JPH0742547B2 - High strength alloy galvanized steel sheet - Google Patents
High strength alloy galvanized steel sheetInfo
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- JPH0742547B2 JPH0742547B2 JP2276788A JP27678890A JPH0742547B2 JP H0742547 B2 JPH0742547 B2 JP H0742547B2 JP 2276788 A JP2276788 A JP 2276788A JP 27678890 A JP27678890 A JP 27678890A JP H0742547 B2 JPH0742547 B2 JP H0742547B2
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は、高強度合金化溶融亜鉛めっき鋼板に関するも
のである。TECHNICAL FIELD The present invention relates to a high-strength hot-dip galvanized steel sheet.
（従来の技術） 鋼板の高強度化には、、固溶強化、析出強化、組織強化
など種々の方法があるが、延性、深絞り性、張出し性等
の加工性を損なうことのない固溶強化法が主として採用
される。固溶強化のために鋼に添加される元素としては
Mn、Si、Ｐが代表的であるが、同一添加量での強化能は
Ｐ、Si、Mnの順に大きく、合金添加コストがこの順で小
さくなることからＰ、Siを主体とした成分設計がなされ
ている。更に、溶融亜鉛めっき鋼板の製造においては、
Siは難還元性酸化膜を生成して鋼板と溶融亜鉛との濡れ
性を低下させ、不めっきを誘発する。従って、Siを一定
範囲内に制限して、Ｐによる強化を行うことが一般的で
ある。(Prior Art) There are various methods such as solid solution strengthening, precipitation strengthening, and microstructure strengthening for strengthening steel sheets, but solid solution that does not impair workability such as ductility, deep drawability, and overhanging property. The strengthening method is mainly adopted. The elements added to steel for solution strengthening are
Mn, Si, and P are typical, but the strengthening ability with the same addition amount is larger in the order of P, Si, and Mn, and the alloy addition cost decreases in this order, so the component design mainly composed of P and Si is Has been done. Furthermore, in the production of hot-dip galvanized steel sheet,
Si forms a hard-to-reduce oxide film, lowers the wettability between the steel sheet and molten zinc, and induces non-plating. Therefore, it is common to limit Si to a certain range and strengthen with P.
（発明が解決しようとする課題） かかるＰを主体とする高強度化においては、合金化溶融
亜鉛めっき鋼板を製造する際の合金化反応が著しく抑制
され、連続ラインにおける鋼板の通板速度を低く制限せ
ざるを得ないために、生産能率上の大きい問題となって
いた。(Problems to be Solved by the Invention) In strengthening mainly with P, the alloying reaction at the time of producing an alloyed hot-dip galvanized steel sheet is significantly suppressed, and the steel sheet passing speed in the continuous line is lowered. Since there was no choice but to limit it, it became a big problem in production efficiency.
本発明の目的は、かかる現状に鑑みて確実にかつ迅速に
合金化でき、生産性を著しく向上し得る高強度合金化溶
融亜鉛めっき鋼板を提供しようとするものである。An object of the present invention is to provide a high-strength hot-dip galvanized steel sheet that can be reliably and quickly alloyed in view of the present situation and can markedly improve productivity.
（課題を解決するための手段） 本発明の要旨とするところは下記のとおりである。(Means for Solving the Problems) The gist of the present invention is as follows.
（１） 重量％で、C:0.0060％以下、Si:1.0％以下、M
n:0.42％以上1.2％未満、P:0.030％以上0.10％以下、S:
0.1％以下、Al:0.005％以上0.1％以下、N:0.0060％以
下、およびNb、Ti、Ｂのいずれか１種あるいは２種以上
（但し、Ti−Ｂ複合系は除く）を、Nb:0.003％以上0.00
4％以下、Ti:0.003％以上0.045％以下、B:0.0002％以上
0.0040％以下の範囲で含有し、残部Feおよび不可避的不
純物からなる鋼において、Mn、Ｐ量を下記数式の範囲内
とし、引張強度35kgf/mm2以上の高強度鋼板表面に合金
化溶融亜鉛めっきを施した高強度合金化溶融亜鉛めっき
鋼板。(1) C: 0.0060% or less, Si: 1.0% or less, M by weight%
n: 0.42% or more and less than 1.2%, P: 0.030% or more and 0.10% or less, S:
0.1% or less, Al: 0.005% or more and 0.1% or less, N: 0.0060% or less, and any one or more of Nb, Ti, and B (however, Ti-B composite system is excluded), Nb: 0.003 % Or more 0.00
4% or less, Ti: 0.003% or more and 0.045% or less, B: 0.0002% or more
In steel containing 0.0040% or less and balance Fe and unavoidable impurities, the amount of Mn and P should be within the range of the following formula, and hot-dip galvannealing of high strength steel sheet with tensile strength of 35 kgf / mm 2 or more should be performed. High strength alloyed hot dip galvanized steel sheet.
Mn（重量％）≧10・Ｐ（重量％） （２） Mn、Ｐ量を下記数式の範囲内とした前項１記載
の高強度合金化溶融亜鉛めっき鋼板。Mn (weight%) ≧ 10 · P (weight%) (2) The high-strength alloyed hot-dip galvanized steel sheet according to the above item 1, wherein the amounts of Mn and P are within the range of the following mathematical formula.
Mn（重量％）≧10・Ｐ（重量％）＋0.45％ 以下、本発明を詳細に説明する。Mn (wt%) ≧ 10 · P (wt%) + 0.45% Hereinafter, the present invention will be described in detail.
本発明者らは、高強度合金化溶融亜鉛めっき鋼板を製造
するにあたり、鋼板成分のMn、Ｐ量をMn（重量％）≧10
・Ｐ（重量％）に制限することにより、高い合金化速度
が得られるとの新規知見を得た。In producing the high-strength hot-dip galvanized steel sheet, the present inventors set the Mn and P contents of the steel sheet components to Mn (wt%) ≧ 10.
-Obtaining new knowledge that a high alloying rate can be obtained by limiting to P (wt%).
第１図ではMn、Ｐ以外の成分が本発明の範囲内の冷延鋼
板を連続溶融亜鉛めっきラインにて溶融亜鉛めっき、合
金化処理した場合の適正な合金化処理（めっき層中Fe濃
度:8〜10％）の可能な最大通板速度（図中数字は合金化
処理可能な最大通板速度mpm）を示し、この値が大きい
ほど優れた合金化速度を有することになる。めっきに先
立つ焼鈍は、800℃で45秒間行い、めっき浴に侵入する
鋼板温度は475℃、めっき浴温度は455℃とし、合金化処
理は加熱ガス量を500m3/Hr一定として行い、板温はMn、
Ｐ量に応じて480〜520℃に加熱した。Mn、Ｐ量を本発明
の範囲内とすることにより、従来鋼と比較して著しく合
金化速度に優れた高強度合金化溶融亜鉛めっき鋼板とな
る。In FIG. 1, a proper alloying treatment (Fe concentration in the plating layer: Fe concentration in the plating layer: cold rolled steel sheet in which the components other than Mn and P are within the scope of the present invention is galvanized and alloyed in a continuous hot dip galvanizing line. The maximum possible striping speed (8 to 10%) (the number in the figure is the maximum striping speed that can be alloyed, mpm), and the larger this value, the better the alloying rate. Annealing prior to plating is performed at 800 ° C for 45 seconds, the temperature of the steel plate that enters the plating bath is 475 ° C, the temperature of the plating bath is 455 ° C, and the alloying process is performed with a constant heating gas amount of 500 m 3 / Hr. Is Mn,
It heated at 480-520 degreeC according to P amount. By setting the amounts of Mn and P within the range of the present invention, a high-strength galvannealed steel sheet having a significantly higher alloying rate than the conventional steel can be obtained.
このようにMn、Ｐの範囲を特定することにより、合金化
速度を向上することのできる理由は、Mn、Ｐの表面濃化
挙動の相違に基づくものである。Ｐは、本来、表面に濃
化して浴中のAlと化合物を形成し、これにより著しく合
金化を抑制する。本発明者等は、MnがＰと共存し、かつ
Ｐに対する比が一定値以上、即ち、Mn（重量％）≧10・
Ｐ（重量％）の場合には、Mnが優先的に表面濃化するこ
とを知見した。かかる条件下においては、MnがＰよりも
優先酸化することにより、Ｐの表面濃化が抑制され、Ｐ
の合金化抑制効果を排除できるものである。The reason why the alloying rate can be improved by specifying the ranges of Mn and P in this way is based on the difference in the surface concentration behavior of Mn and P. Originally, P is concentrated on the surface to form a compound with Al in the bath, thereby significantly suppressing alloying. The present inventors have found that Mn coexists with P, and the ratio to P is a certain value or more, that is, Mn (% by weight) ≧ 10.
It was found that in the case of P (% by weight), Mn preferentially thickens the surface. Under such conditions, Mn is preferentially oxidized over P, so that the surface concentration of P is suppressed and
The effect of suppressing the alloying of can be eliminated.
このようにして、合金化速度を向上するとともに、更に
深絞り等過酷な加工性を要求され、めっき金属の密着性
を一層強固なものとするためには、第２図に示すMn、Ｐ
量と合金層の密着性（評価基準は実施例と同じ）の関係
から明らかなように、Mn、Ｐ量を、Mn（重量％）≦10・
Ｐ（重量％）＋0.45％の範囲に制限することが望まし
い。従って、加工度合いの大きい部品に適用される合金
化溶融亜鉛めっき鋼板の製造にあたっては、前記の如
く、Mn（重量％）≧10・Ｐ（重量％）で、かつMn（重量
％）≦10・Ｐ（重量％）＋0.45％の条件を満たす成分設
計が有利である。In this way, in order to improve the alloying speed and further demand severe workability such as deep drawing and further strengthen the adhesion of the plated metal, Mn, P shown in FIG.
As is clear from the relationship between the amount and the adhesiveness of the alloy layer (the evaluation criteria are the same as those in the examples), the amount of Mn and P is Mn (wt%) ≦ 10.
It is desirable to limit it to the range of P (weight%) + 0.45%. Therefore, in the production of the alloyed hot-dip galvanized steel sheet applied to parts with a high degree of processing, as described above, Mn (wt%) ≧ 10 · P (wt%) and Mn (wt%) ≦ 10 · A component design that satisfies the condition of P (% by weight) + 0.45% is advantageous.
このようにしてMn、Ｐ量を特定範囲にするとこによって
めっき密着性が向上する理由は、該範囲ではMnの優先酸
化による表面濃化が顕著となり、均一なめっき性、合金
化が阻害され難くなるためである。The reason why the plating adhesion is improved by setting the amounts of Mn and P in the specific ranges is that the surface concentration due to the preferential oxidation of Mn becomes remarkable in the range, and uniform plating properties and alloying are less likely to be hindered. This is because
Mn、Ｐ以外の添加元素の含有量を限定する理由は以下の
如くである。The reason for limiting the content of the additive elements other than Mn and P is as follows.
ＣはNb、Tiと炭化物を形成して延性を低下せしめるた
め、0.0060％以下とする。C forms a carbide with Nb and Ti and reduces the ductility, so it is made 0.0060% or less.
Siは難還元性酸化膜を生成して鋼板と溶融亜鉛との濡れ
性を低下せしめ、不めっきを誘発するため、1.0％以下
とする。Si forms a hard-to-reduce oxide film, reduces the wettability between the steel sheet and molten zinc, and induces non-plating, so it is 1.0% or less.
Mnは0.42％未満ではMnSの形成が不十分で熱間圧延時に
脆性割れを引き起こす。また、1.2％以上では脆弱な合
金層の生成を促進してめっき密着性を低下せしめる。従
って、上記Mn、Ｐ量の関係式で示される条件に加え、0.
42％以上1.2％未満とする。If Mn is less than 0.42%, the formation of MnS is insufficient and brittle cracking occurs during hot rolling. On the other hand, if it is 1.2% or more, the formation of a brittle alloy layer is promoted to lower the plating adhesion. Therefore, in addition to the condition shown by the above relational expression of Mn and P,
42% or more and less than 1.2%.
Ｐは上記Mn、Ｐ量の関係式で示される条件に加え、0.03
0％以上0.10％以下とする。0.030％未満では強化のため
に添加するMn、Ｐ量が多くなってコスト高となり、0.10
％を越えると粒界に偏析して深絞り成形後の脆性破壊を
招くためである。P is 0.03 in addition to the condition shown by the above relational expression of Mn and P amount.
0% or more and 0.10% or less. If it is less than 0.030%, the amount of Mn and P added for strengthening increases and the cost becomes high.
This is because if it exceeds 0.1%, it segregates at the grain boundaries and causes brittle fracture after deep drawing.
本発明の対象とする合金化溶融亜鉛めっき鋼板は引張強
度35kgf/mm2以上の高強度鋼板とする。引張強度35kgf/m
m2未満の鋼板ではＰ、Mn等の添加量が少ないため本来の
合金化速度が比較的大きく、本発明の効果が顕著に得ら
れないためである。The galvannealed steel sheet targeted by the present invention is a high-strength steel sheet having a tensile strength of 35 kgf / mm 2 or more. Tensile strength 35kgf / m
This is because the original alloying rate is relatively high and the effect of the present invention cannot be remarkably obtained in the steel sheet having a size of less than m 2 because the addition amount of P, Mn, etc. is small.
ＳはMnSとして析出せしめるが、加工性劣化や必要なMn
添加量の上昇を招くため0.1％以下とする。S precipitates as MnS, but it deteriorates workability and requires Mn
0.1% or less because it causes an increase in the amount added.
Alは脱酸のために添加し、0.005％未満では未脱酸に起
因する介在物の上昇による加工性の低下を引き起こし、
0.1％を越えると焼鈍時の粒成長を抑制することによる
加工性の低下を引き起こすため、0.005％以上0.1％以下
とする。Al is added for deoxidation, and if it is less than 0.005%, it causes a decrease in workability due to an increase in inclusions due to undeoxidized,
If it exceeds 0.1%, the workability is deteriorated by suppressing the grain growth during annealing, so the content is made 0.005% to 0.1%.
ＮはTiNもしくはAlNとして析出せしめるが、0.0060％を
越えると添加するTiあるいはAl量の増加によりコスト高
となる。従って、Ｎは0.0060％以下とする。N is precipitated as TiN or AlN, but if it exceeds 0.0060%, the cost increases due to an increase in the amount of Ti or Al added. Therefore, N is 0.0060% or less.
Nb、Ti、Ｂは鋼中のＣ、Ｎを炭窒素化物として析出せし
めて機械的性質におよぼすＣ、Ｎの悪影響を無害化する
ために添加する。Ｃの析出にはNb、Tiが有効であり、Ｎ
の析出にはTi、Ｂの添加が効果的である。かかる目的に
対し、Nbは0.003％以上0.04％以下、Tiは0.003％以上0.
045％以下、Ｂは0.0002％以上0.0040％以下の添加量が
必要である。いずれも下限値未満の添加量では炭窒化物
の析出が不十分で機械的性質の改善効果は小さく、逆に
上限値を越える添加量では再結晶温度の上昇や粒成長の
抑制を招き望ましくない。Nb、Ti、Ｂの添加は単独、複
合添加（但し、Ti−Ｂの複合添加を除く）いずれも可能
である。Nb, Ti, and B are added in order to make C and N in the steel precipitate as carbonitrides and render the harmful effects of C and N on mechanical properties harmless. Nb and Ti are effective for the precipitation of C.
The addition of Ti and B is effective for the precipitation of Ti. For this purpose, Nb is 0.003% to 0.04% and Ti is 0.003% to 0.
The amount of addition is 045% or less and B is 0.0002% or more and 0.0040% or less. In any case, if the addition amount is less than the lower limit value, precipitation of carbonitride is insufficient and the effect of improving mechanical properties is small. Conversely, if the addition amount exceeds the upper limit value, recrystallization temperature rises and grain growth is suppressed, which is not desirable. . Nb, Ti, and B can be added individually or in combination (excluding Ti-B in addition).
熱間圧延、冷間圧延の条件は通常の操業条件でよい。The conditions of hot rolling and cold rolling may be normal operating conditions.
溶融亜鉛めっき条件、合金化処理条件に関しても特に規
定する必要はない。めっき量の如何を問わず本発明は有
効であるが、特にめっき付着量が片面50g/m2以上の場合
に効果は著しい。There is no particular need to specify hot dip galvanizing conditions or alloying treatment conditions. The present invention is effective regardless of the plating amount, but the effect is remarkable especially when the coating amount is 50 g / m 2 or more on one side.
合金化溶融亜鉛めっき鋼板の後処理として、塗装性を改
善するための鉄−亜鉛合金電気めっき、耐食性を向上せ
しめるためのクロメート処理等を実施する場合がある
が、これらは、本発明の効果を何等損なうものではな
く、いずれの後処理を行うこともできる。As a post-treatment of the galvannealed steel sheet, iron-zinc alloy electroplating for improving paintability, and chromate treatment for improving corrosion resistance may be carried out, but these have the effect of the present invention. Any post-processing can be performed without any loss.
（実施例） 次に本発明の実施例を比較例とともに挙げる。(Example) Next, the Example of this invention is given with a comparative example.
注1:合金化溶融亜鉛めっき鋼板の製造は、連続亜鉛めっ
き設備で、焼鈍は還元炉方式の焼鈍炉で（775〜820℃）
−（25−60秒）の条件で行った。めっき浴への侵入板温
度は470〜510℃、めっき浴温度は455〜465℃、めっき浴
の組成は、Al:0.11〜0.16重量％、Fe:0.02〜0.04重量
％、残部Znおよび不可避的不純物、めっき量は片面あた
り30〜90g/m2である。めっきを施した後、ガス加熱方式
の合金化炉で合金化処理を行い、合金化溶融亜鉛めっき
鋼板とした。合金化処理を行うために鋼板の加熱に用い
たガス量は全条件で一定の500m3/Hr、合金化処理時の平
均板温度は通板速度に対応して490〜510℃、加熱時間は
15〜30秒であった。50℃以下まで冷却した後0.8〜1.2％
の調質圧延を施した。 Note 1: Manufacture of galvannealed steel sheet is continuous galvanizing equipment, and annealing is a reducing furnace type annealing furnace (775-820 ℃)
-(25-60 seconds). Penetration plate temperature into the plating bath is 470 to 510 ℃, plating bath temperature is 455 to 465 ℃, plating bath composition is Al: 0.11 to 0.16 wt%, Fe: 0.02 to 0.04 wt%, balance Zn and unavoidable impurities The plating amount is 30 to 90 g / m 2 per side. After plating, alloying treatment was performed in a gas heating type alloying furnace to obtain a galvannealed steel sheet. The amount of gas used for heating the steel sheet to perform the alloying treatment is 500 m 3 / Hr, which is constant under all conditions, the average sheet temperature during the alloying treatment is 490 to 510 ° C corresponding to the sheet passing speed, and the heating time is
It was 15 to 30 seconds. 0.8-1.2% after cooling to below 50 ℃
Was temper-rolled.
注2:合金化速度の評価は、板幅方向全面の合金化処理
（めっき層中Fe濃度:8〜10％）の可能な最大通板速度で
評価した。Note 2: The alloying rate was evaluated by the maximum sheeting rate at which the entire surface in the sheet width direction can be alloyed (Fe concentration in the plating layer: 8-10%).
注3:合金層密着性は溶着曲げ試験後の曲げ内面のめっき
層を市販セロテープで強制剥離してその剥離量で評価し
た（〔良好〕１５〔不良〕,3が出荷限界）。Note 3: Adhesion of the alloy layer was evaluated by forcibly peeling the plating layer on the inner surface of the bend after the welding bending test with a commercially available cellophane tape and evaluating the amount of peeling ([good] 15 [bad], 3 is the shipping limit).
注4:機械的性質は、JIS5号試験片（引張強度、全伸
び）、JIS13号Ｂ試験片（ｒ値）を用いて引張試験によ
り求めた。Note 4: Mechanical properties were determined by a tensile test using JIS No. 5 test pieces (tensile strength, total elongation) and JIS No. 13 B test pieces (r value).
このように本発明の鋼板は、いずれも極めて優れた合金
化処理速度を有し、比較例鋼板に対する優位性が明白で
ある。比較例のNo1,2,3はMn添加量が本発明範囲よりも
低いために、合金化速度が著しく低く、生産能率が劣
る。As described above, each of the steel sheets of the present invention has an extremely excellent alloying treatment rate, and its superiority to the comparative steel sheet is clear. In Comparative Examples No. 1, 2, and 3, since the amount of Mn added was lower than the range of the present invention, the alloying rate was remarkably low and the production efficiency was poor.
また、本発明鋼板No.1,2,3,5,6,7は、めっき密着性が特
に良好であり、厳しい加工を施す用途に対しても十分適
用することができる。Further, the steel sheets Nos. 1, 2, 3, 5, 6, and 7 of the present invention have particularly good plating adhesion and can be sufficiently applied to applications where severe processing is performed.
（発明の効果） 本発明によれば、高強度鋼板において、確実にかつ迅速
に合金化でき、高強度合金化溶融亜鉛めっき鋼板の生産
性を著しく向上することができる。また、めっき密着性
も向上させることができる等の優れた効果が得られる。(Effect of the Invention) According to the present invention, a high-strength steel sheet can be reliably and quickly alloyed, and the productivity of the high-strength galvannealed steel sheet can be significantly improved. Further, excellent effects such as improvement in plating adhesion can be obtained.
第１図はMn、Ｐ量と合金化速度の関係を示す説明図、第
２図はMn、Ｐ量とめっき層密着性の関係を示す説明図で
ある。FIG. 1 is an explanatory diagram showing the relationship between the amount of Mn and P and the alloying rate, and FIG. 2 is an explanatory diagram showing the relationship between the amount of Mn and P and the adhesion of the plating layer.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 山田 正人 愛知県東海市東海町５―３ 新日本製鐵株 式會社名古屋製鐵所内 (56)参考文献 特開 平３−264649（ＪＰ，Ａ) 特開 平２−236262（ＪＰ，Ａ) 特開 平２−163346（ＪＰ，Ａ) 特開 平１−184227（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Masato Yamada Inventor Masato Yamada 5-3 Tokai-cho, Tokai City, Aichi Pref. Nippon Steel Co., Ltd. Inside the Nagoya Works (56) Reference JP-A-3-264649 (JP, A) JP-A-2-236262 (JP, A) JP-A-2-163346 (JP, A) JP-A-1-184227 (JP, A)
Claims (2)
下、Mn:0.42％以上1.2％未満、P:0.030％以上0.10％以
下、S:0.1％以下、Al:0.005％以上0.1％以下、N:0.0060
％以下、およびNb、Ti、Ｂのいずれか１種あるいは２種
以上（但し、Ti−Ｂ複合系は除く）を、Nb:0.003％以上
0.04％以下、Ti:0.003％以上0.045％以下、B:0.0002％
以上0.0040％以下の範囲で含有し、残部Feおよび不可避
的不純物からなる鋼において、Mn、Ｐ量を下記数式の範
囲内とし、引張強度35kgf/mm2以上の高強度鋼板表面に
合金化溶融亜鉛めっきを施した高強度合金化溶融亜鉛め
っき鋼板。 Mn（重量％）≧10・Ｐ（重量％）1. By weight%, C: 0.0060% or less, Si: 1.0% or less, Mn: 0.42% or more and less than 1.2%, P: 0.030% or more and 0.10% or less, S: 0.1% or less, Al: 0.005% or more 0.1% or less, N: 0.0060
% Or less, and any one or more of Nb, Ti, and B (excluding Ti-B composite system), Nb: 0.003% or more
0.04% or less, Ti: 0.003% or more and 0.045% or less, B: 0.0002%
In the steel containing 0.0040% or more and the balance Fe and unavoidable impurities, the amount of Mn and P is within the range of the following formula, and the alloyed molten zinc is applied to the surface of the high strength steel plate with the tensile strength of 35 kgf / mm 2 or more. High-strength galvannealed steel sheet with plating. Mn (wt%) ≧ 10 · P (wt%)
１記載の高強度合金化溶融亜鉛めっき鋼板。 Mn（重量％）≧10・Ｐ（重量％）＋0.45％2. The high-strength galvannealed steel sheet according to claim 1, wherein the amounts of Mn and P are within the range of the following formula. Mn (wt%) ≧ 10 ・ P (wt%) + 0.45%
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2276788A JPH0742547B2 (en) | 1990-10-16 | 1990-10-16 | High strength alloy galvanized steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2276788A JPH0742547B2 (en) | 1990-10-16 | 1990-10-16 | High strength alloy galvanized steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04154937A JPH04154937A (en) | 1992-05-27 |
| JPH0742547B2 true JPH0742547B2 (en) | 1995-05-10 |
Family
ID=17574385
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2276788A Expired - Lifetime JPH0742547B2 (en) | 1990-10-16 | 1990-10-16 | High strength alloy galvanized steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0742547B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1995021947A1 (en) * | 1994-02-15 | 1995-08-17 | Kawasaki Steel Corporation | High tension alloyed molten zinc-plated steel plate having excellent plating characteristics and method off manufacturing the same |
| US5897967A (en) * | 1996-08-01 | 1999-04-27 | Sumitomo Metal Industries, Ltd. | Galvannealed steel sheet and manufacturing method thereof |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59190332A (en) * | 1983-04-14 | 1984-10-29 | Nippon Steel Corp | Production of galvanized steel plate for ultradeep drawing having extremely good secondary processability |
| JPS6126757A (en) * | 1984-07-17 | 1986-02-06 | Kawasaki Steel Corp | Cold rolled steel sheet for deep drawing having sintering hardness |
| JPS6164821A (en) * | 1984-09-05 | 1986-04-03 | Kawasaki Steel Corp | Manufacture of high tension molten zinc plating steel plate having excellent forming property |
| JPS62188768A (en) * | 1986-02-13 | 1987-08-18 | Kawasaki Steel Corp | Alloying hot dip galvanized high tension cold rolled steel sheet and its manufacture |
| JPS6347338A (en) * | 1986-08-15 | 1988-02-29 | Sumitomo Metal Ind Ltd | Production of high tension zinc hot dip coated steel sheet |
| JPS6369923A (en) * | 1986-09-09 | 1988-03-30 | Sumitomo Metal Ind Ltd | Production of cold rolled steel sheet for deep drawing having excellent baking hardenability |
| JP2530338B2 (en) * | 1987-08-31 | 1996-09-04 | 住友金属工業株式会社 | High strength cold rolled steel sheet with good formability and its manufacturing method |
| JPH01184227A (en) * | 1988-01-18 | 1989-07-21 | Sumitomo Metal Ind Ltd | Production of alloyed and galvanized steel sheet for drawing |
| JPH0756062B2 (en) * | 1988-06-08 | 1995-06-14 | 株式会社神戸製鋼所 | High-strength cold-rolled steel sheet for super deep drawing with excellent vertical crack resistance |
| JP2576894B2 (en) * | 1988-12-15 | 1997-01-29 | 日新製鋼株式会社 | Hot-dip galvanized high-tensile cold-rolled steel sheet excellent in press formability and method for producing the same |
| JP2809671B2 (en) * | 1989-03-09 | 1998-10-15 | 川崎製鉄株式会社 | Manufacturing method of hot-dip galvanized steel sheet with excellent deep drawability |
-
1990
- 1990-10-16 JP JP2276788A patent/JPH0742547B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04154937A (en) | 1992-05-27 |
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