JPS637335A - Production of high-strength high gamma value cold rolled steel sheet - Google Patents
Production of high-strength high gamma value cold rolled steel sheetInfo
- Publication number
- JPS637335A JPS637335A JP14996686A JP14996686A JPS637335A JP S637335 A JPS637335 A JP S637335A JP 14996686 A JP14996686 A JP 14996686A JP 14996686 A JP14996686 A JP 14996686A JP S637335 A JPS637335 A JP S637335A
- Authority
- JP
- Japan
- Prior art keywords
- strength
- steel
- annealing
- rolling
- steel sheet
- 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
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 9
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 238000000137 annealing Methods 0.000 claims abstract description 29
- 238000005098 hot rolling Methods 0.000 claims abstract description 14
- 238000005097 cold rolling Methods 0.000 claims abstract description 11
- 238000005096 rolling process Methods 0.000 claims abstract description 11
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910001208 Crucible steel Inorganic materials 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 abstract description 50
- 239000010959 steel Substances 0.000 abstract description 50
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 230000003796 beauty Effects 0.000 abstract description 5
- 238000000034 method Methods 0.000 description 15
- 230000000694 effects Effects 0.000 description 10
- 238000001556 precipitation Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000007689 inspection Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000012827 research and development Methods 0.000 description 2
- 238000004804 winding Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000655 Killed steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 241001648319 Toronia toru Species 0.000 description 1
- RQMIWLMVTCKXAQ-UHFFFAOYSA-N [AlH3].[C] Chemical compound [AlH3].[C] RQMIWLMVTCKXAQ-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000003556 assay Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 125000000101 thioether group Chemical group 0.000 description 1
- 230000009466 transformation Effects 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、表面疵のない高強度高ｒ値冷延鋼板を製造す
る方法に関するもので、特に付加工程を含まない通常の
工程で経済的に製造することのできるものである。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to a method for producing a high-strength, high-r-value cold-rolled steel sheet free of surface defects, and particularly relates to a method for manufacturing a cold-rolled steel sheet with high strength and high r-value, which is economical in a normal process that does not include additional steps. It can be manufactured in
（従来の技術）
近年、安全対策や省エネルギーの観点から自動車用鋼板
の高強度化が進み、各種高強度鋼板の研究開発が行なわ
れ現在に至るもまだ活発である。(Prior Art) In recent years, steel plates for automobiles have been made to have higher strength from the viewpoint of safety measures and energy conservation, and research and development of various high-strength steel plates has been carried out and is still active to this day.
自動車用鋼板にとっての生命は高度の成形性と表面美麗
度である。しかし、合金化等によって高強度化されると
、これら特性、特に成形性は劣化するのが普通であり、
自動車用鋼板の高強度化にあたってはこれら特性の維持
が大きな課題となる。The lifeblood of automotive steel sheets is high formability and surface beauty. However, when the strength is increased by alloying, etc., these properties, especially formability, usually deteriorate.
Maintaining these properties is a major challenge in increasing the strength of automotive steel sheets.
薄鋼板の成形性には、伸びで代表される延性とＦ値で代
表される深絞り性とがある。（注、Ｆ値は塑性異方性を
表わす指標で、ある方向に引っ張った時にｒ＝（幅対数
ひずみ〕／〔板厚対数ひずみ〕で定義され、Ｆ＝ （ｒ
（圧延方向）＋「（圧延方向と直角）＋２ｒ（圧延方
向に４５度）〕÷４である。Ｆ値と深絞り性とは良く対
応すると言われている。）
このうち、伸び〜強度関係については研究開発が進み、
相当に強度が高い場合でも伸びの大きいいわゆるＴＳ−
Ｅβバランスの優れた鋼板が開発されている。（注、Ｔ
Ｓ：引張強度、Ｅｌ：伸−び）しかし、１値〜強度関係
については、それほど高強度側にまで開発されていない
。すなわち？≧１．５を有する深絞り用と言えるもので
はせいぜい引張強度４０ ｋｇｆ／＊ｍ”級までが現状
実用化されているに過ぎない。Formability of thin steel sheets includes ductility, which is represented by elongation, and deep drawability, which is represented by F value. (Note: F value is an index expressing plastic anisotropy, and is defined as r = (width logarithmic strain) / [thickness logarithmic strain] when pulled in a certain direction, and F = (r
(Rolling direction) + "(perpendicular to the rolling direction) + 2r (45 degrees to the rolling direction)] ÷ 4. It is said that the F value and deep drawability correspond well.) Among these, the relationship between elongation and strength is Research and development is progressing on
So-called TS-, which has a large elongation even when the strength is considerably high.
Steel sheets with excellent Eβ balance have been developed. (Note, T
(S: tensile strength, El: elongation) However, the relationship between one value and strength has not been developed to the high strength side. In other words? ≧1.5, which can be said to be used for deep drawing, has a tensile strength of up to 40 kgf/*m'' class at most, which is currently in practical use.
しかし、高強度〜高を値の達成手段としてＣｕ添加は知
られている。すなわち特開昭５９−７６８２４号公報、
特開昭５９−７６８２５号公報および特公昭５８−４２
２４８号公報記載の技術がそれである。これらの技術に
より、引張強度が５０に＋ｒｆ／鶴２級でＦ ＝ １．
５以上のものが得られる。However, Cu addition is known as a means of achieving high to high strength values. That is, Japanese Patent Application Laid-Open No. 59-76824,
Japanese Unexamined Patent Publication No. 59-76825 and Japanese Patent Publication No. 58-42
This is the technique described in Publication No. 248. With these techniques, the tensile strength is increased to 50+RF/Tsuru grade 2 and F = 1.
5 or more can be obtained.
しかしながら、これらの技術においてはＣｕを有効に作
用させるために、熱延板の焼鈍および／または熱延板の
析出処理を必須としており、これは鋼板の生産性を著し
く損ない、そのため、鋼板のコスト上昇をもたらし、実
用化を困難なものにしていた。However, these techniques require annealing of the hot-rolled sheet and/or precipitation treatment of the hot-rolled sheet in order to make Cu work effectively, which significantly impairs the productivity of the steel sheet and therefore reduces the cost of the steel sheet. This caused a rise in the amount of carbon dioxide, making it difficult to put it into practical use.
すなわち、特開昭５９−７６８２４号公報では、その特
許請求の範囲（２）、 （３）にはＣｕ添加鋼が記載さ
れているが、熱延板を８５０〜９５０℃という極めて高
温度で溶体化処理した後さらに５００℃以上の温度で焼
鈍し、しかる後に冷延・焼鈍することが要件となってい
る。特開昭５９−７６８２５号公報ではやはり、その特
許請求の範囲（２）〜（４）にはＣｕ添加鋼が記載され
ているが、５００℃以上の温度で熱延板を焼鈍した後、
冷延・焼鈍することが要件となっている。さらにまた、
特公昭５８−４２２４８号公報では特許請求の範囲には
付加工程に関する記載はないが、高ｒ値を示す実施例で
は熱延板の付加熱処理を行なっている。このように従来
技術では大量生産素材としてはまず避けるべき工程付加
を必須要件としている。That is, in JP-A-59-76824, claims (2) and (3) thereof describe Cu-added steel; After the chemical treatment, it is required that the steel be further annealed at a temperature of 500° C. or higher, and then cold rolled and annealed. JP-A-59-76825 also describes Cu-added steel in its claims (2) to (4), but after annealing the hot-rolled sheet at a temperature of 500°C or higher,
Cold rolling and annealing are required. Furthermore,
Although Japanese Patent Publication No. 58-42248 does not include any description of an additional process in the claims, additional heat treatment of the hot-rolled sheet is carried out in the examples showing a high r value. As described above, in the prior art, as a material for mass production, the addition of processes that should be avoided is an essential requirement.
冷延鋼板としてもう一つの重要な要件である表面美麗度
にとってＣｕ添加はこれまで必ずしも好適ではなく、こ
れもまたＣｕ添加鋼の実用化阻害要因と言える。Ｃｕ添
加鋼ではＣｕへげと呼ばれる表面疵が生じる。このため
、Ｃｕ添加量の制限やＮｉ複合添加により防止が計られ
ている。そうすると強度やｆ値が不十分になったり、コ
ストアンプになるというような欠点が重畳される。特に
、自動車外板や準外板には不向きであった。Up to now, Cu addition has not always been suitable for surface beauty, which is another important requirement for cold-rolled steel sheets, and this can also be said to be a factor inhibiting the practical use of Cu-added steel. In Cu-added steel, surface flaws called Cu flakes occur. Therefore, attempts have been made to prevent this by limiting the amount of Cu added and adding Ni in combination. In this case, disadvantages such as insufficient strength and f-number and cost increase are added. In particular, it was unsuitable for automobile exterior panels and semi-exterior panels.
（発明が解決しようとする問題点）
本発明はこの様な状況に鑑み、５０ ｋｇｆ／＊ｍ”以
上の引張強度と１．５以上のｔ値を有し、かつ自動車外
板にも耐える表面美麗度を兼ね備える高強度冷延鋼板を
、特別な付加工程のない通常の工程においてその工程条
件を特定し、かつ特定の添加成分との組合わせによって
供給しようとするものである。(Problems to be Solved by the Invention) In view of these circumstances, the present invention provides a surface that has a tensile strength of 50 kgf/*m" or more, a t value of 1.5 or more, and is resistant to automobile exterior panels. The objective is to supply high-strength cold-rolled steel sheets with good beauty in a normal process without special additional processes by specifying the process conditions and by combining them with specific additive components.
（問題点を解決するための手段）
本発明の要旨とするところは、Ｃ： ０．０３〜０．１
０％、Ｓｉ：０．２％以下、Ｍｎ：０．９〜２．０％、
Ｐ ： ０．１％以下、Ｃｕ：０．６〜１．５％、Ａｌ
： ０．０１〜０．１％、Ｎ ： ０．００７０％以下
を含み、残部不可避的不純物元素からなる鋼を連続鋳造
してスラブとし、これを直接、もしくは１０００〜１０
８０℃に加熱後熱間圧延を行ない、８６０〜９３０°Ｃ
で圧延を終了し、６２０〜７５０℃に巻取り、続いて、
６５〜８５％の圧下率で冷間圧延を行った後昇温速度１
０〜１００℃／時、焼鈍温度６５０〜８００°Ｃ１焼鈍
保定時間２〜２０時間で箱焼鈍を行うことを特徴とする
高強度高を値冷延鋼板の製造方法にある。(Means for solving the problems) The gist of the present invention is that C: 0.03 to 0.1
0%, Si: 0.2% or less, Mn: 0.9 to 2.0%,
P: 0.1% or less, Cu: 0.6-1.5%, Al
: 0.01 to 0.1%, N : 0.0070% or less, and the remainder consists of unavoidable impurity elements, is continuously cast into a slab, and this is directly or
After heating to 80°C, hot rolling is performed to 860-930°C.
Finish rolling at 620-750°C, and then
After cold rolling with a reduction ratio of 65 to 85%, the temperature increase rate is 1.
A method for producing a cold-rolled steel sheet with high strength, characterized by box annealing at 0 to 100°C/hour, an annealing temperature of 650 to 800°C, and an annealing holding time of 2 to 20 hours.
すなわち、本発明は、比較的多量のＣｕを添加した鋼を
出発材としこれを連続鋳造し、かつ熱延条件を特定する
ことでＣｕの溶体化状態を確保しつつＣｕへげの防止を
達成し、続いて、熱延後コイルを高’／Ｌ巻取すること
で適正なＣｕ析出状態を得ることに成功したものである
。That is, the present invention uses steel to which a relatively large amount of Cu has been added as a starting material, continuously casts it, and specifies hot rolling conditions, thereby achieving prevention of Cu flaking while ensuring the solution state of Cu. However, by subsequently winding the hot-rolled coil at high'/L, it was possible to obtain an appropriate Cu precipitation state.
次に、本発明構成要件の数値限定理由について述べる。Next, the reasons for limiting the numerical values of the constituent elements of the present invention will be described.
まず、Ｃは０．０３〜０．１０％必要である。０．０３
％未満では強度が得られず、０．１％を越えるとｔ値、
伸びが低くなる。First, C is required in an amount of 0.03 to 0.10%. 0.03
If it is less than 0.1%, no strength can be obtained, and if it exceeds 0.1%, the t value,
Elongation becomes lower.
Ｓｉは？値を劣化させずに鋼を強化するが、焼鈍時に板
表層にテンパーカラーを生じ易く、表面美麗度を重んじ
る本発明では０．２％以下に限定した。What about Si? Although it strengthens the steel without deteriorating its value, it tends to cause temper color on the surface layer of the plate during annealing, so in the present invention, where surface beauty is important, it is limited to 0.2% or less.
厳しい自動車外板に適用する場合には０．０３％以下と
することが好ましい。When applied to severe automobile outer panels, the content is preferably 0.03% or less.
Ｍｎは強度を確保するために必要であるが、それ以外に
Ｃとあいまって鋼の変態点を調整し、Ｃｕの溶体・析出
挙動を補助する効果をもたらす。０．９％未満ではこれ
らの効果が少なく、２．０％超ではかえってｔ値を低下
させる。Mn is necessary to ensure strength, but in addition to that, together with C it has the effect of adjusting the transformation point of steel and assisting the solution/precipitation behavior of Cu. If it is less than 0.9%, these effects will be small, and if it exceeds 2.0%, the t value will actually decrease.
Ｐは、ｆ値を損なうことなしに鋼を強化する。P strengthens the steel without compromising the f value.
しかし、Ｐは鋼を脆化させ、加工後の粒界破壊を発生さ
せる可能性があるので上限を０．１％とする。However, P embrittles the steel and may cause intergranular fracture after working, so the upper limit is set at 0.1%.
この加工脆化が問題となる場合には０．０１％以内の高
純度にすることが好ましい。If this process embrittlement is a problem, it is preferable to have a high purity of 0.01% or less.
Ａｌは脱酸およびＮの固定のために０．０１〜Ｏ９１％
必要である。下限値未満ではこれらの作用が不十分であ
り、上限を越えると不純物が増し、鋼の延性を劣化させ
る。Al is 0.01-91% for deoxidation and N fixation.
is necessary. Below the lower limit, these effects are insufficient, and above the upper limit, impurities increase and deteriorate the ductility of the steel.
Ｎば低炭素アルミキルド鋼はどではないが、ＡＩＮ析出
時に補助的にｒ値を高める作用がある。Although N is not the same as low carbon aluminum killed steel, it has the effect of increasing the r value as an auxiliary during AIN precipitation.
このため、０．００７０％以内添加する。これを越える
とＡＩＮ析出量が増し延性を劣化させる。Therefore, it is added within 0.0070%. If this value is exceeded, the amount of AIN precipitation increases and the ductility deteriorates.
次にＣｕは本発明において基本をなす元素である。Next, Cu is a basic element in the present invention.
すなわち、Ｃｕは鋼の強度を高め、を値を高めるために
必要な反面、Ｃｕ添加鋼の害であるＣｕへげの原因とも
なる。本発明では付加工程をなくすためにＣｕは比較的
多量に添加する。０．６％未満では付加工程省略は困難
である。好ましくは０．９％以上とすべきである。−方
、１．５％超程度で強度、を値に必要なＣｕ析出物量と
しては飽和し、また鋼の経済性を損なうので、上限は１
．５％とした。That is, although Cu is necessary to increase the strength of steel and increase its value, it also causes Cu flaking, which is a problem with Cu-added steel. In the present invention, Cu is added in a relatively large amount in order to eliminate the addition step. If it is less than 0.6%, it is difficult to omit the additional step. Preferably it should be 0.9% or more. On the other hand, if it exceeds 1.5%, the amount of Cu precipitates required for strength is saturated, and it also impairs the economic efficiency of the steel, so the upper limit is 1.
．． It was set at 5%.
なお、硫化物系介在物は圧延により展伸しその切欠効果
のために鋼板の曲げ成形性などの成形性を劣化させる。Incidentally, sulfide-based inclusions are expanded by rolling, and their notch effect deteriorates the formability such as the bending formability of the steel sheet.
そのため、Ｓを０．０１０％以下とすることは望ましい
。さらに、Ｃａ、 ＲＥＭ、 Ｍｇの１種以上を添加し
て硫化物の組成を変え、圧延による展伸を抑−えること
が好ましい。その場合、之等の各元素は０．００１０〜
０．０１００％の添加が必要である。Therefore, it is desirable that S be 0.010% or less. Furthermore, it is preferable to add one or more of Ca, REM, and Mg to change the composition of the sulfide to suppress elongation due to rolling. In that case, each element such as 0.0010~
Addition of 0.0100% is required.
いずれも下限値未満では効果がなく、上限値を越すとか
えって全介在物量が増し材質を劣化させる。If the lower limit is less than the lower limit, there is no effect, and if the upper limit is exceeded, the total amount of inclusions increases and the quality of the material deteriorates.
次に製造工程であるが、まず、鋳造は連続鋳造でなけれ
ばならない。連続鋳造ではスラブ厚が小さく比較的速や
かに冷却されるのでＣｕへげに繋がるＣｕ表面濃化が少
ない。そしてこのスラブはそのままか、あるいは加熱炉
に入れる場合は１０００〜１０８０℃に加熱してから熱
延を行う。１０００℃未満の加熱では熱延がしがたく、
また、１０８０℃を越えるとＣｕへげが生ずる。熱延は
比較的高温で行ない、８６０〜９３０℃で終了する。８
６０℃未満ではＣｕ析出が生じ、付加工程なしでは高を
値・高強度とはならない。また、９３０℃を越えると、
フェライト結晶粒が粗大化しｔ値、伸びが劣化する。熱
延後ランアウトテーブル上で冷却を行ない、６２０〜７
５０℃の温度範囲で巻取る。６２０℃未満ではＣｕ析出
が十分でなく、７５０℃超ではＣｕ析出物が粗大化して
しまい、いずれも高を値・高強度とならない。ランアウ
トテーブルでの冷却は通常で良いが、巻取での析出促進
の意味で２０〜ｂ
延コイルは冷延・焼鈍されるが、冷延圧下率は十分なｒ
値を確保するには６５％以上必要である。Next is the manufacturing process. First, casting must be continuous casting. In continuous casting, the slab thickness is small and the slab is cooled relatively quickly, so there is little concentration of Cu surface that leads to Cu flaking. Then, this slab is hot-rolled either as it is or, if placed in a heating furnace, after being heated to 1000 to 1080°C. It is difficult to hot-roll when heated below 1000℃,
Further, when the temperature exceeds 1080°C, Cu flaking occurs. Hot rolling is performed at a relatively high temperature and is completed at 860-930°C. 8
If the temperature is lower than 60°C, Cu precipitation occurs, and high values and strength cannot be achieved without an additional process. In addition, when the temperature exceeds 930℃,
The ferrite crystal grains become coarse and the t value and elongation deteriorate. After hot rolling, it is cooled on a run-out table, and 620-7
Wind up in a temperature range of 50°C. If the temperature is lower than 620°C, Cu precipitation will not be sufficient, and if the temperature exceeds 750°C, the Cu precipitates will become coarse, and in both cases high values and high strength will not be achieved. Normal cooling on the runout table is sufficient, but in order to promote precipitation during coiling, the rolled coil is cold rolled and annealed, but the cold rolling reduction rate is sufficient.
65% or more is required to secure the value.
圧下率は通常の範囲では高いほど良いが、上限値は工業
的に圧下可能な値である８５％とした。焼鈍昇温速度は
１００℃／時以下としなければならない。これより大き
くなると良好なＦ値が得られない。下限値は１０℃／時
とした。この値で十分に特性が得られるが、いたずらに
時間をかけて昇温することは経済性を損なうからである
。焼鈍温度は６５０〜８００℃、焼鈍保定時間は２〜２
０時間でなければならない。いずれも下限値未満ではフ
ェライト結晶の再結晶・成長が十分でなく低を値・低延
性となる。それぞれの上限値付近で特性は飽和し、
また、高温長時間はどコストアップとなるので８００℃
および２０時間を上限値と定めた。焼鈍はタイトコイル
、オープンコイルを問わないが、生産性の高いタイトコ
イル焼鈍が好ましい。その場合、焼鈍温度の上限は７５
０℃程度である。The higher the rolling reduction rate is in the normal range, the better, but the upper limit was set to 85%, which is a value that can be rolled down industrially. The annealing temperature increase rate must be 100° C./hour or less. If it is larger than this, a good F value cannot be obtained. The lower limit was 10°C/hour. This is because although sufficient characteristics can be obtained with this value, economical efficiency is impaired if the temperature is increased unnecessarily over a long period of time. Annealing temperature is 650-800℃, annealing retention time is 2-2
Must be 0 hours. If both values are below the lower limit, recrystallization and growth of ferrite crystals will not be sufficient, resulting in low values and low ductility. The characteristics are saturated near the upper limit of each, and the cost increases due to high temperatures for long periods of time, so 800℃
and 20 hours was set as the upper limit. Although tight coil annealing or open coil annealing may be used, tight coil annealing is preferred because of its high productivity. In that case, the upper limit of the annealing temperature is 75
The temperature is about 0°C.
（実施例−１）
第１表に示す成分の鋼を溶製し、連続鋳造−熱延を行な
った。鋼Ａ、Ｂは直送、泪Ｃ−Ｆはスラブを１０５０℃
に再加熱して熱延した。鋼Ａ、Ｃ，Ｅは本発明にしたが
った鋼成分であるが、鋼ＢはＣｕが、鋼りはＣ，Ｍｎが
、綱ＦはＣ，Ｓｔがそれぞれ本発明範囲と異なる。これ
らの綱をＦＴ（仕上温度）＝８８０〜９１０℃で熱延し
た後、直ちに約３０’ｃ ／ ｓの平均冷却速度で冷却
し、６６０〜６８０℃で巻取った。この綱を酸洗後８０
％の冷延を行ない、続いて、昇温速度３０℃／時、保定
７２０℃、１２時間の焼鈍をおこない最後に１．０％の
スキンバス圧延を行なった。結果の機械的性質および表
面検定評点を第２表に示す。機械試験はＪＩＳ２２２０
１５号試験片を用い、ＪＩＳ Ｚ ２２４１記載の方法
にしたがって実施した。表面検定は出荷時検査に準じて
行なった。評点は１から５まであり、数値が大きくなる
ほどへげ、すり疵、介在物露出等の表面欠陥が著しい。(Example 1) Steel having the components shown in Table 1 was melted and continuously cast and hot rolled. Steel A and B are delivered directly, and Slabs C-F are heated to 1050℃.
It was reheated and hot rolled. Steels A, C, and E have steel components according to the present invention, but steel B has Cu, steel steel has C and Mn, and steel F has C and St, which are different from the scope of the present invention. After hot rolling these ropes at FT (finishing temperature) = 880-910 °C, they were immediately cooled at an average cooling rate of about 30'c/s and coiled at 660-680 °C. After pickling this rope, 80
% cold rolling was performed, followed by annealing at a heating rate of 30° C./hour and a holding temperature of 720° C. for 12 hours, and finally skin bath rolling of 1.0%. The resulting mechanical properties and surface assay scores are shown in Table 2. Mechanical test is JIS2220
The test was carried out using a No. 15 test piece according to the method described in JIS Z 2241. The surface inspection was conducted in accordance with the inspection at the time of shipment. Ratings range from 1 to 5, and the higher the number, the more serious surface defects such as flaws, scratches, and exposed inclusions.
評点１は欠陥を認め得なかったことを示し、通常評点２
以下が出荷可能である。A rating of 1 indicates that no defects were found, and a rating of 2 is normal.
The following can be shipped.
第２表より明らかなように、本発明にしたがった綱Ａ、
Ｃ，Ｅは５０ ｋＫｆ／ｘ＊”以上の引張強度と１．５
を越えるｔ値を有し、延性も良好である。表面状態も全
く問題がない。これに対し、鋼Ｂでは強度、ｒ値が足り
ず、ＭＤでは強度が大幅に低下している。鋼Ｆはｔ値が
低い上に、テンパーカラーのために評点が落ちている。As is clear from Table 2, rope A according to the present invention,
C and E have a tensile strength of 50 kKf/x*” or more and 1.5
It has a t value exceeding , and has good ductility. There are no problems with the surface condition. On the other hand, steel B lacks strength and r value, and the strength of MD is significantly reduced. Steel F has a low t value and a lower rating due to its temper color.
これより本発明の成分条件の必要性が明らかである。From this, the necessity of the component conditions of the present invention is clear.
（実施例−２）
第１表に示す鋼の内符号Ａ−ＣおよびＥの鋼を用い、第
３表に示す熱延条件で熱延を行なった。(Example 2) Using the steels shown in Table 1, steels with internal codes A-C and E were hot-rolled under the hot-rolling conditions shown in Table 3.
隘１〜４では直送熱延を、！！ｈ５〜１１では再加熱後
熱延を行なった。魚１２ではインゴット法で鋳込み、再
加熱後熱延を行なった。なお、患７では 。Direct delivery of hot rolling in rooms 1 to 4! ! From h5 to h11, hot rolling was performed after reheating. Fish No. 12 was cast by the ingot method, reheated, and then hot rolled. In addition, in patient 7.
熱延後、９００℃、２時間のＣυ溶体化処理と６５０℃
、１２時間の析出処理を行なった。すなわち、これは従
来の典型的なＣｕ添加鋼における付加工程である。熱延
板はその後７８．６％ないし８０％の冷延が施され、続
いて昇温速度＝３０″Ｃ／時、焼鈍温度ニア２０℃／時
、焼鈍時間：１２時間の焼鈍が施された。１．０％スキ
ンパス圧延後の材質・表面状態を同じく第３表に示す、
この実施例では主としてＣＣ−熱延の条件の影響を見て
いるが、１１ｈ１．３，４．８の例が本発明にしたがっ
ており、その他はいずれかの条件において本発明と異な
る。After hot rolling, Cυ solution treatment at 900℃ for 2 hours and 650℃
, a precipitation treatment was performed for 12 hours. That is, this is an additional step in typical conventional Cu-added steel. The hot-rolled sheet was then cold-rolled from 78.6% to 80%, and then annealed at a heating rate of 30″C/hour, annealing temperature of near 20°C/hour, and annealing time: 12 hours. The material and surface condition after 1.0% skin pass rolling are also shown in Table 3.
In this example, the influence of CC-hot rolling conditions is mainly observed, but examples of 11h1.3 and 4.8 are in accordance with the present invention, and the others differ from the present invention in any of the conditions.
そして本発明と異なったものは強度、延性、ｒ値、表面
状態のいずれかひとつ以上において劣化している。ただ
し、丸７の鋼のように特別の付加処理を施したものは良
好な特性を示す。言い替えれば、本発明で付加工程省略
が実現されたことを示している。Those different from the present invention are deteriorated in one or more of strength, ductility, r value, and surface condition. However, steels that have undergone special additional treatment, such as round 7 steel, exhibit good properties. In other words, the present invention shows that the additional process can be omitted.
この実施例より、ＣＣ１熱延、巻取条件の影響は明らか
である。From this example, the influence of CC1 hot rolling and winding conditions is clear.
（実施例−３）
次に、冷延・焼鈍条件の影響を示す実施例について述べ
る。(Example 3) Next, an example showing the influence of cold rolling and annealing conditions will be described.
冷延・焼鈍条件と結果を第４表に示す。用いた鋼は第１
表＠Ａである。徹２〜４の鋼は本発明条件に従っており
本発明が目的とする良好な特性を有する。それに対して
、患１の鋼では冷延率が、Ｎａ３の鋼では昇温速度が、
阻６の鋼では焼鈍温度が、Ｎ１１７の綱では焼鈍時間が
それぞれ本発明と相違しており、その結果、低を値ある
いは低強度となっている。この実施例より、本発明にお
ける冷延・焼鈍条件の効果は明らかである。Table 4 shows the cold rolling/annealing conditions and results. The steel used is the first
Table @A. The steels of Toru 2 to 4 comply with the conditions of the present invention and have the good properties aimed at by the present invention. On the other hand, the cold rolling rate of the steel with No. 1 and the heating rate of the steel with Na3,
The annealing temperature of the No. 6 steel and the annealing time of the N117 steel are different from those of the present invention, and as a result, the steel has a low value or a low strength. From this example, the effects of cold rolling and annealing conditions in the present invention are clear.
（発明の効果）
自動車を中心とする材料の高強度化は、素材の有効利用
の観点から当然進展するものでなければならない。しか
しながら、薄鋼板においては成形性劣化がネックとなり
その進展が阻まれていた。(Effects of the Invention) Increasing the strength of materials mainly for automobiles must naturally progress from the viewpoint of effective use of materials. However, progress in thin steel sheets has been hindered by deterioration in formability.
本発明によって、この制限が引張強度６０ ｋｇｆ／ｍ
ｍ”級まで緩和され、これによって、−種の飽和状態に
あった鋼板の高強度化に新展開が開けたのであって、そ
の経済的な効果は大きい。With the present invention, this limit is reduced to a tensile strength of 60 kgf/m
This has opened up a new development in increasing the strength of steel sheets that had been saturated with - grade, and the economic effects are significant.
また、鋼中Ｃｕは、鋼の耐食性を高めると推定され、高
強度化に伴う薄手化によって生ずる耐食寿命を補うこと
が期待される。すなわち、高強度化、高耐食性化という
三大課題の両立という展開が可能でこの意味からも本発
明の効果は極めて大きい。Further, Cu in steel is estimated to improve the corrosion resistance of steel, and is expected to compensate for the corrosion resistance life caused by thinning due to higher strength. That is, it is possible to achieve both of the three major problems of high strength and high corrosion resistance, and in this sense, the effects of the present invention are extremely large.
Claims (1)
：０．９〜２．０％、Ｐ：０．１％以下、Ｃｕ：０．６
〜１．５％、Ａｌ：０．０１〜０．１％、Ｎ：０．００
７０％以下を含み、残部不可避的不純物元素からなる鋼
を連続鋳造してスラブとし、これを直接、もしくは１０
００〜１０８０℃に加熱後熱間圧延を行ない、８６０〜
９３０℃で圧延を終了し、６２０〜７５０℃に巻取り、
続いて、６５〜８５％の圧下率で冷間圧延を行った後昇
温速度１０〜１００℃／時、焼鈍温度６５０〜８００℃
、焼鈍保定時間２〜２０時間で箱焼鈍を行うことを特徴
とする高強度高＠ｒ＠値冷延綱板の製造方法。C: 0.03 to 0.10%, Si: 0.2% or less, Mn
: 0.9 to 2.0%, P: 0.1% or less, Cu: 0.6
~1.5%, Al: 0.01~0.1%, N: 0.00
Continuously cast steel containing 70% or less and the remainder consisting of unavoidable impurity elements to form a slab, which can be directly or
After heating to 00~1080℃, hot rolling is carried out to 860~1080℃.
Finish rolling at 930°C, wind up at 620-750°C,
Subsequently, after performing cold rolling at a reduction rate of 65 to 85%, the temperature increase rate was 10 to 100°C/hour, and the annealing temperature was 650 to 800°C.
A method for producing a high-strength, high-value cold-rolled steel sheet, characterized in that box annealing is performed with an annealing holding time of 2 to 20 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61149966A JPH0699756B2 (en) | 1986-06-26 | 1986-06-26 | Method for manufacturing high strength high r value cold rolled steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61149966A JPH0699756B2 (en) | 1986-06-26 | 1986-06-26 | Method for manufacturing high strength high r value cold rolled steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS637335A true JPS637335A (en) | 1988-01-13 |
| JPH0699756B2 JPH0699756B2 (en) | 1994-12-07 |
Family
ID=15486504
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61149966A Expired - Lifetime JPH0699756B2 (en) | 1986-06-26 | 1986-06-26 | Method for manufacturing high strength high r value cold rolled steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0699756B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003018857A1 (en) * | 2001-08-24 | 2003-03-06 | Nippon Steel Corporation | Steel plate exhibiting excellent workability and method for producing the same |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5842248A (en) * | 1981-08-19 | 1983-03-11 | フエアチアイルド・カメラ・アンド・インストルメント・コ−ポレ−シヨン | Wire bonding technique for integrated circuit chip |
| JPS6112975A (en) * | 1984-06-12 | 1986-01-21 | テイツクリラン ベリテヒタート オユ | Substancially non-extensible fabric having water resistance and weatherability, its production and constitutional material obtained therefrom |
-
1986
- 1986-06-26 JP JP61149966A patent/JPH0699756B2/en not_active Expired - Lifetime
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5842248A (en) * | 1981-08-19 | 1983-03-11 | フエアチアイルド・カメラ・アンド・インストルメント・コ−ポレ−シヨン | Wire bonding technique for integrated circuit chip |
| JPS6112975A (en) * | 1984-06-12 | 1986-01-21 | テイツクリラン ベリテヒタート オユ | Substancially non-extensible fabric having water resistance and weatherability, its production and constitutional material obtained therefrom |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003018857A1 (en) * | 2001-08-24 | 2003-03-06 | Nippon Steel Corporation | Steel plate exhibiting excellent workability and method for producing the same |
| US7534312B2 (en) | 2001-08-24 | 2009-05-19 | Nippon Steel Corporation | Steel plate exhibiting excellent workability and method for producing the same |
| US7749343B2 (en) | 2001-08-24 | 2010-07-06 | Nippon Steel Corporation | Method to produce steel sheet excellent in workability |
| US7776161B2 (en) | 2001-08-24 | 2010-08-17 | Nippon Steel Corporation | Cold-rolled steel sheet excellent in workability |
| US8052807B2 (en) | 2001-08-24 | 2011-11-08 | Nippon Steel Corporation | Steel sheet excellent in workability |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0699756B2 (en) | 1994-12-07 |
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