JPH0517848A - Cold rolled dead soft steel sheet for ultradeep drawing - Google Patents

Cold rolled dead soft steel sheet for ultradeep drawing

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Publication number
JPH0517848A
JPH0517848A JP19576491A JP19576491A JPH0517848A JP H0517848 A JPH0517848 A JP H0517848A JP 19576491 A JP19576491 A JP 19576491A JP 19576491 A JP19576491 A JP 19576491A JP H0517848 A JPH0517848 A JP H0517848A
Authority
JP
Japan
Prior art keywords
less
steel sheet
steel
value
mns
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
JP19576491A
Other languages
Japanese (ja)
Other versions
JP3023014B2 (en
Inventor
Hidenori Shirasawa
白沢秀則
Takafusa Iwai
岩井隆房
Yoshinobu Omiya
大宮良信
Yoichi Mukai
向井陽一
Shunichi Hashimoto
橋本俊一
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.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
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Filing date
Publication date
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Priority to JP3195764A priority Critical patent/JP3023014B2/en
Publication of JPH0517848A publication Critical patent/JPH0517848A/en
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Publication of JP3023014B2 publication Critical patent/JP3023014B2/en
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Abstract

PURPOSE:To improve the productivity and yield of a cold rolled steel sheet for ultradeep drawing by preparing a steel incorporating specified wt.% C, Al, N, etc., incorporating a specified atomic equivalent ratio of Ti and specifying the volume ratio of TiS to MnS. CONSTITUTION:A steel is incorporated with, by weight, <=0.0015% C, 0.2 to 0.5% Mn, <=0.01% P, <=0.01% S, 0.01 to 0.1% Al and <=0.005% N. Moreover, Ti is incorporated by the atomic equivalent ratio of the total of N and C or above and the atomic equivalent ratio of N, S and C or below. Furthermore, TiS and MnS as precipitates satisfy the relationship of >=10MnS/TiS by volume. Then, the balance is consisting of Fe and other impurity elements. In such a manner, the pressing workability of a steel sheet for pressing working used for automobile bodies or the like can be improved.

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、特にランクフォード値
(r値)の改善を可能にした超深絞り用冷延極軟鋼板に関
するものである。
BACKGROUND OF THE INVENTION The present invention is particularly applicable to Rankford values.
The present invention relates to a cold rolled extra soft steel sheet for ultra deep drawing, which enables improvement of (r value).

【0002】[0002]

【従来の技術及び発明が解決しようとする課題】自動車
部品、特にフェンダー等の部品の成形では深絞り性が要
求されており、従来から、ランクフォード値(r値)が2
前後の超深絞り用冷延鋼板が使用されていた。更に近
年、ユーザーニーズの多様化或いはファッション性の追
及に伴い、高度なプレス成形性の求められる部品が増加
しつつある。
2. Description of the Related Art Deep-drawability is required in the molding of automobile parts, especially parts such as fenders. Conventionally, the Rankford value (r value) is 2
Front and rear cold-rolled steel sheets for ultra-deep drawing were used. Further, in recent years, with the diversification of user needs or the pursuit of fashionability, the number of parts that require a high degree of press moldability is increasing.

【0003】この種の超深絞り用冷延鋼板としては、従
来、極低C鋼にC及びNを十分固着するに必要な量のT
i或いはNbを添加したIF鋼(Interstitial Free St
eel)が良く知られている。
As a cold-rolled steel sheet for ultra-deep drawing of this type, conventionally, an amount of T required to sufficiently fix C and N to an ultra-low C steel is conventionally used.
IF steel with i or Nb (Interstitial Free St
eel) is well known.

【0004】しかしながら、これらの鋼においては、T
iはN、S及びCの総量の原子当量比以下の添加では固
溶Cが残存し、十分な特性を得ることができないと言わ
れてきた。また、Mnは、焼鈍時の粒成長性を劣化させ
る成分として知られており、高r値を得るためにはC、
N、Sの総量の原子当量比以上の十分なTiの添加、及
びMnの低減を行うことが必要であると言われている。
そのため、Tiの多量添加によるコストアップ、MnSの
十分な析出が行われないことによるスラブの熱間脆性割
れ等の問題点があった。
However, in these steels, T
It has been said that when the addition of i is less than the atomic equivalent ratio of the total amount of N, S and C, the solid solution C remains and sufficient characteristics cannot be obtained. Further, Mn is known as a component that deteriorates the grain growth property during annealing, and in order to obtain a high r value, C,
It is said that it is necessary to sufficiently add Ti in an amount equal to or more than the atomic equivalent ratio of the total amount of N and S and to reduce Mn.
Therefore, there are problems such as an increase in cost due to the addition of a large amount of Ti and a hot brittle crack of the slab due to insufficient precipitation of MnS.

【0005】なお、高張力鋼板に関する技術ではある
が、Ti添加極低炭素冷延鋼板にMnを添加することによ
り、r値が向上することが「鉄と鋼」、76(199
0)、p.422に示されている。この鋼板はP、Mnを複
合添加した高張力鋼板であり、Mnを添加することによ
りMnSが形成され、その結果、FeTiPの析出状況を
変化させ、r値に好ましい再結晶集合組織を形成させる
役割を果たすためであると説明されている。
Although it is a technology relating to high-strength steel sheets, the r value can be improved by adding Mn to Ti-added ultra-low carbon cold-rolled steel sheets in "Iron and Steel", 76 (199).
0), p.422. This steel sheet is a high-strength steel sheet in which P and Mn are added in combination, and MnS is formed by adding Mn. As a result, the role of changing the precipitation state of FeTiP and forming a recrystallized texture preferable for r value It is explained that it is for fulfilling.

【0006】以上のように、従来の超深絞り用冷延鋼板
では、Ti添加IF鋼によってある程度の前進が得られ
たとはいえ、各種特性値のより一層の向上、それに伴う
操業条件の緩和、歩留りの向上等、残された課題も多
い。この点、冷延極軟鋼板において低コストで優れた深
絞り性が付与できるならば、その実用上の効果は大きい
が、未だそのような技術は確立されていない。
As described above, in the conventional cold-rolled steel sheet for ultra-deep drawing, although the Ti-added IF steel has made some progress, the various characteristic values are further improved and the operating conditions are reduced accordingly. There are many remaining issues such as improvement in yield. In this respect, if cold-rolled ultra mild steel sheet can be provided with low cost and excellent deep drawability, its practical effect is great, but such a technique has not been established yet.

【0007】一方、しかし、この技術は高張力鋼板にお
けるr値改善法であり、冷延軟鋼板に対しては全く未定
である。
On the other hand, however, this technique is an r-value improving method for high-strength steel sheets and is not yet determined for cold-rolled mild steel sheets.

【0008】本発明は、上記従来技術の問題点を解決
し、少ないTi添加量でr値を改善し得る超深絞り用極
低炭素冷延鋼板を提供することを目的とするものであ
る。
An object of the present invention is to solve the above-mentioned problems of the prior art and to provide an ultra-low carbon cold-rolled steel sheet for ultra deep drawing which can improve the r value with a small amount of Ti added.

【0009】[0009]

【課題を解決するための手段】本発明者は、前記課題を
解決するため、Ti量を低減してr値を顕著に改善し得
る方策について鋭意研究を重ねた。その結果、極低C−
IF鋼において、Pを積極的に添加せず、Mnを添加す
ることによりMnSが析出し、TiS分のTiがTiCの析
出に働くため、Ti添加量がC、N、Sの原子当量比以
下であっても固溶Cが残存せず、またMnSはTiSに比
べて粗大に析出するため、焼鈍時の回復、再結晶過程で
の粒成長性が良くなり、優れた深絞り性を持つことを見
い出した。これによってその製造コストが低減でき、ま
た熱間加工時の脆化を抑制できる超深絞り用冷延鋼板を
見い出し、ここに本発明を完成したものである。
In order to solve the above-mentioned problems, the inventor of the present invention has conducted extensive studies on a method capable of significantly improving the r value by reducing the Ti amount. As a result, extremely low C-
In IF steel, MnS precipitates by not adding P positively and adding Mn, and Ti in TiS acts on precipitation of TiC. Therefore, the Ti addition amount is less than the atomic equivalent ratio of C, N, and S. However, solid solution C does not remain, and MnS precipitates coarser than TiS, so recovery during annealing, grain growth during recrystallization, and good deep drawability are possible. Found out. As a result, the present invention has been completed by finding a cold-rolled steel sheet for ultra-deep drawing which can reduce its manufacturing cost and can suppress brittleness during hot working.

【0010】すなわち、本発明は、C:0.0015%以
下、Mn:0.2〜0.5%、P:0.01%以下、S:0.0
1%以下、Al:0.01〜0.1%、N:0.005%以下
を含み、更にTiをNとCの総量の原子当量比以上でN
とSとCの総量の原子当量比以下を含み、かつ、析出物
のTiSとMnSが体積比でMnS/TiS≧10の関係を
満たし、残部がFe及びその他の不純物元素からなるこ
とを特徴とする超深絞り用冷延極軟鋼板を要旨とするも
のである。
That is, according to the present invention, C: 0.0015% or less, Mn: 0.2 to 0.5%, P: 0.01% or less, S: 0.0
1% or less, Al: 0.01 to 0.1%, N: 0.005% or less, and Ti is N at an atomic equivalent ratio of the total amount of N and C or more.
And the atomic equivalent ratio of the total amount of S and C is not more than, and the TiS and MnS of the precipitate satisfy the relationship of MnS / TiS ≧ 10 by volume ratio, and the balance is Fe and other impurity elements. The subject is a cold rolled extra soft steel sheet for ultra deep drawing.

【0011】以下に本発明を更に詳述する。The present invention will be described in more detail below.

【0012】[0012]

【作用】本発明における化学成分の限定理由は以下のと
おりである。
The reason for limiting the chemical components in the present invention is as follows.

【0013】C:従来のIF鋼は約0.002%以上の
Cを含み、それを固定するに十分なTiを添加して、初
めて高r値が得られた。これは固溶Cが冷延もしくは回
復再結晶過程で転位の移動に影響を及ぼし、(111)集
合組織の発達を抑制することがその原因であると知られ
ている。しかし、本発明では、C量を0.0015%以
下にするものであり、これにより、その析出、固定のた
めに添加する炭窒化物形成元素の絶対量を少なくするこ
とができ、析出物の量も低減できる。よって、C量は
0.0015%以下とする。
C: Conventional IF steel contains about 0.002% or more of C, and a high r value was obtained only when Ti was added enough to fix it. It is known that this is because solid solution C affects the movement of dislocations in the cold rolling or recovery recrystallization process and suppresses the development of (111) texture. However, in the present invention, the amount of C is set to 0.0015% or less, whereby the absolute amount of carbonitride forming element added for precipitation and fixation can be reduced, and The amount can also be reduced. Therefore, the C content is 0.0015% or less.

【0014】Mn、Ti:Mnを0.2〜0.5%、Tiを
N、Cの総量の原子当量比以上及びC、N、Sの総量の
原子当量比以下とし、かつ、MnS/TiS≧10となる
ように添加することにより、冷延板の焼鈍時の粒成長性
が良好になり、r値を向上することができる。MnS/
TiS比が10未満では、微細な析出物が多く、大きな
r値が得られない(図1参照)。また、Mnが0.2%未満
ではMnSが十分析出できず、0.5%を超えると固溶M
nによる悪影響の方が大きくなり、r値の低下を来た
す。
Mn, Ti: Mn is 0.2 to 0.5%, Ti is more than the atomic equivalent ratio of the total amount of N, C and less than the atomic equivalent ratio of the total amount of C, N, S, and MnS / TiS. By adding so that ≧ 10, the grain growth property during annealing of the cold-rolled sheet becomes good, and the r value can be improved. MnS /
When the TiS ratio is less than 10, there are many fine precipitates and a large r value cannot be obtained (see FIG. 1). If Mn is less than 0.2%, MnS cannot be sufficiently precipitated, and if it exceeds 0.5%, solid solution M is formed.
The adverse effect of n becomes larger and the r value decreases.

【0015】また、TiがN、Cの総量の原子当量比未
満ではTiN、TiCが十分に析出できず、一方、Tiを
多量添加すると微細なTiSばかりが析出し、焼鈍時の
粒成長性を劣化させ、更にコストアップの要因ともなる
ので、Ti添加量はN、Cの総量の原子当量比以上、か
つ、N、S、Cの総量の原子当量比以下とする。
Further, when Ti is less than the atomic equivalent ratio of the total amount of N and C, TiN and TiC cannot be sufficiently precipitated. On the other hand, when Ti is added in a large amount, only fine TiS is precipitated and grain growth during annealing is improved. Since it causes deterioration and further increases the cost, the Ti addition amount is set to the atomic equivalent ratio of the total amount of N, C or more and the atomic equivalent ratio of the total amount of N, S, C or less.

【0016】P:本発明鋼の目的は成形性の優れた極軟
鋼板を提供することにあるから、強度増加をもたらすS
i、Pなどの添加を極力抑える必要がある。Pについて
は製鋼過程でのバラツキを考慮し、0.01%を上限と
する。下限値は特に定めないが、0.005%程度が現
在の技術では最小値となる。
P: Since the purpose of the steel of the present invention is to provide an ultra-soft steel plate having excellent formability, S which brings about an increase in strength.
It is necessary to suppress addition of i, P, etc. as much as possible. The upper limit of P is 0.01% in consideration of variations in the steelmaking process. Although the lower limit value is not specified, about 0.005% is the minimum value in the current technology.

【0017】S:Sはr値には何等悪影響を及ぼさない
が、S量が増加すると析出するMnSの絶対量も増加
し、伸びフランジ性に代表される局部延性を劣化させる
ため、0.01%以下に制限しなければならない。
S: S has no adverse effect on the r value, but as the amount of S increases, the absolute amount of MnS that precipitates also increases, deteriorating the local ductility represented by stretch flangeability. Must be limited to% or less.

【0018】Al:Alは脱酸に必要な元素であり、十分
な脱酸を行うには最低0.01%が必要である。しか
し、逆に0.1%を超えると脱酸が飽和に達するだけで
なく、アルミナ系介在物が発生し、成形性を劣化させ
る。よって、Al量は0.01〜0.1%の範囲とする。
Al: Al is an element necessary for deoxidation, and at least 0.01% is necessary for sufficient deoxidation. However, on the contrary, when the content exceeds 0.1%, not only the deoxidation reaches saturation but also alumina-based inclusions are generated to deteriorate the formability. Therefore, the amount of Al is set in the range of 0.01 to 0.1%.

【0019】N:Nの増加に伴い、それを固定するに必
要なTiの添加量が多くなり、コストアップを招く他、
析出物量も増加し、粒成長性が劣化し、r値の向上が得
にくくなるため、Nはできるだけ低レベル、好ましくは
0.004%以下が望ましいが、所望の材質を得るに必
要な最低限の値が0.005%であることから、0.00
5%を上限値とする。
N: As N is increased, the amount of Ti required to fix the N is increased, which causes an increase in cost.
The amount of precipitates also increases, the grain growth property deteriorates, and it becomes difficult to improve the r value. Therefore, N is preferably as low as possible, preferably 0.004% or less, but it is the minimum necessary to obtain the desired material. Since the value of is 0.005%, it is 0.00
The upper limit value is 5%.

【0020】その他:Siは、前述のように強度増加を
もたらし、また表面性状や化成処理性が劣化するため、
意図的な添加は行わず、極力少ない方が良い。
Others: Si brings about an increase in strength as described above, and the surface properties and chemical conversion treatability are deteriorated.
It is better not to add it intentionally and to minimize it.

【0021】上記化学成分を有する本発明鋼板の製造条
件は特に制限するものではないが、以下に好ましい製造
条件を示す。
The production conditions for the steel sheet of the present invention having the above chemical components are not particularly limited, but the preferred production conditions are shown below.

【0022】本発明鋼は通常行われる転炉等で溶製さ
れ、溶鋼は鋼片とされるが、その方法としては造塊法で
も連続鋳造法でもかまわない。鋼片は室温まで冷却され
た後、熱延加熱炉に装入されるが、その際、一旦室温ま
で冷却せず、加熱炉に装入するHCR法でもかまわな
い。また、鋼片を再加熱することなくそのまま圧延する
ことはもとより、短時間の保熱及び/又は部分的な加熱
の後に熱延しても本発明の効果は何等損なわれるもので
はない。鋼片の加熱温度については通常の1000〜1
300℃でよいが、仕上温度のAr3点が確保できるので
あれば、できるだけ低いことが望ましい。
The steel of the present invention is smelted in a converter or the like which is usually used, and the molten steel is made into a slab, but the method may be an ingot casting method or a continuous casting method. The steel slab is charged to the hot rolling heating furnace after being cooled to room temperature. At that time, the HCR method may be used in which the steel slab is not once cooled to room temperature but is charged to the heating furnace. Further, the effect of the present invention is not impaired at all by rolling the steel slab as it is without reheating it, or by hot rolling after heat retention for a short time and / or partial heating. About the heating temperature of the billet is usually 1000-1
The temperature may be 300 ° C., but if the Ar 3 point of the finishing temperature can be secured, it is preferably as low as possible.

【0023】熱延条件は、オーステナイト域での熱延終
了が好ましい。仕上温度がAr3点未満になると冷延、焼
鈍後の特性を害する集合組織が形成されるので、Ar3
以上が望ましい。巻取温度は、従来は高温ほど析出物が
完全に析出し、残存固溶Cが減少し、r値が向上すると
されていたが、本発明鋼のようにC量が極めて低い鋼に
おいては、500℃以下の低温巻取でも残存固溶Cが少
なく、r値低下は殆どない。
The hot rolling condition is preferably the end of hot rolling in the austenite region. When the finishing temperature is less than Ar 3 points, a texture that impairs the properties after cold rolling and annealing is formed, so Ar 3 points or more is desirable. As for the coiling temperature, it has been conventionally said that the higher the temperature, the more the precipitates are completely precipitated, the residual solid solution C is decreased, and the r value is improved, but in the steel such as the steel of the present invention, the C content is extremely low, Even at a low temperature of 500 ° C. or less, the residual solid solution C is small and the r value hardly decreases.

【0024】冷延条件は、冷延率が65%以上85%以
下であれば、高いほどr値の向上が得られる。しかしな
がら、最低限65%の冷延を加えれば所望の特性が得ら
れ、一方85%以上の冷延は通常のタンデムミルで1回
の圧延で完了することは不可能である。
As for the cold rolling conditions, if the cold rolling rate is 65% or more and 85% or less, the higher the r value is, the higher the r value can be obtained. However, the desired properties can be obtained by adding a minimum of 65% cold rolling, while the cold rolling of 85% or more cannot be completed by one rolling in a normal tandem mill.

【0025】焼鈍条件は、均熱温度が再結晶温度以上、
Ac3点未満の範囲であれば加熱、冷却条件は特に規制す
る必要がない。しかしながら、Ac3点を超えてオーステ
ナイト域まで加熱すると、γ→α変態時にランダム核生
成をもたらし、極端にr値が劣化する。
The annealing conditions are such that the soaking temperature is higher than the recrystallization temperature,
It is not necessary to regulate heating and cooling conditions as long as the Ac is less than 3 points. However, when heating beyond the Ac 3 point to the austenite region, random nucleation occurs during the γ → α transformation, and the r value is extremely deteriorated.

【0026】本発明鋼は、冷延前にC、NがTiによっ
て殆ど固定され、冷延、焼鈍後も殆ど分解することがな
いため、過時効処理は特に必要でないが、現状の連続焼
鈍ラインに設置されている過時効帯を通板し、通常のA
lキルド鋼に採用されているような過時効処理を加えて
も、何ら材質を劣化させるものではない。
In the steel of the present invention, C and N are almost fixed by Ti before cold rolling and hardly decomposed even after cold rolling and annealing. Therefore, overaging treatment is not particularly required, but the current continuous annealing line is used. Passing the overaging zone installed in the
l The addition of overageing treatment such as that used for killed steel does not deteriorate the material.

【0027】次に本発明の実施例を示す。Next, examples of the present invention will be described.

【0028】[0028]

【実施例】【Example】

【表1】 に示す化学成分の供試鋼を熱間圧延した後、巻取、酸洗
し、78%の圧下率で冷間圧延を施し、板厚0.8mmの
冷延板を得た。この冷延板に850℃×1分の焼鈍を施
し、引張試験を行った。なお、MnS/TiS比について
は透過電子顕微鏡、EDXを用いてある視野内の析出物
の観察、分析を行い求めた。それらの結果を
[Table 1] After hot-rolling the sample steel having the chemical composition shown in (1), it was wound, pickled, and cold-rolled at a reduction rate of 78% to obtain a cold-rolled sheet having a sheet thickness of 0.8 mm. This cold-rolled sheet was annealed at 850 ° C. for 1 minute and a tensile test was conducted. The MnS / TiS ratio was determined by observing and analyzing precipitates in a certain visual field using a transmission electron microscope and EDX. Those results

【表2】 に示す。[Table 2] Shown in.

【0029】なお、Ti*は、全Ti量からTiN分とTi
S分を差し引いた値である(表1の脚注参照)。また、r
値は圧延方向に平行な方向の値、直角方向の値、45゜
方向の値の平均値である(表2の脚注参照)。
Note that Ti * is TiN and Ti from the total Ti amount.
It is the value after subtracting S (see footnote in Table 1). Also, r
The values are average values of the values in the direction parallel to the rolling direction, the values in the right angle direction, and the values in the 45 ° direction (see footnote in Table 2).

【0030】表2より明らかなように、本発明鋼は、原
子濃度比(Ti*/C)が1以下のTi添加量の少ない成分
において、また巻取温度が500℃以下と低くても、高
いr値を示している。また、Mn量が0.36%でr=
2.54と高いr値を示している。
As is clear from Table 2, in the steel of the present invention, in the components having a small atomic amount of Ti (Ti * / C) of 1 or less and the coiling temperature is as low as 500 ° C. or less, It shows a high r value. When the Mn amount is 0.36%, r =
It shows a high r value of 2.54.

【0031】[0031]

【発明の効果】以上詳述したように、本発明によれば、
少ないTi添加量でr値の高い超深絞り用冷延鋼板が得
られる。なおかつ、低温巻取法によっても高温巻取材と
同等の高r値が得られ、巻取温度を低くして製造できる
ことより酸洗性が向上し、更にコイルトップ部やボトム
部でのr値の低下を小さくすることができるため、生産
性、歩留りが向上する。特に自動車ボディ等に用いるプ
レス加工用鋼板のプレス加工性を改善でき、工業的価値
は多大である。
As described in detail above, according to the present invention,
A cold rolled steel sheet for ultra deep drawing having a high r value can be obtained with a small amount of Ti added. In addition, the low-temperature winding method provides a high r-value that is equivalent to that of the high-temperature winding material, and the picking-up property is improved due to the fact that the coil can be manufactured at a lower winding temperature, and the r-value decreases at the coil top and bottom. Can be reduced, so that the productivity and the yield are improved. In particular, the press workability of the steel plate for press work used for automobile bodies and the like can be improved, and the industrial value is great.

【図面の簡単な説明】[Brief description of drawings]

【図1】MnS/TiS比とr値の関係を示した図であ
る。
FIG. 1 is a diagram showing a relationship between an MnS / TiS ratio and an r value.

Claims (1)

【特許請求の範囲】 【請求項1】 重量%で(以下、同じ)、C:0.0015
%以下、Mn:0.2〜0.5%、P:0.01%以下、S:
0.01%以下、Al:0.01〜0.1%、N:0.005
%以下を含み、更にTiをNとCの総量の原子当量比以
上でNとSとCの総量の原子当量比以下を含み、かつ、
析出物のTiSとMnSが体積比でMnS/TiS≧10の
関係を満たし、残部がFe及びその他の不純物元素から
なることを特徴とする超深絞り用冷延極軟鋼板。
Claims: 1. In% by weight (hereinafter the same), C: 0.0015
% Or less, Mn: 0.2 to 0.5%, P: 0.01% or less, S:
0.01% or less, Al: 0.01 to 0.1%, N: 0.005
% Or less, and Ti in an amount equal to or more than the atomic equivalent ratio of the total amount of N and C and equal to or less than the atomic equivalent ratio of the total amount of N, S, and C, and
A cold-rolled extra-soft steel sheet for ultra-deep drawing, wherein TiS and MnS of the precipitate satisfy the relationship of MnS / TiS ≧ 10 in volume ratio, and the balance is Fe and other impurity elements.
JP3195764A 1991-07-10 1991-07-10 Cold rolled mild steel sheet for ultra deep drawing Expired - Fee Related JP3023014B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP3195764A JP3023014B2 (en) 1991-07-10 1991-07-10 Cold rolled mild steel sheet for ultra deep drawing

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP3195764A JP3023014B2 (en) 1991-07-10 1991-07-10 Cold rolled mild steel sheet for ultra deep drawing

Publications (2)

Publication Number Publication Date
JPH0517848A true JPH0517848A (en) 1993-01-26
JP3023014B2 JP3023014B2 (en) 2000-03-21

Family

ID=16346574

Family Applications (1)

Application Number Title Priority Date Filing Date
JP3195764A Expired - Fee Related JP3023014B2 (en) 1991-07-10 1991-07-10 Cold rolled mild steel sheet for ultra deep drawing

Country Status (1)

Country Link
JP (1) JP3023014B2 (en)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
BRPI0601188B1 (en) 2005-04-15 2018-06-26 Seda S.P.A. ISOLATED CONTAINER; METHOD OF MANUFACTURING THE SAME AND APPARATUS FOR MANUFACTURING
DE202006018406U1 (en) 2006-12-05 2008-04-10 Seda S.P.A. packaging

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