JPS63171832A - Production of cold rolled steel sheet having excellent ordinary temperature non-aging property and baking hardenability - Google Patents
Production of cold rolled steel sheet having excellent ordinary temperature non-aging property and baking hardenabilityInfo
- Publication number
- JPS63171832A JPS63171832A JP193287A JP193287A JPS63171832A JP S63171832 A JPS63171832 A JP S63171832A JP 193287 A JP193287 A JP 193287A JP 193287 A JP193287 A JP 193287A JP S63171832 A JPS63171832 A JP S63171832A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- rolled steel
- amount
- temp
- aging
- 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
Links
- 230000003679 aging effect Effects 0.000 title claims abstract description 17
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 10
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 19
- 239000010959 steel Substances 0.000 claims abstract description 19
- 238000011282 treatment Methods 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 238000005097 cold rolling Methods 0.000 claims abstract description 6
- 238000005096 rolling process Methods 0.000 claims abstract description 6
- 238000001953 recrystallisation Methods 0.000 claims abstract description 5
- 238000000137 annealing Methods 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052782 aluminium Inorganic materials 0.000 abstract description 3
- 230000032683 aging Effects 0.000 description 14
- 239000006104 solid solution Substances 0.000 description 14
- 238000000034 method Methods 0.000 description 9
- 239000007787 solid Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 230000035882 stress Effects 0.000 description 5
- 239000000654 additive Substances 0.000 description 4
- 230000000996 additive effect Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 229910000655 Killed steel Inorganic materials 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000001112 coagulating effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は常温非時効性及び焼付硬化性が優れ、さらに良
好な加工性を有する冷延鋼板の製造方法に関するもので
藁る。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a method for producing a cold-rolled steel sheet that has excellent non-aging properties at room temperature and bake hardenability, and also has good workability.
（従来の技術）
自動車の外板用素材として用いられる冷延鋼板は、深絞
り性、張出し性、形状性及び常温非時効性に優れている
ことが要求されるが、近年では耐プント性を向上させる
ために自動車製造工程中の塗装焼付く通常１７０℃前後
）後、鋼板の降伏応力が上昇する特性、すなわち焼付硬
化性が要求されることが多くなっている。(Prior art) Cold-rolled steel sheets used as materials for automobile exterior panels are required to have excellent deep drawability, stretchability, shapeability, and non-aging properties at room temperature. In order to improve this property, steel sheets are often required to have the property of increasing their yield stress after paint baking (usually around 170°C) during the automobile manufacturing process, that is, bake hardenability.
ところで、常温時効と焼付硬化はともに鋼板出荷時に鋼
板中に残存している固溶Ｃが拡散し、転位に偏析するこ
とによって起こる現象である。従って、焼付硬化量を増
加させるために固溶Ｃを多く残存させると常温非時効性
は劣化してしまう。By the way, room temperature aging and bake hardening are both phenomena that occur when solid solution C remaining in the steel plate at the time of shipment diffuses and segregates into dislocations. Therefore, if a large amount of solid solute C remains in order to increase the amount of bake hardening, the non-aging property at room temperature will deteriorate.
常温非時効で高焼付硬化という相矛盾した特性を得るた
めに今日まで幾多の技術が開発されてきたが、それらの
多くには共通の技術思想が見い出される。A number of techniques have been developed to date to obtain the contradictory characteristics of non-aging at room temperature and high bake hardening, but a common technical idea can be found in many of them.
すなわち、鋼が硬化したりあるいはストレツチャー・ス
トレインが発生するにはある程度の量の固溶Ｃが転位ま
で拡散しなければならない、１００’ｃｘ１時間（常温
非時効性を評価するときの熱処理条件）におけるＣの拡
散距離は１３００人であるが、１７０℃×２０分（焼付
硬化性を評価するときの熱処理条件）では５７００人と
なる。つまり、同量の固溶Ｃが残存していれば、後者の
場合により多くの固溶Ｃが転位に到達できるわけである
。従って、焼鈍後適当量の固溶Ｃを残存させると１００
℃×１時間ではストレツチャ・ストレインの発生は起こ
らないが、１７０℃×２０分では、焼付硬化の生じるこ
とが可能な固溶Ｃ量が存在する。過去の技術の多くは、
この適当量の固溶Ｃを残存させる方法について検討した
ものである。In other words, in order for the steel to harden or stretch strain to occur, a certain amount of solid solute C must diffuse to dislocations at 100'c x 1 hour (heat treatment conditions used to evaluate room temperature non-aging properties). The diffusion distance of C is 1,300 people, but it becomes 5,700 people at 170°C for 20 minutes (heat treatment conditions when evaluating bake hardenability). In other words, if the same amount of solid solution C remains, more solid solution C can reach the dislocation in the latter case. Therefore, if an appropriate amount of solid solution C remains after annealing, 100
C. for 1 hour, no stretch strain occurs, but at 170.degree. C. for 20 minutes, there is an amount of solid solute C that can cause bake hardening. Many of the past technologies
A method for leaving an appropriate amount of solid solution C was investigated.
具体的な例をあげれば、特公昭５９−２７２６号公報は
焼鈍温度を２相域で行ない、セメンタイトを凝集させ冷
却後のＣの析出サイトを減らすことによって適当量の残
存固溶Ｃを得る技術である。さらに特公昭５７−５７９
３７号公報では冷却速度をも規定した方法が示されてい
る。また、特公昭６０−１７００４号公報ではＷｂ添加
極低炭素鋼を用い連続焼鈍後６５０℃までの冷却速度を
制御することによって適当量の固溶Ｃを残存させる方法
が示されている。To give a specific example, Japanese Patent Publication No. 59-2726 discloses a technique for obtaining an appropriate amount of residual solid solution C by performing annealing at a two-phase temperature, coagulating cementite, and reducing the number of C precipitation sites after cooling. It is. Furthermore, special public service 57-579
No. 37 discloses a method in which the cooling rate is also specified. Further, Japanese Patent Publication No. 60-17004 discloses a method in which an appropriate amount of solid solution C is left by controlling the cooling rate to 650° C. after continuous annealing using Wb-added ultra-low carbon steel.
（発明が解決しようとする問題点）
しかしながら、従来のかかる技術では常温非時効性は良
好であるが、焼付硬化量が小さくユーザーの要求を十分
満足させることはできない。(Problems to be Solved by the Invention) However, although the conventional technology has good non-aging properties at room temperature, the amount of bake hardening is small and cannot fully satisfy user requirements.
（問題点を解決するための手段）
そこで、本発明者らはかかる問題を解決するため詳細な
研究を行なった結果、通常のアルミキルド鋼にＭｏ、
Ｓｎ＋ ｓｂのうちいずれか１種を添加することによっ
て常温非時効性を保ちながら従来よりも高い焼付硬化性
を得ることを見い出したのである。(Means for solving the problem) Therefore, the present inventors conducted detailed research to solve the problem, and found that Mo.
It was discovered that by adding one of Sn+sb, it is possible to obtain higher bake hardenability than before while maintaining non-aging property at room temperature.
すなわち、本発明の要旨とするところは、重量％で
Ｃ： ０．０１〜０．０４％、 Ｍｎ： ０．０５〜０
．４％。That is, the gist of the present invention is that C: 0.01 to 0.04%, Mn: 0.05 to 0 in weight%.
．． 4%.
Ｐ：０．０３％以下、Ｔｏｔａｌ Ａ ｌ ： ０．０
．２〜０．０８％。P: 0.03% or less, Total Al: 0.0
．． 2-0.08%.
かつ（イ） Ｍｏ： ０．０６〜０．３５％（ロ）Ｓｎ
：０．０１〜０．１％
（ハ）Ｓｂ：０．０１〜０．１％
のうちいずれか１種を含有し、残部はＦｅ及び不可避的
不純物からなる熱延鋼板を冷間圧延した後再結晶温度以
上Ａｒｓ点以下の温度範囲での加熱、冷却、２５０℃以
上４００℃以下の温度範囲での過時効処理のそれぞれを
施こす連続焼鈍を行ない、次いで調質圧延することを特
徴とする常温非時効性及び焼付硬化性の優れた冷延鋼板
の製造方法にある。and (a) Mo: 0.06-0.35% (b) Sn
: 0.01 to 0.1% (c) Sb: After cold rolling a hot rolled steel sheet containing any one of 0.01 to 0.1%, the remainder being Fe and unavoidable impurities. It is characterized by successive annealing in which heating is performed in a temperature range above the recrystallization temperature and below the Ars point, cooling, and overaging treatment in a temperature range above 250°C and below 400°C, followed by temper rolling. The present invention provides a method for producing a cold-rolled steel sheet with excellent non-aging properties and bake hardenability at room temperature.
以下に本発明の詳細な説明する。最初に本発明の対象と
する鋼における各成分の限定理由について述べる。The present invention will be explained in detail below. First, the reasons for limiting each component in the steel targeted by the present invention will be described.
まず、Ｃは０．０１％以上存在しないと連続焼鈍後Ｃの
過飽和度が足りなくなり、常温非時効性が劣化する。ま
た、０．０４％を超えるとｒ値や延性の劣化をもたらす
ので、Ｃは０．０１〜０．０４％とした。First, if 0.01% or more of C is not present, the degree of supersaturation of C will be insufficient after continuous annealing, and the non-aging property at room temperature will deteriorate. Moreover, since if it exceeds 0.04%, the r value and ductility will deteriorate, so the C content is set to 0.01 to 0.04%.
Ｍｎはその量が低い程、ｒ値が向上する。従ってできる
限り低い方が好ましいが、熱間脆性を引き起こすＳを無
害化するため０．０５〜０．４％にする必要がある。The lower the amount of Mn, the higher the r value. Therefore, it is preferable to keep the content as low as possible, but it is necessary to keep it at 0.05 to 0.4% in order to render S, which causes hot embrittlement, harmless.
Ｐもその量が低い程ｒ値が向上するので、０．０３％以
下とする。Since the lower the amount of P, the better the r value is, it is set to 0.03% or less.
Ｔｏｔａｌ Ａｔ’ は強力な脱酸剤としての役割を
有するのみならず、鋼中のＮをＡＪ！Ｎとして固定し固
溶Ｎによる常温時効を防止する働きがあるので０．０２
％以上は必要である。しかしながら０．０８％を超える
とｒ値が劣化するためＴｏｔａｌ Ａ１ は０．０２
〜０．０８％とする。Total At' not only acts as a strong deoxidizing agent, but also removes N in steel from AJ! 0.02 because it is fixed as N and has the function of preventing room temperature aging due to solid solution N.
% or more is necessary. However, if it exceeds 0.08%, the r value deteriorates, so Total A1 is 0.02
~0.08%.
次に本発明における最も重要な特徴であるＭｏ。Next, Mo is the most important feature of the present invention.
Ｓｎ＋ ｓｂの添加理由について述べる。The reason for adding Sn+sb will be described.
前述したように出荷時に残存している固溶Ｃ量によって
常温非時効性と焼付硬化量が一義的に定まるが、本発明
者らは従来と同程度の常温非時効性を保ちつつより高い
焼付硬化性を有するような添加元素を見い出した。すな
わち、供試材として第１表に示すような成分を有する鋼
について通常の手段により製鋼、造塊、熱延（仕上げ温
度８８０℃、巻取り温度７１０℃）、冷延（圧下率７５
％）等を行ない厚さ０．８鶴の冷延板とした後、８１０
℃で７０秒間加熱し、約１００℃／ｓｅｃで冷却し、次
いで３５０℃で４分間の過時効処理を行なった後、１％
のスキンパスを施した。As mentioned above, the amount of solid solution C remaining at the time of shipment uniquely determines the non-aging property at room temperature and the amount of bake hardening. We have discovered an additive element that has hardenability. That is, steel having the components shown in Table 1 as a test material was manufactured by normal means, ingot-formed, hot rolled (finishing temperature 880°C, coiling temperature 710°C), and cold rolled (reduction ratio 75°C).
%) etc. to make a cold-rolled plate with a thickness of 0.8 mm, and then
After heating at ℃ for 70 seconds, cooling at about 100℃/sec, and then overaging at 350℃ for 4 minutes, 1%
A skin pass was applied.
各試料について人工時効処理（１００℃×１時間）後の
降伏伸びによって常温非時効性を評価した。これは降伏
伸びが０．２％以下まではストレッチャ・ストレインが
発生しないという対応関係があるからである。また、焼
付硬化性は〔２％引張−１７０℃×２０分熱処理後の降
伏応力〕−〔２％引張時の応力〕をもって評価した。各
元素の添加量に対する焼付硬化量を第１図に、また人工
時効後の降伏伸びを第２図に示す。両図かられかるよう
にアルミキルド鋼にこれらの元素を添加すると、焼付硬
化量は増加していくが、人工時効後の降伏伸びは０．２
％以下のままほとんど変化しない。The room temperature non-aging property of each sample was evaluated by the yield elongation after artificial aging treatment (100°C x 1 hour). This is because there is a correspondence relationship in which stretcher strain does not occur until the yield elongation is 0.2% or less. In addition, the bake hardenability was evaluated by [2% tension - yield stress after heat treatment at 170°C for 20 minutes] - [stress at 2% tension]. Figure 1 shows the amount of bake hardening with respect to the amount of each element added, and Figure 2 shows the yield elongation after artificial aging. As can be seen from both figures, when these elements are added to aluminum killed steel, the amount of bake hardening increases, but the yield elongation after artificial aging is 0.2.
% and remains almost unchanged.
第１図から焼付硬化量が顕著に増加しはじめるのは、Ｍ
ｏの場合０．０６％以上、Ｓｎの場合は０．０１％以上
、またｓｂの場合は０．０１％以上である。これらの元
素の添加量を増す程焼付硬化量は上昇するが、−男鹿工
性は劣化していく。ｒ値への影響を示したのが第３図で
ある。同図からｒ値が急激に劣化するのは、ＭＯの場合
は０．３５％超、Ｓｎでは０、１％超、ｓｂでは０．１
％超である。以上よりＭｏは０．０６〜０．３５％、Ｓ
ｎは０．０１〜０．１％、ｓｂは０．０１〜０．１％と
した。From Fig. 1, the amount of bake hardening starts to increase noticeably because M
In the case of o, it is 0.06% or more, in the case of Sn, it is 0.01% or more, and in the case of sb, it is 0.01% or more. As the amount of these elements added increases, the amount of bake hardening increases, but the Oga workability deteriorates. FIG. 3 shows the influence on the r value. From the same figure, the r value rapidly deteriorates by more than 0.35% for MO, 0.1% for Sn, and 0.1% for sb.
% or more. From the above, Mo is 0.06-0.35%, S
n was 0.01 to 0.1%, and sb was 0.01 to 0.1%.
？１ｏ、 Ｓｎ、 Ｓｂを添加することによって焼付硬
化量が増加するという現象の原因を調べるために、本実
験に用いた試験材に残存する固溶Ｃ量を内部摩擦法によ
って測定したところ、各−加元素が増えるほど固溶Ｃ量
が増加し、かつ固溶Ｃ量と焼付硬化量との対応関係は従
来から報告されている関係と一致することがわかった。? In order to investigate the cause of the phenomenon that the amount of bake hardening increases with the addition of 1o, Sn, and Sb, the amount of solid solute C remaining in the test material used in this experiment was measured by the internal friction method, and it was found that each - It was found that as the added element increases, the amount of solid solute C increases, and the correspondence relationship between the amount of solid solute C and the amount of bake hardening coincides with the relationship that has been previously reported.
従って、各添加元素の増量によって焼付硬化量が上昇し
たのは、残存固溶Ｃが増加したためであるといえる。残
存固溶Ｃ量が増加する理由についてはさだがではないが
、これら元素が、Ｃの拡散を遅らせること、あるいは炭
化物の析出の進行を抑制すること、などがありうると思
われる。また、これらの添加元素を増量することによっ
て焼付硬化量が上昇（すなわち残存固溶Ｃ量が増加）す
るにもかかわらず、常温非時効性が劣化しない理由につ
いても現在のところ明らかではないが、本発明者らは以
下のように推測している。Therefore, it can be said that the increase in the amount of bake hardening due to the increase in the amount of each additive element is due to the increase in the residual solid solution C. Although we cannot say anything about the reason why the amount of residual solid solution C increases, it is thought that these elements may delay the diffusion of C or suppress the progress of carbide precipitation. Furthermore, although the amount of bake hardening increases (that is, the amount of residual solid solute C increases) by increasing the amount of these additive elements, it is currently not clear why the non-aging property at room temperature does not deteriorate. The present inventors speculate as follows.
すなわち、一般に鋼を軽加工する場合鋼中に転位の移動
の障害となるものが存在するとそうでない場合に比べて
同じ加工度に対する転位密度が高くなる。これは鋼に加
えられた全歪量を確保するのに転移の移動距離でかせげ
ない分を転位密度の上昇によって、補わなければならな
いからである。That is, in general, when steel is lightly worked, if something that obstructs the movement of dislocations is present in the steel, the dislocation density for the same working degree will be higher than when there is no obstacle to the movement of dislocations. This is because, in order to ensure the total amount of strain applied to the steel, the amount that cannot be gained by the distance traveled by the dislocations must be compensated for by increasing the dislocation density.
Ｍｏ＋ Ｓｎ＋ ｓｂはいずれもＦｅに比べてその原子
半径が大きい。これらの元素が固溶していると転位の移
動の障害となり、スキンパス圧延時の転位密度の増加分
が大きくなる。残存固溶Ｃの増加にもかかわらず、常温
非時効性が劣化しないのはこのためであると考えられる
。Both Mo+ Sn+ sb have a larger atomic radius than Fe. When these elements are in solid solution, they become an obstacle to the movement of dislocations, and the increase in dislocation density during skin pass rolling becomes large. This is thought to be the reason why the non-aging property at room temperature does not deteriorate despite the increase in residual solid solution C.
次に、製造条件の限定理由について述べる。まず、通常
の熱延を終了した後の冷延における冷延圧下率は、加工
性とくにｒ値を確保するためには６０％以上が望ましい
、連続焼鈍における加熱温度を再結晶温度以上とするの
は鋼を軟質化するための必要条件である。また＾ｒ１点
を超えて焼鈍するとｒ値が劣化するので加熱温度は再結
晶温度以上Ａｒ、点板下とする。加熱時間は特に限定し
ないが、長時間加熱すると異常粒成長が起こり肌荒れの
原因となる恐れがあるので５分以内が望ましい。Next, the reasons for limiting the manufacturing conditions will be described. First, the cold rolling reduction ratio in cold rolling after finishing normal hot rolling is preferably 60% or more in order to ensure workability, especially the r value. is a necessary condition for softening steel. Also, if annealing is performed beyond the ^r1 point, the r value will deteriorate, so the heating temperature should be Ar above the recrystallization temperature and below the dot plate. The heating time is not particularly limited, but heating for a long time may cause abnormal grain growth and cause rough skin, so it is preferably within 5 minutes.
加熱後の冷却速度は特に限定しないが、過時効処理の時
間を短縮するためには５℃／ｓｅｃ以上が望ましい。The cooling rate after heating is not particularly limited, but is preferably 5° C./sec or more in order to shorten the overaging treatment time.
過時効処理についてはその温度を４００℃超にすると残
存固溶Ｃ量が多くなりすぎ常温非時効性が劣化するため
４００℃以下とする。また、２５０℃未満の温度では過
時効処理の時間を長くしなければならない、従って、過
時効処理の温度は２５０℃以上４００℃以下とする。過
時効処理の時間は特に限定しないが、連続焼鈍の性質上
、３０分以内が望ましい、調質圧延はストレッチ中・ス
トレインを消すために欠かせない工程である。圧下率は
特に限定しないが、１％程度が望ましい。Regarding the over-aging treatment, if the temperature exceeds 400°C, the amount of residual solid solution C increases too much and the non-aging property at room temperature deteriorates, so the temperature is set at 400°C or lower. Further, at a temperature lower than 250°C, the overaging treatment time must be lengthened. Therefore, the overaging treatment temperature is set to 250°C or more and 400°C or less. The time for overaging treatment is not particularly limited, but due to the nature of continuous annealing, it is preferably within 30 minutes. Temper rolling is an essential step to eliminate strain during stretching. The rolling reduction rate is not particularly limited, but is preferably about 1%.
なお、本発明法に用いられる鋼は通常の製鋼、連鋳ある
いは普通造塊、分塊、熱延、冷延の各種工程を経て冷延
鋼板とすることができる。The steel used in the method of the present invention can be made into cold-rolled steel sheets through various processes such as ordinary steel manufacturing, continuous casting, ordinary ingot making, blooming, hot rolling, and cold rolling.
次に、実施例により本発明の効果をさらに具体的に示す
。Next, the effects of the present invention will be illustrated more specifically by examples.
（実施例）
第２表に示す鋼について通常の工程を経て厚さ０．８ｍ
の冷延板を製造した後、第３表に示す条件で、連続焼鈍
及び過時効処理を行ない、１％のスキンパスを施し、し
かるのち、第３表に示す時効前の機械的性質を調べ、さ
らに人工時効処理（１００℃×１時間）後の降伏伸び及
び焼付硬化量を〔２％歪−１７０℃×２０分後の降伏応
力〕−〔２％歪時の応力〕の条件で測定した。なお、こ
れら機械的特性値はすべてＪＩＳ Ｓ号試験片をインス
トロン型引張試験機により測定した値である。(Example) The steel shown in Table 2 was processed to a thickness of 0.8 m through the normal process.
After producing a cold-rolled sheet, it was subjected to continuous annealing and over-aging treatment under the conditions shown in Table 3, subjected to a 1% skin pass, and then examined for mechanical properties before aging shown in Table 3. Further, the yield elongation and bake hardening amount after artificial aging treatment (100°C x 1 hour) were measured under the following conditions: [2% strain - yield stress after 170°C x 20 minutes] - [stress at 2% strain]. Note that all of these mechanical property values are values measured using an Instron type tensile tester using a JIS No. S test piece.
第３表において賦香１１ｈｌ〜患ｌｌは本発明例、Ｎ１
１２〜阻１８が比較例である０本発明例はいずれも人工
時効後の降伏伸びが０．２％以下とストレッチャ・スト
レインが発生しない条件を満たし、かつ焼付硬化量は４
−８ ｋｇ ｆ ／ ｔｍ ”〜６．２ ｋｇ ｆ ／
ｗ ”と高い値になっている。またｒ値も１．４以上
あり加工性も優れている。これに対して比較例！ｌｈｌ
５゜嵐１７及びＮａ１８は人工時効後の降伏伸びは０
．２％以下であるが、焼付硬化量は３．７ ｋｇ ｆ
／１ｍ”〜４、Ｏｋｇｆ／ｍ冨と低い、また、嵐１６は
焼付硬化量は５．２ｋｇｆ／ｆｉ”と高いが、人工時効
後の降伏伸びが０．５％もあり常温非時効性を満足して
いない、比較例隘１２〜患１４は添加元素を多量に含有
するため常温非時効でかつ高い焼付硬化性を有するがｒ
値が劣化した例である。In Table 3, incense 11hl to patient 1 are examples of the present invention, N1
12 to 18 are comparative examples. All of the invention examples have a yield elongation of 0.2% or less after artificial aging, which satisfies the condition that no stretcher strain occurs, and the bake hardening amount is 4.
-8 kg f/tm”~6.2 kg f/
It has a high value of ``w''. Also, the r value is 1.4 or more and the workability is excellent.In comparison, the comparative example! lhl
5゜Arashi 17 and Na18 have 0 yield elongation after artificial aging.
．． Although it is less than 2%, the bake hardening amount is 3.7 kg f
Arashi 16 has a high bake hardening amount of 5.2 kgf/fi'', but the yield elongation after artificial aging is as high as 0.5%, making it non-aging at room temperature. Comparative Examples Nos. 12 to 14, which are not satisfied, contain a large amount of additive elements, so they are non-aging at room temperature and have high bake hardenability.
This is an example where the value has deteriorated.
（発明の効果）
以上の実施例からも明らかなように、本発明によれば常
温非時効性に優れかつ高い焼付硬化性を有する冷延鋼板
の製造が可能となり産業上の効果は極めて顕著である。(Effects of the Invention) As is clear from the above examples, the present invention makes it possible to produce cold-rolled steel sheets that have excellent room-temperature non-aging properties and high bake hardenability, and the industrial effects are extremely significant. be.
第１図は焼付硬化量に及ぼすＭｏ、 Ｓｎ、 Ｓｂ各元
素の添加量の影響を示した図、第２図は人工時効後の降
伏伸びに及ぼすＭｏ＋ Ｓｎ、 ｓｂ各元素の添加量の
影響を示した図、第３図はｒ値に及ぼすＭｏ、 Ｓｎ。
ｓｂ各元素の添加量の影響を示した図である。
第１図
庫疋元衆ｔ（％）
第２図
添加元泉量（％）Figure 1 shows the effects of the amounts of Mo, Sn, and Sb added on the amount of bake hardening, and Figure 2 shows the effects of the amounts of Mo+Sn and sb added on the yield elongation after artificial aging. The figure shown in Figure 3 shows the effects of Mo and Sn on the r value. sb is a diagram showing the influence of the amount of each element added. Figure 1: Added source water (%) Figure 2: Added source amount (%)
Claims (1)
、Ｐ：０．０３％以下、Ｔｏｔａｌ Ａｌ：０．０２〜
０．０８％かつ（イ）Ｍｏ：０．０６〜０．３５％ （ロ）Ｓｎ：０．０１〜０．１％ （ハ）Ｓｂ：０．０１〜０．１％ のうちいずれか１種を含有し、残部はＦｅ及び不可避的
不純物からなる熱延鋼板を冷間圧延した後再結晶温度以
上Ａｒ＿３点以下の温度範囲での加熱、冷却、２５０℃
以上４００℃以下の温度範囲での過時効処理のそれぞれ
を施こす連続焼鈍を行ない、次いで調質圧延することを
特徴とする常温非時効性及び焼付硬化性の優れた冷延鋼
板の製造方法。[Claims] C: 0.01 to 0.04%, Mn: 0.05 to 0.4% by weight
, P: 0.03% or less, Total Al: 0.02~
Any one of the following: 0.08% and (a) Mo: 0.06-0.35% (b) Sn: 0.01-0.1% (c) Sb: 0.01-0.1% After cold-rolling a hot-rolled steel sheet containing Fe and the remainder consisting of Fe and unavoidable impurities, heating and cooling in a temperature range from the recrystallization temperature to Ar_3 points at 250 ° C.
A method for producing a cold-rolled steel sheet with excellent room-temperature non-aging properties and bake hardenability, characterized by carrying out continuous annealing with each of the over-aging treatments in a temperature range of 400° C. or less, followed by temper rolling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP193287A JPH07100818B2 (en) | 1987-01-09 | 1987-01-09 | Method for producing cold-rolled steel sheet excellent in normal temperature non-aging property and bake hardenability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP193287A JPH07100818B2 (en) | 1987-01-09 | 1987-01-09 | Method for producing cold-rolled steel sheet excellent in normal temperature non-aging property and bake hardenability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63171832A true JPS63171832A (en) | 1988-07-15 |
| JPH07100818B2 JPH07100818B2 (en) | 1995-11-01 |
Family
ID=11515380
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP193287A Expired - Lifetime JPH07100818B2 (en) | 1987-01-09 | 1987-01-09 | Method for producing cold-rolled steel sheet excellent in normal temperature non-aging property and bake hardenability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07100818B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100544538B1 (en) * | 2001-12-21 | 2006-01-24 | 주식회사 포스코 | High Strength Bake Hardening Steel Sheet With Good Workability and Non Aging Property at Room Temperature and A Method for Manufacturing Thereof |
| WO2007067014A1 (en) * | 2005-12-09 | 2007-06-14 | Posco | Tole d'acier laminee a froid de haute resistance possedant une excellente propriete de formabilite et de revetement, tole d'acier plaquee de metal a base de zinc fabriquee a partir de cette tole et procece de fabrication de celle-ci |
| WO2012043420A1 (en) * | 2010-09-29 | 2012-04-05 | Ｊｆｅスチール株式会社 | High-strength hot-dip galvanized steel sheet with excellent deep drawability and stretch flangeability, and process for producing same |
-
1987
- 1987-01-09 JP JP193287A patent/JPH07100818B2/en not_active Expired - Lifetime
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100544538B1 (en) * | 2001-12-21 | 2006-01-24 | 주식회사 포스코 | High Strength Bake Hardening Steel Sheet With Good Workability and Non Aging Property at Room Temperature and A Method for Manufacturing Thereof |
| WO2007067014A1 (en) * | 2005-12-09 | 2007-06-14 | Posco | Tole d'acier laminee a froid de haute resistance possedant une excellente propriete de formabilite et de revetement, tole d'acier plaquee de metal a base de zinc fabriquee a partir de cette tole et procece de fabrication de celle-ci |
| WO2012043420A1 (en) * | 2010-09-29 | 2012-04-05 | Ｊｆｅスチール株式会社 | High-strength hot-dip galvanized steel sheet with excellent deep drawability and stretch flangeability, and process for producing same |
| JP2012092427A (en) * | 2010-09-29 | 2012-05-17 | Jfe Steel Corp | High strength hot dip galvanized steel sheet excellent in deep drawability and stretch flangeability, and its producing method |
| US9598755B2 (en) | 2010-09-29 | 2017-03-21 | Jfe Steel Corporation | High strength galvanized steel sheet having excellent deep drawability and stretch flangeability and method for manufacturing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07100818B2 (en) | 1995-11-01 |
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