JPS5831035A - Production of zinc hot dipped steel plate having excellent workability and baking hardenability - Google Patents
Production of zinc hot dipped steel plate having excellent workability and baking hardenabilityInfo
- Publication number
- JPS5831035A JPS5831035A JP12941581A JP12941581A JPS5831035A JP S5831035 A JPS5831035 A JP S5831035A JP 12941581 A JP12941581 A JP 12941581A JP 12941581 A JP12941581 A JP 12941581A JP S5831035 A JPS5831035 A JP S5831035A
- Authority
- JP
- Japan
- Prior art keywords
- steel plate
- hot
- zinc hot
- rolled
- cold
- 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
- 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
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)
- Coating With Molten Metal (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は加工性が優れかつ焼付硬化性を有する浴融亜鉛
メッキ鋼板′の製造方法の創案に係り、プレス成形性の
ような加工性に優れ、しかも焼付硬化性を有する溶融亜
鉛メッキ鋼板を低コスト且つ容易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 a method for producing a bath-dip galvanized steel sheet that has excellent workability and bake hardenability. The object of the present invention is to provide a method for easily manufacturing hot-dip galvanized steel sheets at low cost.
溶融亜鉛メッキ鋼板の製造方法には種々あるが、ゼンヅ
ミャ方法などのようにライン内焼鈍炉を有する連続式溶
融亜鉛メツキラインによるものが経済的に有利なものと
して一般的である。しかしこのライン内焼鈍方式による
ものは急熱急冷の短時間焼鈍を基本とするものであるか
らその製品はプレス成形性が劣る欠点を有しており、こ
の故に従来においてこの溶融亜鉛メッキ鋼板の用途とし
又はあまり加工性を必要としないものが大部分であった
。ところがこのものが優れた防錆能力を有することにつ
い1近時再認識され、自動車部品その他の高度の加工性
が賛求される用途にも大量に使用されつつあり、上記し
たような従来技術によるものでもこのような目的に対し
それなりの検討が加えられているが、材質的ないしコス
ト的に必ずしも好ましい技術が確立されるに到っていな
い。蓋しこのライン内焼鈍方式の連続溶融亜鉛メツキラ
インを用いて加工性の好声しい溶融亜鉛メッキ鋼板を得
るための技術としては、■過時効処理を行うこと、■前
焼鈍材を素材とすること、■脱ガス極低C−几添加鋼な
どの所謂IF鋼(Interatitjal Free
5teel lを素材とすることの如きかあるが、■
は過飽和固溶Cの析出を図り、加工性(主として延性)
と時効性の改善を行うものであるけれどもこの方法によ
るものは加工性の主体である深絞り性の改善に対し℃は
何等の効果がない。又■は冷延後で連続式溶融亜鉛メツ
キライン処理前に箱焼鈍を行うもので深絞り性の優れた
鋼板の製造が可能であっても前記箱焼鈍工程のために製
造コスト的に頗る不利とならざるを得ない。There are various methods for producing hot-dip galvanized steel sheets, but the most common method is one that uses a continuous hot-dip galvanizing line with an in-line annealing furnace, such as the Sendzmya method, as it is economically advantageous. However, since this in-line annealing method is based on short-time annealing using rapid heating and rapid cooling, the product has the disadvantage of poor press formability, and for this reason, the conventional use of hot-dip galvanized steel sheets has been limited. The majority of the materials were of low quality or did not require much workability. However, recently it has been recognized again that this material has excellent rust prevention ability, and it is being used in large quantities in automobile parts and other applications that require a high degree of workability. Although some studies have been made for this purpose, no technology that is necessarily favorable in terms of material or cost has yet been established. The techniques for obtaining hot-dip galvanized steel sheets with good workability using a continuous hot-dip galvanizing line with in-line annealing are: ■ performing over-aging treatment, and ■ using pre-annealed material as the material. , so-called IF steels (Interaitjal Free
There is something like using 5teel l as the material, but ■
aims to precipitate supersaturated solid solution C and improve workability (mainly ductility)
However, this method has no effect on improving deep drawability, which is the main component of workability. In addition, (2) is a method in which box annealing is performed after cold rolling and before processing on a continuous hot-dip galvanizing line, and even though it is possible to manufacture steel sheets with excellent deep drawability, the box annealing process has a significant disadvantage in terms of manufacturing costs. I have no choice but to do so.
更に■は再結晶温度以上の焼鈍温度さえ確保されればよ
いので焼鈍工程は非常に単純であるが、nなどの特殊な
炭窒化物形成元素な多量に添加し、この炭窒化物形成元
素添加量は固溶CとNを完全に固定するために必セな量
の数倍種度とされ素材の製造コストが極めて高なる不利
があり、しかし固溶C,Nが完全に固定される結果、そ
の製品に焼付硬化性が全く期待できないこととなり成形
後の塗装焼付工程などの低温゛短時間な熱処理によって
鋼板の降伏強度が上昇しないこととなつ曵近時における
自動車部品などの製品とし又有効な特性が求め得ないこ
ととなる欠点がある。Furthermore, the annealing process is very simple as it is only necessary to ensure an annealing temperature higher than the recrystallization temperature. The amount is several times more specific than the amount necessary to completely fix the solid solution C and N, which has the disadvantage of extremely high manufacturing costs, but as a result, the solid solution C and N are completely fixed. However, the product cannot be expected to have any bake hardenability, and the yield strength of the steel plate will not increase due to low temperature and short heat treatment such as the paint baking process after forming, making it useful for products such as automobile parts in the near future. There is a drawback that it is not possible to obtain suitable characteristics.
本発明は上記17たよりな実情に鑑み検討して創案され
たものであって、C: 0.010〜0.03 Qチ、
SL:0−30チ以下、111 : 0.05〜(1,
30%、P:0.01〜0.15%、st:0.020
’A以下、sol−M: 0.020−0.HJOチ
、N : 0.0080−以下であって残部がhおよび
不可避不純物より成る鋼を仕上温度A8点以上、巻取温
度650〜750Cで、熱間圧延し、常法により冷間圧
延率5〇−以上の冷延を行い、連続式溶融亜鉛メツキラ
インでA、〜A3点間における焼鈍を行い犠鉛メッキす
ることを提案するものである。The present invention was created by considering the above-mentioned 17 important circumstances, and has C: 0.010 to 0.03 Qchi,
SL: 0-30 inches or less, 111: 0.05-(1,
30%, P: 0.01-0.15%, st: 0.020
'A and below, sol-M: 0.020-0. HJO, N: 0.0080- or less, with the balance consisting of h and unavoidable impurities, is hot rolled at a finishing temperature of A8 or higher and a coiling temperature of 650 to 750C, and then cold rolled at a cold rolling rate of 5 by a conventional method. It is proposed to perform cold rolling of 〇- or above, and perform sacrificial lead plating by annealing between points A and A on a continuous hot-dip galvanizing line.
Nllちこのような本発明について更に曲間すると、先
ず鋼の成分組成限定理由は以下の通りである。To elaborate further on the present invention, first, the reasons for limiting the composition of steel are as follows.
Cは、(1,010〜0.030チとするもので、この
Cが0.Q l 0 %以下では炭化物が殆んど認めら
れず、Cが略全量固浴する領域で時効性劣化が著しくな
って本発明の特質を得ることができない゛。又0.03
01以上は炭化物の量が増大して加工性を害するので好
ましくないものであり、即ち本発明は深絞り性改善の観
点から熱延高温巻取を行いその炭化物を凝集粗大化させ
ることを必須条件とすることは後述の通りであるが、C
fiが高く炭化物量が増すとこのような深絞り性改善効
果が減少する。しかも熱延高温巻取によってその炭化物
が粗大化すると、深絞り性が改善される反面において延
性、張出し性に対して好ましくない結果が認められ、こ
れは粗大カーバイトが冷延時に破砕されて微小クラック
を生成し該クラックは焼鈍後も完全に消失せず、又熱延
板炭化物が粗大化している結果冷延焼鈍後の炭化物も均
一分散した状態とならず群落を形成して延性を害するこ
となどKよるものと考えられ、これらの事情から熱延高
温巻取による悪影響が増大するので上限を0.030−
とじた。C is (1,010 to 0.030 cm). When this C is 0.Ql 0% or less, hardly any carbides are observed, and aging deterioration occurs in the region where almost all of the C is in a solid bath. The characteristics of the present invention cannot be obtained.
01 or more is undesirable because the amount of carbides increases and impairs workability.In other words, from the viewpoint of improving deep drawability, the present invention requires hot-rolling and high-temperature winding to coagulate and coarsen the carbides. As will be explained later, C
When fi is high and the amount of carbide increases, this effect of improving deep drawability decreases. Moreover, when the carbide becomes coarse due to hot rolling and high temperature coiling, although deep drawability is improved, unfavorable results are observed for ductility and stretchability. Cracks are generated and the cracks do not disappear completely even after annealing, and as a result of the coarsening of the carbides in the hot rolled sheet, the carbides after cold rolling annealing are not uniformly dispersed and form clusters, impairing ductility. It is thought that this is due to K, and for these reasons, the adverse effects of hot rolling and high temperature coiling increase, so the upper limit has been set to 0.030-
Closed.
SLは、亜鉛メッキの密着性を害する元素であるから最
大を0.3−とすることが必畳である。Since SL is an element that impairs the adhesion of zinc plating, it is essential to set the maximum value to 0.3-.
−は、深絞り性改善の観点からは低いはと望ましいので
0.30−を上限とするが、表面性状や熱間脆性の問題
を考慮して0.05 ’Isを下限とした。- is desirably low from the viewpoint of improving deep drawability, so the upper limit is set to 0.30-, but the lower limit is set to 0.05'Is in consideration of surface texture and hot embrittlement problems.
Pは、強度レベルの調整を目的として
0.01〜0.15%を含有させる。即ちこのPは加工
性を余り害することなぐ強度を、上昇させるのに有効な
元素であるが、0.150−を超えるとメッキ密着性を
害すると共に溶接性や加工性を害することとなるので好
ましくなく、一方0.O1優り下は製鋼作業上の困難が
あり、コスト上昇を招く。P is contained in an amount of 0.01 to 0.15% for the purpose of adjusting the strength level. That is, P is an effective element for increasing strength without significantly impairing workability, but if it exceeds 0.150, it impairs plating adhesion and impairs weldability and workability, so it is preferable. On the other hand, 0. If the steel is O1 or lower, there will be difficulties in steelmaking operations, leading to an increase in costs.
Sは、延性を害する元素であり、その最大を0.020
1とすることが必要である。S is an element that impairs ductility, and its maximum value is 0.020
It is necessary to set it to 1.
sol・〃は、脱酸を図り、又〃NとしてNを同定する
ために必要な元素であって、
0.020−以下ではこれらの目的を充分に達せられな
いこととなり、又0.100−以上では表面疵を発生し
易く、しかもコスト的にも不利となるので、これ゛を上
限とする。sol・〃 is an element necessary for deoxidizing and identifying N as 〃N, and if it is less than 0.020-, these purposes cannot be fully achieved, and if it is less than 0.100- The above is likely to cause surface defects and is also disadvantageous in terms of cost, so this is set as the upper limit.
Nは、必然的に混入するものであるが少ない程好ましく
、0.0080チ以上では延性が劣化するので好ましく
ない。Although N is inevitably mixed, the smaller the amount, the better; if it exceeds 0.0080 inches, the ductility deteriorates, so it is not preferable.
次に熱延条件としては仕上温度をA3点9上とし、巻取
温度を650〜750Cとする。Next, as the hot rolling conditions, the finishing temperature is set to be above A3 point 9, and the coiling temperature is set to 650 to 750C.
即ち仕上温度がA8点以下の低温では良好な深絞り性が
得られない。巻取温度については熱延板の炭化物が粗大
化し、又MNの析出が完全に得られ・るためKは650
0以上が必要であり、しかも表層に異常粗大粒を発生し
ないため和は750℃以下とする。製品の優れた深絞り
性を得るためにはこのような高温巻取をなすことが必須
条件となる。That is, good deep drawability cannot be obtained when the finishing temperature is low, below the A8 point. Regarding the coiling temperature, the carbide in the hot rolled sheet becomes coarse and the precipitation of MN is completely obtained, so K is 650.
0 or more is required, and the sum is set to 750°C or less in order to avoid generating abnormally coarse grains on the surface layer. In order to obtain excellent deep drawability of the product, such high-temperature winding is an essential condition.
脱スケール後の冷延に関しては、良好な深絞り性を得る
上において5〇−以トの冷延率とすることが必要である
。Regarding cold rolling after descaling, it is necessary to use a cold rolling rate of 50 or more in order to obtain good deep drawability.
浴融亜鉛メツキラインにおける通板条件とし7ては、焼
鈍加熱温度をA、〜A3点間の温度′とする。即ちこの
焼鈍加熱温度がA1点以下のときは熱延高温巻取で生じ
た粗大炭化物が大きな塊状炭化物の群落とl−て存在す
るため延性が損われることとなり、A、点以上の温度で
焼鈍すること忙より該炭化物は拡散してその悪影替を有
効に軽減し得る。A、・〜A8A8点間゛囲では高温相
炭化物の拡散均一化が進み、更にこのような高温焼鈍は
フェライト粒の成長を促進し又深絞り性の改善に対して
も有利であるが、A3点を超えると集合組織がランダム
化して深絞り性が劣化することとなり、これを上限とす
る。As the sheet passing condition 7 in the bath dip galvanizing line, the annealing heating temperature is set to a temperature between points A and A. That is, when this annealing heating temperature is below A1 point, coarse carbides generated during hot rolling and high temperature coiling exist as clusters of large lumpy carbides, resulting in loss of ductility; The carbide can diffuse and effectively reduce its negative effects. In the area between A, . If this point is exceeded, the texture becomes random and deep drawability deteriorates, so this is set as the upper limit.
本発明における連続溶融亜鉛メッキ鋼板の製造方法は上
記のような限定によって適切に目的を達することができ
、その効果はヒートサイクルの如何を問わない。即ち殊
更に特殊な過時効処理などを含まない通常のヒートサイ
クルを用いてもその目的を遅し得る。但し適当な過時効
処理を組合わせ又もよいことは勿論で、適当な過時効処
理を組合わせることにより固溶C量をコントロールすれ
ば任意の焼付硬化性を的確に得ることができる。又本発
明の効果は亜鉛メッキの種類に影響されることがなく、
例えば溶融亜鉛メッキ鋼板の裸耐食性向上を目的として
ガルバニール処理するような場合においても有効である
。The method for producing a continuous hot-dip galvanized steel sheet according to the present invention can appropriately achieve its purpose with the above-mentioned limitations, and its effects are irrespective of the heat cycle. That is, even if a normal heat cycle without any special overaging treatment is used, the purpose may be delayed. However, it is of course possible to combine appropriate over-aging treatments, and by controlling the amount of solid solute C in combination with appropriate over-aging treatments, desired bake hardenability can be obtained accurately. Furthermore, the effects of the present invention are not affected by the type of galvanizing.
For example, it is also effective when galvanizing a hot-dip galvanized steel sheet for the purpose of improving its bare corrosion resistance.
本発明に゛よるものの具体的な実施例について比較例と
共に説明すると以下の如く、である。Specific examples according to the present invention are explained below along with comparative examples.
次の第1表に示すような各鋼を出鋼し、連続鋳造してス
ラブとした。Each steel shown in Table 1 below was tapped and continuously cast into slabs.
第1表 註:0印の附されたものが本発明の範囲内の鋼である。Table 1 Note: Steels marked with a 0 are within the scope of the present invention.
上記のような各鋼は板厚2.8■に熱延され、仕−ヒげ
温度870℃、巻取温度700℃で巻取られてから酸洗
脱スケールし、次いで()、8m(冷延率71,4%)
K冷却してから連続式浴融亜鉛メツキラインに通板して
焼鈍および亜鉛メッキ処理した。Each of the above-mentioned steels was hot-rolled to a thickness of 2.8 mm, coiled at a finishing temperature of 870°C and a coiling temperature of 700°C, and then pickled and descaled. extension rate 71.4%)
After cooling, the sheet was passed through a continuous bath dip galvanizing line for annealing and galvanizing.
この亜鉛メツキラインにおける通板条件と、それKよつ
′″C得られた製品の機械的性質を要約して示すと、次
の第2表の通りである。The following Table 2 summarizes the sheet passing conditions in this galvanizing line and the mechanical properties of the resulting products.
第2表
註=BH性は2−引張予歪後のl 70CX20分の処
理による応力上昇量で
評価した。Note to Table 2 = BH properties were evaluated by the amount of stress increase due to treatment with 170CX for 20 minutes after 2-tensile prestrain.
即ち、第2fIの結果によれば本発明法によって製造し
た鋼板は総てi値が1.4を超え、深絞り性に優れてい
る。又これらの結果な図示しているのが第1図であるか
、従来法によってji!li造した比較材に比し本発明
によるものは延性レベルが良好であることも明らかであ
る。、更に本発明によるものは3に4/−以上の焼付硬
化性を有することも確認された。即ち本発明法による鋼
板は加工性、焼付硬化性に優れると共に亜鉛メッキ鋼板
としての優れた耐食性をも兼備したものがあるから外気
条件下に曝される自動車材料その他に用いるに適した材
料として有用であることが確認され九以上説明したよう
な本発明によれば、加ニー往、焼付硬化性および耐食性
に優れた鋼板を低コスト且つ容易VC!11!造するこ
とができるもので、工業的にその効果の大きい発明であ
る。That is, according to the results of the second fI, all the steel plates manufactured by the method of the present invention have an i value exceeding 1.4 and are excellent in deep drawability. Also, these results are shown in FIG. 1, or by the conventional method. It is also clear that the ductility level of the material according to the invention is better than that of the comparative material manufactured by Li. Furthermore, it was confirmed that the material according to the present invention had a bake hardenability of 3 to 4/- or more. In other words, the steel sheets produced by the method of the present invention have excellent workability and bake hardenability as well as excellent corrosion resistance as galvanized steel sheets, so they are useful as materials suitable for use in automobile materials and other materials exposed to outside air conditions. According to the present invention, which has been confirmed to be VC and has been explained above, a steel plate having excellent bending properties, bake hardenability, and corrosion resistance can be produced easily and at low cost. 11! This invention is industrially highly effective.
図面は本発明の技術的内容を示すものであって、第1図
は強度と延性のバランス関係について本発明によるもの
と従来法によるものとを比較し1示した図表である。The drawings show the technical contents of the present invention, and FIG. 1 is a chart showing a comparison of the balance between strength and ductility between the present invention and the conventional method.
Claims (1)
以下、Th: 0.05〜0.30%、P : 0.0
1〜0.15%、S : 0.020 %以下、5ol
−Al4:0.020〜0.100S、N : 0.0
080 S以Fであって残部がhおよび不可避不純物よ
り成る鋼を仕上温度A8点以上、巻取温度650〜75
0℃で熱間圧延し、常法により冷間圧延率509G以上
の冷延を行い、連続式溶融亜鉛メツキラインでA+ ”
”’As 点1sJIIにおける焼鈍を行い亜鉛メッキ
することを特徴とする加工性が優れかつ焼付硬化性を有
する浴融亜鉛メッキ鋼板の製造方法。C: 0.010-0.030%, st: 0.30%
Below, Th: 0.05-0.30%, P: 0.0
1-0.15%, S: 0.020% or less, 5ol
-Al4: 0.020-0.100S, N: 0.0
Steel with a temperature of 080 S or higher and the remainder consisting of h and unavoidable impurities at a finishing temperature of A8 or higher and a coiling temperature of 650 to 75
Hot rolled at 0℃, cold rolled at a cold rolling rate of 509G or more using a conventional method, and A+ on a continuous hot dip galvanizing line.
``'As A method for producing a bath-dip galvanized steel sheet having excellent workability and bake hardenability, which comprises annealing at point 1sJII and galvanizing.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP12941581A JPS5831035A (en) | 1981-08-20 | 1981-08-20 | Production of zinc hot dipped steel plate having excellent workability and baking hardenability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP12941581A JPS5831035A (en) | 1981-08-20 | 1981-08-20 | Production of zinc hot dipped steel plate having excellent workability and baking hardenability |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5831035A true JPS5831035A (en) | 1983-02-23 |
JPS6114219B2 JPS6114219B2 (en) | 1986-04-17 |
Family
ID=15008960
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP12941581A Granted JPS5831035A (en) | 1981-08-20 | 1981-08-20 | Production of zinc hot dipped steel plate having excellent workability and baking hardenability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS5831035A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5852431A (en) * | 1981-09-19 | 1983-03-28 | Sumitomo Metal Ind Ltd | Production of thermally hardenable galvanized steel plate |
JPS5852432A (en) * | 1981-09-19 | 1983-03-28 | Sumitomo Metal Ind Ltd | Production of thermally hardenable thin steel sheet |
EP0931847A1 (en) * | 1997-11-26 | 1999-07-28 | Kawasaki Steel Corporation | Process for producing plated steel sheet |
WO2015079699A1 (en) | 2013-11-28 | 2015-06-04 | Jfeスチール株式会社 | Bake-hardened hot-dip galvanized steel sheet |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5236962A (en) * | 1975-09-18 | 1977-03-22 | Sansha Electric Mfg Co Ltd | Firing circuit for thyristor |
JPS5244720A (en) * | 1975-10-07 | 1977-04-08 | Nippon Steel Corp | Method of producing galvanized steel plates having excellent workabili ty amd high tensile strength |
JPS5770269A (en) * | 1980-10-20 | 1982-04-30 | Sumitomo Metal Ind Ltd | Preparation of alloying treated galvanized sheet iron |
-
1981
- 1981-08-20 JP JP12941581A patent/JPS5831035A/en active Granted
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5236962A (en) * | 1975-09-18 | 1977-03-22 | Sansha Electric Mfg Co Ltd | Firing circuit for thyristor |
JPS5244720A (en) * | 1975-10-07 | 1977-04-08 | Nippon Steel Corp | Method of producing galvanized steel plates having excellent workabili ty amd high tensile strength |
JPS5770269A (en) * | 1980-10-20 | 1982-04-30 | Sumitomo Metal Ind Ltd | Preparation of alloying treated galvanized sheet iron |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5852431A (en) * | 1981-09-19 | 1983-03-28 | Sumitomo Metal Ind Ltd | Production of thermally hardenable galvanized steel plate |
JPS5852432A (en) * | 1981-09-19 | 1983-03-28 | Sumitomo Metal Ind Ltd | Production of thermally hardenable thin steel sheet |
EP0931847A1 (en) * | 1997-11-26 | 1999-07-28 | Kawasaki Steel Corporation | Process for producing plated steel sheet |
US6068887A (en) * | 1997-11-26 | 2000-05-30 | Kawasaki Steel Corporation | Process for producing plated steel sheet |
WO2015079699A1 (en) | 2013-11-28 | 2015-06-04 | Jfeスチール株式会社 | Bake-hardened hot-dip galvanized steel sheet |
KR20160075716A (en) | 2013-11-28 | 2016-06-29 | 제이에프이 스틸 가부시키가이샤 | Bake-hardened hot-dip galvanized steel sheet |
US9920394B2 (en) | 2013-11-28 | 2018-03-20 | Jfe Steel Corporation | Bake-hardening galvanized steel sheet |
Also Published As
Publication number | Publication date |
---|---|
JPS6114219B2 (en) | 1986-04-17 |
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