JPH0756054B2 - Method for manufacturing cold-rolled steel sheet for processing with excellent fatigue resistance of spot welded joints - Google Patents
Method for manufacturing cold-rolled steel sheet for processing with excellent fatigue resistance of spot welded jointsInfo
- Publication number
- JPH0756054B2 JPH0756054B2 JP31840488A JP31840488A JPH0756054B2 JP H0756054 B2 JPH0756054 B2 JP H0756054B2 JP 31840488 A JP31840488 A JP 31840488A JP 31840488 A JP31840488 A JP 31840488A JP H0756054 B2 JPH0756054 B2 JP H0756054B2
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- cold
- steel sheet
- fatigue resistance
- rolled steel
- Prior art date
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- Heat Treatment Of Sheet Steel (AREA)
Description
【発明の詳細な説明】 (産業上の利用分野) この発明は、曲げ加工、プレス成形加工、絞り成形加
工、深絞り加工および超深絞加工などの用途に用いて好
適な加工用冷延鋼板の製造方法に関し、とくにスポット
溶接継手の耐疲労特性の有利な改善を図ったものであ
る。TECHNICAL FIELD The present invention relates to a cold-rolled steel sheet suitable for use in applications such as bending, press forming, drawing, deep drawing and ultra deep drawing. In particular, the present invention is intended to improve the fatigue resistance of spot welded joints.
(従来の技術) 冷却鋼板は、その優れた加工性ゆえに、プレス成形や深
絞り加工など加工用鋼板として広く用いられている。し
かしながらその有用性ゆえに、加工性の他にも幾多の特
性について良好な材質を有することが要求されている。
冷延鋼板はスポット溶接されることが極めて多く、自動
車の組み立て工程がそのよい例である。一台の乗用車の
スポット溶接の打点数は数千点にも及ぶ。溶接継手部分
は外部から荷重が加わった時に応力が集中し多く、自動
車走行時の繰り返し応力による疲労破壊は重大事故を招
きかねない。したがって、加工用冷延鋼板においてスポ
ット溶接継手の疲労強度はきわめて重要な特性である。(Prior Art) Cooled steel sheets are widely used as steel sheets for working such as press forming and deep drawing due to their excellent workability. However, because of its usefulness, it is required to have a good material for many properties in addition to workability.
Cold-rolled steel sheets are very often spot-welded, and the automobile assembly process is a good example. The number of spot welding spots for a single passenger car reaches to several thousand. Since stress is concentrated on the welded joint part when a load is applied from the outside, fatigue failure due to repeated stress during running of a vehicle may cause a serious accident. Therefore, the fatigue strength of the spot-welded joint is a very important property in the cold-rolled steel sheet for working.
一方、冷延鋼板の製造工程が従来の箱焼鈍から連続焼鈍
に変化するにつれて、極低炭素鋼が多用されるようにな
った。極低炭素鋼は条件によってスポット溶接継手の疲
労強度が低いことがある。On the other hand, as the manufacturing process of cold-rolled steel sheets has changed from conventional box annealing to continuous annealing, ultra-low carbon steel has come to be widely used. Extra-low carbon steel may have low fatigue strength in spot welded joints depending on the conditions.
ここに自動車などの安全性を向上させることは今や世界
的なテーマであり、従来の鋼板よりもスポット溶接継手
の疲労強度を一層向上させることが重要な課題となって
いる。Here, improving the safety of automobiles and the like is now a global theme, and further improving the fatigue strength of spot-welded joints has become an important issue compared to conventional steel sheets.
この発明の加工用鋼板に近い技術としては、たとえば特
開昭54-135616号公報、特開昭53-52222号公報、特開昭6
1-246344号公報、特開昭58-25436号公報、特開昭53-137
021号公報、特開昭58-110659号公報および特開昭57-454
55号公報などがあるが、いずれも冷延鋼板の機械的特性
の改善をその特徴としていて、スポット溶接継手の疲労
強度に関する記載はない。Techniques similar to the steel sheet for processing of the present invention include, for example, Japanese Patent Laid-Open Nos. 54-135616, 53-52222, and 6-.
1-246344, JP-A-58-25436, JP-A-53-137
021, JP-A-58-110659 and JP-A-57-454
No. 55, etc., but all of them are characterized by the improvement of the mechanical properties of the cold rolled steel sheet, and there is no description about the fatigue strength of spot welded joints.
(発明が解決しようとする課題) プレス成形等の加工性に優れるのは勿論のこと、とくに
スポット溶接継手の耐疲労特性に優れる鋼板を得ること
が、この発明の目的である。(Problems to be Solved by the Invention) It is an object of the present invention to obtain a steel sheet which is excellent not only in workability such as press forming but also particularly in fatigue resistance of spot welded joints.
(課題を解決するための手段) さて発明者らは、鋼板のスポット溶接継手の耐疲労特性
の向上を図るべく鋭意研究を重ねた結果、とくにO,Alお
よびNの成分組成を適正範囲に規制することが所期した
目的の達成に関し、極めて有効であることを突き止め、
この発明を完成させるに至ったのである。(Means for Solving the Problems) As a result of intensive studies to improve the fatigue resistance of spot welded joints of steel sheets, the inventors have regulated the composition of O, Al, and N within an appropriate range. Find that it is extremely effective in achieving the intended purpose,
It came to complete this invention.
すなわちこの発明は、 C:0.0028wt%(以下単に%で示す)以下、 Si:1.0%以下、 Mn:1.0%以下、 P:0.15%以下、 S:0.0200%以下、 O:0.0045%以下、 N:0.0020%以下および Al:(30×%N)〜0.15% を含み、ときにはさらに Nb:0.001〜0.025%および B:0.0002〜0.0020% のうちから選んだ少なくとも一種 を含有し、残部はFeおよび不可避的不純物からなる鋼片
を、600℃以上の仕上げ温度で熱間圧延し、ついで圧下
率:60%以上で冷間圧延したのち、Ac3変態点以下の温度
で再結晶焼鈍を施すことからなるスポット溶接継手の耐
疲労特性に優れる加工用冷延鋼板の製造方法である。That is, the present invention is C: 0.0028 wt% (hereinafter simply referred to as%), Si: 1.0% or less, Mn: 1.0% or less, P: 0.15% or less, S: 0.0200% or less, O: 0.0045% or less, N : 0.0020% or less and Al: (30 x% N) to 0.15%, and sometimes at least one selected from Nb: 0.001 to 0.025% and B: 0.0002 to 0.0020%, with the balance being Fe and unavoidable. A steel slab consisting of mechanical impurities is hot-rolled at a finishing temperature of 600 ° C or more, then cold-rolled at a rolling reduction of 60% or more, and then subjected to recrystallization annealing at a temperature below the Ac 3 transformation point. This is a method for manufacturing a cold-rolled steel sheet for processing, which has excellent fatigue resistance of spot-welded joints.
(作用) 冷延鋼板のスポット溶接継手の疲労特性は、鋼板を素材
とする製品において極めて重要な特性であるにもかかわ
らが、従来、鋼成分の影響に関しての研究は少ない。(Function) Although the fatigue characteristics of spot welded joints of cold-rolled steel sheets are extremely important characteristics in products made of steel sheets, there have been few studies on the influence of steel components.
発明者らは、冷延鋼板のスポット溶接継手の疲労特性に
及ぼす鋼成分の影響について研究を重ね、以下のような
知見を得た。The inventors have conducted extensive research on the effect of steel components on the fatigue properties of spot-welded joints of cold-rolled steel sheets, and have obtained the following findings.
第1図に、0.8mm厚の冷延鋼板の剪断引張りにおける疲
労限界値(1千万回)と0量及びAl/N比との関係につい
て調べた結果を示す。他の鋼成分および製造条件は表1
に示すとおりである。表2にはスポット溶接条件を示
す。なおナゲット径は約5mmとなるように溶接電流を調
整した。FIG. 1 shows the results of an examination of the relationship between the fatigue limit value (10 million times) in shear tension of a 0.8 mm thick cold-rolled steel sheet, 0 content and the Al / N ratio. Other steel composition and manufacturing conditions are shown in Table 1.
As shown in. Table 2 shows spot welding conditions. The welding current was adjusted so that the nugget diameter was about 5 mm.
第1図には、従来の低炭素Alキルド箱焼鈍材より高い疲
労限界値を有する領域をハッチングにより示したが、0
が0.0045%以下及びAl/Nが30以上がその領域に対応す
る。 In FIG. 1, a region having a higher fatigue limit value than that of the conventional low carbon Al killed box annealed material is shown by hatching.
0.0045% or less and Al / N of 30 or more correspond to the region.
この理由を解明すべく、疲労限界値の高い試料の溶接部
の断面について硬度分布を調査したところ、溶融部から
熱影響部にいたる硬度差が従来鋼板より小さく、しかも
滑らかな分布をしていることが判明した。このことが応
力負荷時に、継手部分の応力集中による疲労クラックの
発生及び伝播に対して有利に作用するものと考えられ
る。To elucidate the reason for this, an examination of the hardness distribution in the cross section of the welded portion of a sample with a high fatigue limit showed that the difference in hardness from the fusion zone to the heat-affected zone was smaller than that of conventional steel sheets, and the distribution was smooth. It has been found. This is considered to have an advantageous effect on the occurrence and propagation of fatigue cracks due to stress concentration in the joint portion when stress is applied.
さらにNbおよび/またはBを適正量添加した場合には疲
労限界値が一層高くなることも併せて見いだされた。Further, it was also found that the fatigue limit value becomes higher when Nb and / or B is added in an appropriate amount.
以下、この発明において素材の成分組成を前記範囲に限
定した理由について述べる。The reason why the component composition of the raw material is limited to the above range in the present invention will be described below.
C:Cは、良好な伸び、r値を有する鋼板を得るためには
従来の低炭材より低い極低炭素系でなければならない。
また、C量が低いほうが耐疲労特性に有利である。した
がって、Cは極力低減することが好ましいが、0.0028%
以下で許容できる。とくに好ましい範囲は0.0015%以下
である。C: C must be a very low carbon type which is lower than that of conventional low carbon materials in order to obtain a steel sheet having good elongation and r value.
Further, the lower the C content, the more advantageous the fatigue resistance. Therefore, it is preferable to reduce C as much as possible, but 0.0028%
The following is acceptable. A particularly preferred range is 0.0015% or less.
Si:Siは1.0%より多く存在すると鋼板の伸びおよび絞り
性を劣化させるので、1.0%以下とする。Si: If Si is present in an amount of more than 1.0%, the elongation and drawability of the steel sheet deteriorate, so the content is made 1.0% or less.
Mn:MnもSiと同様、過剰な添加は鋼板の伸びおよび絞り
性を劣化させるので、1.0%以下とする。Similar to Si, Mn: Mn is 1.0% or less because excessive addition deteriorates elongation and drawability of the steel sheet.
P:Pは0.15%を超えて多量に含有されると粒界への偏析
量が増し脆化するので0.15%以下に制限した。P: P is limited to 0.15% or less because if it is contained in a large amount exceeding 0.15%, the segregation amount at grain boundaries increases and embrittlement occurs.
S:Sは0.0200%を超えて多量に添加されると耐腐食性の
急激な劣化を招くので0.0200%以下に制限する。とはい
えあまりに低すぎると脱スケール性が劣化し表面性状が
悪化するので0.0035%以上とするのが好ましい。S: S is limited to 0.0200% or less because if added in excess of 0.0200%, it causes rapid deterioration of corrosion resistance. However, if it is too low, the descaling property is deteriorated and the surface properties are deteriorated, so 0.0035% or more is preferable.
O:Oの範囲はこの発明においてとくに重要であり、O量
を0.0045%以下まで抑制しないと従来鋼板以上の耐疲労
特性が得られない。これは固溶状態のOもしくは酸化物
状態のO量が疲労クラックの発生及び伝播に対して影響
するためと考えられる。とくに好ましい範囲は0.0035%
以下である。The range of O: O is particularly important in the present invention, and unless the O content is suppressed to 0.0045% or less, the fatigue resistance characteristics higher than those of conventional steel sheets cannot be obtained. It is considered that this is because the amount of O in the solid solution state or the amount of O in the oxide state affects the occurrence and propagation of fatigue cracks. Particularly preferred range is 0.0035%
It is the following.
N:Nが多くなると材質が劣化するだけでなく後述するよ
うに必要とするAl量が過剰となり表面性状を劣化させる
ので、0.0020%以下とする。とくに好ましくは0.0017%
以下である。If N: N increases, not only the material deteriorates, but also the required amount of Al becomes excessive and the surface quality deteriorates as described later, so the content is made 0.0020% or less. Particularly preferably 0.0017%
It is the following.
Al:Alの範囲もこの発明においてとくに重要であり、N
量との関係においてAl/Nを30以上、とくに好ましくは35
以上とする必要がある。The range of Al: Al is also particularly important in this invention,
Al / N in relation to the amount of 30 or more, particularly preferably 35
It is necessary to be above.
ここに固溶状態のAlもしくはAlNの析出物としての分布
状態が溶接熱影響部の組織に影響して耐疲労特性を向上
させていると考えられる。It is considered that the distribution state of Al or AlN in the form of a solid solution as a precipitate affects the structure of the weld heat affected zone to improve the fatigue resistance.
しかしながらあまりに多量の添加は、上述したとおり表
面性状の劣化を招くので0.15%以下とする必要がある。However, the addition of too much causes deterioration of the surface properties as described above, so it is necessary to set the content to 0.15% or less.
以上述べたところのほか、この発明においては、耐疲労
特性のより一層の向上を目的として、Nb:0.001〜0.025
%、B:0.0002〜0.0020%の1種もしくは2種を添加する
ことができる。In addition to what has been described above, in the present invention, for the purpose of further improving the fatigue resistance, Nb: 0.001 to 0.025
%, B: 0.0002 to 0.0020% of 1 type or 2 types can be added.
次にこの発明に従う製造法について説明する。Next, the manufacturing method according to the present invention will be described.
先ず製鋼法については、常法に従って行えば良く、この
発明ではそれらの条件はとくに限定しない。熱間圧延に
おいては、仕上げ温度が600℃に満たないと深絞り性が
劣化するので、600℃以上とする。冷間圧延においては
少くとも60%の圧下率でないと十分な加工性が得られな
い。冷間圧延後の連続焼鈍時における焼鈍温度は、通常
のごとく再結晶温度以上であればよいが、望ましくは
(1次再結晶温度+30℃)以上で焼鈍するのがよい。ま
た焼鈍温度がAc3を超えると粗大な結晶粒となるので、A
c3以下の温度で焼鈍する必要がある。ここの焼鈍法とし
ては箱焼鈍を用いてもよい。First, the steel-making method may be carried out according to a conventional method, and the conditions are not particularly limited in the present invention. In hot rolling, if the finishing temperature is less than 600 ° C, the deep drawability deteriorates, so the temperature is set to 600 ° C or higher. In cold rolling, sufficient workability cannot be obtained unless the rolling reduction is at least 60%. The annealing temperature at the time of continuous annealing after cold rolling may be a recrystallization temperature or higher as usual, but it is preferably an annealing temperature of (primary recrystallization temperature + 30 ° C.) or higher. Also, if the annealing temperature exceeds Ac 3 , coarse grains are formed, so A
It is necessary to anneal at a temperature below c 3 . Box annealing may be used as the annealing method here.
なお焼鈍後の調質圧延は、板形状矯正などの目的で通常
範囲(板厚(mm)%程度)で行って構わない。Note that the temper rolling after annealing may be performed within a normal range (about plate thickness (mm)%) for the purpose of straightening the plate shape.
(実施例) 表3に示す種々の組成(No.1〜18)になる鋼スラブを、
仕上げ温度:850〜900℃で熱間圧延したのち、圧下率:71
〜78%で0.8mm厚まで冷間圧延し、ついで790〜830℃の
温度範囲で連続焼鈍を施した。なおNo.18は、従来の低
炭素Alキルド鋼であり、箱焼鈍によって製造したもので
ある。(Example) Steel slabs having various compositions (No. 1 to 18) shown in Table 3 were prepared.
Finishing temperature: After hot rolling at 850-900 ℃, rolling reduction: 71
It was cold rolled to a thickness of 0.8 mm at ~ 78%, and then continuously annealed in the temperature range of 790 to 830 ° C. No. 18 is a conventional low carbon Al killed steel, which is manufactured by box annealing.
かくして得られた冷延板の機械的諸性質および引張りせ
ん断時の疲労限(1千万回)について調べた結果を表4
に示す。なお引張り試験はJIS No.5試験片を用いて行っ
た。また溶接条件は前掲表2に示したとおりである。Table 4 shows the results obtained by examining the mechanical properties of the cold-rolled sheet thus obtained and the fatigue limit (10 million cycles) during tensile shearing.
Shown in. The tensile test was performed using JIS No. 5 test pieces. The welding conditions are as shown in Table 2 above.
表4より明らかなように、この発明に従い得られた冷延
鋼板はいずれも、比較例や従来例に比べて機械的性質は
勿論のこと、耐疲労特性が格段に優れている。 As is clear from Table 4, all of the cold-rolled steel sheets obtained according to the present invention have not only mechanical properties but also excellent fatigue resistance characteristics as compared with Comparative Examples and Conventional Examples.
(発明の効果) かくしてこの発明によれば、成形加工性はいうまでもな
く、とくにスポット溶接継手の耐疲労特性に優れた加工
用冷延鋼板を得ることができる。(Effects of the Invention) Thus, according to the present invention, it is possible to obtain a cold-rolled steel sheet for working which is excellent not only in formability but particularly in fatigue resistance of spot welded joints.
第1図は、スポット溶接継手の引張りせん断疲労限に及
ぼすO量およびAl/N比の影響を示したグラフである。FIG. 1 is a graph showing the effects of O content and Al / N ratio on the tensile shear fatigue limit of spot welded joints.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 阿部 英夫 千葉県千葉市川崎町1番地 川崎製鉄株式 会社技術研究本部内 (72)発明者 西村 恵次 千葉県千葉市川崎町1番地 川崎製鉄株式 会社千葉製鉄所内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Hideo Abe 1 Kawasaki-cho, Chiba-shi, Chiba Kawasaki Steel Co., Ltd. Technical Research Headquarters (72) Inventor Keiji Nishimura 1 Kawasaki-cho, Chiba-shi Kawasaki Steel Co., Ltd. Chiba Works
Claims (2)
を、600℃以上の仕上げ温度で熱間圧延し、ついで圧下
率:60%以上で冷間圧延したのち、Ac3変態点以下の温度
で再結晶焼鈍を施すことを特徴とするスポット溶接継手
の耐疲労特性に優れる加工用冷延鋼板の製造方法。1. C: 0.0028 wt% or less, Si: 1.0 wt% or less, Mn: 1.0 wt% or less, P: 0.15 wt% or less, S: 0.0200 wt% or less, O: 0.0045 wt% or less, N: 0.0020 A steel slab containing less than wt% and Al: (30 x% N) to 0.15 wt% with the balance Fe and unavoidable impurities is hot-rolled at a finishing temperature of 600 ° C or more, and then a rolling reduction of 60 % Of cold rolling and then recrystallization annealing at a temperature of Ac 3 transformation point or lower. A method for producing a cold-rolled steel sheet having excellent fatigue resistance of a spot-welded joint.
を、600℃以上の仕上げ温度で熱間圧延し、ついで圧下
率:60%以上で冷間圧延したのち、Ac3変態点以下の温度
で再結晶焼鈍を施すことを特徴とするスポット溶接継手
の耐疲労特性に優れる加工用冷延鋼板の製造方法。2. C: 0.0028 wt% or less, Si: 1.0 wt% or less, Mn: 1.0 wt% or less, P: 0.15 wt% or less, S: 0.0200 wt% or less, O: 0.0045 wt% or less, N: 0.0020 wt% or less and Al: (30 x% N) to 0.15 wt%, and at least one selected from Nb: 0.001 to 0.025 wt% and B: 0.0002 to 0.0020 wt% with the balance being Fe and A steel slab consisting of unavoidable impurities is hot-rolled at a finishing temperature of 600 ° C or more, then cold-rolled at a rolling reduction of 60% or more, and then subjected to recrystallization annealing at a temperature not higher than the Ac 3 transformation point. A method for producing a cold-rolled steel sheet for working, which is excellent in fatigue resistance of a spot welded joint.
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP31840488A JPH0756054B2 (en) | 1988-12-19 | 1988-12-19 | Method for manufacturing cold-rolled steel sheet for processing with excellent fatigue resistance of spot welded joints |
US07/449,724 US5053194A (en) | 1988-12-19 | 1989-12-12 | Formable thin steel sheets |
EP89313064A EP0375273B1 (en) | 1988-12-19 | 1989-12-14 | Formable thin steel sheets and method of producing the same |
DE68922200T DE68922200T2 (en) | 1988-12-19 | 1989-12-14 | Formable thin steel sheets and method of making the same. |
CA002005676A CA2005676C (en) | 1988-12-19 | 1989-12-15 | Formable thin steel sheets and method of producing the same |
AU46912/89A AU608183B2 (en) | 1988-12-19 | 1989-12-18 | Formable thin steel sheets and method of producing the same |
KR1019890019000A KR970001408B1 (en) | 1988-12-19 | 1989-12-19 | Method of producing formable thin steel sheets |
US07/696,683 US5156694A (en) | 1988-12-19 | 1991-05-07 | Method of producing formable thin steel sheets |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP31840488A JPH0756054B2 (en) | 1988-12-19 | 1988-12-19 | Method for manufacturing cold-rolled steel sheet for processing with excellent fatigue resistance of spot welded joints |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH02163323A JPH02163323A (en) | 1990-06-22 |
JPH0756054B2 true JPH0756054B2 (en) | 1995-06-14 |
Family
ID=18098774
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP31840488A Expired - Fee Related JPH0756054B2 (en) | 1988-12-19 | 1988-12-19 | Method for manufacturing cold-rolled steel sheet for processing with excellent fatigue resistance of spot welded joints |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0756054B2 (en) |
-
1988
- 1988-12-19 JP JP31840488A patent/JPH0756054B2/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
JPH02163323A (en) | 1990-06-22 |
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