JPS5825733B2 - Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workability - Google Patents
Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workabilityInfo
- Publication number
- JPS5825733B2 JPS5825733B2 JP54153392A JP15339279A JPS5825733B2 JP S5825733 B2 JPS5825733 B2 JP S5825733B2 JP 54153392 A JP54153392 A JP 54153392A JP 15339279 A JP15339279 A JP 15339279A JP S5825733 B2 JPS5825733 B2 JP S5825733B2
- Authority
- JP
- Japan
- Prior art keywords
- weldability
- cooling
- rolled steel
- strength
- workability
- 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.)
- Expired
Links
- 239000010960 cold rolled steel Substances 0.000 title claims description 11
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 238000000034 method Methods 0.000 title description 7
- 238000001816 cooling Methods 0.000 claims description 28
- 229910000831 Steel Inorganic materials 0.000 claims description 11
- 238000002791 soaking Methods 0.000 claims description 11
- 239000010959 steel Substances 0.000 claims description 11
- 238000000137 annealing Methods 0.000 claims description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 238000007796 conventional method Methods 0.000 claims description 3
- 238000010438 heat treatment Methods 0.000 claims description 3
- 238000005098 hot rolling Methods 0.000 claims description 3
- 238000005097 cold rolling Methods 0.000 claims 2
- 239000012535 impurity Substances 0.000 claims 2
- 239000000203 mixture Substances 0.000 description 7
- 238000003303 reheating Methods 0.000 description 5
- 230000002411 adverse Effects 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000007654 immersion Methods 0.000 description 2
- 238000002347 injection Methods 0.000 description 2
- 239000007924 injection Substances 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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 Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Description
【発明の詳細な説明】
この発明は溶接性、塗装性及び加工性共に良い高強度冷
延鋼板を製造する方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for producing a high-strength cold-rolled steel sheet that has good weldability, paintability, and workability.
最近、自動車用鋼板として高強度冷延鋼板が用いられる
様になって来た。Recently, high-strength cold-rolled steel sheets have come to be used as steel sheets for automobiles.
高強度冷延鋼板の製造法としては、最近は連続焼鈍を活
用した製造法が主流であるが、通常は強度付与元素(例
えばC,Mn、Si、P、Cr等)の多量添加が必要で
ある。Recently, the mainstream manufacturing method for high-strength cold-rolled steel sheets has been to utilize continuous annealing, but it usually requires the addition of large amounts of strength-imparting elements (e.g., C, Mn, Si, P, Cr, etc.). be.
しかるにこの種の元素、例えばC,Mn、Siが多量に
含有される結果、製品を溶接した場合、溶接部の強度を
劣化させたり或いは溶接部の疲労度が増大するなど溶接
性に悪影響を及ぼす。However, as a result of containing large amounts of these types of elements, such as C, Mn, and Si, when products are welded, they adversely affect weldability, such as deteriorating the strength of the welded part or increasing the fatigue level of the welded part. .
更に製品に塗装する場合の塗装性(密着性)に対しても
好ましからざる影響を与えるものである。Furthermore, it has an undesirable effect on the paintability (adhesion) when painting products.
この様なことからこの種の合金元素の添加量を少なくし
て加工性の良い高強度冷延鋼板を製造する技術が待望さ
れていた。For this reason, there has been a long-awaited technology for manufacturing high-strength cold-rolled steel sheets with good workability by reducing the amount of this type of alloying element added.
この発明は上記の要望に応えるべくなされたもので、そ
の基本的思想は溶接性、塗装性に悪影響を与える強度付
与元素の添加量を最少必要限度として、最終連続焼鈍に
おける均熱後の一次冷却に、特に気水冷却を採用してコ
ントロールされた冷却速度を用いる。This invention was made in response to the above-mentioned demands, and its basic idea is to minimize the amount of strength-imparting elements that adversely affect weldability and paintability, and to In particular, air-water cooling is employed to provide controlled cooling rates.
これにより従来法の欠点を有利に解決できると共に、強
度−延性バランスの極めて良い50〜80kg/m4の
高強度冷延鋼板の製造が可能となるものである。As a result, the drawbacks of the conventional method can be advantageously solved, and a high-strength cold-rolled steel sheet of 50 to 80 kg/m 4 with an extremely good balance of strength and ductility can be manufactured.
以下に成分の限度理由を説明する。The reasons for the limits on ingredients are explained below.
C,Si、Mnは鋼に強度を付与する元素であり、夫々
C0,05%以上、Mn0.7%以上含有させることは
必要であるが、これらの元素の含有量が多くなると本発
明の目的、すなわち溶接性、塗装性に悪影響が出て来る
ので、夫々の上限値をC0,12%以下、Si1.2%
以下、Mn1.5%以下に限定した。C, Si, and Mn are elements that give strength to steel, and it is necessary to contain 0.05% or more of C and 0.7% or more of Mn, respectively, but if the content of these elements increases, the object of the present invention will be impaired. In other words, this will have an adverse effect on weldability and paintability, so the respective upper limits should be set to 0.12% or less for CO and 1.2% for Si.
Hereinafter, Mn was limited to 1.5% or less.
Pは鋼に強度を付与する最も好ましい元素で、C,Mn
、Siと異なり溶接性、塗装性にあまり悪影響を与えな
いで有効に強度を付与する。P is the most preferable element that imparts strength to steel, and C, Mn
, unlike Si, effectively imparts strength without significantly affecting weldability and paintability.
その量は少ないと所望の強度が不足するので下限は0.
04%とし、上限はあまり添加量が多くなると強度−延
性バランスが悪くなると共に、影響は少ないが溶接性を
劣化させるので0.15%とした。If the amount is small, the desired strength will be insufficient, so the lower limit is 0.
04%, and the upper limit was set at 0.15% because if the amount added is too large, the strength-ductility balance will deteriorate and, although the effect is small, weldability will deteriorate.
A[は鋼の脱酸に必要な元素で0.01%未満では不足
であり、0.10%超は必要ない。A[ is an element necessary for deoxidizing steel; less than 0.01% is insufficient, and more than 0.10% is not necessary.
その他の成分については少ない方が望ましいが、必要に
応じて添加することはさまたげない。As for other components, it is desirable to have a smaller amount, but there is no hindrance to adding them as necessary.
この様な成分組成の鋼は常法に従って連続鋳造法又はイ
ンゴット−分塊法でスラブとなし、熱延及び冷延を行な
い、次いで特徴的な連続焼鈍を行なう。Steel having such a composition is formed into a slab by a continuous casting method or an ingot-blosking method according to conventional methods, hot-rolled and cold-rolled, and then subjected to characteristic continuous annealing.
熱延時の巻取温度は高温の方が好ましく、例えば650
℃以上を採用することが強度−延性バランス上望ましい
。The coiling temperature during hot rolling is preferably a high temperature, for example 650
It is desirable to adopt a temperature of ℃ or higher in terms of strength-ductility balance.
以下連続焼鈍条件について詳しく説明する。The continuous annealing conditions will be explained in detail below.
本発明で採用する連続焼鈍は次の2つのヒートサイクル
がある。The continuous annealing employed in the present invention includes the following two heat cycles.
その一つは加熱−均熱−急速冷却であり、他の一つは加
熱−均熱一過時効処理温度までの急速冷却−過時効処理
である。One of them is heating-soaking-rapid cooling, and the other is heating-soaking and rapid cooling to the over-aging treatment temperature-overaging treatment.
先ず第1のヒートサイクルにおいて加熱は、生産性など
の理由から急速加熱が望ましく、この観点から最も好ま
しい手段は噴流加熱方式である。First, in the first heat cycle, rapid heating is desirable for reasons such as productivity, and from this point of view, the most preferable means is a jet heating method.
均熱は730°C〜850℃の温度で20秒〜2分間行
なう。Soaking is performed at a temperature of 730°C to 850°C for 20 seconds to 2 minutes.
これは、730℃未満、20秒未満では十分な再結晶と
粒成長が行われず、所望の延性が確保できない。This is because if the temperature is less than 730° C. and less than 20 seconds, sufficient recrystallization and grain growth will not occur, and the desired ductility cannot be secured.
一方850℃以上の均熱温度では高温すぎて強度−延性
バランスが悪くなる。On the other hand, a soaking temperature of 850° C. or higher is too high and the strength-ductility balance deteriorates.
均熱時間の上限は長くてもよいが、炉長が長くなるなど
設備、経済上の理由から2分に限定した。Although the upper limit of the soaking time may be longer, it was limited to 2 minutes for equipment and economic reasons such as the length of the furnace being longer.
上記の均熱を終了後は急速冷却を行なう。After completing the above soaking, rapid cooling is performed.
この冷却速度は30〜b
30℃/sec未満では所望の強度を確保する前記の合
金元素の添加量が多くなって、これは溶接性、塗装性の
劣化につながるものである。If the cooling rate is less than 30 DEG C./sec, the amount of the alloying element added to ensure the desired strength increases, which leads to deterioration of weldability and paintability.
一方冷却速度が300 ’C/secを超えると急冷に
より生じるマルテンサイト量が多くなり強度−延性バラ
ンスが悪くなる。On the other hand, if the cooling rate exceeds 300'C/sec, the amount of martensite produced by rapid cooling increases, resulting in poor strength-ductility balance.
この様な理由によって本発明では均熱終了後の冷却速度
を30〜b
これによって鋼の成分組成との組合せにより溶接性、塗
装性の良い強度−延性バランスのとれた高強度冷延鋼板
を最も経済的に得るものである。For these reasons, in the present invention, the cooling rate after soaking is set at 30 to 30 b. This, in combination with the composition of the steel, makes it possible to produce high-strength cold-rolled steel sheets with good weldability, paintability, and a good balance of strength and ductility. It is something that can be obtained economically.
上記所定範囲の冷却速度は、従来の水浸漬とか、ガスク
ーリング或いは水噴射などの冷却方式では得難く、気体
と液体の混合物による気−液混合物噴射方式によって容
易に得られるものである。A cooling rate within the above-mentioned predetermined range is difficult to obtain with conventional cooling methods such as water immersion, gas cooling, or water injection, but can be easily obtained with a gas-liquid mixture injection method using a mixture of gas and liquid.
しかもこの方式によれば急冷でありながらストリップ巾
方向の均一冷却が可能となり、ストリップの形状性の向
上、材質の均質化が遠戚できるものである。Moreover, according to this method, uniform cooling in the width direction of the strip is possible even though it is rapid cooling, and it is possible to improve the shape of the strip and to make the material homogeneous.
更にこの方式によれば、任意のストリップ温度での冷却
終点制御が可能であり、後記する第2のヒートサイクル
の実施を極めて有利なものとすることが出来る。Furthermore, according to this method, it is possible to control the cooling end point at an arbitrary strip temperature, making it extremely advantageous to carry out the second heat cycle described later.
第2のヒートサイクルにおける5 000C〜300℃
の過時効処理は鋼中に固溶しているCを析出させ、さら
に延性の向上を計るものであるが、本発明では均熱終了
後行なう30〜b
冷を上記過時効処理温度域で停止させ、再加熱すること
なく過時効処理につなげるものである。5 000C to 300℃ in the second heat cycle
The over-aging treatment is to precipitate C dissolved in the steel and further improve the ductility, but in the present invention, the 30 to 30 b cooling performed after the soaking is stopped in the above over-aging treatment temperature range. This allows for over-aging treatment without reheating.
この様に室温冷却−再加熱のヒートサイクルを経ないの
で、Cの析出物の分布状態が著しく改善され、フェライ
トの結晶粒内での微細析出がなくなり、粒界に比較的大
きく析出する様になる。In this way, since the heat cycle of room temperature cooling and reheating is not performed, the distribution state of C precipitates is significantly improved, and fine precipitation within the ferrite crystal grains is eliminated, and relatively large precipitation occurs at grain boundaries. Become.
その結果過時効処理により十分なる延性が得られるもの
である。As a result, sufficient ductility can be obtained by overaging treatment.
この様に本発明のヒートサイクルが2種類あり、降伏比
(降伏点/抗張力)の低さを重視する場合には第1のヒ
ートサイクルを採用し、強度−延性バランスを重視する
場合には第2のヒートサイクルを採用するものである。As described above, there are two types of heat cycles in the present invention.The first heat cycle is adopted when a low yield ratio (yield point/tensile strength) is important, and the first heat cycle is adopted when a balance between strength and ductility is important. 2 heat cycles are adopted.
過時効処理時間は一般に採用されている程度でよく、例
えば30秒〜5分間位が適当である。The overaging treatment time may be within a generally employed range, for example, approximately 30 seconds to 5 minutes.
以下本発明を実施例に基づいて説明する。The present invention will be explained below based on examples.
第1表に示す各種成分組成の鋼を溶製し、熱延によって
2,5間板厚の熱延鋼帯となし、更に冷延によってQ、
7 mm厚の冷延鋼板とした。Steels with various compositions shown in Table 1 are melted, hot-rolled into hot-rolled steel strips with a thickness of 2.5 mm, and then cold-rolled into Q.
A cold-rolled steel plate with a thickness of 7 mm was used.
これを連続焼鈍するに当り、第2表の如く過時効処理あ
り、なしの場合について均熱後の冷却速度を種々変えた
。During continuous annealing, the cooling rate after soaking was varied with and without overaging treatment as shown in Table 2.
又過時効処理ありの場合において、均熱後の冷却を室温
まで行って再加熱後過時効処理した場合と均熱後の冷却
を過時効処理温度で停止させ、再加熱することなく過時
効処理した場合の2種類を示した。In addition, in the case of overaging treatment, there are cases where cooling after soaking is performed to room temperature and then overaging treatment is performed after reheating, and cases where cooling after soaking is stopped at the overaging treatment temperature and overaging treatment is performed without reheating. Two types of cases are shown below.
溶接性、塗装性及び材質の試験結果を第1表に併示する
。The test results for weldability, paintability, and material properties are also shown in Table 1.
第1表においてAとBは、成分は同種にしてヒートサイ
クルをAが冷却終点制御して過時効処理(e)、Bが再
加熱後過時効処理(a)を行ったものである。In Table 1, A and B have the same components, and the heat cycle is controlled by the cooling end point in A and overaging treatment (e), and in B the overaging treatment is performed after reheating (a).
このA、Bを比較すれば明らかな如くAはBよりも降伏
点が低く伸びが大きく、冷却終点制御の優位性が判る。Comparing A and B, it is clear that A has a lower yield point and greater elongation than B, demonstrating the superiority of cooling end point control.
次に、CとDは夫々300C/5ec(b)、水中浸漬
冷却(h)により抗張力が60k19/mmになる様に
成分組成をコントロールした場合を示している。Next, C and D show the case where the component composition was controlled so that the tensile strength was 60k19/mm by 300C/5ec (b) and water immersion cooling (h), respectively.
CはDに比較して降伏点、伸びが良好なことが判る。It can be seen that C has a better yield point and elongation than D.
E、Fは夫々10℃/secの徐冷(a)、100℃/
secの急開C)を行なって抗張力が70kg/mtM
となる様に成分組成を調整した場合である。E and F are slow cooling (a) at 10°C/sec and 100°C/sec, respectively.
The tensile strength is 70kg/mtM after rapid opening C) of sec.
This is the case when the component composition is adjusted so that
連続焼鈍条件(a)の場合には合金元素を多量に必要と
する結果塗装性、溶接性共に悪い結果となっている。In the case of continuous annealing condition (a), a large amount of alloying elements is required, resulting in poor paintability and weldability.
最後にGとHは夫々300℃/secの急冷(f)、3
50℃/SeCノ急冷(g)ノ場合ヲ示シ、急冷(g)
ノ場合には冷却速度が早すぎて、伸びが低下しているこ
とが判る。Finally, G and H are each rapidly cooled at 300℃/sec (f), 3
The case of 50℃/SeC quenching (g) is shown, quenching (g)
It can be seen that in case No, the cooling rate was too fast and the elongation decreased.
上記の実施例からも明らかな如く本発明例A。As is clear from the above examples, Example A of the present invention.
C,E、Gによれば、強度−延性のバランスがよく、か
つ塗装性、溶接性共に良い冷延鋼板が得られるものであ
る。According to C, E, and G, cold-rolled steel sheets with good strength-ductility balance and good paintability and weldability can be obtained.
Claims (1)
、7〜1.5%、 Po、04〜0.15%、5olA
10.01〜0.10%、その他Fe及び不可避的不純
物を含有する鋼を常法に従って、熱延、冷延後連続焼鈍
を行うに当り、730’C〜850℃で20秒〜2分間
均熱後、気水冷却により30℃〜300℃/秒の冷却速
度で急冷することを特徴とする塗装性、溶接性及び加工
性の良い高強度冷延鋼板の製造方法。 2 C0,05〜0.12%、Si<1.2%、Mn
0、7〜1.5%、 P O,04〜0.15%、5o
lA10.01〜0.10%、その他Fe及び不可避的
不純物を含有する鋼を常法に従って、熱延、冷延後連続
焼鈍を行うに当り、730’C〜850℃で20秒〜2
分間均熱後、気水冷却により、30℃〜300’C/秒
の冷却速度で500〜300℃の温度範囲まで急冷し、
その後300〜500℃の温度で過時効処理を行なうこ
とを特徴とする塗装性、溶接性及び加工性の良い高強度
冷延鋼板の製造方法。[Claims] 1 C0.05-0.12%, Si<1.2%, Mn0
, 7-1.5%, Po, 04-0.15%, 5olA
10.01~0.10%, other Fe and unavoidable impurities are subjected to continuous annealing after hot rolling and cold rolling according to a conventional method. A method for producing a high-strength cold-rolled steel sheet with good paintability, weldability, and workability, which comprises rapidly cooling the steel plate with air and water at a cooling rate of 30° C. to 300° C./sec after heating. 2 C0.05~0.12%, Si<1.2%, Mn
0, 7-1.5%, PO, 04-0.15%, 5o
When carrying out continuous annealing after hot rolling and cold rolling of steel containing 10.01 to 0.10% of lA, other Fe and unavoidable impurities, it was heated at 730'C to 850°C for 20 seconds to 2 hours.
After soaking for a minute, it is rapidly cooled to a temperature range of 500 to 300°C by air-water cooling at a cooling rate of 30°C to 300'C/sec,
A method for producing a high-strength cold-rolled steel sheet with good paintability, weldability, and workability, which comprises subsequently performing an overaging treatment at a temperature of 300 to 500°C.
Priority Applications (10)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP54153392A JPS5825733B2 (en) | 1979-11-27 | 1979-11-27 | Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workability |
NLAANVRAGE8006403,A NL184789C (en) | 1979-11-27 | 1980-11-24 | METHOD FOR MANUFACTURING A COLD-ROLLED STEEL SHEET |
DE3044338A DE3044338C2 (en) | 1979-11-27 | 1980-11-25 | Process for producing cold sheet and its use |
SE8008248A SE435733B (en) | 1979-11-27 | 1980-11-25 | SET FOR MANUFACTURING A HOGHALL FIXED, COLD ROLLED STEEL PLATE |
FR8025127A FR2470164A1 (en) | 1979-11-27 | 1980-11-26 | PROCESS FOR THE MANUFACTURE OF A HIGH TRACTION COLD ROLLED STEEL SHEET HAVING EXCELLENT PAINTING, WELDING AND FORMING ABILITY |
BE2/58878A BE886351A (en) | 1979-11-27 | 1980-11-26 | PROCESS FOR THE MANUFACTURE OF A HIGH STRENGTH SCREWED STEEL SHEET HAVING EXCELLENT ABILITY FOR WELDING PAINT AND TREATMENT |
BR8007715A BR8007715A (en) | 1979-11-27 | 1980-11-26 | PROCESS FOR THE PRODUCTION OF A COLD LAMINATED STEEL SHEET, OF HIGH RESISTANCE, HAVING EXCELLENT PAINTING AND WELDING |
IT26282/80A IT1134492B (en) | 1979-11-27 | 1980-11-27 | PROCEDURE FOR PRODUCING A HIGH STRENGTH STEEL SHEET, COLD ROLLED, WITH EXCELLENT PAINTABILITY |
CA000365649A CA1142068A (en) | 1979-11-27 | 1980-11-27 | Process for producing high strength cold rolled steel sheet having excellent paintability, weldability and workability |
GB8037996A GB2066290B (en) | 1979-11-27 | 1980-11-27 | Processes for producing high strenght cold rolled steel sheets |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP54153392A JPS5825733B2 (en) | 1979-11-27 | 1979-11-27 | Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workability |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5677330A JPS5677330A (en) | 1981-06-25 |
JPS5825733B2 true JPS5825733B2 (en) | 1983-05-30 |
Family
ID=15561479
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP54153392A Expired JPS5825733B2 (en) | 1979-11-27 | 1979-11-27 | Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workability |
Country Status (10)
Country | Link |
---|---|
JP (1) | JPS5825733B2 (en) |
BE (1) | BE886351A (en) |
BR (1) | BR8007715A (en) |
CA (1) | CA1142068A (en) |
DE (1) | DE3044338C2 (en) |
FR (1) | FR2470164A1 (en) |
GB (1) | GB2066290B (en) |
IT (1) | IT1134492B (en) |
NL (1) | NL184789C (en) |
SE (1) | SE435733B (en) |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5935653A (en) * | 1982-08-19 | 1984-02-27 | Kawasaki Steel Corp | High-tension hot-rolled steel plate |
JPS60144658U (en) * | 1984-02-29 | 1985-09-25 | リグナイト株式会社 | Corrosion-resistant structure of steel sheet piles |
MX165036B (en) * | 1987-04-10 | 1992-10-16 | Signode Corp | CONTINUOUS TREATMENT OF COLD ROLLED CARBON MANGANESE STEEL |
CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled steel sheet with good forming performance and preparation method thereof |
EP2455499B1 (en) * | 2009-07-08 | 2017-12-13 | Toyo Kohan Co., Ltd. | Process for production of cold-rolled steel sheet having excellent press moldability |
CN105483354B (en) * | 2015-12-23 | 2017-09-29 | 中钢集团邢台机械轧辊有限公司 | The heat treatment method of large high-speed steel cold roll |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4923727B1 (en) * | 1969-12-16 | 1974-06-18 | ||
JPS5551410B2 (en) * | 1974-01-31 | 1980-12-24 | ||
JPS5157623A (en) * | 1974-11-18 | 1976-05-20 | Nippon Kokan Kk | Takaitosoyakitsukekokaseitosugureta hijikoseiomotsukochoryokureienkohanno seizohoho |
JPS5536051B2 (en) * | 1974-12-05 | 1980-09-18 | ||
US4033789A (en) * | 1976-03-19 | 1977-07-05 | Jones & Laughlin Steel Corporation | Method of producing a high strength steel having uniform elongation |
BE846024A (en) * | 1976-09-09 | 1977-03-09 | PROCESS FOR THE CONTINUOUS THERMAL TREATMENT OF SHEETS |
-
1979
- 1979-11-27 JP JP54153392A patent/JPS5825733B2/en not_active Expired
-
1980
- 1980-11-24 NL NLAANVRAGE8006403,A patent/NL184789C/en not_active IP Right Cessation
- 1980-11-25 DE DE3044338A patent/DE3044338C2/en not_active Expired
- 1980-11-25 SE SE8008248A patent/SE435733B/en not_active IP Right Cessation
- 1980-11-26 FR FR8025127A patent/FR2470164A1/en active Granted
- 1980-11-26 BR BR8007715A patent/BR8007715A/en not_active IP Right Cessation
- 1980-11-26 BE BE2/58878A patent/BE886351A/en not_active IP Right Cessation
- 1980-11-27 GB GB8037996A patent/GB2066290B/en not_active Expired
- 1980-11-27 CA CA000365649A patent/CA1142068A/en not_active Expired
- 1980-11-27 IT IT26282/80A patent/IT1134492B/en active
Also Published As
Publication number | Publication date |
---|---|
FR2470164B1 (en) | 1984-11-09 |
DE3044338A1 (en) | 1981-06-25 |
IT1134492B (en) | 1986-08-13 |
FR2470164A1 (en) | 1981-05-29 |
CA1142068A (en) | 1983-03-01 |
JPS5677330A (en) | 1981-06-25 |
NL184789B (en) | 1989-06-01 |
GB2066290B (en) | 1983-03-23 |
NL8006403A (en) | 1981-07-01 |
NL184789C (en) | 1989-11-01 |
BR8007715A (en) | 1981-06-09 |
BE886351A (en) | 1981-03-16 |
DE3044338C2 (en) | 1987-01-08 |
SE435733B (en) | 1984-10-15 |
GB2066290A (en) | 1981-07-08 |
SE8008248L (en) | 1981-05-28 |
IT8026282A0 (en) | 1980-11-27 |
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