JPH06256903A - Galvannealed steel sheet excellent in press workability and plating peeling resistance - Google Patents
Galvannealed steel sheet excellent in press workability and plating peeling resistanceInfo
- Publication number
- JPH06256903A JPH06256903A JP5043122A JP4312293A JPH06256903A JP H06256903 A JPH06256903 A JP H06256903A JP 5043122 A JP5043122 A JP 5043122A JP 4312293 A JP4312293 A JP 4312293A JP H06256903 A JPH06256903 A JP H06256903A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- steel sheet
- less
- plating
- resistance
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 63
- 239000010959 steel Substances 0.000 title claims abstract description 63
- 238000007747 plating Methods 0.000 title claims description 40
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 14
- 239000008397 galvanized steel Substances 0.000 claims description 14
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 12
- 238000000227 grinding Methods 0.000 abstract description 11
- 229910052717 sulfur Inorganic materials 0.000 abstract description 9
- 229910052758 niobium Inorganic materials 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910052745 lead Inorganic materials 0.000 abstract description 2
- 229910052760 oxygen Inorganic materials 0.000 abstract description 2
- 238000005244 galvannealing Methods 0.000 abstract 2
- 239000010410 layer Substances 0.000 description 28
- 238000005275 alloying Methods 0.000 description 20
- 238000000034 method Methods 0.000 description 15
- 239000000463 material Substances 0.000 description 13
- 238000011282 treatment Methods 0.000 description 11
- 238000012360 testing method Methods 0.000 description 10
- 238000012937 correction Methods 0.000 description 9
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 238000005246 galvanizing Methods 0.000 description 7
- 230000009467 reduction Effects 0.000 description 7
- 229910018084 Al-Fe Inorganic materials 0.000 description 6
- 229910018192 Al—Fe Inorganic materials 0.000 description 6
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 6
- 238000005097 cold rolling Methods 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000000137 annealing Methods 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 238000005554 pickling Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 238000002791 soaking Methods 0.000 description 4
- 229910052725 zinc Inorganic materials 0.000 description 4
- 239000011701 zinc Substances 0.000 description 4
- 229910000640 Fe alloy Inorganic materials 0.000 description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 238000005238 degreasing Methods 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229920000298 Cellophane Polymers 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 239000011324 bead Substances 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000020169 heat generation Effects 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910018085 Al-F Inorganic materials 0.000 description 1
- 229910018179 Al—F Inorganic materials 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 229910019142 PO4 Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- ZCDOYSPFYFSLEW-UHFFFAOYSA-N chromate(2-) Chemical compound [O-][Cr]([O-])(=O)=O ZCDOYSPFYFSLEW-UHFFFAOYSA-N 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000032798 delamination Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000010409 ironing Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000003449 preventive effect Effects 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000007586 pull-out test Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は自動車車体外板等に用い
られるプレス加工性と耐めっき剥離性に優れた合金化溶
融亜鉛めっき鋼板に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an alloyed hot-dip galvanized steel sheet having excellent press workability and resistance to delamination, which is used for outer panels of automobile bodies.
【０００２】[0002]
【従来の技術】近年、自動車車体の防錆力強化が求めら
れ、向上策として亜鉛系の表面処理鋼板が指向されてい
る。その中で、特に溶融亜鉛めっき鋼板は、経済的に優
れており、さらに、加熱処理によりめっき層をＦｅ−Ｚ
ｎ合金（合金化溶融亜鉛めっき鋼板）とすることにより
溶接性と塗装後の耐食性を改善することができる。2. Description of the Related Art In recent years, there has been a demand for strengthening the rust preventive power of automobile bodies, and zinc-based surface-treated steel sheets have been directed as an improvement measure. Among them, the hot dip galvanized steel sheet is economically excellent, and further, the heat treatment is applied to the Fe-Z plated layer.
By using an n alloy (alloyed hot-dip galvanized steel sheet), weldability and corrosion resistance after coating can be improved.
【０００３】自動車車体の外板に用いられる合金化溶融
亜鉛めっき（以下ＧＡと称する）鋼板は、意匠性を高め
る目的で高度のプレス加工が施されるため、求められる
材質として、延性（伸びＥｌ）と絞り性（ランクフォー
ド値、ｒ値）はより高いものになっている。これらの解
決策としては、鋼板の材質面では鋼中のＣ、Ｎ、Ｐ、Ｓ
等の低減が最適な熱延、冷延プロセスと共に多数開発さ
れている。Alloyed hot-dip galvanized (hereinafter referred to as GA) steel sheets used for outer panels of automobile bodies are subjected to a high degree of press working for the purpose of enhancing the designability, and therefore are required to have ductility (elongation El). ) And drawability (Rankford value, r value) are higher. As a solution to these problems, in terms of the material of the steel plate, C, N, P, S in the steel
Many reductions have been developed along with optimal hot rolling and cold rolling processes.
【０００４】一方、ＧＡ鋼板のめっき層に求められる特
性としては、加工時の鋼板の変形に追従できずに粉化し
て剥離するパウダリング及びプレスダイスにしごかれて
鱗片状に剥離するフレーキングが起りにくいことが求め
られる。これらが発生するとプレスダイスに貯って押し
疵を発生する。あるいはめっき本来の防食性を失うこと
が問題になる。ＧＡ鋼板のめっき層は一般には低Ｆｅ含
有率から順にζ、δ1、Гの３つのＺｎ−Ｆｅ合金相か
らなるといわれ、パウダリングについてはГ相、フレー
キングについてはζ相が原因になるといわれている。On the other hand, the characteristics required for the coating layer of the GA steel sheet are powdering, which cannot follow the deformation of the steel sheet during processing and is separated by powder, and flaking, which is peeled into scales by being squeezed by a press die. It is required to be hard to happen. When these occur, they are accumulated in the press die and push defects occur. Alternatively, there is a problem in that the corrosion resistance inherent to plating is lost. It is said that the plating layer of a GA steel plate is generally composed of three Zn-Fe alloy phases of ζ, δ 1 , and Γ in order of low Fe content. For powdering, the Γ phase and for flaking are caused by the ζ phase. ing.
【０００５】ところで、Ｃ、Ｎ、Ｐ、Ｓ低減材に溶融亜
鉛めっきを行いＧＡ鋼板を製造したところ、延性、ｒ値
の材質は満足するが、鋼板粒界での合金化を過度に加速
してしまい、Г相形成量を増加させ、耐パウダリング性
を低下させることが明らかになった。そして、耐パウダ
リング性を確保するにはГ相を実質的に生成しない合金
化度（Ｆｅ濃度）に抑制する必要がある。しかしこの場
合、例えば特開平２−１１７４５号公報に開示するごと
き、単にГ相が生じ難いようにＦｅ含有率のみを規定し
た場合には製造条件によってはめっき表層にζ相が厚く
存在し、プレス加工時のしごきが強くなるとフレーキン
グ性が起り易くなるという新たな問題を引き起こす。By the way, when a GA steel sheet was manufactured by hot-dip galvanizing a C, N, P and S reducing material, the ductility and r value of the material were satisfied, but the alloying at the steel sheet grain boundary was excessively accelerated. It was revealed that the amount of Γ phase formation was increased and the powdering resistance was lowered. Then, in order to secure the powdering resistance, it is necessary to suppress the alloying degree (Fe concentration) so that the Γ phase is not substantially generated. However, in this case, as disclosed in, for example, Japanese Patent Application Laid-Open No. 2-11745, when only the Fe content is specified so that the Γ phase is not easily generated, depending on the manufacturing conditions, the ζ phase exists thickly in the plating surface layer, When the ironing during processing becomes strong, flaking property is likely to occur, which causes a new problem.
【０００６】[0006]
【発明が解決しようとする課題】本発明では、鋼中の
Ｃ、Ｎ、Ｐ、Ｓを低減して鋼材質を得た鋼板を素材とし
て耐パウダリング性と耐フレーキング性を両立する合金
化溶融亜鉛めっき鋼板を得ることを目的とする。DISCLOSURE OF THE INVENTION In the present invention, a steel sheet obtained by reducing C, N, P and S in steel to obtain a steel material is used as an alloying material which has both powdering resistance and flaking resistance. The purpose is to obtain a galvanized steel sheet.
【０００７】[0007]
【課題を解決するための手段】本発明は、Ｃ：０．００
１５重量％以下、Ｓｉ：０．１重量％以下、Ｍｎ：０．
０３重量％以上０．３重量％以下、Ａｌ：０．０１重量
％以上０．１重量％以下、Ｐ：０．０１重量％以下、
Ｓ：０．００５重量％以下、Ｏ：０．００５重量％以
下、Ｎ：０．００５重量％以下、を含有し、かつ０．０
３重量％以下のＴｉあるいは０．０３重量％以下のＮｂ
少なくとも一種以上を、 Ｃ／１２≦Ｔｉ＊／４８＋Ｎｂ／９３≦Ｃ／２ を満足する範囲で含有する鋼板表面にＦｅ：９重量％以
上１２重量％以下、Ａｌ：０．３重量％以上、１．５重
量％以下Ｐｂ：０．１重量％以下を含有する合金化溶融
亜鉛めっき層を２５ｇ／ｍ2 以上７０ｇ／ｍ2 以下形成
したことを特徴とするプレス加工性と耐めっき剥離性に
優れた合金化溶融亜鉛めっき鋼板である。The present invention provides C: 0.00
15% by weight or less, Si: 0.1% by weight or less, Mn: 0.
03 wt% or more and 0.3 wt% or less, Al: 0.01 wt% or more and 0.1 wt% or less, P: 0.01 wt% or less,
S: 0.005 wt% or less, O: 0.005 wt% or less, N: 0.005 wt% or less, and 0.0
3% by weight or less of Ti or 0.03% by weight or less of Nb
Fe: 9% by weight or more and 12% by weight or less, Al: 0.3% by weight or more, 1 or more on the steel plate surface containing at least one or more of C / 12 ≦ Ti * / 48 + Nb / 93 ≦ C / 2 Excellent in press workability and plating peeling resistance, which is characterized in that an alloyed hot-dip galvanized layer containing Pb: 0.1 wt% or less is formed in an amount of 25 g / m 2 or more and 70 g / m 2 or less. Alloyed hot-dip galvanized steel sheet.
【０００８】ただし、Ｔｉ＊はＴｉ−（４８Ｎ／１４＋
４８Ｓ／３２）≧０のときはＴｉ＊＝Ｔｉ−（４８Ｎ／
１４＋４８Ｓ／３２）、Ｔｉ−（４８Ｎ／１４＋４８Ｓ
／３２）＜０のときはＴｉ＊＝０とする。また、上記鋼
板組成にさらにＢを０．００１重量％以下含有してもよ
い。However, Ti * is Ti- (48N / 14 +
When 48S / 32) ≧ 0, Ti * = Ti− (48N /
14 + 48S / 32), Ti- (48N / 14 + 48S
/ 32) <0, Ti * = 0. Further, the steel sheet composition may further contain B in an amount of 0.001% by weight or less.
【０００９】[0009]
【作用】以下に本発明の目的である加工性と耐めっき剥
離性に優れる合金化溶融亜鉛めっき鋼板について述べ
る。まず、めっき素材となる鋼板の鋼中成分は求められ
る材質を満足し、かつ経済的に生産する目的から以下の
ように決定される。The alloyed hot-dip galvanized steel sheet which is the object of the present invention and which is excellent in workability and resistance to peeling of plating is described below. First, the steel composition of the steel sheet that is the plating material is determined as follows for the purpose of satisfying the required material and producing economically.
【００１０】Ｃ：Ｃは鋼の強度を直接決定する元素であ
り、本発明の目的である極めて高い加工性（高Ｅｌ，ｒ
値）を得るには含有量は少ない程よく、０．００１５重
量％以下であることを必要とする。 Ｎ、Ｐ、Ｓ：Ｎ、Ｐ、Ｓはいずれも鋼中に固溶してＥ
ｌ、ｒ値を低下させる。よってＣ同様に含有量は少ない
程よく、それぞれ０．００５重量％、０．０１重量％、
０．００５重量％以下が必要と考える。C: C is an element that directly determines the strength of steel, and is an extremely high workability (high El, r) which is the object of the present invention.
In order to obtain (value), the smaller the content, the better, and it is necessary that the content is 0.0015% by weight or less. N, P, S: N, P, S all form a solid solution in the steel and become E
Decrease the l and r values. Therefore, like C, the smaller the content, the better, and 0.005% by weight, 0.01% by weight, and
It is considered that 0.005% by weight or less is necessary.
【００１１】Ｏ：Ｏも鋼中に過剰に存在すると酸化物と
して析出し、Ｅｌ、ｒ値を低下させる。よって、０．０
０５％を上限とする。 Ｍｎ：Ｍｎは鋼中に固溶するＳと化合し、析出して無害
化するために有効であり、少量が固溶することによって
は材質上影響は少ない。しかし、０．３重量％を越える
と徐々にＥｌ、ｒ値を低下させる。よって、０．０３重
量％以上、０．３重量％以下とする。O: If O is also excessively present in the steel, it precipitates as an oxide and reduces the El and r values. Therefore, 0.0
The upper limit is 05%. Mn: Mn is effective in combining with S which forms a solid solution in the steel to precipitate and render it harmless, and a small amount of solid solution has little effect on the material. However, when it exceeds 0.3% by weight, the El and r values are gradually reduced. Therefore, 0.03% by weight or more and 0.3% by weight or less.
【００１２】Ｓｉ：ＳｉもＭｎ同様に多量に鋼中に存在
するとＥｌ、ｒ値を低下させ、また、めっき濡れ性を阻
害する。よって上限を０．１重量％とする。 Ｔｉ、Ｎｂ：Ｔｉ、ＮｂはＣと化合してＴｉＣ、ＮｂＣ
として析出し、加工性を向上する。よって、Ｃとの原子
比で１以上が必要である。ただし、過剰の添加は経済性
を損ねるため上限は原子比６とする。また、それぞれの
添加量の上限も０．０３重量％とするのが好ましい。但
し、ＴｉはＣ以上にＮ、Ｓと化合し易いためＮ、Ｓ当量
を差し引いたＴｉ量を用いる必要がある。Si: Si, like Mn, if present in a large amount in steel, lowers the El and r values, and also impairs the wettability of the plating. Therefore, the upper limit is set to 0.1% by weight. Ti, Nb: Ti, Nb are combined with C to form TiC, NbC
To improve the workability. Therefore, the atomic ratio with C must be 1 or more. However, since the excessive addition impairs the economical efficiency, the upper limit of the atomic ratio is 6. Further, it is preferable that the upper limit of the addition amount of each is 0.03% by weight. However, since Ti is more likely to combine with N and S than with C, it is necessary to use the amount of Ti with N and S equivalents subtracted.
【００１３】つまり、Ｔｉ、Ｎｂ量は下式を満足するも
のとする。 Ｃ／１２≦Ｔｉ＊／４８＋Ｎｂ／９３≦Ｃ／２ （ここで、Ｔｉ＊は、Ｔｉ−（４８Ｎ／１４＋４８Ｓ／
３２）≧０のときはＴｉ＊＝Ｔｉ−（４８Ｎ／１４＋４
８Ｓ／３２）、（Ｔｉ−４８Ｎ／１４＋４８Ｓ／３２）
＜０のときはＴｉ＊＝０とする。） Ａｌ：ＡｌはＴｉ、Ｎｂを添加する際にこれらが酸化し
て損失することを防止するために０．０１重量％以上必
要であり、また鋼中のＮ、Ｓと化合して無害化に効果が
ある。しかし、０．１重量％を越えて添加しても効果は
飽和し、経済的でない。That is, the amounts of Ti and Nb satisfy the following equation. C / 12 ≦ Ti * / 48 + Nb / 93 ≦ C / 2 (where Ti * is Ti− (48N / 14 + 48S /
32) When ≧ 0, Ti * = Ti− (48N / 14 + 4
8S / 32), (Ti-48N / 14 + 48S / 32)
When <0, Ti * = 0. ) Al: Al is required to be 0.01% by weight or more in order to prevent the oxidation and loss of Ti and Nb when they are added, and it is made harmless by combining with N and S in steel. effective. However, even if added over 0.1% by weight, the effect is saturated and it is not economical.
【００１４】また、本発明の鋼板においては、上記基本
組成に加えてさらにＢを０．００１重量％以下含有する
のがより好ましい。Ｂは粒界を強化し、スポット溶接性
と２次加工脆性を改善するうえで有効であるためであ
る。しかし、０．００１重量％を越えて添加すると、絞
り性を損うので上限を０．００１重量％とする。次に、
めっき層の成分についてその限定理由を述べる。Further, in the steel sheet of the present invention, it is more preferable that B is contained in an amount of 0.001% by weight or less in addition to the above basic composition. This is because B is effective in strengthening grain boundaries and improving spot weldability and secondary work brittleness. However, if added in excess of 0.001% by weight, the drawability is impaired, so the upper limit is made 0.001% by weight. next,
The reasons for limiting the components of the plating layer will be described.
【００１５】合金化溶融亜鉛めっき鋼板は溶融亜鉛浴に
鋼板を浸漬後該鋼板を加熱することにより、素地鋼板の
Ｆｅをめっき層中に拡散しＺｎ−Ｆｅ合金層とすること
で単なる亜鉛めっき鋼板より、耐食性、化成処理性、ス
ポット溶接性を著しく向上するものであり、このような
機能はめっき層中のＦｅ含有量を９重量％以上とするこ
とにより好適に達成される。また、フレーキングの原因
となるζ層を発達させないためにも９重量％以上が必要
である。一方Ｆｅ含有量が１２重量％を越えると、めっ
き層中のＡｌ含有量を後述する範囲に制御したとしても
硬くて脆いГ層が発達してしまいプレス成形性を阻害す
る。よって、めっき層中のＦｅ含有量は９〜１２重量％
以下でなければならない。The alloyed hot-dip galvanized steel sheet is simply a galvanized steel sheet by immersing the steel sheet in a hot-dip zinc bath and then heating the steel sheet to diffuse Fe of the base steel sheet into the plated layer to form a Zn-Fe alloy layer. As a result, corrosion resistance, chemical conversion treatment property, and spot weldability are remarkably improved, and such a function is preferably achieved by setting the Fe content in the plating layer to 9% by weight or more. Further, in order not to develop the ζ layer which causes flaking, the content is required to be 9% by weight or more. On the other hand, when the Fe content exceeds 12% by weight, a hard and brittle Γ layer develops even if the Al content in the plating layer is controlled within the range described below, which impairs press formability. Therefore, the Fe content in the plating layer is 9 to 12% by weight.
Must be:
【００１６】めっき層中のＡｌ含有量は合金化処理時に
形成されるＺｎ−Ｆｅ合金の相構成に影響を与えるもの
であり、その量が０．３重量％未満ではГ層が発達しパ
ウダリングを生じ易くなり、１．５重量％超では十分な
合金化が得られ難い。よってめっき層中のＡｌ含有量は
０．３〜１．５重量％とする。めっき層中のＰｂは耐食
性に悪影響を及ぼすので０．０２重量％以下に制限す
る。The Al content in the plating layer has an influence on the phase composition of the Zn-Fe alloy formed during the alloying treatment. If the content is less than 0.3% by weight, the Γ layer develops and powdering occurs. Is likely to occur, and if it exceeds 1.5% by weight, it is difficult to obtain sufficient alloying. Therefore, the Al content in the plating layer is 0.3 to 1.5% by weight. Since Pb in the plating layer adversely affects the corrosion resistance, it is limited to 0.02% by weight or less.
【００１７】めっき層の目付量は耐食性の面から２５ｇ
／ｍ2 以上必要であるが、厚過ぎると、プレス成形時に
鋼板の変形に追随しきれなくなりパウダリングを生じる
ので上限を７０ｇ／ｃｍ2 とする。本発明の鋼板の製造
方法は特に限定するものではないが、その好適な製造例
について、次に説明する。The coating weight of the plating layer is 25 g from the viewpoint of corrosion resistance.
/ M 2 or more is necessary, but if it is too thick, it cannot follow the deformation of the steel sheet during press forming and powdering occurs, so the upper limit is made 70 g / cm 2 . The method for producing the steel sheet of the present invention is not particularly limited, but a preferred production example thereof will be described below.
【００１８】前記組成に調整された溶鋼を連続鋳造法に
よってスラブとし、熱間圧延、冷間圧延を経て冷間鋼板
とする。熱延では高加工性を得るために仕上温度はＡｒ
3 変態点前後の８５０〜９２０℃が好ましく、巻取温度
は６００℃以上にすることが好ましい。更に冷延におい
ても圧下率５０％以上とすることが好ましい。溶融亜鉛
めっきにおいては、まず焼鈍還元に先立ち鋼板表面を清
浄化するが、この方法としては、脱脂、酸洗等によって
もよく燃焼によってもよい。鋼板はその後焼鈍還元され
るが、雰囲気としては数％〜数十％のＮ2 を含むＨ2 を
用いるのが適当であり、露点は０℃以下とすることが好
ましい。材質の確保のため焼鈍還元温度は再結晶温度以
上が必要であるが、生産性を考えると、７８０℃以上と
することが好ましい。The molten steel adjusted to the above composition is made into a slab by a continuous casting method, and hot rolled and cold rolled to obtain a cold steel sheet. In hot rolling, the finishing temperature is Ar to obtain high workability.
The temperature is preferably 850 to 920 ° C before and after the three transformation points, and the winding temperature is preferably 600 ° C or higher. Further, it is preferable that the rolling reduction is 50% or more even in cold rolling. In hot dip galvanizing, the surface of the steel sheet is first cleaned prior to annealing reduction, but this method may be degreasing, pickling, or burning. The steel sheet is then annealed and reduced, but it is appropriate to use H 2 containing several% to several tens% of N 2 as an atmosphere, and the dew point is preferably 0 ° C. or lower. The annealing reduction temperature needs to be higher than the recrystallization temperature in order to secure the material, but in view of productivity, it is preferably 780 ° C. or higher.
【００１９】焼鈍還元後の鋼板は還元ガス中で冷却後そ
のまま溶融亜鉛めっき浴に導入されるが、その浴成分及
び温度は以下のように決定される。 浴中Ａｌ濃度：本発明はめっき浴中で生成するＡｌ−Ｆ
ｅ合金層量を制御してδ1 相主体の合金化を図り、耐パ
ウダリング性と耐フレーキング性を確保するが、そのた
めにはＡｌ−Ｆｅ合金層量が合金中のＡｌ量で０．１５
ｇ／ｍ2 以上にするのがよく、浴中のＡｌ量は０．１３
重量％以上が必要となり、効率よくＡｌ−Ｆｅ合金層を
形成するには０．１４５重量％以上が好ましい。一方、
Ａｌ−Ｆｅ層量がＡｌ量で０．５ｇ／ｍ2 を越えると合
金化の抑制が過剰になり生産性を阻害するおそれがあ
る。つまり、合金化後のめっき中ではＡｌ−Ｆｅ層以外
のめっき中のＡｌを含め１．５重量％のＡｌを上限とす
るのが良い。よって浴中Ａｌ濃度の上限は０．２重量％
となる。The steel sheet after the annealing reduction is introduced into the hot dip galvanizing bath as it is after being cooled in a reducing gas, and its bath components and temperature are determined as follows. Al concentration in the bath: The present invention produces Al-F in the plating bath.
The alloy layer amount is controlled to achieve alloying mainly in the δ 1 phase to secure powdering resistance and flaking resistance. For that purpose, the Al-Fe alloy layer amount is 0. 15
g / m 2 or more is recommended, and the amount of Al in the bath is 0.13
The amount is required to be 0.1% by weight or more, and 0.145% by weight or more is preferable for efficiently forming the Al-Fe alloy layer. on the other hand,
When the amount of Al-Fe layer exceeds 0.5 g / m 2 in terms of Al amount, alloying may be excessively suppressed and productivity may be impaired. That is, in the plating after alloying, it is preferable that the upper limit is 1.5% by weight of Al including Al in the plating other than the Al—Fe layer. Therefore, the upper limit of Al concentration in the bath is 0.2% by weight.
Becomes
【００２０】浴中Ｐｂ濃度：浴中ＰｂはＡｌと異なり溶
融めっき時にめっき中に濃化することはない。しかし、
めっき層中の濃度が０．１重量％を越えると、耐食性が
懸念され、浴中Ｐｂ濃度の上限は０．１重量％とする。
また、本発明の鋼板はそのままでも、自動車、家電、建
材等の各種用途に裸、プレコート、ポストコート、ラミ
ネート、あるいはクロメート処理、リン酸塩処理等各種
化成処理を施した形態で使用できるが、合金化溶融亜鉛
めっき層の上層にさらに、Ｆｅ、Ｚｎ、Ｎｉ、の一種以
上を含有するめっきを施すと、耐食性や塗装性がいっそ
う向上し好ましい。Concentration of Pb in the bath: Unlike Al, Pb in the bath does not concentrate during plating during hot dipping. But,
If the concentration in the plating layer exceeds 0.1% by weight, corrosion resistance may be a concern, and the upper limit of the Pb concentration in the bath is 0.1% by weight.
Further, the steel sheet of the present invention can be used as it is, for various applications such as automobiles, home appliances, and building materials, naked, pre-coated, post-coated, laminated, or subjected to various chemical conversion treatments such as chromate treatment and phosphate treatment, It is preferable to further perform plating containing one or more of Fe, Zn, and Ni on the upper layer of the galvannealed layer because the corrosion resistance and the coating property are further improved.
【００２１】めっき浴浸漬後の鋼板は合金化処理を行い
合金化度（Ｆｅ）９〜１２％のＧＡ鋼板とする。以上に
よりプレス加工性と耐めっき剥離性に優れる合金化溶融
亜鉛めっき鋼板が製造できる。The steel sheet after immersion in the plating bath is subjected to alloying treatment to obtain a GA steel sheet having an alloying degree (Fe) of 9 to 12%. As described above, an alloyed hot-dip galvanized steel sheet excellent in press workability and resistance to peeling of plating can be manufactured.
【００２２】[0022]
【実施例】以下に本発明の効果について実施例を以て説
明する。めっきには装置に縦型の溶融亜鉛めっき実験装
置を用い、焼鈍還元ガスには５％水素含有窒素を用い
て、７０ｍｍ×２００ｍｍの鋼板にめっきを行った。め
っきの合金化処理にはめっき鋼板に直接通電し抵抗発熱
量をコントロールするタイプの加熱炉を用いた。供試鋼
板は真空溶解炉で溶製し、予め熱延及び冷延を行い板厚
０．７ｍｍにし、めっき装置挿入前に電解脱脂及び塩酸
酸洗を行った。熱延の仕上げ温度変化は９００℃、一旦
冷却後にコイル巻取後の熱履歴を模して７００℃−１時
間の均熱、冷却酸洗後に冷延は圧下率７５％で行った。
供試鋼板の成分を表１、表２に、めっき条件及び合金化
処理前のめっき層の組成を表３に、合金化後のめっき鋼
板の特性を表４、表５に示す。なお、鋼板材質について
はＣＧＬを模して、冷延後の鋼板を焼鈍８５０℃−２０
秒、冷却中５００℃−３０秒保持する合金化溶融亜鉛め
っきサイクルで熱処理して求め、表２に鋼中成分と併せ
て示した。EXAMPLES The effects of the present invention will be described below with reference to examples. A vertical hot-dip galvanizing test device was used for the plating, and 5% hydrogen-containing nitrogen was used as the annealing reducing gas to plate a 70 mm × 200 mm steel plate. For the alloying treatment of the plating, a heating furnace of the type in which the amount of resistance heat generation was controlled by directly energizing the plated steel sheet was used. The test steel sheet was melted in a vacuum melting furnace, hot-rolled and cold-rolled in advance to a plate thickness of 0.7 mm, and electrolytic degreasing and hydrochloric acid pickling were performed before inserting the plating apparatus. The change in the finishing temperature of hot rolling was 900 ° C., the temperature was once cooled, soaking the heat history after coiling at 700 ° C. for 1 hour soaking, and after cold pickling, cold rolling was performed at a rolling reduction of 75%.
The components of the test steel sheet are shown in Tables 1 and 2, the plating conditions and the composition of the plating layer before alloying treatment are shown in Table 3, and the properties of the plated steel sheet after alloying are shown in Tables 4 and 5. Regarding the material of the steel sheet, the steel sheet after cold rolling was annealed at 850 ° C.-20, imitating CGL.
Seconds, heat treatment was performed in an alloying hot dip galvanizing cycle in which the temperature was maintained at 500 ° C. for 30 seconds, and the results are shown in Table 2 together with the components in the steel.
【００２３】表３中のＡｌ−Ｆｅ量の測定では合金化処
理前のめっき鋼板を発煙硝酸に浸漬して亜鉛（η）相を
除去し、不動態化して溶け残ったＡｌ−Ｆｅ合金層を塩
酸に溶解してＡｌ量を原子吸光法により測定した。めっ
き鋼板の評価には鋼板材質として伸び率（Ｅｌ）、ｒ値
を引張試験より求め、めっき層の特性としては耐パウダ
リング性と耐フレーキング性を求めた。パウダリング性
の評価は合金化後のめっき鋼板を９０度曲げ、曲げ戻し
し、剥離しためっきを予め添付したセロハンテープで採
取し、その量から１〜５の段階に評価した。１は良、５
は悪である。耐フレーキング性は合金化後の鋼板を１０
ｍｍ幅に切断し、図１に示すビード式引き抜き試験機で
試験した。ビード式引抜き試験機は凹部材１と凸部材３
との間の曲通路を通って試験片２を引き抜くものであ
る。試験片を無塗油で、押え荷重１００ｋｇｆ、引き抜
き速度５００ｍｍ／ｍｉｎで引抜きテストして、剥離し
ためっきをセロハンテープで採取し、目視でフレーキン
グの有無を〇×の２段階に評価した。In the measurement of the amount of Al-Fe in Table 3, the plated steel sheet before the alloying treatment was immersed in fuming nitric acid to remove the zinc (η) phase, and the Al-Fe alloy layer which was passivated and left unmelted was formed. It was dissolved in hydrochloric acid and the amount of Al was measured by an atomic absorption method. For the evaluation of the plated steel sheet, the elongation rate (El) and r value were obtained as a steel sheet material by a tensile test, and as the characteristics of the plated layer, powdering resistance and flaking resistance were obtained. To evaluate the powdering property, the plated steel sheet after alloying was bent 90 degrees, bent back, and the peeled plating was sampled with a cellophane tape attached in advance, and the amount was evaluated on a scale of 1 to 5. 1 is good, 5
Is evil. Flaking resistance is 10
It was cut to a width of mm and tested by the bead pullout tester shown in FIG. The bead type pull-out tester has a concave member 1 and a convex member 3.
The test piece 2 is pulled out through a curved path between The test piece was subjected to a pulling test with no pressing oil at a pressing load of 100 kgf and a pulling speed of 500 mm / min, and the peeled plating was sampled with cellophane tape, and the presence or absence of flaking was visually evaluated in two grades of ◯ ×.
【００２４】表４、５から明らかなように、本発明によ
り高い加工性と優れた耐めっき剥離性を有する合金化溶
融亜鉛めっき鋼板が製造できる。As is apparent from Tables 4 and 5, the present invention makes it possible to produce an alloyed hot-dip galvanized steel sheet having high workability and excellent plating peel resistance.
【００２５】[0025]
【表１】 [Table 1]
【００２６】[0026]
【表２】 [Table 2]
【００２７】[0027]
【表３】 [Table 3]
【００２８】[0028]
【表４】 [Table 4]
【００２９】[0029]
【表５】 [Table 5]
【００３０】[0030]
【発明の効果】本発明により高度のプレス加工性と優れ
た耐めっき剥離を有する合金化溶融亜鉛めっき鋼板が製
造できる。According to the present invention, an alloyed hot-dip galvanized steel sheet having a high degree of press workability and excellent peeling resistance to plating can be produced.
【図面の簡単な説明】[Brief description of drawings]
【図１】ビード式引抜試験の説明図である。FIG. 1 is an explanatory diagram of a bead-type pull-out test.
１ 凹部材 ２ 試験片 ３ 凸部材 1 concave material 2 test piece 3 convex member
─────────────────────────────────────────────────────
─────────────────────────────────────────────────── ───
【手続補正書】[Procedure amendment]
【提出日】平成５年１０月１８日[Submission date] October 18, 1993
【手続補正１】[Procedure Amendment 1]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００２２[Name of item to be corrected] 0022
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００２２】[0022]
【実施例】以下に本発明の効果について実施例を以て説
明する。めっきには装置に縦型の溶融亜鉛めっき実験装
置を用い、焼鈍還元ガスには５％水素含有窒素を用い
て、７０ｍｍ×２００ｍｍの鋼板にめっきを行った。め
っきの合金化処理にはめっき鋼板に直接通電し抵抗発熱
量をコントロールするタイプの加熱炉を用いた。供試鋼
板は真空溶解炉で溶製し、予め熱延及び冷延を行い板厚
０．７ｍｍにし、めっき装置挿入前に電解脱脂及び塩酸
酸洗を行った。熱延の仕上げ温度変化は９００℃、一旦
冷却後にコイル巻取後の熱履歴を模して７００℃−１時
間の均熱、冷却酸洗後に冷延は圧下率７５％で行った。
供試鋼板の成分を表１、表２に、めっき条件及び合金化
処理前のめっき層の組成及び合金化後のめっき鋼板の特
性を表３に示す。なお、鋼板材質についてはＣＧＬを模
して、冷延後の鋼板を焼鈍８５０℃−２０秒、冷却中５
００℃−３０秒保持する合金化溶融亜鉛めっきサイクル
で熱処理して求め、表２に鋼中成分と併せて示した。EXAMPLES The effects of the present invention will be described below with reference to examples. A vertical hot-dip galvanizing test device was used for the plating, and 5% hydrogen-containing nitrogen was used as the annealing reducing gas to plate a 70 mm × 200 mm steel plate. For the alloying treatment of the plating, a heating furnace of the type in which the amount of resistance heat generation was controlled by directly energizing the plated steel sheet was used. The test steel sheet was melted in a vacuum melting furnace, hot-rolled and cold-rolled in advance to a plate thickness of 0.7 mm, and electrolytic degreasing and hydrochloric acid pickling were performed before inserting the plating apparatus. The change in the finishing temperature of hot rolling was 900 ° C., the temperature was once cooled, soaking the heat history after coiling at 700 ° C. for 1 hour soaking, and after cold pickling, cold rolling was performed at a rolling reduction of 75%.
The components of the test steel sheet are shown in Tables 1 and 2, and the plating conditions, the composition of the plating layer before the alloying treatment, and the properties of the plated steel sheet after the alloying are shown in Table 3 . Regarding the material of the steel sheet, the steel sheet after cold rolling was annealed at 850 ° C. for 20 seconds while simulating CGL, and was cooled for 5 seconds.
It was obtained by heat treatment in an alloying hot-dip galvanizing cycle holding at 00 ° C for 30 seconds, and shown in Table 2 together with the components in steel.
【手続補正２】[Procedure Amendment 2]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００２４[Name of item to be corrected] 0024
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００２４】表３から明らかなように、本発明により高
い加工性と優れた耐めっき剥離性を有する合金化溶融亜
鉛めっき鋼板が製造できる。As is clear from Table 3 , the present invention makes it possible to produce an alloyed hot-dip galvanized steel sheet having high workability and excellent resistance to peeling of plating.
【手続補正３】[Procedure 3]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００２７[Name of item to be corrected] 0027
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００２７】[0027]
【表３】 [Table 3]
【手続補正４】[Procedure amendment 4]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００２８[Correction target item name] 0028
【補正方法】削除[Correction method] Delete
【手続補正５】[Procedure Amendment 5]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００２９[Name of item to be corrected] 0029
【補正方法】削除[Correction method] Delete
Claims (2)
０３重量％以下のＮｂ少なくとも一種以上を、 Ｃ／１２≦Ｔｉ＊／４８＋Ｎｂ／９３≦Ｃ／２ を満足する範囲で含有する鋼板表面に Ｆｅ：９重量％以上１２重量％以下、 Ａｌ：０．３重量％以上、１．５重量％以下 Ｐｂ：０．１重量％以下 を含有する合金化溶融亜鉛めっき層を２５ｇ／ｍ2 以上
７０ｇ／ｍ2 以下形成したことを特徴とするプレス加工
性と耐めっき剥離性に優れた合金化溶融亜鉛めっき鋼
板。ただし、Ｔｉ＊はＴｉ−（４８Ｎ／１４＋４８Ｓ／
３２）≧０のときはＴｉ＊＝Ｔｉ−（４８Ｎ／１４＋４
８Ｓ／３２）、Ｔｉ−（４８Ｎ／１４＋４８Ｓ／３２）
＜０のときはＴｉ＊＝０とする。1. C: 0.0015% by weight or less, Si: 0.1% by weight or less, Mn: 0.03% by weight or more and 0.3% by weight or less, Al: 0.01% by weight or more and 0.1% by weight % Or less, P: 0.01% by weight or less, S: 0.005% by weight or less, O: 0.005% by weight or less, N: 0.005% by weight or less, and 0.03% by weight or less Ti or 0.
Fe: 9% by weight or more and 12% by weight or less, Al: 0. 3% by weight or more on the surface of the steel sheet containing at least one Nb in an amount satisfying C / 12 ≦ Ti * / 48 + Nb / 93 ≦ C / 2. 3% by weight or more and 1.5% by weight or less Pb: 0.1% by weight or less of an alloyed hot-dip galvanized layer is formed at 25 g / m 2 or more and 70 g / m 2 or less, and press workability. Alloyed hot-dip galvanized steel sheet with excellent resistance to stripping. However, Ti * is Ti- (48N / 14 + 48S /
32) When ≧ 0, Ti * = Ti− (48N / 14 + 4
8S / 32), Ti- (48N / 14 + 48S / 32)
When <0, Ti * = 0.
０．００１重量％以下含有するものであるプレス加工性
と耐めっき剥離性に優れた合金化溶融亜鉛めっき鋼板。2. An alloyed hot-dip galvanized steel sheet having excellent press workability and resistance to peeling of plating, which further contains 0.001% by weight or less of B in the steel sheet composition according to claim 1.
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04312293A JP3318385B2 (en) | 1993-03-04 | 1993-03-04 | Alloyed hot-dip galvanized steel sheet with excellent press workability and plating resistance |
| DE69404338T DE69404338T2 (en) | 1993-03-04 | 1994-03-03 | Alloyed hot-dipped galvanized steel strip |
| EP94103185A EP0613961B1 (en) | 1993-03-04 | 1994-03-03 | Alloyed hot dip galvanized steel sheet |
| CN94104090A CN1125188C (en) | 1993-03-04 | 1994-03-04 | Alloyed hot dip galvanized steel sheet background of the invention |
| CA002116984A CA2116984A1 (en) | 1993-03-04 | 1994-03-04 | Alloyed hot dip galvanized steel sheet |
| KR1019940004192A KR100261522B1 (en) | 1993-03-04 | 1994-03-04 | Alloyed hot dip galvanized steel sheet |
| TW083101991A TW380165B (en) | 1993-03-04 | 1994-03-08 | Alloyed hot dip galvanized steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04312293A JP3318385B2 (en) | 1993-03-04 | 1993-03-04 | Alloyed hot-dip galvanized steel sheet with excellent press workability and plating resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06256903A true JPH06256903A (en) | 1994-09-13 |
| JP3318385B2 JP3318385B2 (en) | 2002-08-26 |
Family
ID=12655038
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP04312293A Expired - Fee Related JP3318385B2 (en) | 1993-03-04 | 1993-03-04 | Alloyed hot-dip galvanized steel sheet with excellent press workability and plating resistance |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0613961B1 (en) |
| JP (1) | JP3318385B2 (en) |
| KR (1) | KR100261522B1 (en) |
| CN (1) | CN1125188C (en) |
| CA (1) | CA2116984A1 (en) |
| DE (1) | DE69404338T2 (en) |
| TW (1) | TW380165B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006206954A (en) * | 2005-01-27 | 2006-08-10 | Nippon Steel Corp | Hot dip galvannealed steel sheet having excellent press formability and film adhesion at the time of press forming |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20010056280A (en) * | 1999-12-14 | 2001-07-04 | 이구택 | Galvannealing method for decreasing crater |
| TW536557B (en) * | 2000-09-12 | 2003-06-11 | Kawasaki Steel Co | High tensile strength hot dip plated steel sheet and method for production thereof |
| KR20060033811A (en) * | 2003-08-29 | 2006-04-19 | 제이에프이 스틸 가부시키가이샤 | Hot dip zinc plated steel sheet and method for production thereof |
| KR101091442B1 (en) * | 2003-12-29 | 2011-12-07 | 주식회사 포스코 | Hot-dip galvannealed steel sheet having excellent galvanized adhesion properity and method for manufacturing thereof |
| WO2007048883A1 (en) * | 2005-10-27 | 2007-05-03 | Usinor | Method of producing a part with very high mechanical properties from a rolled coated sheet |
| CN100519058C (en) * | 2007-04-20 | 2009-07-29 | 攀枝花钢铁(集团)公司 | Method for producing deep drawing skin-passed hot-dip galvanizing sheet steel |
| CN100591793C (en) * | 2008-07-30 | 2010-02-24 | 攀钢集团研究院有限公司 | Manufacturing method of hot dip galvanizing steel plate |
| CN101948981A (en) * | 2010-08-25 | 2011-01-19 | 青岛海信电器股份有限公司 | Hot galvanized steel plate and manufacturing method and application thereof and back shell of LED liquid crystal television |
| TWI507538B (en) * | 2011-09-30 | 2015-11-11 | Nippon Steel & Sumitomo Metal Corp | With excellent burn the attachment strength of the hardenable galvannealed steel sheet, a high strength galvannealed steel sheet and manufacturing method, etc. |
| CN104372279A (en) * | 2014-09-17 | 2015-02-25 | 朱忠良 | Hot dipping galvanized steel plate with characteristics of excellent stamping property and corrosion resistance |
| KR102513358B1 (en) * | 2020-12-17 | 2023-03-24 | 주식회사 포스코 | Different coating steel plate and display device |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4287008A (en) * | 1979-11-08 | 1981-09-01 | Bethlehem Steel Corporation | Method of improving the ductility of the coating of an aluminum-zinc alloy coated ferrous product |
| JPS61276962A (en) * | 1985-05-31 | 1986-12-06 | Kawasaki Steel Corp | Alloyed and galvanized steel sheet for deep drawing having excellent baking hardenability and powdering resistance |
| JPS6240353A (en) * | 1985-08-14 | 1987-02-21 | Sumitomo Metal Ind Ltd | Production of alloyed zinc plated steel sheet |
| JPS62142755A (en) * | 1985-12-17 | 1987-06-26 | Nippon Steel Corp | Alloyed hot dip galvanized steel sheet and its manufacture |
| JP2695260B2 (en) * | 1989-12-19 | 1997-12-24 | 川崎製鉄株式会社 | Method for producing alloyed hot-dip galvanized steel sheet excellent in press formability |
| JP2812770B2 (en) * | 1990-02-06 | 1998-10-22 | 新日本製鐵株式会社 | Manufacturing method of alloyed hot-dip galvanized cold-rolled steel sheet for deep drawing with excellent bake hardenability and powdering resistance |
| JP2619550B2 (en) * | 1990-03-20 | 1997-06-11 | 川崎製鉄株式会社 | Manufacturing method of galvannealed steel sheet |
| JPH046260A (en) * | 1990-04-25 | 1992-01-10 | Sumitomo Metal Ind Ltd | Production of ultra-deep-drawable galvanized sheet |
| JPH07116581B2 (en) * | 1990-05-22 | 1995-12-13 | 新日本製鐵株式会社 | High strength alloyed hot dip galvanized steel sheet with less plating peeling due to processing and excellent bake hardenability |
| JP2932701B2 (en) * | 1991-01-09 | 1999-08-09 | 住友金属工業株式会社 | Galvannealed steel sheet |
| CN1053268A (en) * | 1991-01-09 | 1991-07-24 | 河北省冶金研究所 | The double dipping hot plating technology of the high anti-corrosion of steel wire |
| JP3271354B2 (en) * | 1993-02-16 | 2002-04-02 | ミノルタ株式会社 | Image processing device |
-
1993
- 1993-03-04 JP JP04312293A patent/JP3318385B2/en not_active Expired - Fee Related
-
1994
- 1994-03-03 EP EP94103185A patent/EP0613961B1/en not_active Revoked
- 1994-03-03 DE DE69404338T patent/DE69404338T2/en not_active Revoked
- 1994-03-04 KR KR1019940004192A patent/KR100261522B1/en not_active IP Right Cessation
- 1994-03-04 CN CN94104090A patent/CN1125188C/en not_active Expired - Lifetime
- 1994-03-04 CA CA002116984A patent/CA2116984A1/en not_active Abandoned
- 1994-03-08 TW TW083101991A patent/TW380165B/en not_active IP Right Cessation
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006206954A (en) * | 2005-01-27 | 2006-08-10 | Nippon Steel Corp | Hot dip galvannealed steel sheet having excellent press formability and film adhesion at the time of press forming |
| JP4486518B2 (en) * | 2005-01-27 | 2010-06-23 | 新日本製鐵株式会社 | Alloyed hot-dip galvanized steel sheet with excellent press formability and coating adhesion during press forming |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1096060A (en) | 1994-12-07 |
| KR940021750A (en) | 1994-10-19 |
| EP0613961B1 (en) | 1997-07-23 |
| EP0613961A1 (en) | 1994-09-07 |
| TW380165B (en) | 2000-01-21 |
| DE69404338T2 (en) | 1997-11-13 |
| CN1125188C (en) | 2003-10-22 |
| JP3318385B2 (en) | 2002-08-26 |
| KR100261522B1 (en) | 2000-07-15 |
| CA2116984A1 (en) | 1994-09-05 |
| DE69404338D1 (en) | 1997-09-04 |
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