JPH04318150A - Light high strengch steel sheet for molding - Google Patents

Light high strengch steel sheet for molding

Info

Publication number
JPH04318150A
JPH04318150A JP10956191A JP10956191A JPH04318150A JP H04318150 A JPH04318150 A JP H04318150A JP 10956191 A JP10956191 A JP 10956191A JP 10956191 A JP10956191 A JP 10956191A JP H04318150 A JPH04318150 A JP H04318150A
Authority
JP
Japan
Prior art keywords
less
steel
added
steel sheet
formability
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.)
Granted
Application number
JP10956191A
Other languages
Japanese (ja)
Other versions
JP2517492B2 (en
Inventor
Hiroyuki Tsunoda
角田 浩之
Katsumi Tanigawa
谷川 克己
Yoshihiro Hosoya
佳弘 細谷
Akihiko Nishimoto
昭彦 西本
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Engineering Corp
Original Assignee
NKK Corp
Nippon Kokan Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by NKK Corp, Nippon Kokan Ltd filed Critical NKK Corp
Priority to JP3109561A priority Critical patent/JP2517492B2/en
Publication of JPH04318150A publication Critical patent/JPH04318150A/en
Application granted granted Critical
Publication of JP2517492B2 publication Critical patent/JP2517492B2/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

PURPOSE:To improve moldability together with to make a steel plate light in weight and to make have high strength by specifying contents of C, Si, Mn, P and S and, moreover, specifying an adding content of Al. CONSTITUTION:A component of this steel sheet is to be 0.02-0.1% C, <=0.5% Si, 0.2-2.0% Mn, <=0.05% P, <=0.01% S, 0.5-5.0% Al and residue consisting of Fe and inevitable impurities. But a condition 4.2/Al>=(15XC+Mn+0.7)/Al>=0.7 is to be satisfied. A steel sheet having 0.5-3mm thickness and <=7.75g/cm<2> density is manufactured by controlling the condition of rolling, annealing etc.

Description

【発明の詳細な説明】[Detailed description of the invention]

【0001】0001

【産業上の利用分野】本発明は、主として自動車車体に
使用される、成形性に優れ、高強度でしかも軽量な鋼板
に関するものである。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel plate which is excellent in formability, has high strength and is lightweight, which is mainly used for automobile bodies.

【0002】0002

【従来の技術】近年、地球環境保全の見地から自動車の
燃費向上が望まれており、その達成を目的として車体を
軽量化しようとする動きが活発になっている。
BACKGROUND OF THE INVENTION In recent years, it has been desired to improve the fuel efficiency of automobiles from the viewpoint of global environmental conservation, and there has been an active movement toward reducing the weight of automobile bodies in order to achieve this goal.

【0003】車体軽量化の考え方としては、車体構造の
最適化と素材自身の軽量化の二つが挙げられるが、素材
自身の軽量化の方法としては、車体用鋼板の高強度化に
よる薄肉化、アルミニウムなどの低比重金属の使用、プ
ラスチックなどの軽量素材、FRP、ラミネート鋼板な
どの複合材料の適用がなされている。
[0003] There are two ways to reduce the weight of a car body: optimizing the car body structure and reducing the weight of the material itself. Methods of reducing the weight of the material itself include making the steel plate for the car body thinner by increasing its strength, The use of low specific gravity metals such as aluminum, lightweight materials such as plastics, and composite materials such as FRP and laminated steel sheets are being applied.

【0004】0004

【発明が解決しようとする課題】しかしながら、車体剛
性、耐デント性、衝撃に対する強度は素材自身の強度よ
りも部品の板厚に大きく支配されるものであり、鋼板の
薄肉化には限界がある。また、アルミニウムは鋼に比べ
て成形性、溶接性などの点で劣っており、素材のコスト
も高いという難点がある。プラスチックは鋼ほどの強度
がないため、構造部材として使用することは不可能であ
り、リサイクルにも問題がある。更に、FRPは衝撃や
疲労に対する強度において信頼性が低く、ラミネート鋼
板はプレス加工時に剥離が生ずる可能性があるために、
曲げや絞りのきびしい部材への適用は困難である。
[Problem to be solved by the invention] However, the rigidity of the vehicle body, dent resistance, and strength against impact are largely controlled by the thickness of the parts rather than the strength of the material itself, and there is a limit to the thinning of steel plates. . Additionally, aluminum is inferior to steel in terms of formability, weldability, etc., and the cost of the material is also high. Plastics are not as strong as steel, so they cannot be used as structural members, and recycling is problematic. Furthermore, FRP has low reliability in terms of impact and fatigue strength, and laminated steel plates may peel during press processing.
It is difficult to apply it to members that are severely bent or drawn.

【0005】上記のように、従来の素材軽量化の考え方
では自動車車体部品に要求される特性をすべて満たすこ
とは不可能であり、部品製造コストの面でも問題があっ
た。本発明は、かかる事情に鑑みて成されたものであり
、強度、成形性及びコスト面に優れ、なおかつ薄肉化す
ることなしに軽量化を達成できる鋼板を提供しようとす
るものである。
[0005] As described above, with the conventional concept of material weight reduction, it is impossible to satisfy all the characteristics required for automobile body parts, and there are also problems in terms of parts manufacturing costs. The present invention has been made in view of the above circumstances, and aims to provide a steel plate that is excellent in strength, formability, and cost, and that can achieve weight reduction without thinning.

【0006】[0006]

【課題を解決するための手段】本発明者らは、鋼が高強
度であって、成形性およびコスト面において優れている
長所を活かし、しかも素材の軽量化を達成することにつ
いて検討を重ね、FeにAlを多量に添加して鋼板自体
を軽量化することに着目した。
[Means for Solving the Problems] The present inventors have repeatedly studied ways to take advantage of the advantages of steel, which is high strength, excellent formability and cost, and to achieve a reduction in the weight of the material. We focused on reducing the weight of the steel plate itself by adding a large amount of Al to Fe.

【0007】フェライト安定化元素であるAlを多量に
添加した鋼板は、電磁用の鋼板としては既に実用化され
ている。しかし、高Al化した場合はγ→α変態点が上
昇するため、熱延仕上温度を変態点以上とすることが困
難となり、さらに多量にAlを添加した場合はフェライ
ト単相組織となる。これらは、熱延板組織を粗粒化させ
最終製品組織の粗粒化を狙いとした電磁鋼板に対しては
好ましいが、良好な成形性を必要とする鋼板には不適と
なる。また、電磁鋼板の場合は電磁特性の向上を目的と
して〈100〉//ND集合組織を発達させるが、この
ような集合組織は鋼板の深絞り性に対しては好ましくな
い。さらに、電磁鋼板では磁気的なロスを少なくするた
めに板厚を薄くしており、これは先に述べた車体剛性、
耐デント性、衝撃に対する強度に関しては不利である。
Steel sheets to which a large amount of Al, which is a ferrite stabilizing element, is added have already been put into practical use as electromagnetic steel sheets. However, when the Al content is increased, the γ→α transformation point rises, making it difficult to raise the hot rolling finishing temperature above the transformation point, and when a large amount of Al is added, a ferrite single-phase structure results. These are preferable for electrical steel sheets aimed at coarsening the structure of the hot-rolled sheet and coarsening the structure of the final product, but are unsuitable for steel sheets that require good formability. Furthermore, in the case of electrical steel sheets, a <100>//ND texture is developed for the purpose of improving electromagnetic properties, but such a texture is unfavorable for the deep drawability of the steel sheet. Furthermore, the thickness of electromagnetic steel sheets is made thinner to reduce magnetic loss, which increases the rigidity of the car body and
It is disadvantageous in terms of dent resistance and impact strength.

【0008】本発明者らは以上の問題点を解決するため
に研究を重ねた結果、オーステナイト安定化元素を多量
に添加してAlとバランスさせることにより組織がフェ
ライト単相になるのを避け、熱延時の時のγ→α変態に
より熱延板の組織を細粒化させ、冷延、焼鈍後に成形性
に有利な<111>//ND集合組織を発達させること
によって、多量のAlを添加しても成形性を損なわず、
しかも軽量化を達成できること、また、熱延鋼板の場合
にもγ→α変態を利用して組織を整粒化させることによ
り成形性を向上させることができることを初めて見出し
、本発明に至ったもので以下の如くである。
[0008] As a result of repeated research by the present inventors to solve the above problems, we added a large amount of austenite stabilizing elements to balance it with Al, thereby avoiding the structure from becoming a single ferrite phase. A large amount of Al is added by making the structure of the hot rolled sheet finer by the γ→α transformation during hot rolling, and developing a <111>//ND texture that is advantageous for formability after cold rolling and annealing. without impairing formability even when
Moreover, it was discovered for the first time that weight reduction can be achieved, and that formability can be improved even in the case of hot-rolled steel sheets by using the γ→α transformation to regularize the structure, which led to the present invention. It is as follows.

【0009】(1)C:0.02〜0.1wt%、Si
:0.5wt%以下、Mn:0.2〜2.0wt%、P
:0.05wt%以下、S:0.01wt%以下、Al
:0.5〜5.0wt%、ただし、4.2/Al≧(1
5×C+Mn+0.7)/Al≧0.7を含有し、残部
がFe及び不可避的不純物より成り、板厚が0.5mm
以上3mm以下で、7.75g/cm3 以下の密度を
有することを特徴とする成形用軽量高強度鋼板。 (2)C:0.02〜0.1wt%、Si:0.5wt
%以下、Mn:0.2〜2.0wt%、P:0.05w
t%以下、S:0.01wt%以下、Al:0.5〜5
.0wt%、Ni:0.05〜1.0wt%、Cu:0
.05〜0.5wt%、ただし、4.2/Al≧(15
×C+Mn+Ni+2×Cu+0.7)/Al≧0.7
を含有し、残部がFe及び不可避的不純物より成り、板
厚が0.5mm以上3mm以下で、7.75g/cm3
 以下の密度を有することを特徴とする成形用軽量高強
度鋼板。 (3)Nb:0.05wt%以下、Ti:0.05wt
%以下、V:0.05wt%以下、Zr:0.05wt
%以下、B:0.005wt%以下のうちの1種又は2
種以上を合計で0.05wt%以下で含有することを特
徴とする上記(1)または(2)に記載の成形用軽量高
強度鋼板。
(1) C: 0.02 to 0.1 wt%, Si
: 0.5 wt% or less, Mn: 0.2 to 2.0 wt%, P
: 0.05wt% or less, S: 0.01wt% or less, Al
:0.5-5.0wt%, however, 4.2/Al≧(1
5×C+Mn+0.7)/Al≧0.7, the remainder consists of Fe and inevitable impurities, and the plate thickness is 0.5 mm.
A lightweight high-strength steel plate for forming, characterized in that it has a thickness of 3 mm or less and a density of 7.75 g/cm3 or less. (2) C: 0.02-0.1wt%, Si: 0.5wt
% or less, Mn: 0.2-2.0wt%, P: 0.05w
t% or less, S: 0.01wt% or less, Al: 0.5-5
.. 0wt%, Ni: 0.05-1.0wt%, Cu: 0
.. 05 to 0.5 wt%, provided that 4.2/Al≧(15
×C+Mn+Ni+2×Cu+0.7)/Al≧0.7
with the balance consisting of Fe and unavoidable impurities, the plate thickness is 0.5 mm or more and 3 mm or less, and 7.75 g/cm3
A lightweight high-strength steel plate for forming, characterized by having the following density: (3) Nb: 0.05wt% or less, Ti: 0.05wt
% or less, V: 0.05wt% or less, Zr: 0.05wt
% or less, B: 1 or 2 of 0.005 wt% or less
The lightweight, high-strength steel sheet for forming according to (1) or (2) above, characterized in that it contains at least 0.05 wt% of at least one type of carbon dioxide in total.

【0010】0010

【作用】上記したような本発明について、先ず本発明に
おける合金元素の限定理由は以下の如くである。
[Operation] Regarding the present invention as described above, first, the reasons for limiting the alloying elements in the present invention are as follows.

【0011】Alは、本発明においては最も重要な元素
であって、添加量が多いほど鋼の密度を低下させ、素材
の軽量化を促進することができる。従って、あまり少量
の添加では密度低減が少ないため、Alの下限を0.5
%とする。しかし、5.0%を越えて添加した場合、鋼
がフェライト単相になるのを避けるために過剰なオース
テナイト安定化元素を添加しなければならず、それによ
って成形性が著しく低下する。しかも、鋼が著しく脆化
するので冷間圧延する場合には割れが発生しやすいため
、冷延鋼板への適用は困難である。従って、Alの上限
は5.0%とする。
[0011] Al is the most important element in the present invention, and the greater the amount added, the lower the density of the steel, and the more weight reduction of the material can be promoted. Therefore, the lower limit of Al is set at 0.5 because the density reduction is small if too small a quantity is added.
%. However, when added in excess of 5.0%, excessive austenite stabilizing elements must be added to avoid the steel becoming a single ferrite phase, thereby significantly reducing formability. Moreover, since the steel becomes extremely brittle and cracks are likely to occur during cold rolling, it is difficult to apply it to cold rolled steel sheets. Therefore, the upper limit of Al is 5.0%.

【0012】Cは、オーステナイト安定化元素であり、
適量のC添加により熱間圧延時に鋼がγ→α変態を経る
ことを利用して組織を整粒化、細粒化できる。その結果
、熱延板の成形性が向上すると同時に、冷延後の焼鈍時
には粒界からの<111>//ND集合組織の核発生が
促進され、冷圧焼鈍板の成形性が改善される。Cが0.
02%以下であるとこれらの作用が現れない。一方、あ
まり多量に添加すると逆に集合組織が悪くなって成形性
が低下し、耐時効性も劣化する。従って上限を0.1%
とする。
C is an austenite stabilizing element,
By adding an appropriate amount of C, the steel undergoes γ→α transformation during hot rolling, which makes it possible to make the structure regular and fine-grained. As a result, the formability of the hot-rolled sheet is improved, and at the same time, nucleation of <111>//ND texture from grain boundaries is promoted during annealing after cold rolling, and the formability of the cold-rolled annealed sheet is improved. . C is 0.
If it is less than 0.02%, these effects will not appear. On the other hand, if it is added in too large a quantity, the texture will deteriorate, resulting in poor formability and aging resistance. Therefore, the upper limit is 0.1%
shall be.

【0013】Mnは、オーステナイト安定化元素であっ
て、Alを多量に添加したとき鋼がフェライト単相にな
るのを防ぐ重要な元素である。Cと同様、その効果を発
揮させるためには0.2%以上の添加を必須とする。但
し、過剰に添加するとやはり成形性が低下するので2.
0%以下に限定する。
Mn is an austenite stabilizing element and is an important element that prevents steel from becoming a single ferrite phase when a large amount of Al is added. Similar to C, addition of 0.2% or more is essential to exhibit its effect. However, if it is added in excess, the moldability will decrease, so 2.
Limited to 0% or less.

【0014】本発明においては、C、Mnをオーステナ
イト安定化元素のベースとしているが、Ni、Cuも有
効であり、これらの元素を複合して添加すると一層効果
的である。
In the present invention, C and Mn are used as the base elements for stabilizing austenite, but Ni and Cu are also effective, and it is even more effective to add a combination of these elements.

【0015】Niもオーステナイト安定化元素であり、
その作用を発揮させるには0.05%以上の添加を必要
とする。しかし、高価であるため過剰に添加するとコス
トアップを招くので、その上限を1.0%とする。
Ni is also an austenite stabilizing element,
In order to exhibit its effect, it is necessary to add 0.05% or more. However, since it is expensive, adding it in excess will increase the cost, so the upper limit is set at 1.0%.

【0016】Cuもオーステナイトを安定化する作用を
有し、0.05%以上添加しないとその作用は現れない
。 しかし、0.5%を超えて添加するとε相の析出により
成形性が低下する。従って、上限を0.5%とする。
[0016] Cu also has the effect of stabilizing austenite, and this effect does not appear unless it is added in an amount of 0.05% or more. However, if it is added in an amount exceeding 0.5%, formability deteriorates due to precipitation of the ε phase. Therefore, the upper limit is set at 0.5%.

【0017】上記したAl、C、Mn、Ni、Cuのバ
ランスは、本発明においては非常に重要である。なぜな
ら、Al添加量に対してオーステナイト安定化元素であ
るC、Mn、Ni、Cuが不足すると鋼がフェライト単
相組織となって、成形性が悪くなるからである。一方、
オーステナイト安定化元素が過剰になった場合もやはり
成形性が低下する。このことを避けるために、4.2/
Al≧(15×C+Mn+Ni+2×Cu+0.7)/
Al≧0.7を満たすようなAl、C、Mn、Ni、C
uバランスを保つ必要がある。図1に、この式とE1の
関係を表わすグラフを示すが、この図においてハッチン
グの施された範囲、即ち上記の式を満たし、且つC:0
.02〜0.1wt%、Mn:0.2〜2.0wt%、
Ni:0.05〜1.0wt%、Cu:0.05〜1.
0wt%、Al:0.5〜5.0wt%とすることによ
り好ましい成形性を得しめる。また、Ni、Cuを添加
しない場合には、4.2/Al≧(15×C+Mn+0
.7)/Al≧0.7を満たすようにC、Mnを添加す
ればよい。
The balance of Al, C, Mn, Ni, and Cu described above is very important in the present invention. This is because if the austenite stabilizing elements C, Mn, Ni, and Cu are insufficient relative to the amount of Al added, the steel becomes a ferrite single-phase structure, resulting in poor formability. on the other hand,
Excessive austenite stabilizing elements also reduce formability. To avoid this, 4.2/
Al≧(15×C+Mn+Ni+2×Cu+0.7)/
Al, C, Mn, Ni, C that satisfies Al≧0.7
u Need to maintain balance. FIG. 1 shows a graph showing the relationship between this formula and E1. In this figure, the hatched range corresponds to the range that satisfies the above formula and C: 0
.. 02-0.1 wt%, Mn: 0.2-2.0 wt%,
Ni: 0.05-1.0 wt%, Cu: 0.05-1.
By setting the content to 0 wt% and Al: 0.5 to 5.0 wt%, preferable moldability can be obtained. In addition, when Ni and Cu are not added, 4.2/Al≧(15×C+Mn+0
.. 7) C and Mn may be added so as to satisfy /Al≧0.7.

【0018】Siは、フェライト安定化元素であって、
オーステナイト安定化元素の効果を損なうので少ない方
がよく、しかも鋼を脆化させるため、その上限を0.5
%とする。0.1%以下とすれば一層好ましい。
[0018] Si is a ferrite stabilizing element,
Since it impairs the effect of the austenite stabilizing element, it is better to have less, and since it also makes the steel brittle, the upper limit should be set at 0.5.
%. It is more preferable to set it to 0.1% or less.

【0019】Pも、フェライト安定化元素であるが、そ
の作用はSiよりも大きいので添加量を一層少なくする
必要があり、0.05%を上限とする。できれば0.0
1%以下とするのがよい。
P is also a ferrite stabilizing element, but its action is greater than that of Si, so it is necessary to reduce the amount added, and the upper limit is 0.05%. Preferably 0.0
It is preferable to keep it at 1% or less.

【0020】Sは鋼の延性を著しく損ない、又スポット
溶接性も低下させるため0.01%以下に限定する。
[0020] S significantly impairs the ductility of steel and also reduces spot weldability, so it is limited to 0.01% or less.

【0021】本発明においてはNb、Ti、V、Zrを
添加することによって微細な炭窒化物がスラブ加熱時ま
たは熱間圧延時に析出し、その効果によって熱延板組織
をさらに細粒化できる。ただし、0.05%を越えて添
加すると、鋼のオーステナイト化に寄与するC量が不足
してしまう。また、Bも組織を細粒化する作用があるが
、0.005%を超えて添加しても効果は飽和してしま
う。 従って、Nb:0.05%以下、Ti:0.05%以下
、V:0.05%以下、Zr:0.05%以下、B:0
.005%以下として、合計の添加量の上限を0.05
%とする。
In the present invention, by adding Nb, Ti, V, and Zr, fine carbonitrides are precipitated during slab heating or hot rolling, and this effect makes it possible to further refine the grain structure of the hot rolled sheet. However, if added in excess of 0.05%, the amount of C that contributes to austenitization of steel will be insufficient. Further, B also has the effect of refining the structure, but the effect is saturated even if it is added in an amount exceeding 0.005%. Therefore, Nb: 0.05% or less, Ti: 0.05% or less, V: 0.05% or less, Zr: 0.05% or less, B: 0
.. 0.05% or less, and the upper limit of the total amount added is 0.05%.
%.

【0022】上記のような組成を有する鋼は、一般的に
は熱間圧延のみで、もしくはその後に冷間圧延および焼
鈍を施して鋼板とされる。この場合、熱間圧延を加熱温
度1200℃以下、圧下率50%以上、仕上温度はγ→
α変態点以上、巻取温度550〜750℃で行うことに
より一層好ましいTS−Elバランスが得られる。また
、冷間圧延時の圧下率は50%以上とするのが好ましい
。焼鈍は、連続焼鈍およびバッチ焼鈍のいずれで行なっ
ても構わないが、連続焼鈍は800℃以上、バッチ焼鈍
は700℃以上の焼鈍温度とすることにより<111>
//ND集合組織が発達しやすくなり、鋼板の成形性を
更に向上させることができる。
[0022] Steel having the above composition is generally made into a steel plate by only hot rolling or by subsequent cold rolling and annealing. In this case, hot rolling is carried out at a heating temperature of 1200°C or less, a reduction rate of 50% or more, and a finishing temperature of γ→
A more preferable TS-El balance can be obtained by carrying out the winding at a temperature higher than the α transformation point and a winding temperature of 550 to 750°C. Further, it is preferable that the rolling reduction during cold rolling is 50% or more. Annealing may be performed by either continuous annealing or batch annealing, but by setting the annealing temperature to 800 ° C. or higher for continuous annealing and 700 ° C. or higher for batch annealing, <111>
//The ND texture develops more easily, and the formability of the steel sheet can be further improved.

【0023】本発明では、鋼板の厚さは0.5mm以上
3mm以下とする。板厚を0.5mm以上とすることに
よって、車体などとした場合における剛性、耐デント性
、耐衝撃強度などを適切に確保し、またその上限を3m
mとすることにより、構造部材としての成形性を得しめ
るとともに軽量化を図るためである。
In the present invention, the thickness of the steel plate is 0.5 mm or more and 3 mm or less. By setting the plate thickness to 0.5 mm or more, we can ensure appropriate rigidity, dent resistance, impact resistance, etc. when used as a car body, and the upper limit is 3 m.
This is to achieve moldability as a structural member and to reduce weight by setting it to m.

【0024】また、密度を7.75g/cm3 以下と
することによって1%以上の密度低減率を得ることがで
き、鋼板としての強度を確保しながらなおかつ軽量化を
図らしめることができる。
Further, by setting the density to 7.75 g/cm 3 or less, it is possible to obtain a density reduction rate of 1% or more, and it is possible to reduce the weight while ensuring the strength of the steel plate.

【0025】[0025]

【実施例1】本発明によるものの具体的な実施例につい
て説明すると、本発明者らが具体的に採用した本発明例
および比較例による代表的な鋼の化学成分は次の表1に
示す如くであって、C2, C4, D2, D3, 
D4, D8,E2, E3, E4, E5, F2
, F3, G2, G3は本発明例であり、その他は
比較例である。
[Example 1] To explain a specific example according to the present invention, the chemical composition of typical steel according to the present invention example and comparative example specifically adopted by the present inventors is as shown in Table 1 below. and C2, C4, D2, D3,
D4, D8, E2, E3, E4, E5, F2
, F3, G2, and G3 are examples of the present invention, and the others are comparative examples.

【0026】[0026]

【表1】[Table 1]

【0027】前記した表1のような組成の鋼を溶製、鋳
造し、加熱温度1200℃、圧下率87%、仕上温度9
00〜950℃、巻取温度640〜700℃の熱間圧延
をなし、次いで圧下率80%で冷間圧延をなし、板厚0
.7mmの冷延板とした。又このようにして得られた冷
延板は850℃の連続焼鈍と1.0%の調圧を施して製
品となし、得られた製品について、その機械的特性と密
度を調査した結果は次の表2に示す如くであった。
[0027] Steel having the composition as shown in Table 1 was melted and cast, and the heating temperature was 1200°C, the reduction rate was 87%, and the finishing temperature was 9.
00 to 950°C and a coiling temperature of 640 to 700°C, followed by cold rolling at a reduction rate of 80% to obtain a plate with a thickness of 0.
.. It was made into a 7 mm cold rolled plate. In addition, the cold-rolled sheets thus obtained were subjected to continuous annealing at 850°C and pressure adjustment of 1.0% to produce products.The mechanical properties and density of the obtained products were investigated, and the results are as follows. The results were as shown in Table 2.

【0028】[0028]

【表2】[Table 2]

【0029】即ち表2の結果に示すように、本発明によ
る試料No. 4、6、9、10、11、15、18、
19、20、21、24、25、28、29は1%を越
え、2%以上の密度低減率を有しており、TSにおいて
も40Kgf/mm2 以上と良好である。またElは
30%以上、r値は1.0以上のものが得られている。
That is, as shown in the results in Table 2, sample No. 1 according to the present invention. 4, 6, 9, 10, 11, 15, 18,
Nos. 19, 20, 21, 24, 25, 28, and 29 have a density reduction rate of more than 1% and 2% or more, and the TS is also good at 40 Kgf/mm2 or more. Further, an El of 30% or more and an r value of 1.0 or more were obtained.

【0030】これに対し、比較例である試料No. 1
、2ではAl添加量が不足しているために軽量化の効果
が現れておらず、一方Al過剰の試料No. 31、3
2では冷間圧延時に割れが生じるので実用にはならない
。また、C、Mn、Ni、Cuが不足している試料No
. 3、8、17、23、27、及びC、Mn、Ni、
Cuが過剰である試料No. 7、16、22、26、
30ではElが大幅に低下しているのでプレス加工には
適さないことが明らかである。
On the other hand, sample No. 1, which is a comparative example, 1
In Sample No. 2, the weight reduction effect did not appear because the amount of Al added was insufficient, while in Sample No. 2 with excess Al. 31, 3
In No. 2, cracks occur during cold rolling, so it is not practical. In addition, sample No. lacking C, Mn, Ni, and Cu
.. 3, 8, 17, 23, 27, and C, Mn, Ni,
Sample No. with excess Cu. 7, 16, 22, 26,
It is clear that No. 30 is not suitable for press working because El is significantly reduced.

【0031】[0031]

【実施例2】前記した表1の鋼E2を、次の表3に示す
条件で熱間圧延、冷間圧延および焼鈍を施して板厚さ1
.0mmの冷延鋼板を製造した。1.0%の調圧を施し
た後の機械的特性を表4に示す。
[Example 2] Steel E2 in Table 1 above was hot rolled, cold rolled and annealed under the conditions shown in Table 3 below to give a plate thickness of 1.
.. A 0 mm cold rolled steel plate was manufactured. Table 4 shows the mechanical properties after applying 1.0% pressure adjustment.

【0032】[0032]

【表3】[Table 3]

【0033】[0033]

【表4】[Table 4]

【0034】表4より、熱間圧延を加熱温度1200℃
以下、圧下率50%以上、仕上温度γ→α変態点以上、
巻取温度550〜750℃で行い、冷間圧延時の圧下率
は50%以上、焼鈍は連続焼鈍の場合800℃以上、バ
ッチ焼鈍の場合700℃以上の焼鈍温度とすると、鋼板
の成形製を更に工場させることができることがわかる。
From Table 4, the heating temperature for hot rolling is 1200°C.
Below, the reduction rate is 50% or more, the finishing temperature is γ→α transformation point or more,
If the coiling temperature is 550 to 750°C, the rolling reduction during cold rolling is 50% or more, and the annealing temperature is 800°C or more for continuous annealing or 700°C or more for batch annealing, the forming of the steel sheet can be made. It turns out that it is possible to make more factories.

【0035】前記した表1の鋼を用いて、加熱温度11
60℃、圧下率90%、仕上温度890〜930℃、巻
取温度620〜710℃で熱間圧延を行い、板厚1.6
mmの熱延鋼板を製造した。これらの鋼板の機械的特性
を調査した結果を表5に示す。
[0035] Using the steel shown in Table 1 above, heating temperature 11
Hot rolling was performed at 60°C, rolling reduction rate of 90%, finishing temperature of 890-930°C, and coiling temperature of 620-710°C, resulting in a plate thickness of 1.6
A hot-rolled steel plate of mm was manufactured. Table 5 shows the results of investigating the mechanical properties of these steel plates.

【0036】[0036]

【表5】[Table 5]

【0037】表5より、熱延鋼板においても本発明に従
うものは密度低減率が大きく、しかも成形性に優れてい
ることが明らかである。
From Table 5, it is clear that the hot rolled steel sheets according to the present invention have a large density reduction rate and are excellent in formability.

【0038】[0038]

【発明の効果】以上説明したような本発明によるときは
、低密度かつ高強度な鋼板が製造できるので、板厚を減
少させなくても軽量化が達成でき、しかも成形品の強度
を維持することが可能であるため、産業上の利用価値は
非常に大きく、特に、自動車車体などの軽量化に対して
極めて有益であるから工業的にその効果の大きい発明で
ある。
[Effects of the Invention] According to the present invention as explained above, a low-density and high-strength steel plate can be manufactured, so weight reduction can be achieved without reducing the plate thickness, and the strength of the molded product can be maintained. Since it is possible to do this, it has great industrial utility value, and is particularly useful for reducing the weight of automobile bodies, so it is an invention with great industrial effects.

【図面の簡単な説明】[Brief explanation of the drawing]

【図1】Al,C,Mn,Ni,CuのバランスとEl
の関係を示した図表である。
[Figure 1] Balance of Al, C, Mn, Ni, Cu and El
This is a chart showing the relationship between

Claims (3)

【特許請求の範囲】[Claims] 【請求項1】  C:0.02〜0.1wt%、Si:
0.5wt%以下、Mn:0.2〜2.0wt%、P:
0.05wt%以下、S:0.01wt%以下、Al:
0.5〜5.0wt%、ただし、4.2/Al≧(15
×C+Mn+0.7)/Al≧0.7を含有し、残部が
Fe及び不可避的不純物より成り、板厚が0.5mm以
上3mm以下で、7.75g/cm3 以下の密度を有
することを特徴とする成形用軽量高強度鋼板。
[Claim 1] C: 0.02 to 0.1 wt%, Si:
0.5 wt% or less, Mn: 0.2 to 2.0 wt%, P:
0.05wt% or less, S: 0.01wt% or less, Al:
0.5 to 5.0 wt%, provided that 4.2/Al≧(15
×C+Mn+0.7)/Al≧0.7, the remainder consists of Fe and unavoidable impurities, the thickness is 0.5 mm or more and 3 mm or less, and the density is 7.75 g/cm3 or less. A lightweight high-strength steel plate for forming.
【請求項2】  C:0.02〜0.1wt%、Si:
0.5wt%以下、Mn:0.2〜2.0wt%、P:
0.05wt%以下、S:0.01wt%以下、Al:
0.5〜5.0wt%、Ni:0.05〜1.0wt%
、Cu:0.05〜0.5wt%、ただし、4.2/A
l≧(15×C+Mn+Ni+2×Cu+0.7)/A
l≧0.7を含有し、残部がFe及び不可避的不純物よ
り成り、板厚が0.5mm以上3mm以下で、7.75
g/cm3 以下の密度を有することを特徴とする成形
用軽量高強度鋼板。
[Claim 2] C: 0.02 to 0.1 wt%, Si:
0.5 wt% or less, Mn: 0.2 to 2.0 wt%, P:
0.05wt% or less, S: 0.01wt% or less, Al:
0.5-5.0wt%, Ni: 0.05-1.0wt%
, Cu: 0.05 to 0.5 wt%, however, 4.2/A
l≧(15×C+Mn+Ni+2×Cu+0.7)/A
l≧0.7, the remainder consists of Fe and unavoidable impurities, the plate thickness is 0.5 mm or more and 3 mm or less, and 7.75
A lightweight high-strength steel plate for forming, characterized by having a density of g/cm3 or less.
【請求項3】  Nb:0.05wt%以下、Ti:0
.05wt%以下、V:0.05wt%以下、Zr:0
.05wt%以下、B:0.005wt%以下のうちの
1種又は2種以上を合計で0.05wt%以下で含有す
ることを特徴とする請求項1または請求項2に記載の成
形用軽量高強度鋼板。
[Claim 3] Nb: 0.05wt% or less, Ti: 0
.. 05wt% or less, V: 0.05wt% or less, Zr: 0
.. 05 wt% or less, and B: 0.005 wt% or less in a total amount of 0.05 wt% or less. Strength steel plate.
JP3109561A 1991-04-16 1991-04-16 Lightweight and high strength steel plate for automobile body Expired - Lifetime JP2517492B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP3109561A JP2517492B2 (en) 1991-04-16 1991-04-16 Lightweight and high strength steel plate for automobile body

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP3109561A JP2517492B2 (en) 1991-04-16 1991-04-16 Lightweight and high strength steel plate for automobile body

Publications (2)

Publication Number Publication Date
JPH04318150A true JPH04318150A (en) 1992-11-09
JP2517492B2 JP2517492B2 (en) 1996-07-24

Family

ID=14513361

Family Applications (1)

Application Number Title Priority Date Filing Date
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Country Status (1)

Country Link
JP (1) JP2517492B2 (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19605696A1 (en) * 1995-06-16 1996-12-19 Thyssen Stahl Ag Ferritic steel and process for its manufacture and use
DE19634524A1 (en) * 1996-08-27 1998-04-09 Krupp Ag Hoesch Krupp Lightweight steel and its use for vehicle parts and facade cladding
JP2007321168A (en) * 2006-05-30 2007-12-13 Jfe Steel Kk High-rigidity low-density steel sheet and its manufacturing method

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS53106324A (en) * 1977-02-28 1978-09-16 Nisshin Steel Co Ltd Method of producing steel product having good oscillating damping property
JPS5629653A (en) * 1979-08-14 1981-03-25 Sumitomo Metal Ind Ltd Structural steel having excellent vibration damping property
JPS5662926A (en) * 1979-10-29 1981-05-29 Kawasaki Steel Corp Production of steel sheet having super high r value
JPH0310046A (en) * 1989-06-05 1991-01-17 Sumitomo Metal Ind Ltd Fine-grained bainite steel

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS53106324A (en) * 1977-02-28 1978-09-16 Nisshin Steel Co Ltd Method of producing steel product having good oscillating damping property
JPS5629653A (en) * 1979-08-14 1981-03-25 Sumitomo Metal Ind Ltd Structural steel having excellent vibration damping property
JPS5662926A (en) * 1979-10-29 1981-05-29 Kawasaki Steel Corp Production of steel sheet having super high r value
JPH0310046A (en) * 1989-06-05 1991-01-17 Sumitomo Metal Ind Ltd Fine-grained bainite steel

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19605696A1 (en) * 1995-06-16 1996-12-19 Thyssen Stahl Ag Ferritic steel and process for its manufacture and use
DE19605697A1 (en) * 1995-06-16 1996-12-19 Thyssen Stahl Ag Multi-phase steel, production of rolled products and use of the steel
DE19605697C2 (en) * 1995-06-16 1998-05-20 Thyssen Stahl Ag Multi-phase steel, production of rolled products and use of the steel
DE19605696C2 (en) * 1995-06-16 1999-01-07 Thyssen Stahl Ag Ferritic steel and process for its manufacture and use
DE19634524A1 (en) * 1996-08-27 1998-04-09 Krupp Ag Hoesch Krupp Lightweight steel and its use for vehicle parts and facade cladding
US6383662B1 (en) 1996-08-27 2002-05-07 Georg Frommeyer Light weight steel and its use for car parts and facade linings
JP2007321168A (en) * 2006-05-30 2007-12-13 Jfe Steel Kk High-rigidity low-density steel sheet and its manufacturing method

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