT DU GROUPE COCKERILL SAMBRE, en abrégé: RD-CS | Flat product, such as sheet, made from ductile high-yield steel and process for manufacturing the same |
| WO2000003041A1 (en) * | 1998-07-08 | 2000-01-20 | Recherche Et Developpement Du Groupe Cockerill Sambre, Rd-Cs | Flat product, such as sheet metal, made of steel with high yield strength having good ductility and method for making same |
| US6395108B2 (en) | 1998-07-08 | 2002-05-28 | Recherche Et Developpement Du Groupe Cockerill Sambre | Flat product, such as sheet, made of steel having a high yield strength and exhibiting good ductility and process for manufacturing this product |
| US7381372B2 (en) | 2000-07-06 | 2008-06-03 | Sysmex Corporation | Sample suction apparatus |
| US7867451B2 (en) | 2000-07-06 | 2011-01-11 | Sysmex Corporation | Sample suction apparatus |
| JP2014025091A (en) * | 2012-07-25 | 2014-02-06 | Nippon Steel & Sumitomo Metal | Steel material and manufacturing method therefor |
| WO2015102050A1 (en) * | 2014-01-06 | 2015-07-09 | 新日鐵住金株式会社 | Steel material and process for producing same |
| US10266911B2 (en) | 2014-01-06 | 2019-04-23 | Nippon Steel & Sumitomo Metal Corporation | Hot-formed member and manufacturing method of same |
| US10774405B2 (en) | 2014-01-06 | 2020-09-15 | Nippon Steel Corporation | Steel and method of manufacturing the same |
| CN107354385A (en) * | 2017-07-11 | 2017-11-17 | 北京科技大学 | A kind of preparation method of automobile using superhigh-strength hot forming steel |
| JP2021518489A (en) * | 2018-03-30 | 2021-08-02 | エーケー スティール プロパティ−ズ、インク． | Low alloy 3rd generation advanced high-strength steel and manufacturing process |
| CN112063931A (en) * | 2020-09-07 | 2020-12-11 | 清华大学 | Low-carbon medium-manganese high-residual-austenite high-toughness steel and heat treatment method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2807566B2 (en) | Austenitic high manganese steel having excellent formability, strength and weldability, and method for producing the same | |
| US7879160B2 (en) | Cold rolled dual-phase steel sheet | |
| EP2465962B1 (en) | High-strength steel sheets and processes for production of the same | |
| JP3292671B2 (en) | Hot-rolled steel strip for cold-rolled steel sheet with good deep drawability and aging resistance | |
| WO2005095663A1 (en) | High-rigidity high-strength thin steel sheet and method for producing same | |
| JPH0635619B2 (en) | Manufacturing method of high strength steel sheet with good ductility | |
| JPH073328A (en) | Production of high strength hot rolled steel sheet excellent in processability | |
| JPH07188834A (en) | High strength steel sheet having high ductility and its production | |
| JPH05311323A (en) | Dual-phase steel plate having high strength and high workability and production thereof | |
| JP2006097109A (en) | High-carbon hot-rolled steel sheet and manufacturing method therefor | |
| JPH1036911A (en) | Production of ferritic stainless steel excellent in surface characteristic | |
| JP3332172B2 (en) | High strength hot rolled steel sheet with excellent strength-stretch flange balance and strength-ductility balance | |
| JP2734842B2 (en) | High workability hot-rolled high-strength steel sheet and its manufacturing method | |
| JPH03170618A (en) | Highly efficient production of cold-rolled steel sheet extremely excellent in workability | |
| JP2004277789A (en) | High-strength and high-ductility cold-rolled steel sheet superior in secondary adhesiveness for hot salt water, and manufacturing method therefor | |
| JPH06179922A (en) | Production of high tensile strength steel sheet for deep drawing | |
| JPS63166931A (en) | Manufacture of high tension hot rolled steel sheet having high magnetic flux density | |
| JPH0665645A (en) | Production of high ductility hot rolled high tensile strength steel sheet | |
| JP2658706B2 (en) | Manufacturing method of high strength and high ductility cold rolled steel sheet with excellent aging resistance | |
| JP3774644B2 (en) | Steel plate for enamel excellent in workability, aging property and enamel characteristics and method for producing the same | |
| JP2981629B2 (en) | Method for manufacturing bake hardenable steel sheet with composite structure excellent in deep drawability | |
| JPS63179046A (en) | High-strength sheet metal excellent in workability and season cracking resistance and its production | |
| JP2790018B2 (en) | Manufacturing method of hot rolled steel sheet with excellent workability | |
| JP2017171979A (en) | High young modulus ultra-thin steel sheet excellent in deep drawability and manufacturing method therefor | |
| JPH03146640A (en) | High strength hot rolled steel sheet excellent in workability and its manufacture |