JPS5811743A - Manufacture of soft cold-rolled steel plate which is excellent in aging resistance, by continuous annealing - Google Patents
Manufacture of soft cold-rolled steel plate which is excellent in aging resistance, by continuous annealingInfo
- Publication number
- JPS5811743A JPS5811743A JP10878281A JP10878281A JPS5811743A JP S5811743 A JPS5811743 A JP S5811743A JP 10878281 A JP10878281 A JP 10878281A JP 10878281 A JP10878281 A JP 10878281A JP S5811743 A JPS5811743 A JP S5811743A
- Authority
- JP
- Japan
- Prior art keywords
- temperature
- annealing
- cooling
- cooling rate
- rolled steel
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は連続W8鈍による耐時効性の優れた軟質冷延鋼
板の製造方法の創案に係り、耐時効性の優れた軟質冷延
剛板を的1i11に製造することのできる方法を提供し
ようとするものである。[Detailed Description of the Invention] The present invention relates to the creation of a method for manufacturing a soft cold-rolled steel sheet with excellent aging resistance by continuous W8 dulling, and aims at manufacturing a soft cold-rolled steel sheet with excellent aging resistance. The aim is to provide a method that allows for
連続焼鈍によって絞り用冷延鋼板を製造することについ
ては従来からそれなりに知られているが、この連続焼鈍
によって絞り用冷延鋼板の製造が可能となった背景には
、熱延時の巻取り温度を^めてAANの析出およびカー
バイトの粗大化を図っておくことKLす、乍延後の急速
加熱焼鈍でも、絞り用鋼板として好ましい貴結晶フェラ
イト粒の十分な粒成長を促すこと、および絞り用鋼板に
おいて材質劣化の主因となる歪時効性を響滅する目的か
ら、フェライト中の侵入型固溶元素、l#KCを短時間
処理で析出させるため、焼鈍後、急速冷却にエリCを逼
飽和固溶状態とした上でその過飽和度を駆動力として過
時効処理を行なうこと、02点がある。The production of cold-rolled steel sheets for drawing by continuous annealing has been well known for some time, but the reason behind the production of cold-rolled steel sheets for drawing by continuous annealing is In addition, even during rapid heating annealing after rolling, sufficient grain growth of noble crystal ferrite grains, which is preferable as a steel sheet for drawing, should be promoted, and drawing should be carried out. In order to precipitate l#KC, an interstitial solid solution element in ferrite, in a short time in order to eliminate strain aging, which is the main cause of material deterioration in steel sheets for industrial use, after annealing, ERIC is saturated during rapid cooling. Point 02 is to bring it into a solid solution state and then perform an overaging treatment using the supersaturation degree as a driving force.
しかし、連続焼鈍で製造した軟質冷延鋼板は、通常の箱
焼鈍法で製造した軟質冷延鋼板が有する低強度、高嫁性
、高深絞り性、非時効性の纏べての要件を満足するまで
Kは至っておらず、絞り用鋼板としては中級グレード以
下に位置する製品が主体である。これは、短時間の加熱
焼鈍では、十分なフエチイト粒成長が得られない。フェ
ライト中の固溶Cを過時効処理段階で完全に析出させる
ことができないなどの点が支配畳因となっている。そこ
で、連続焼鈍で工9軟質な冷娠鋼板の製造を目的として
、フェライトの粒成長を促す方法およびフェライト中の
侵入型固溶元素(と<vcC)を時効が[11とならな
いレベルまで下げる方法について多くの検討がなされて
いる。この円、前者については通常の低C系の鋼におい
ても、高温焼鈍を行うなどして、比較的容易に所望の材
質レベルを得ることが可能である。しかし、後者につい
ては、コストを度外視すると、予め脱ガス処理によって
鋼中のCを低減させた上で残存するCを固定するに尾る
πなどを添加する方法などがあるが、低コストで有利に
展開出来る技術は未だ見出されていない。これは、従来
の連続焼鈍では、過時効処理段階で十分にフェライト中
の固溶Cを析出させることが出来ないためである。However, soft cold-rolled steel sheets manufactured by continuous annealing satisfy all the requirements of low strength, high marriageability, high deep drawability, and non-aging properties of soft cold-rolled steel sheets manufactured by ordinary box annealing. K has not yet been achieved, and steel sheets for drawing are mainly products that are below intermediate grade. This is because short-time heating annealing does not allow sufficient growth of feetite grains. The dominant factor is that solid solution C in ferrite cannot be completely precipitated in the overaging treatment stage. Therefore, with the aim of manufacturing soft cold steel sheets with continuous annealing, we have developed a method to promote ferrite grain growth and a method to reduce the interstitial solid solution elements (and <vcC) in ferrite to a level where aging does not become [11]. Many studies have been made regarding this. Regarding the former, it is possible to obtain a desired material level relatively easily even with ordinary low-C steel by performing high-temperature annealing. However, regarding the latter, if we ignore the cost, there are methods such as reducing C in the steel by degassing in advance and then adding π or the like to fix the remaining C, but this method is advantageous at low cost. No technology has yet been discovered that can be used to develop this technology. This is because conventional continuous annealing cannot sufficiently precipitate solid solution C in ferrite during the overaging treatment stage.
本発明は上記したような実情に鑑み検討を1ねて創案さ
れたものであって、特別K11II殊元素を添加するこ
となく、連続焼鈍方法の改善のみKより軟質冷延鋼板の
耐時効性を有効に向上させることに成功した。即ち本発
明においてを1連続焼鈍における焼鈍加熱温度からの冷
却/豐ターンを;ントロールすること#cLり材質の劣
化tt伴うことなく、時効性を著しく改善するものであ
って、この冷却パターンのコントロールについては以下
の条件を満足させることを骨子とする。The present invention was devised after careful consideration in view of the above-mentioned circumstances, and is intended to improve the aging resistance of soft cold-rolled steel sheets by improving the continuous annealing method without adding special K11II special elements. succeeded in improving it effectively. That is, in the present invention, the aging property is significantly improved without deterioration of the material by controlling the cooling/turning from the annealing heating temperature in one continuous annealing, and the cooling pattern is controlled. The main point is to satisfy the following conditions.
■ 焼鈍加熱温度からの冷却過程で、鋼中温度がムr1
変態温度以上のgA斌での冷゛却速度(vl )を下記
の条件にコントロールする。■ During the cooling process from the annealing heating temperature, the temperature inside the steel is uneven.
The cooling rate (vl) at gA above the transformation temperature is controlled under the following conditions.
焼鈍温度(T))>750℃の場合
V* <−0,2Tj+180 (C/秒)焼鈍温度
(Tj)<750℃の場合
Vtは任意とする。When annealing temperature (Tj)>750°C, V* <-0,2Tj+180 (C/sec) When annealing temperature (Tj)<750°C, Vt is arbitrary.
■ 鋼中温度が、Arlから急冷開始温度TQ(600
℃から500℃の温度範囲の任意の温度)K至るまでの
冷却速!(Vs)を。■ The temperature in the steel changes from Arl to the quenching start temperature TQ (600
Any temperature in the temperature range from °C to 500 °C ) cooling rate up to K! (Vs).
40℃/秒以上100℃/秒以下の範囲とする。The temperature should be in the range of 40°C/sec or more and 100°C/sec or less.
■ −帯温度が、TQから200℃以下に至るまでの冷
却速度(Vs )t’ 250で7秒以上とする。- Cooling rate (Vs) t' 250 for 7 seconds or more until the zone temperature reaches 200°C or less from TQ.
■ 係る鋼中を300℃以上%400℃以下の温度で過
時効処理を行う。■ Perform overaging treatment on the steel at a temperature of 300°C or higher and 400°C or lower.
本発明は、上記の諸条件を満足させて連続焼鈍を行うこ
とに1って、優れた延性と遅時効性を具備した絞り用冷
延鋼板の製造を可能にするものであり、通常使用されて
いる一般の軟質冷延鋼板用の鋼種全てに適用出来るもの
である。The present invention makes it possible to manufacture a cold-rolled steel sheet for drawing with excellent ductility and slow aging properties by performing continuous annealing while satisfying the above conditions. It can be applied to all general steel types for soft cold-rolled steel sheets.
本発明を構成する上記の各要件について更I/Ca12
明をすると、先ず連続焼鈍にて、優れた耐時効性を有す
る冷延鋼板を製造するためKは、既に述べたように焼鈍
温度からの冷却溝相で、フェライト中の固溶Cを過飽和
状態とし、この1飽種度を駆動力として過時効処理段I
Il#に@i待時間フェライト中の固溶Cの析出を図る
。こ\で、この過飽和度が不十分な場合は、十分なC析
出の駆動力が得られないため、長時間の過時効処理を必
要とするばかりか、Cの十分な析出を図ることが出来ず
、残存固溶CKよる焼鈍板の歪時効が問題となる。Further information on each of the above requirements constituting the present invention I/Ca12
To be clear, in order to produce a cold-rolled steel sheet with excellent aging resistance through continuous annealing, K is used to supersaturate solid solution C in ferrite in the cooling groove phase from the annealing temperature, as mentioned above. Using this 1 saturation type as a driving force, the overaging treatment stage I
Attempt to precipitate solid solution C in ferrite during @i waiting time in Il#. If this degree of supersaturation is insufficient, sufficient driving force for C precipitation cannot be obtained, which not only necessitates a long overaging treatment but also makes it impossible to achieve sufficient C precipitation. First, strain aging of the annealed plate due to residual solid solution CK becomes a problem.
そこで、連#!#i鈍においては、過時効処理前に然る
べき急冷処理を行う訳であるが、その時どの程度の過飽
和固溶C量に達した場合に、過時効処理で焼M&の歪時
効が間亀にならない程度まで固#Ctl−減少させ得る
がにっ−て説明すると、第1図は、過時効処理後の時効
指数にお工ぼす急冷時の過飽和同浴C量の影響を示した
ものである。即ち図中の点はC量0.015〜0.04
4憾の種々の鋼について示したものであるが、過時効処
理後の時効指数は鋼成分によらず、急冷時の固溶C1l
と過時効処理条件ではソー義的に決まることが解かる。So, consecutive #! For #i blunt, appropriate quenching treatment is performed before overaging treatment, but at what level of supersaturated solid solute C is reached at that time, strain aging of fired M& is not slowed down by overaging treatment. Figure 1 shows the influence of the amount of C in the supersaturated bath during quenching on the aging index after overaging treatment. . In other words, the points in the figure indicate the C content of 0.015 to 0.04.
This is shown for 4 different steels, but the aging index after overaging treatment is independent of the steel composition, and the solid solute C1l during quenching is
It can be seen that under the over-aging treatment conditions, it is determined in a So-like manner.
つまり、歪時効かはy問題とならないレベルである時効
指数(AI)〈3.5kII7/−を得るためには1冷
時の固溶C1Q−息を、Q−”)80XIO″″’ (
>138 ppm )とすれ(> 156 ppwa
)とするのが好ましいが、−一般的にはAx(a、5に
9//−であれば歪時効性は問題とならない、斯うしだ
ム1の規定については、別に第2図に明記する所である
。In other words, in order to obtain an aging index (AI) <3.5kII7/-, which is at a level where strain aging is not a problem, the solid solute C1Q-breath during cooling is Q-")80XIO""' (
>138 ppm) and (>156 ppwa
), but in general, strain aging is not a problem if Ax (a, 5 to 9//-).The provisions of ``Shidam 1'' are separately specified in Figure 2. This is the place to do it.
従って、連続焼鈍で製造する軟質冷延鋼板の時効性を改
善するためには、過時効処理前にフェライト中の固溶C
1をQ−’ >80 X10−4とすべく、連続焼鈍熱
サイクルを制御する必要がある。つまり、本発明は上記
の工5な思alK基づいているもので、連続焼鈍過8K
j?いて、焼鈍板の延性の劣化を米たすことなく所望の
過飽和固溶C量を得る冷却/#ターンを規定することに
新規性がある。Therefore, in order to improve the aging properties of soft cold-rolled steel sheets manufactured by continuous annealing, it is necessary to
It is necessary to control the continuous annealing heat cycle in order to make Q-'>80X10-4. In other words, the present invention is based on the above-mentioned technical concept, and the continuous annealing process is 8K.
j? Therefore, there is a novelty in defining the cooling/#turn to obtain the desired amount of supersaturated solid solution C without compromising the deterioration of the ductility of the annealed plate.
次KIiM温度(T〕)からの冷却条件について規定理
由を詳細に説明すると、第3図は後述する第1表中の鋼
1.3について連続焼鈍加熱・冷却退場でのフェライト
中のlii溶C量の変化を示したものである。この第3
図から明かなように、加熱温度で1分の均熱を行う場合
、フェライト中の固溶Cは、鋼のCl1Kよらず、Fs
−C系状態図から予想される#tソ平向値に達する。然
し、冷却過程(空冷)でのフェライト中の固lWCは著
しく非平衡の伏動で冷却されることが解り、この非平殉
冷却の6度はC量お工び温度に1って異る。そこで、急
冷を行う時点で出来る限りフェライト中の固溶Cilを
増加させるためには、Pb−C系状態図から判断して、
Arl変態温度以上の湿度領域はできる限り冷却速度を
遅くして平衡状Ill#c近い状態で、ArI変ism
度以下の湿度領域はできる限り冷却速度を速くして非平
衡状■で冷却を行うのが有効であると考えられる。To explain in detail the reasons for specifying the cooling conditions from the following KIiM temperature (T), Figure 3 shows the Lii molten C in ferrite during continuous annealing heating and cooling for Steel 1.3 in Table 1, which will be described later. This shows the change in quantity. This third
As is clear from the figure, when soaking for 1 minute at the heating temperature, the solid solution C in ferrite does not depend on Cl1K of steel, but on Fs
- The #t so-plane value expected from the C system phase diagram is reached. However, during the cooling process (air cooling), it was found that the solid lWC in the ferrite was cooled by a significantly non-equilibrium downward movement, and this non-equilibrium cooling of 6 degrees was 1 degree different from the carbon content and processing temperature. . Therefore, in order to increase the solid solution C in the ferrite as much as possible at the time of rapid cooling, judging from the Pb-C system phase diagram,
In the humidity region above the Arl transformation temperature, the cooling rate is slowed down as much as possible to maintain a state close to the equilibrium state Ill#c, and ArI transformation is carried out.
It is considered effective to perform cooling in a non-equilibrium state (2) by increasing the cooling rate as much as possible in the humidity region below 30°C.
第4図(alは、焼鈍温度から2.5〜b秒の範囲の冷
却速度で冷却したときの、Ar1(ニア00℃)でのフ
ェライト中の固溶C量を、各々の冷却速度で700Cま
で冷却した後直ちに焼き入れ処理を行った状Vで測定し
た結果を示す、この図から明かな工うに、高温で焼鈍を
行った場合、700℃の固溶C量を第1図で示したQ″
′″”)80X10−’とするためには、冷却速度を遅
くする必要がある。Figure 4 (al is the amount of solid solute C in ferrite at Ar1 (near 00°C) when cooled at a cooling rate in the range of 2.5 to b seconds from the annealing temperature, at 700°C at each cooling rate. It is clear from this figure that the amount of solid solute C at 700℃ is shown in Figure 1 when annealing is performed at high temperature. Q″
In order to obtain 80×10-', it is necessary to slow down the cooling rate.
そこで、700℃での固溶CtttQ″″唱〉80XI
O″″4とするために必要な冷却速度を、各焼鈍温度に
対して整理した結果を第4図(b) K示す、それKよ
ると、焼鈍温度が750℃以上では、鋼帯の冷却速度(
vl)を次式の条件とすることで700℃で固fe#C
tをq−1≧80X10−4とすることができる。Therefore, solid solution CtttQ″″ chanting〉80XI at 700℃
Figure 4 (b) shows the results of the cooling rate required for each annealing temperature in order to obtain O''4. speed(
vl) under the conditions of the following formula, it becomes solid fe#C at 700℃.
t can be q-1≧80X10-4.
vl(0,2Ta+180 (CIf/pl)焼鈍温
度Tj<750℃では、c>o、o1j根度の鋼は焼鈍
温度で既にq−”>5oxto−4となり、700℃ま
での冷却で減少することはなく、従って冷却速度は任意
で良い。vl(0,2Ta+180 (CIf/pl) At an annealing temperature Tj<750°C, steel with c>o, o1j hardness already has q-”>5oxto-4 at the annealing temperature, which decreases when cooled to 700°C. Therefore, the cooling rate can be set arbitrarily.
次に、Arlから急冷開始温度(TQ)に至るまでの冷
却速度(7重)とTQが、TQでのフェライト中の固#
Cflと過時効処理後の全伸びおよび降伏強度(1,5
憾調圧時)K如何なる彫物をおよぼすかについて第5図
に示す。Next, the cooling rate (7 times) from Arl to the quenching start temperature (TQ) and TQ are the solid # of the ferrite at TQ.
Cfl and total elongation and yield strength after overaging treatment (1,5
Fig. 5 shows what carvings are produced when the pressure is adjusted.
急冷開始温度TQでの固溶CtをQ−1≧80XIO−
’とするには、TQを500℃以上でかつArlからT
Qまでの冷却速度を40℃/秒以上とする必要がある。Solid solution Ct at quenching start temperature TQ is Q-1≧80XIO-
'To set TQ to 500℃ or higher and from Arl to T
The cooling rate to Q must be 40° C./second or higher.
TQ<500℃ではフェライト中の固溶Cは急激に平両
状NK近づくため光分なCの過飽和状態を実現すること
は峻しい。これに対し、TQから急速冷却(水焼き入れ
)処理後350℃×2分の過時効処理を行った時の、降
伏強度と全伸びの変化については、ムrIからTQまで
の冷却速 一度が100℃/秒以上となる場合は、降伏
強度の増大と共に全伸びの低下が顕著となる。When TQ<500°C, the solid solution C in the ferrite rapidly approaches the flat-sided NK, so it is difficult to achieve optical supersaturation of C. On the other hand, regarding the changes in yield strength and total elongation when performing overaging treatment at 350°C for 2 minutes after rapid cooling (water quenching) treatment from TQ, the cooling rate from MrI to TQ once When the temperature is 100° C./second or more, the yield strength increases and the total elongation decreases significantly.
また、TQが600℃を越える場合は、十分な過砲和固
scmを得ることは可能であるが、反面降伏強度レベル
の増加と全伸びレベルの低下が著しく絞り用鋼板として
は好ましくない・
従って、ArlからTQまでの冷却速度(Vs)t−4
0℃/秒以上、100℃/秒以下に規定し、又TQを6
00℃以下、500℃以上の温度範囲に規定する。In addition, if TQ exceeds 600℃, it is possible to obtain sufficient overload strength scm, but on the other hand, the yield strength level increases and the total elongation level decreases significantly, making it undesirable as a steel plate for drawing. , cooling rate from Arl to TQ (Vs) t-4
Specified at 0℃/second or more and 100℃/second or less, and TQ is 6
The temperature range is defined as 00°C or lower and 500°C or higher.
更にこの急速冷却TQから200℃以下までの冷却速度
(V、)の効果については、第6図に示す通りである。Furthermore, the effect of the cooling rate (V,) from this rapid cooling TQ to 200° C. or less is as shown in FIG.
即ち本来、TQでの固溶Cの過飽和度を最大限に過時効
処理におけ。That is, originally, the degree of supersaturation of solid solution C in TQ was maximized in the overaging treatment.
るC析出の駆動力として有効に作用させるためKは、T
Q以下のi!度は出来る限り急冷を行うべきである。し
かし、実質的には250℃/抄以上で冷却を行えば、過
時効処理後の時効指数を3.5 kgf/−以下とする
ことが可能である。従って、TQから200℃以下の温
度までの冷却を250℃/秒以上に規定する。In order to effectively act as a driving force for C precipitation, K is
i below Q! Cooling should be performed as rapidly as possible. However, if cooling is substantially performed at 250°C/paper or higher, it is possible to reduce the aging index after overaging treatment to 3.5 kgf/- or less. Therefore, cooling from TQ to a temperature of 200°C or less is specified at 250°C/sec or more.
上記した一連の冷却条件で冷却した後、300℃から4
00℃の温度で過時効処理を行うととに工って良好な延
性と共に優れた遅時効性を具備した冷延鋼板の製造が可
能となる。過時効処理条件については、%に畦細な規定
は行わないが、300℃未満では十分な1時効処理を行
うには長時間を要するため好、I L < trい。ま
た400℃を越える温度では析出Cのp+固溶が問題と
なり、逆に固溶Cが増えるため時効性が劣化する。これ
らの理由から過時効処理は300℃から400℃の温度
範囲で行うことを前提とする。After cooling under the above series of cooling conditions, from 300℃ to 4℃
By performing the overaging treatment at a temperature of 0.000C, it becomes possible to produce a cold rolled steel sheet having good ductility and excellent slow aging properties. Regarding the over-aging treatment conditions, there are no detailed regulations regarding the percentage, but if the temperature is less than 300°C, it will take a long time to perform a sufficient aging treatment, so it is preferable that I L < tr. Moreover, at temperatures exceeding 400° C., p+ solid solution of precipitated C becomes a problem, and conversely, the solid solution C increases, resulting in deterioration of aging properties. For these reasons, it is assumed that the overaging treatment is carried out at a temperature range of 300°C to 400°C.
以上のエラな本発明の基本的構成要件からなる遅続焼鈍
熱サイクルを示すと@7崗の如くなる。The delayed annealing thermal cycle consisting of the basic constituent elements of the present invention described above is as shown in @7.
さて、本発明は一般の軟質冷延鋼抜用の鋼111総べて
に適用できることは前記した通りであるが、実質的には
、0.010憾<c<0.0501の範囲とすべきであ
る。これはCが0.010−以下の鋼では本発明で規定
した冷却条件でも光分な固溶Cの過砲和状11な達成す
ることは難しい。またCが0.050憾以上の鋼では実
際上充分な延性を得ることが内輪となるからである。Now, as mentioned above, the present invention can be applied to all steels 111 for general soft cold rolled steel drawing, but substantially the range should be 0.010<c<0.0501. It is. This is difficult to achieve in steels with a carbon content of 0.010 or less, since even under the cooling conditions specified in the present invention, there is an optical overblast of solid solute carbon. In addition, in steels with C of 0.050 or more, it is essential to obtain sufficient ductility in practice.
また&は、多量に含有されるとA系介在物の増加を来た
し、延性を劣化させる。従って軟質鋼板としてはy所望
の延性を確保できる上限として0.1憾を規定する。Moreover, when & is contained in a large amount, it causes an increase in A-based inclusions and deteriorates ductility. Therefore, for a soft steel plate, 0.1 is specified as the upper limit that can ensure the desired ductility.
−は、多量に含有されるとランクフォード値の低下を来
たすため絞り用鋼板としては上限を規定する必要がある
。また、下限については−を下げ過ぎるとBによる熱間
脆性を抑制することができなくなるため、強度の脱S処
理を行わねばならず、コスト上昇をまねく。- If contained in a large amount, the Lankford value decreases, so it is necessary to specify an upper limit for the steel plate for drawing. In addition, if the lower limit is lowered too much, hot embrittlement due to B cannot be suppressed, so S removal treatment must be performed to improve the strength, leading to an increase in cost.
また製鋼上は溶鋼の湯流れが悪化するなどの問題が生ず
る。従って、−は上記の観点から、でそれぞれ焼鈍し、
過時効処理は何れも。In addition, problems arise in steelmaking, such as poor flow of molten steel. Therefore, − is, from the above point of view, annealed at, respectively;
No overage treatment.
350℃×2分→空冷とした・
■発明法(Tj>750℃)Tノー850℃、vl =
8℃/8、 V、=50℃/8、 Vm−1500℃1
5■従米法(Tj〉750℃)Tム=850℃、Vl=
15℃/ S、 Vm = 15℃/8. Vs =1
500で/S■発明法(Tj<7so℃)Tノー700
℃、V、=50℃/B、Vs=1500℃/S■従米法
(T)〈750℃)Tj−700℃、Vt=15で78
、 Vs=1500℃/S得られた鋼板の引張特性値と
時効指数は次の第2表に示す通りである。350°C x 2 minutes → air cooling・ ■Inventive method (Tj>750°C) T no 850°C, vl =
8℃/8, V,=50℃/8, Vm-1500℃1
5 ■ Rice method (Tj〉750℃) Tmu = 850℃, Vl =
15°C/S, Vm = 15°C/8. Vs=1
At 500/S ■ Invention method (Tj<7so℃) T no 700
℃, V, = 50℃/B, Vs = 1500℃/S ■ 78 at Tj - 700℃, Vt = 15
, Vs=1500°C/S The tensile property values and aging index of the obtained steel plate are shown in Table 2 below.
即ち上表から明かな工うに、c<o、ot。That is, as is clear from the above table, c<o, ot.
繋の−では、たとえ発明法!のものでも充分な遅時効性
は得られず、又c<o、oso優の−では絞り用鋼板と
して満足できる延性および低降伏強度が得られない。然
して0.010嘔<c<o、oso嘔の鋼については本
発明法による冷却を行うことKよって伸びの劣化、降伏
gffの上昇を伴うことなく、時効性を著しく改善で負
ることは明がである。Tsuna-no-So, even if it is an invention method! However, if c<o, oso is excellent, satisfactory ductility and low yield strength as a steel sheet for drawing cannot be obtained. However, it is clear that for steels with 0.010<c<o and oso<o>, cooling by the method of the present invention significantly improves aging properties without deteriorating elongation or increasing yield gff. There is.
史に鋼Iにおいて燐鈍後の冷却条件を神々変化させた場
合の過時効処理後における材質と時効4″IIM1に次
の81!3表に示すが、本発明法で規定した冷却条件で
冷却したものにおいてのみ優れた延性を有しながら、し
かも耐時効性の好ましいものが得られる。In the history of steel I, the material and aging after overaging treatment when the cooling conditions after phosphorus annealing were changed dramatically are shown in the following table 81! Only in this way can a material with excellent ductility and favorable aging resistance be obtained.
!3表 本発明法に基づく所の冷却条件:満足−〇。! 3 tables Cooling conditions based on the method of the present invention: Satisfied - ○.
不満足−×
本本1.5噛調圧後、JI85号引張り試験片以上収用
したような本発明によれば、優れた強度と延性のバラン
スを有するとともに耐時効性をも具備した絞り用冷延鋼
板を連続焼鈍KLって的確に製造することを可能ならし
めるものであって、工業的にその効果の大−い発明であ
る。Unsatisfactory - × This invention According to the present invention, the cold-rolled steel sheet for drawing which has an excellent balance of strength and ductility and also has aging resistance, as shown in the JI No. 85 tensile test piece or higher after 1.5 degrees of pressure adjustment. This invention makes it possible to accurately manufacture KL by continuous annealing, and is an industrially highly effective invention.
図面は本発明の技術的内容を示すものであって、第1図
は焼入れ時の固溶C量と過時効処理後の時効指数の関係
を示した図表、第2図は連#IjlIIl!A!FI加
熱、冷却過程におけるフェライト中の固溶C量の変化を
示した図表、第3崗は38℃X16日の時効後における
降伏点伸び回復i+tおよび伸び劣化tK及ぼす時効指
数の影袢を示した図表、第4図はムr1でのフェライト
中固溶C1K及ぼす焼鈍温度からArlまでの冷却速度
(V、)の影響とQ−’>5oxio−aを得るために
必要な焼鈍温度と該冷却速度(vl)の関係を示した図
表、第は650℃の温度(TQ)でのフェライト=溶C
量および羊の温度から水冷後退時効、を行ったときの降
伏強度お1び全伸びk、すAr4からTQtでの冷却速
度の影響をまた図表、絽6図は過時効処理後の時効指及
ぼすTQから室温までの冷却速度の影示した図表、第7
図は本発明による遅綬焼鈍熱サイクルの115!明図で
ある。
特許出願人 日本鋼管株式会社
発 明 者 松 藤 相 路
間 下 村 隆
良問 野 副
修同 小 野
賛同 細 谷 佳
弘第1図
第3図
(:’tfij (bptX)
第2図
p 針31J f6Ary !?”/))HI’A崖R
(’%)第5図
ArljM n21?”ty@p力let (’B/x
)第6図
(11111匈処累; ilD”l:Xη啼!片)第7
図
↑
一一一一瞥吋が
手続補正書く0発)
昭和光年9月7日
特許庁長官島 1)春 樹殿
1、事件の表示
昭和泌年特 許願第1o9732号2、発明の名称
事件との関係特許出願人
名称(氏釦日本鋼管株式会社
4、代理人
昭和 年 月 日 発送
6、補正の対象
−ど−
荀紙の通り −)′補 正
の 内 容
乙本願明細書中第12頁第14行目fこ[急速冷却TQ
JとあるのをC急冷開始温度TQJと訂正する0
2、同第15頁第8行目lこ「Atキルド鋼」とあるの
を(Atキルド鋼」と訂正する0
4本願の添付図面中第5図を別紙の如く訂正する〇以上The drawings show the technical contents of the present invention, and FIG. 1 is a chart showing the relationship between the amount of solid solute C during quenching and the aging index after overaging treatment, and FIG. A! A graph showing the change in the amount of solid solute C in ferrite during the FI heating and cooling process. The third graph shows the influence of the aging index on yield point elongation recovery i+t and elongation deterioration tK after aging at 38°C for 16 days. Figure 4 shows the influence of the cooling rate (V,) from the annealing temperature to Arl on the solid solution C1K in ferrite at mu r1, the annealing temperature necessary to obtain Q-'>5oxio-a, and the cooling rate. A diagram showing the relationship between (vl) and ferrite = molten C at a temperature of 650°C (TQ)
The yield strength (1) and total elongation (k) when subjected to water-cooled backward aging based on the amount and sheep temperature are also shown in the table, and the influence of the cooling rate from Ar4 to TQt. Chart showing the cooling rate from TQ to room temperature, No. 7
The figure shows 115! of the slow ribbon annealing heat cycle according to the present invention! This is a clear diagram. Patent applicant: Nippon Kokan Co., Ltd. Inventor: Aijima Matsufuji Takashi Shimomura
Good question Vice No.
Shudo Ono
Supported by Yoshi Hosoya
HI'A cliff R
('%) Figure 5 ArljM n21? ``ty@p force let ('B/x
) Fig. 6 (11111匈所 Cumulative; ilD”l:Xη啼!片) No. 7
Figure ↑ 11, 1, 1, 1, 1, 2, 2, 2, 2, 2, 3, 3, 3, 3, 3, 3, 3, 3, 3, 4, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 4, 5, 1, 2, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 3, 4, 5, 10, 10, 10, 10, 10, 10s 100s sb 1stsssssssssssssssssss why's' Related patent applicant name (Mr. Nippon Steel Tube Co., Ltd. 4, agent 1939, Month, Day, Dispatch 6, subject of amendment - as per the paper -) 'Contents of amendment B No. 12 in the specification of the present application Page line 14 f [Rapid cooling TQ
Correct J to C quenching start temperature TQJ 0 2, page 15, line 8 l Correct ``At killed steel'' to read (At killed steel) 0 4 In the attached drawings of this application Correct Figure 5 as shown in the attached sheet.
Claims (1)
& : 0.05〜0.30 畳、sel、Aj :
0.02〜0.101、N:0.00501以下であッ
テ残部がh’jおよび不可避不純物からなる鋼を熱延し
て650tl:以上で巻散り、冷延して連続焼鈍するに
あたり、焼鈍時の冷却速度なArl変態点以上の温度域
と、ムr1変園点から急速冷却開始温度TQK到る温度
域およびこのTQから200℃以下に到る温度域とに区
分して葡制御し、Arl変態点以上の温度域においては
焼鈍温度が750’C以下であれば任意の冷却速度で冷
却し、750’C以上の場合において王妃する式を満足
する冷却速度とし、次のArl変腫点からTQK到る温
度域では40〜b から200’C以下に到る温度域における冷却速度を2
50℃/se以上とすることを特徴とする連続焼鈍によ
る耐時効性の優れた軟質冷延鋼板の製造方法。 V凰(−0,2°rム+180C℃/隷)但し%Vlは
、ムr1変態点以上の温度域における冷却速度 〒Aは、焼鈍温度[Claims] C: 0.010 to 0.05011. i: 0.11 or less,
& : 0.05~0.30 Tatami, sel, Aj:
0.02 to 0.101, N: 0.00501 or less and the remainder consists of h'j and unavoidable impurities. The cooling rate is divided into a temperature range above the Arl transformation point, a temperature range from the Mr1 turning point to the rapid cooling start temperature TQK, and a temperature range from this TQ to 200 ° C or less, In the temperature range above the Arl transformation point, if the annealing temperature is 750'C or less, cooling is performed at an arbitrary cooling rate, and if the annealing temperature is 750'C or higher, the cooling rate is set to satisfy the formula that satisfies the following Arl transformation point. In the temperature range from 40 to TQK, the cooling rate in the temperature range from 40 to 200'C is 2.
A method for producing a soft cold-rolled steel sheet with excellent aging resistance by continuous annealing at a temperature of 50° C./se or higher. V 凰 (-0.2°rm+180℃℃/re) However, %Vl is the cooling rate in the temperature range above the Mr1 transformation point〒A is the annealing temperature
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10878281A JPS5811743A (en) | 1981-07-14 | 1981-07-14 | Manufacture of soft cold-rolled steel plate which is excellent in aging resistance, by continuous annealing |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10878281A JPS5811743A (en) | 1981-07-14 | 1981-07-14 | Manufacture of soft cold-rolled steel plate which is excellent in aging resistance, by continuous annealing |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5811743A true JPS5811743A (en) | 1983-01-22 |
JPS619367B2 JPS619367B2 (en) | 1986-03-22 |
Family
ID=14493334
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP10878281A Granted JPS5811743A (en) | 1981-07-14 | 1981-07-14 | Manufacture of soft cold-rolled steel plate which is excellent in aging resistance, by continuous annealing |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS5811743A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6052527A (en) * | 1983-08-31 | 1985-03-25 | Nippon Steel Corp | Production of non-aging cold rolled steel sheet by continuous annealing |
JPS61264158A (en) * | 1985-05-08 | 1986-11-22 | Kobe Steel Ltd | Low carbon steel bar or wire rod for cold forging |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0539021Y2 (en) * | 1988-12-20 | 1993-10-01 |
-
1981
- 1981-07-14 JP JP10878281A patent/JPS5811743A/en active Granted
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6052527A (en) * | 1983-08-31 | 1985-03-25 | Nippon Steel Corp | Production of non-aging cold rolled steel sheet by continuous annealing |
JPS6349726B2 (en) * | 1983-08-31 | 1988-10-05 | Nippon Steel Corp | |
JPS61264158A (en) * | 1985-05-08 | 1986-11-22 | Kobe Steel Ltd | Low carbon steel bar or wire rod for cold forging |
Also Published As
Publication number | Publication date |
---|---|
JPS619367B2 (en) | 1986-03-22 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
SE450390B (en) | SET TO MAKE COLD ROLLED SOFT STEEL PLATE WITH GOOD DEEPABILITY AND AGING STABILITY | |
US4014717A (en) | Method for the production of high-permeability magnetic steel | |
JPS6114213B2 (en) | ||
JPS5811743A (en) | Manufacture of soft cold-rolled steel plate which is excellent in aging resistance, by continuous annealing | |
JPS6156235A (en) | Manufacture of high toughness nontemper steel | |
US4709742A (en) | Method for producing a thin casting of Cr-series stainless steel | |
JP2003073741A (en) | Method for manufacturing ferritic stainless steels sheet superior in workability | |
US3806373A (en) | Process for producing cold-rolled steel plates high in the cold-formability | |
JP2680424B2 (en) | Method for producing low yield strength austenitic stainless steel sheet | |
JPH0192317A (en) | Manufacture of high-strength sheet metal excellent in stretch-flange workability | |
JPH0525548A (en) | Production of cr-ni stainless steel sheet excellent in material and surface quality | |
JPS592725B2 (en) | Method for producing thermosetting high-strength cold-rolled steel sheet for deep drawing | |
JPH03223420A (en) | Production of high strength steel | |
JPS5810447B2 (en) | Manufacturing method by continuous annealing of cold-rolled steel sheets with excellent workability and aging resistance | |
JPH01191748A (en) | Manufacture of cold rolled steel sheet for press forming excellent in material homogeneity in coil | |
JPS5857491B2 (en) | Method for producing thermosetting cold-rolled steel sheet for deep drawing | |
JP3040569B2 (en) | Manufacturing method of surface-treated original sheet by continuous annealing | |
JPS5818407B2 (en) | Manufacturing method of original plate for soft surface treated steel sheet by continuous annealing method | |
JPS5980727A (en) | Manufacture of cold rolled steel sheet with high drawability by continuous annealing | |
JPH04350119A (en) | Production of thick steel plate having homogeneous quality | |
JPS61124533A (en) | Manufacture of nonaging cold rolled steel sheet having good workability by continuous annealing | |
JP3040568B2 (en) | Manufacturing method of surface-treated original sheet by continuous annealing | |
KR100276291B1 (en) | The manufacturing method for cold rolling steel sheet with excellent thickness precision | |
JPH07100817B2 (en) | Method for manufacturing slow-aging cold-rolled steel sheet | |
JPH01177322A (en) | Manufacture of cold rolled steel sheet extremely excellent in deep drawability |