JPS61195919A - Manufacture of cold rolled steel sheet having superior stretcher strain resistance - Google Patents
Manufacture of cold rolled steel sheet having superior stretcher strain resistanceInfo
- Publication number
- JPS61195919A JPS61195919A JP3789285A JP3789285A JPS61195919A JP S61195919 A JPS61195919 A JP S61195919A JP 3789285 A JP3789285 A JP 3789285A JP 3789285 A JP3789285 A JP 3789285A JP S61195919 A JPS61195919 A JP S61195919A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- steel sheet
- present
- cold rolled
- 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.)
- Pending
Links
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、プレス成形時の耐ストレッチャ・ストレイ
ン（以下５ｔ−ｓｔと記す）性の優れた冷延鋼板の製造
方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a method for producing a cold rolled steel sheet with excellent stretcher strain (hereinafter referred to as 5t-st) resistance during press forming.
（従来の技術）
自動車外板等に使用される冷延鋼板には、美観の点より
、プレス成形時に５ｔ−ｓｔが発生しないことが必要で
あり、従来は（ａ）ムＪ−に鋼を箱焼鈍する方法と（ｂ
）極低炭素鋼にＴ１とかＮｂを添加し、０−？Ｈを炭化
物や窒化物として析出させた鋼を連続焼鈍する方法の二
通りがあった。(Prior art) For aesthetic reasons, it is necessary for cold-rolled steel sheets used for automobile exterior panels, etc., that 5t-st does not occur during press forming. Box annealing method and (b
) By adding T1 or Nb to ultra-low carbon steel, 0-? There were two methods of continuous annealing of steel in which H was precipitated as carbides or nitrides.
従来の上記（ａ）の方法は、通常のｕ−に鋼を用いるた
め、素材コストは安く問題はないが、箱焼鈍法で製造す
るため、連続焼鈍法に比し、生産性、コストの面で問題
がある。一方、上記（ｂ）の合金添加方法は、例えば特
開昭５０−７７１８号に見られる如く、非時効鋼板を製
造できるが、高価なＴ１あるいはＮｂ等を添加せねばな
らないし、更にＣを低下させるための脱ガスによる脱炭
コストが高くなるため、素材コストが著しく高くなる等
の問題がある。The conventional method (a) above uses steel for the normal u-, so the material cost is low and there are no problems, but since it is manufactured using the box annealing method, it has lower productivity and cost compared to the continuous annealing method. There is a problem with this. On the other hand, the above alloy addition method (b), as shown in JP-A-50-7718, can produce non-aging steel sheets, but it requires adding expensive T1 or Nb, and further reduces C. Since the cost of decarburization due to degassing increases, there are problems such as a significant increase in material cost.
その他、通常のムＪ−に鋼の連続焼鈍材の時効特性を改
善しようとする試みは数多く行なわれているが、本願発
明の方法が目標としているような完全Ｋ ５ｔ−８ｔが
ない鋼板を造るというレベルの技術のもの、あるいは目
標値を本願発明の方法の同じレベルにしたものは、前記
υ）の合金添加の方法以外は全くない。以下に連続焼鈍
材の時効性を改善する従来法を代表例で説明する。In addition, many attempts have been made to improve the aging characteristics of continuous annealing steel materials, but it has not been possible to produce steel plates without perfect K 5t-8t, which is the goal of the method of the present invention. There is no technique that has the same level of technology as this, or that sets the target value to the same level as the method of the present invention, other than the method of alloy addition in υ) above. Conventional methods for improving the aging properties of continuously annealed materials will be explained below using typical examples.
（ｅ）特公昭４７−３３４０９号の方法は、通常人トに
鋼を用い連続焼鈍の均熱後の冷却租をｓ ｏ ｔ、’ｓ
以上とし、３００℃〜５００℃で過時効処理をする方法
であるが、実施例−２の鋼（５）の時効指数は３、０
ｋｇ ｆ／ｓ−であり、時効特性は改善されているが自
然時効６ケ月後のプレス成形時の５ｔ−ｓｔを完全にｔ
！Ｏにするには末だ不十分である（ ＢＡ１ｉ’のムＪ
−に鋼の時効指数は０〜ｘ、ｏｋｓｆ／−である）。(e) The method of Japanese Patent Publication No. 47-33409 usually uses steel and cools the steel after soaking during continuous annealing.
As above, the method involves over-aging treatment at 300°C to 500°C, but the aging index of the steel (5) of Example-2 is 3.0.
kg f/s-, and the aging characteristics have been improved, but the 5t-st during press forming after 6 months of natural aging is completely
! It's not enough to make it O ( BA1i'mu J
- The aging index of steel is 0~x, oksf/-).
又（ｄ）特開昭５１−２０７１５号の方法は、同様に急
冷するタイプの連続焼鈍の方法で、時効特性を短時間の
過時効処理で時効性を改善するために、急冷の終点を２
００℃〜３５０℃まで過冷却する方法であるが第２表に
記載されている如くムｌ−にで、も時効指数は、４．２
〜５６０ゆν讐であり、完全に５ｔ−ｓｔをなくするに
は、はど遠いレベルである。以上、代表的な二側でもっ
て説明したが、通常のｕ−に鋼を用いて連続焼鈍法で、
５ｔ−ｓｔが完全にｔ！ｏである板を製造する方法は末
だ発明されていない。In addition, (d) the method of JP-A-51-20715 is a continuous annealing method of the same rapid cooling type, and in order to improve the aging characteristics by short-time overaging treatment, the end point of the rapid cooling is set to 2.
The method involves supercooling from 00°C to 350°C, but as shown in Table 2, the aging index is 4.2.
~560 Yen, and it is far from being able to completely eliminate 5t-st. The above was explained using typical two sides, but by continuous annealing method using ordinary u-steel,
5t-st is completely t! No method has yet been invented to produce such a board.
（発明が解決しようとする問題点）
本発明は、高価なＴｌやＮｂを含まない安価な鋼を用い
て、生産性、コストの面で有利である連続焼鈍法で製造
された鋼板の５ｔ−ｓｔを完全に消去せしめる方法であ
る。(Problems to be Solved by the Invention) The present invention provides a 5-t This is a method to completely eliminate st.
（問題点を解決するための手段）
本発明者ら１人連続焼鈍法で完全に非時効性である冷延
鋼板の製造方法について、合金添加の方法を４含めて、
各種の検討をおこなってきた。(Means for Solving the Problems) The present inventors have developed a method for producing completely non-aging cold rolled steel sheets using a continuous annealing method, including four alloy addition methods.
Various studies have been carried out.
その結果、合金添加以外の方法では、即ち鋼の成分や連
続焼鈍法の変更、改善等では、５ｔ−ｓｔを完全に消去
するのは不可能であるとの結論に達し、本発明の方法の
よう々全く別の手段で５ｔ−ｓｔを完全に消去する方法
を検討し本発明の方法を見いだしたものである。As a result, we came to the conclusion that it is impossible to completely eliminate 5t-st by methods other than alloy addition, that is, by changing or improving the steel composition or continuous annealing method. Therefore, we investigated a method of completely erasing 5t-st using completely different means and discovered the method of the present invention.
本発明者らは、これらの各種の検討のなかで鋼板の表裏
面にショット・ブラストを付加し、鋼板の表裏面の表層
部のみに大きな塑性歪を与える本発明の方法を見いだし
たものである。Through these various studies, the present inventors discovered the method of the present invention in which shot blasting is applied to the front and back surfaces of a steel plate to apply large plastic strain only to the surface layer portions of the front and back surfaces of the steel plate. .
即ち要旨とするところは、ａ：ｏ、ｏｏｏｓ〜０．１０
１ｋ、Ｍｎ ： ０．０５〜１．０ Ｔｏ、Ｐ り０．
１０Ｓ、 ８ り０．０４％、１１＜０．００９０％、
ｍｏｌムＪく０．１−１残部Ｆｅおよび不可避的不純物
からなる鋼を連続鋳造又は分塊法にでスラブとし、通常
の熱間圧延、冷間圧延を施し、連続焼鈍した後、ショッ
ト・ブラストで鋼板の表裏面に歪を付与することを特徴
とする耐ストレッチや・ストレイシ性に優れた冷延鋼板
の製造方法である。In other words, the gist is a:o,ooos~0.10
1k, Mn: 0.05-1.0 To, P: 0.
10S, 8 ri 0.04%, 11<0.0090%,
Steel with a mol J of 0.1-1 and the remainder Fe and unavoidable impurities is made into a slab by continuous casting or blooming, subjected to normal hot rolling, cold rolling, continuous annealing, and then shot blasting. This is a method for producing cold-rolled steel sheets with excellent stretch resistance and strain resistance, which is characterized by applying strain to the front and back surfaces of the steel sheet.
以下に本発明の方法について詳細に述べる。The method of the present invention will be described in detail below.
本発明の目的とするプレス成形時の耐５ｔ−ｓｔ性の優
れた冷延鋼板を製造するＫは、まず、鋼の成分を下記の
ように規制する必要がある。To manufacture a cold-rolled steel sheet with excellent 5t-st resistance during press forming, which is the object of the present invention, it is first necessary to regulate the components of the steel as described below.
Ｃ含有量の範囲はｏ、 ｏ ｏ ｏ ｓ〜ｏ、 ｉ ｏ
ｓでなければならない。０．１０Ｓよりも多く含有す
ると延性が低下し、プレス割れが生じるようになる。又
、ｏ、ｏｏｏｓｑｂよりも少なくなると、非時効性とな
るのでショット・ブラストを付加する必要がない。The C content ranges from o, o o o s to o, io
Must be s. When the content is more than 0.10S, ductility decreases and press cracking occurs. Moreover, when it is less than o,ooosqb, it becomes non-aging, so there is no need to add shot blasting.
Ｍｎ含有量は、０．０５〜１．０％でなければならない
。Ｏ，ＯＳ＊より少ないと熱間圧延時にＳによる赤熱脆
性が生じる。又、１．０％より多くなると硬くなり過ぎ
プレス成形性が悪くなる。Mn content must be between 0.05 and 1.0%. If the content is less than O, OS*, red brittleness due to S occurs during hot rolling. Moreover, if it exceeds 1.0%, it becomes too hard and press formability deteriorates.
Ｐ含有量は、０．１−以下でなければならない。The P content must be less than or equal to 0.1.
０．１％よりも多くなると延性が低下し、自動車外板等
のプレス成形ができなくなる。When it exceeds 0.1%, ductility decreases and press forming of automobile outer panels and the like becomes impossible.
Ｓ含有量は、０．０４％以下でなげればならない。The S content must be 0.04% or less.
０．０４％よりも多量に含まれると熱間圧延時に赤熱脆
性が生じるとともに延性、穴拡げ性が低下する。If it is contained in an amount greater than 0.04%, red brittleness occurs during hot rolling, and ductility and hole expandability decrease.
Ｋ含有量は、０．００９０％以下でなければならない。K content must be below 0.0090%.
０．００９０−より多く含まれるとＮ時効が生じ易くな
ったり、五！を添加する場合でも五！Ｈ量が増え過ぎて
硬質化する。If more than 0.0090- is contained, N aging may occur more easily. Even if you add five! If the amount of H increases too much, it becomes hard.
５ｏＪＡＪ含有量は、０．１Ｓ以下でなければならない
。０．１％よりも多量に含まれると硬質化し、延性が低
下する又ム！合金代も高くなる。伺、その他の元素とし
て、Ｂは必要に応じて添加しても本発明の効果を何ら損
なうものではない。The 5oJAJ content must be 0.1S or less. If it is contained in an amount greater than 0.1%, it will become hard and the ductility will decrease! Alloy costs will also increase. However, as another element, B may be added as necessary without impairing the effects of the present invention.
製鋼および熱間圧延条件は何ら規制する必要がなく、例
えば最近注目を集めているＣｏ−ＤＲ工程でも良く、も
ちろん一般的一行なわれている連続鋳造又はｉｎｇｏｔ
法でスラブとし、熱間圧延を行なって熱延コイルとして
も良い。又必要に応じて高温巻取を行なっても良い。There is no need to regulate the steelmaking and hot rolling conditions; for example, the Co-DR process, which has been attracting attention recently, may be used, and of course, the commonly used continuous casting or ingot process may be used.
It is also possible to form a slab by a method and hot-roll it into a hot-rolled coil. Further, high temperature winding may be performed as necessary.
冷間圧延および連続焼鈍条件も何ら規制する必要が々い
。しかし、特に厳しいプレス成形性が要求される用途に
供される冷延鋼板を製造する場合には、時効性とプレス
加工性に優れた冷延鋼板を製造する特開昭５８−５２４
２９号のような連続焼鈍法を適用するのが好ましい。It is also necessary to regulate the conditions of cold rolling and continuous annealing. However, when producing cold-rolled steel sheets for applications that require particularly severe press formability, Japanese Patent Application Laid-Open No. 58-524
It is preferable to apply a continuous annealing method such as No. 29.
以上のようにして連続焼鈍法で製造された冷延鋼板は、
長い時間経過すると、引張り試験の時Ｙ、Ｐ−Ｅｌが生
じたり、プレス成形時に５ｔ−ｓｔが生じたりするよう
になる。このような連続焼鈍材に本発明の方法であるシ
ョット・プラストを鋼板の表裏面より付加し、鋼板の表
裏面層に歪を生じせしめると、長期間独過してもＹ、Ｐ
−Ｅｌが生じたり、５ｔ−ｓｔが発生したりすることは
全く無くなるのである。The cold-rolled steel sheet manufactured by the continuous annealing method as described above is
If a long time passes, Y and P-El will occur during the tensile test, and 5t-st will occur during press molding. When shot plast, which is the method of the present invention, is applied to such continuously annealed material from the front and back surfaces of the steel plate to cause distortion in the front and back layers of the steel plate, Y, P
-El and 5t-st are completely eliminated.
このようにショット・プラストによって、時効後のＹ、
Ｐ−Σノを完全に消去できるようになるのは、ショット
・ブラストによって鋼板の表裏面層のみが塑性変形する
ため、鋼板内に大きな残留応力が生じ、その大きな残留
応力によるＺＰ−Ｂｌの消去効果と、ショット・ブラス
トによる鋼板表裏面層の塑性変形、即ち多くの可動転位
によるＹ、Ｐ−Ｅｌの消去効果とによるものと思われる
。In this way, by shot plast, Y after aging,
What makes it possible to completely eliminate P-Σ is that only the front and back layers of the steel plate are plastically deformed by shot blasting, which creates a large residual stress within the steel plate, and this large residual stress causes ZP-Bl to be erased. This is thought to be due to the plastic deformation of the front and back layers of the steel sheet due to shot blasting, that is, the elimination effect of Y and P-El due to many mobile dislocations.
ショット・づ５ストを付加する工程は、連続焼鈍後調質
圧延を施した後、ショット・ブラストを付加するのがＹ
、Ｐ−Ｅ７を効率的に消去できる。The process of adding shot blasting involves continuous annealing, temper rolling, and then shot blasting.
, P-E7 can be efficiently erased.
このときのショット・ブラストを付加するのは連続焼鈍
ライン内に組み込んで行なっても、又別うイシで行なっ
ても良い、伺ショット・プラストを連続焼鈍後、調質圧
延の前に施してもＬＰ−Ｅｌを消去できる。Shot blasting at this time may be done by incorporating it into the continuous annealing line, or it may be done by a separate stone, or shot blasting may be applied after continuous annealing and before temper rolling. LP-El can be erased.
ショット・ブラストで与える歪量の程度は、鋼板の時効
特性値によって調整すれば良く、時効特性が悪い場合は
ショット・プラストを強く、長くしなければならないし
、時効特性が良い場合は、軽く行なっても良い。The amount of strain applied by shot blasting can be adjusted according to the aging characteristics of the steel plate; if the aging characteristics are poor, the shot blasting should be stronger and longer; if the aging characteristics are good, the shot blasting should be done lightly. It's okay.
ショット・プラストに用いる種類、サイズは鋼板の必要
な表面粗度によって選択すれば良く、ショットでもグリ
ッドでもサンドでも良い。岡本発明の効果を得る手段と
しては、現在の技術レベルでは工業化が比較的容易であ
る点からショット・ブラストが好ましいが、ワイヤープ
ラシンク加工、放電加工、レーザー等鋼板の表面層のみ
に塑性歪を付加できる方法であれば十分な効果が得られ
る。The type and size of the shot plastic may be selected depending on the required surface roughness of the steel plate, and may be shot, grid, or sand. Okamoto: As a means of obtaining the effects of the invention, shot blasting is preferable because it is relatively easy to industrialize at the current technological level, but other methods that apply plastic strain only to the surface layer of the steel plate, such as wire plastic sink processing, electrical discharge machining, and laser, are also preferred. Any method that can add sufficient effects can be obtained.
（作 用）
以上に本発明の作用および用途について説明する。本発
明の作用および用途は大別すると以下の３種がある。(Function) The function and use of the present invention will be explained above. The functions and uses of the present invention can be broadly classified into the following three types.
（６）本発明の主たる用途は、深絞り性と完全非５ｔ−
ｓｔ性が要求される自動車外板用である。(6) The main uses of the present invention are deep drawability and completely non-5t-
It is used for automobile exterior panels that require strong properties.
これは本発明の５ｔ−ｓｔの完全消去作用をフルに活用
することによって低コストな非合金添加型鋼を用い経済
性、生産性に優れた連続焼鈍法で製造を可能にしたもの
である。By making full use of the 5t-st complete erasing effect of the present invention, it is possible to manufacture the steel using a low-cost non-alloyed steel and a continuous annealing method that is highly economical and highly productive.
の）本発明の強力な５ｔ−ｓｔｔ去作用を焼付は硬化型
鋼板（以下ＢＨ錆鋼板に応用し、完全弁５ｔ−ｓｔでか
つ従来のＢＨ錆鋼板ＢＨ量を超えたＢＨ錆鋼板製造する
用途がある。従来法では、完全弁５ｔ−ｓｔのＢＨ錆鋼
板ＢＨ量の限界は約３に９ｆＡ■２であったが、本発明
法を適用すると限界ＢＨ量を５〜６ ｋｇｆ、Ａ−まで
高めることが可能である。) The powerful 5t-stt removal effect of the present invention is applied to hardening type steel plates (hereinafter referred to as BH rust steel plates), and is used to produce BH rust steel plates with a full valve 5t-st and exceeding the BH amount of conventional BH rust steel plates. In the conventional method, the limit of the BH amount of the BH rusted steel plate for a full valve 5 t-st was approximately 3 to 9 fA 2, but by applying the method of the present invention, the limit BH amount can be increased to 5 to 6 kgf, A- It is possible to increase
（ｑ 本発明の強力な５ｔ−ｓｔｔ去作用を焼付処理後
成形される用途の鋼板（以下、耐高温５ｔ−ｓｔ用銅鋼
板よぶ）に適用し、非合金添加鋼を用い連続焼鈍でそれ
を製造することが可能である。(q) Applying the strong 5t-stt removing action of the present invention to a steel plate to be formed after baking treatment (hereinafter referred to as high temperature resistant 5t-st copper steel sheet), it is continuously annealed using non-alloy additive steel. It is possible to manufacture.
（実施例） 以下に実施例により本発明の効果を具体的に説明する。(Example) The effects of the present invention will be specifically explained below using Examples.
第１表に示す成分の鋼を通常の方法で連続鋳造スラブと
し、第１表に示す熱延条件で熱延フィルとし、第１表の
冷延板厚、の冷延コイルを製造し、第２表に示す連続焼
鈍条件で焼鈍し、供試材とした。この供試コイルを別の
ラインで第２表に示す条件でショット・プラストおよび
調質圧延を行なって冷延鋼板を製造した。このようにシ
ョット・ブラストを付加する本発明の方法で製造した冷
延鋼板と従来法で製造した冷延鋼板の時効後の引張り特
性値と２％予歪後１７０℃×２０分処理した時のΔＹ、
Ｐ （ＢＥ量）と２００℃×３０分処理後の引張り時の
Ｙ、Ｐ−ＥＪ値の調査をした。その結果を第３表に示す
。A steel having the composition shown in Table 1 is continuously cast into a slab by the usual method, a hot rolled film is made under the hot rolling conditions shown in Table 1, a cold rolled coil having the cold rolled plate thickness shown in Table 1 is manufactured, The test materials were annealed under the continuous annealing conditions shown in Table 2. This test coil was subjected to shot blasting and temper rolling on a separate line under the conditions shown in Table 2 to produce a cold rolled steel sheet. The tensile properties after aging of the cold-rolled steel sheets manufactured by the method of the present invention in which shot blasting is applied and the cold-rolled steel sheets manufactured by the conventional method, and the tensile properties after 2% pre-straining and treatment at 170°C for 20 minutes. ΔY,
P (BE amount), Y and P-EJ values during tension after treatment at 200°C for 30 minutes were investigated. The results are shown in Table 3.
第 ３ 表
供試コイル１−Ｂ、１−０は、自動車外板用の本発明の
方法の実施例であり、供試コイル１−ムはその比較例で
ある。比較例１−ムは時効後のＹ、Ｐ −ＥＡ！が０．
４−あり、自動車外板には不適であるが、本発明の方法
を適用した１−Ｉ３．ｔ−ｃはＸＰ −Ｅｌが完全にＯ
Ｋなっており、自動車外板用として適用できる。以上の
実施例の結果からも、本発明のショット・ブラストを付
加する方法の５ｔ−ｓｔの消去効果が大きく、優れてい
るかがわかる。Sample coils 1-B and 1-0 in Table 3 are examples of the method of the present invention for automobile exterior panels, and sample coil 1-M is a comparative example thereof. Comparative Example 1 - M is Y, P -EA after aging! is 0.
4-, which is not suitable for automobile exterior panels, but 1-I3. to which the method of the present invention is applied. t-c is XP-El is completely O
K, and can be applied to automobile exterior panels. From the results of the above examples, it can be seen that the 5t-st erasing effect of the method of adding shot blasting of the present invention is large and excellent.
供試コイル２−Ｂは、極低炭素鋼を用いた自動車外板用
の本発明の方法の実施例であり、供試フィル２−ムは、
その比較例である。比較例は時効後のＭＰ−ＫＪが１．
０ ％ ＃す、自動車外板に使えないが、本発明の方法
を適用した２−ムはＺＰ−Ｅｌが完全に０になっており
、自動車外板用として適している。この実施例からも本
発明の方法が極めて有効であることが明確に判る。Test coil 2-B is an example of the method of the present invention for automobile outer panels using ultra-low carbon steel, and test film 2-B is
This is a comparative example. In the comparative example, MP-KJ after aging is 1.
0% #S cannot be used for automobile exterior panels, but the 2-me to which the method of the present invention is applied has completely zero ZP-El and is suitable for automobile exterior panels. This example clearly shows that the method of the present invention is extremely effective.
供試コイル３−Ｂは、高ＢＨ鋼板用の本発明の方法の実
施例であり、供試コイル３−ムはその比較例である。比
較例３−ムはＢＨ量を狙った製造条件であるため、ＢＨ
量はｓ、 １１ｖ／１ｍｌ”となっているが時効後のＭ
Ｐ −Ｅｌは０．３−あり、プレス成形時には５ｔ−ｓ
ｔが発生するが、本発明の方法を適用した３−Ｂは、Ｂ
Ｈ量は従来のＢＨ量限界より高（５，１に９ｆ／−を確
保できており、同時ＫＭＰ−Σ）は４．１％もあり、プ
レス成形時に強列な５ｔ−ｓｔが発生し、５ｔ−ｓｔが
問題になる用途には使用できないが、本発明の方法を適
用した４−ＢはＹ、Ｐ−Σノが０であり、本発明の方法
が５ｔ−ｓｔ防止に対して極めて大きな効果があること
が明白にわかる。Test coil 3-B is an example of the method of the present invention for high BH steel sheets, and test coil 3-B is a comparative example thereof. Comparative Example 3-mu has manufacturing conditions aimed at increasing the amount of BH.
The amount is s, 11v/1ml", but after aging M
P-El is 0.3-, and 5t-s during press molding.
t occurs, but 3-B to which the method of the present invention is applied is B
The H amount is higher than the conventional BH amount limit (9f/- can be secured for 5,1, simultaneous KMP-Σ) is 4.1%, and a strong 5t-st occurs during press forming. Although it cannot be used for applications where 5t-st is a problem, 4-B to which the method of the present invention is applied has Y and P-Σ of 0, and the method of the present invention has an extremely large effect on preventing 5t-st. It is clearly seen that it is effective.
（発明の効果）
以上の説明から明らかな如く、特定の連続焼鈍材にショ
ット・プラストを付加するという本発明の方法は、づレ
ス時の５ｔ−ｓｔの消去効果が極めて顕著であり、従来
の合金添加による非時効化の方法に比し、極めて経済的
で有益な方法である。(Effects of the Invention) As is clear from the above explanation, the method of the present invention, which involves adding shot blast to a specific continuously annealed material, has a very remarkable effect of erasing 5t-st at the time of stress reduction, and compared to the conventional method. This is an extremely economical and useful method compared to non-aging methods using alloy addition.
Claims (1)
は分塊法にてスラブとし、通常の熱間圧延、冷間圧延を
施し、連続焼鈍した後、ショット・ブラストで鋼板の表
裏面に歪を付与することを特徴とする耐ストレッチャ・
ストレイン性に優れた冷延鋼板の製造方法。[Claims] C: 0.0005-0.10%, Mn: 0.05-1.0%, P≦0.10%, S≦0.04%, N≦0.0090%, solAl Steel consisting of ≦0.1%, balance Fe and unavoidable impurities is made into a slab by continuous casting or blooming method, subjected to normal hot rolling, cold rolling, continuous annealing, and then shot blasting to form a steel plate. Stretcher-resistant, characterized by applying distortion to the front and back surfaces.
A method for producing cold-rolled steel sheets with excellent strain properties.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3789285A JPS61195919A (en) | 1985-02-27 | 1985-02-27 | Manufacture of cold rolled steel sheet having superior stretcher strain resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3789285A JPS61195919A (en) | 1985-02-27 | 1985-02-27 | Manufacture of cold rolled steel sheet having superior stretcher strain resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS61195919A true JPS61195919A (en) | 1986-08-30 |
Family
ID=12510190
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3789285A Pending JPS61195919A (en) | 1985-02-27 | 1985-02-27 | Manufacture of cold rolled steel sheet having superior stretcher strain resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61195919A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63134645A (en) * | 1986-11-26 | 1988-06-07 | Nippon Steel Corp | Steel sheet for di can excellent in stretch-flange formability |
| WO1990011849A1 (en) * | 1989-03-30 | 1990-10-18 | Nippon Steel Corporation | Method of producing rollable metal sheet based on quench-solidified thin cast sheet |
| US5286315A (en) * | 1989-03-30 | 1994-02-15 | Nippon Steel Corporation | Process for preparing rollable metal sheet from quenched solidified thin cast sheet as starting material |
| EP0731181A1 (en) * | 1993-12-28 | 1996-09-11 | Fuji Kihan Co., Ltd. | Method of preventing abrasion at sliding portion of metal-product |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57114611A (en) * | 1980-07-02 | 1982-07-16 | Nippon Kokan Kk <Nkk> | Treatment of high tensile zinc hot dipped steel material |
-
1985
- 1985-02-27 JP JP3789285A patent/JPS61195919A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57114611A (en) * | 1980-07-02 | 1982-07-16 | Nippon Kokan Kk <Nkk> | Treatment of high tensile zinc hot dipped steel material |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63134645A (en) * | 1986-11-26 | 1988-06-07 | Nippon Steel Corp | Steel sheet for di can excellent in stretch-flange formability |
| WO1990011849A1 (en) * | 1989-03-30 | 1990-10-18 | Nippon Steel Corporation | Method of producing rollable metal sheet based on quench-solidified thin cast sheet |
| US5286315A (en) * | 1989-03-30 | 1994-02-15 | Nippon Steel Corporation | Process for preparing rollable metal sheet from quenched solidified thin cast sheet as starting material |
| EP0731181A1 (en) * | 1993-12-28 | 1996-09-11 | Fuji Kihan Co., Ltd. | Method of preventing abrasion at sliding portion of metal-product |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2005126733A (en) | Steel sheet for hot press having excellent hot workability, and automotive member | |
| JP4589747B2 (en) | Non-oriented electrical steel sheet with excellent magnetic properties, its manufacturing method and strain relief annealing method | |
| JPS5825436A (en) | Manufacture of deep drawing cold rolling steel plate having slow aging property and small anisotropy | |
| JPH0123530B2 (en) | ||
| JP2010053451A (en) | Cold-rolled steel sheet having aging resistance and superior workability, and method for manufacturing the same | |
| KR970007205B1 (en) | Cold rolled steel sheet for shadow mask and manufacturing method | |
| JPS61195919A (en) | Manufacture of cold rolled steel sheet having superior stretcher strain resistance | |
| JP2005171331A (en) | Steel sheet for soft nitriding having excellent formability, and its production method | |
| JPH0819465B2 (en) | Non-oriented electrical steel sheet manufacturing method | |
| JP2023507639A (en) | HIGH STRENGTH FERRITIC STAINLESS STEEL FOR CLAMP AND METHOD FOR MANUFACTURING SAME | |
| JP3718865B2 (en) | Manufacturing method of lightweight can with excellent bottom pressure strength | |
| JPH0213004B2 (en) | ||
| EP3733903A1 (en) | Grain-oriented electrical steel sheet and manufacturing method therefor | |
| JPH01275736A (en) | Continuously cast steel plate for enameling having excellent workability and its manufacture | |
| JPS641531B2 (en) | ||
| JP2671737B2 (en) | Manufacturing method of thin steel sheet for deep drawing | |
| JPH1046289A (en) | Steel sheet excellent in external appearance of panel and dent resistance after panel working | |
| KR100470640B1 (en) | A high strength bake-hardenable cold rolled steel sheet, and a method for manufacturing it | |
| JP3845871B2 (en) | Method for producing non-oriented electrical steel sheet with high magnetic flux density | |
| JPS6330969B2 (en) | ||
| JP3381440B2 (en) | Manufacturing method of cold rolled steel sheet with excellent deep drawability | |
| JP2504219B2 (en) | Method for manufacturing alloyed galvanized steel sheet for drawing | |
| JPS60190521A (en) | Manufacture of nonoriented electrical steel sheet | |
| JPH0137454B2 (en) | ||
| JPH02263950A (en) | Hot rolled steel sheet for deep drawing and its manufacture |