CA2116984A1 - Alloyed hot dip galvanized steel sheet - Google Patents
Alloyed hot dip galvanized steel sheetInfo
- Publication number
- CA2116984A1 CA2116984A1 CA002116984A CA2116984A CA2116984A1 CA 2116984 A1 CA2116984 A1 CA 2116984A1 CA 002116984 A CA002116984 A CA 002116984A CA 2116984 A CA2116984 A CA 2116984A CA 2116984 A1 CA2116984 A1 CA 2116984A1
- Authority
- CA
- Canada
- Prior art keywords
- weight
- less
- steel sheet
- hot dip
- dip galvanized
- 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.)
- Abandoned
Links
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 20
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 20
- 238000007747 plating Methods 0.000 claims abstract description 38
- 238000000926 separation method Methods 0.000 claims abstract description 10
- 229910000831 Steel Inorganic materials 0.000 claims description 56
- 239000010959 steel Substances 0.000 claims description 56
- 229910052757 nitrogen Inorganic materials 0.000 claims description 13
- 229910001209 Low-carbon steel Inorganic materials 0.000 abstract 1
- 238000005275 alloying Methods 0.000 description 15
- 238000000227 grinding Methods 0.000 description 9
- 229910052717 sulfur Inorganic materials 0.000 description 9
- 238000012545 processing Methods 0.000 description 8
- 230000009467 reduction Effects 0.000 description 8
- 229910018084 Al-Fe Inorganic materials 0.000 description 7
- 229910018192 Al—Fe Inorganic materials 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000005246 galvanizing Methods 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 238000000137 annealing Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910052758 niobium Inorganic materials 0.000 description 6
- 229910052698 phosphorus Inorganic materials 0.000 description 6
- 238000003825 pressing Methods 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 4
- 238000005097 cold rolling Methods 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 239000011701 zinc Substances 0.000 description 4
- 229910000640 Fe alloy Inorganic materials 0.000 description 3
- 239000011324 bead Substances 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229920000298 Cellophane Polymers 0.000 description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 2
- 238000005238 degreasing Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 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
- 239000002253 acid Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- ZCDOYSPFYFSLEW-UHFFFAOYSA-N chromate(2-) Chemical compound [O-][Cr]([O-])(=O)=O ZCDOYSPFYFSLEW-UHFFFAOYSA-N 0.000 description 1
- 239000004035 construction material Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000010030 laminating Methods 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 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
- 238000001953 recrystallisation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000004381 surface treatment Methods 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
Landscapes
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Thermal Sciences (AREA)
- Coating With Molten Metal (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
An alloyed hot dip galvanized steel plate having high press workability and excellent plating separation resistance. The alloyed hot dip galvanized steel plate is obtained by forming an alloyed hot dip galvanized layer which contains 9 - 12 weight % of Fe and 0.3 - 1.5 weight % of Al on the surface of a ultra-low-carbon steel plate so that the amount of the adhesion thereof is from 25g/m2 - 70g/m2.
An alloyed hot dip galvanized steel plate having high press workability and excellent plating separation resistance. The alloyed hot dip galvanized steel plate is obtained by forming an alloyed hot dip galvanized layer which contains 9 - 12 weight % of Fe and 0.3 - 1.5 weight % of Al on the surface of a ultra-low-carbon steel plate so that the amount of the adhesion thereof is from 25g/m2 - 70g/m2.
Description
ALLOYED HOT DIP GALVANIZED STEEL SHEET
BACKGROUND OF THE INVENTION
Field of the Invention The present invention relates to an alloyed hot dip galvanized steel sheet which is used for external vehicle body plates having excellent pressing workability and plating separation resistance.
Descri~tion of Related Art Recently, increased anticorrosive properties for vehicle bodies have been demanded. Industry has therefore been trying to develop adequate galvanized surface treatment steel sheets to meet these demands.
One development has been hot dip galvanized steel sheets, which are economically excellent. Further, it has become possible to improve weldability and corrosion resistance after coating steel sheets by composing a plating layer of Fe-Zn (alloyed hot dip galvanized steel plate) and sub~ecting it to heat treatment.
Higher ductility (elongation El) and higher drawabil~ty (Lankford value, r value) have also been demanded because alloyed hot dip galvanized steel sheets used for external vehicle body sheets (hereinafter sometimes referred to as "GA") are subjected to high-level press processing to improve their design characteristics... To solve problems associated with achieving high ductility and high drawability, a variety of methods for reducing the content of C, N, P, S and the like contained in steels from the viewpoint of the property of the steel sheet as a material have been `. 5; r . ~ "
developed. Optimum hot rolling and cold rolling processes have also been developed.
In conjunction with the demands for the steel sheet, the characteristics demanded for the plating layer of GA
steel sheets are that the plating layer must not exhibit ~ powdering~ in which the structure thereof is powdered and iseparated because it cannot follow the deformation of the steel sheet during processing, and 2) "flaking" in which the structure is separated in the form of scales when it is ironed by means of pressing dies. If such phenomena occur, separated plated particles are collected in the pressing dies, thereby causing highly undesirable indentations on the surface of steel sheets. Also, the corrosion resistance of the plating itself may be lost.
Generally, the plating layer of GA steel sheet is said to be composed of three Zn-Fe alloy phases ~, ~I r r from the viewpoint of low percentage content of Fe. The reason for powdering is believed to originate from the r phase and the reason for flaking is believed to originate from the ~ phase. If GA steel sheet is produced by hot-dip galvanizing the C, N, P, S reduced material, the ductility and r value are satisfied. However, if such a treatment is performed, alloying in the grain boundary of the s~eel sheet is excessively accelerated and increases the amount of r phase formation, thereby reducing powdering resistance. To secure a satisfactory powderlng resistance, it is necessary to restrict the degree of alloying to the level (concentration of Fe) in which substantially no r phase is generated. However, in this case, as disclosed in Japanese Patent Laid-Open No.2-11745, if only the percentage content of Fe is restricted to cause no r phase, the ~ phase may form in a thick layer on the surface of the plating layer depending on production conditions, so that flaking becomes likely to occur when the layer is strongly flattened during pressing.
SUMMARY OF THE INVENTION
Accordingly, it is an object of the present invention to obtain an alloyed hot dip galvanized steel sheet in which the powdering resistance and flaking resistance can be satisfied at the same time by using a :
steel sheet obtained by reducing the content of C, N, P, S contained in the steel plate.
According to the present invention, there is provided an alloyed hot dip galvanized steel sheet having excellent press workability and plating separation resistance, wherein an alloyed hot dip galvanized layer which contains about 9 weight % or more and about 12 weight % or less of Fe, about 0.3 weight % or more and : ::
about 1.5 weight % or less of Al, about 0.1 weight % or less of Pb is formed on the surface of a steel sheet :
which contains about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % or more and about 0.3 weight % or less of Mn, about 0.01 weight % : ;
or more and about 0.1 weight % or less of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, ~1698~
about 0.005 weight % or less of O, about 0.005 weight %
or less of N and further contains at least one of about 0.03 weight 'i~ or less of Ti or about 0.03 weight % or less of Nb in the range in which C/12<Ti*/48 + Nb/93~C/2, the layer being in the thickness of about 25g/m2or more and about 70g/m2or less.
In this case, it is assumed that T* is Ti - (48N/14 + 48S/32) when Ti - (48N/14 + 48S/32)20 and Ti* is 0 when Ti - (48N/14 + 48S/32)~0. Additionally, the steel sheet having the aforementioned composition may contain about 0.001 weight % or less of B.
BRIEF DESCRIPTION OF THE DRAWINGS
Fig. 1 is a schematic, explanatory drawing of a bead type pulling testing apparatus.
pETAILED DESCRIPTION OF THE INVENTION
The alloyed hot dip galvanized steel sheet which has excellent press workability and plating separation resistance which is an object of the present invention will be described below. However, it will be appreciated that the following description is intended to refer to specific embodiments of the invention selected for illustration in the drawing and is not intended to define or limit the invention, other than in the appended claims.
First, the components contained in steel sheet which is to be used as the material for plating are determined ~
as follows in order to satisfy necessary properties and achieve efficient economic production.
211 ~98~
C: C is an element which directly determines the strength of steel. To obtain an extremely high workability (high El, r value) which is an object of the present invention, a smaller content thereof is better.
The content thereof should be about 0.0015 weight % or less.
N, P and S: N, P and S are in the structure of steel to reduce the El and r values. As in the case of C, a smaller content of these elements is better. It is considered that N, P and S must be about 0.005 weight %
or less, about 0.01 weight ~ or less, and about 0.005 weight % or less, respectively.
O: O is precipitated as an oxide if it is excessively contained in steel, thereby reducing the El and r values. Therefore, the content thereof must be about 0.005 weight % maximum.
Mn: If Mn is added into steel, it is combined with S and then precipitated to become non-effective. Thus, when a small amount of Mn is added, there is no remarkable effect from the viewpoint of the material.
However, if the content thereof exceeds about 0.3 weight %, the El and r values decrease gradually. Thus, the content of Mn must be about 0.03 weight ~ or more and about 0.3 weight % or less.
Si: As in the case of Mn, a large amount of Si contain0d in steel reduces the El and r values and blocks the wettability of plating. Thus, the amount of Si is about 0.1 weight % maximum.
r~ :. ::: t.,. - : . '' ' .' ' . " '' ' 2~1 ~98~
Ti and Nb: Ti and Nb are combined with C and precipitated in the form of TiC and NbC, thereby improving workability. Thus, the atomic ratio of Ti and Nb with respect to C needs to be more than about 1.
However, because excessive addition of the elements increases cost, the maximum atomic ratio is about 6.
Additionally, it is desirable that the maximum amount of each component is about 0.03 weight ~. However, because Ti is more likely to be combined with N or S than C, it is necessary to determine the amount of Ti so that it is minus N and S equivalents. Specifically, it is assumed that the amounts of Ti and Nb satisfy the expression described below:
C/12~Ti*/48 + Nb/93<C/2 (where Ti* is Ti - (48N/14 + 48S/32) when Ti -(48N/14 + 48S/32)~0 and Ti* is 0 when (Ti - 48N/14 +
48S/32)<0) Al: The amount of Al needs to be about 0.01 weight % or more to prevent Ti and Nb from being oxidized and lost when Ti and Nb are added. Al is combined with N and S contained in steel, thereby eliminating the effects thereof. However, if the amount of added Al exceeds about 0.1 weight %, the effect is saturated, so that excessive addition of Al is economically meaningless.
B: In the steel sheet according to the present invention, besides the basic composition described above, it is preferable that the amount of B is less than about 0.001 weight %. The reason is that B is effective in strengthening the grain boundary and improving spot weldability and cold working embrittlement. However, if the amount of added B exceeds 0.001 weight %, the drawability is lost. Thus, the maximum amount is about 0.001 weight %.
Next, the reasons for the components of plating layer will be described below.
The alloyed hot dip galvanized steel sheet is produced by immersing a steel sheet in a molten zinc bath and then heating the steel sheet to diffuse Fe contained in the steel sheet into plated layers, thereby forming a Zn-Fe alloy layer. Consequently, the corrosion resistance, phosphatability and spot weldability thereof are markedly better than ordinary galvanized steel plates. These functions are preferably achieved by adjusting the content of Fe to about 9 weight % or more.
Additionally, the amou~t of Fe needs to be about 9 weight % or more to prevent a ~ phase layer from growing. On the other hand, if the content of Fe exceeds about 12 weight %, a hard, brittle r phase layer is developed even if the content of Al in the plating layer is controlled in a range described later, thereby blocking press workability. Thus, the content of Fe contained in the plating layer must be about 9-12 weight %.
~he content of Al contained in the plating layer affects the phase composition of the Zn-Fe alloy which is formed at the time of alloying. If the amount of Al is less than about 0.3 weight %, the r phase layer is developed so that undesirable powdering becomes likely.
If the amount of Al exceeds about 1.5 weight %, insufficient alloying is achieved. ~hus, the amount of Al contained in the plating layer is about 0.3 weight % -about 1.5 weight ~.
Pb contained in the plating layer is restricted to about 0.2 weight % or less because it badly affects the corrosion resistance of the plating layer.
The amount of the plating layer applied needs to be about 25g/m2 from the viewpoint of corrosion resistance.
However, if the plating layer is too thick, the layer cannot follow the deformation of the steel sheet when pressing is performed, thereby resulting in powdering.
Thus, the maximum amount of plating applied to the steel plate i8 determined to be about 70g/cm2.
Although the steel sheet production method according to the present invention is not particularly restricted to a specific method, a preferred production example will be described below.
Molten steel which is adjusted to the aforementioned composition i8 processed into a slab by means of a continuous casting method. The slab is then processed into cold finished steel plates through hot rolling and cold rolling. In hot rolling, it is desirable that the finishing temperature is about 850C - 920C which is near the Ar3 transformation point to obtain high processing properties. It is desirable that the winding temperature is about 600C or more. Further, in the cold rolling step, it is desirable that the rolling reduction is about 50% or more.
In hot dip galvanizing, the surface of a steel sheet is purified before annealing reduction is performed.
Degreasing, pickling or burning are permissible methods.
The steel sheet is then subjected to annealing reduction.
It is appropriate to use an H2 atmosphere containing between several % and several tens ~ of N2. It is also desirable that the dew point be 0C or less. Although the annealing reduction temperature needs to be higher than the recrystallization temperature to secure a preferred material, it is desirable that the annealing ~, reduction temperature is about 780C or more.
After annealing reduction is performed, the steel sheet is cooled in reducing gas and introduced to a hot dip galvanizing bath. The components and the temperature of the bath are determined as follows.
Concentration of Al in the bath: One purpose of the present invention is to secure powdering resistance and flaking resistance by controlling the amount of the Al-Fe alloy layer generated in the galvanizing bath to achieve alloying of mainly ~1 phase. The amount of the Al-Fe alloy layer should be ad~usted so that the amount of Al contained in the alloy is 0.15g/m2 or more for this purpose. Thus, the amount of Al in the bath needs to be about 0.13 weight % or more. To form the Al-Fe alloy layer effectively, it is desirable that the amount of Al is about 0.145 weight % or more. On the other hand, if ---, .. ' "' :' ', ' ~ ' ."' '' '' ' .' . `'` :
211698~
the amount of the Al-Fe layer is increased so that the amount of Al exceeds about O.Sg/m2, alloying is excessively restricted, so that productivity may be blocked. Namely, in the plating layer after alloying is S performed, it is desirable that the amount of Al including Al contained in layers other than the Al-Fe layer is about 1.5 weight % at most. Thus, the maximum concentration of Al contained in the bath is about 0.2 weight %.
Concentration of Pb in the bath: Unlike Al, Pb in the bath is not concentrated on the plating during hot dipping. However, if the concentration of Pb in the ~ ~
plating layer exceeds about 0.1 weight %, corrosion ~ r ' resistance may drop. Thus, the upper limit of the lS concentration of Pb in the bath is about 0.1 weight %.
The steel sheet of the present invention can be used for various applications including automobiles, household electric appliances, construction materials, and the like in bare condition and/or in a condition which undergoes pre-coating, po~t-coating, laminating, chromate ~;
treatment, phosphate treatment or the like. Moreover, if the top layer of the alloyed hot dip galvanized plating layer is further coated with a plating layer containing at least one of Fe, Zn and Ni, the corrosion resistance is further improved.
After the steel sheet is immersed in the plating bath, it is subjected to alloying processing to obtain a GA steel sheet in which the degree of alloying (Fe) is 2~ 16984 9 - 12~.
In the process described above, alloyed hot dip galvanized steel sheet which has excellent press processing and plating separation resistance can be obtained.
EXAMPLES:
Advantages of the present invention will be described with reference to examples thereof. Using a vertical type hot dip galvanizing experimental apparatus as a plating apparatus, a steel of 70mm x 200 mm was ;
plated in an atmosphere containing an-annealing reduction gas of 5%-hydrogen containing nitrogen. A heating oven which controlled the amount of heat generated by resistance by directly feeding power to a plated steel sheet was used for the alloying treatment of the plating.
A specimen of steel sheet wa~ softened by means of a vacuum melting furnace, and hot rolled and cold rolled to adjust the thickness of the sheet to 0.7 mm. The sheet wa~ sub~ected to electrolytic degreasing and pickling with hydrochloric acid before it was inserted into a plating apparatus. The hot rolling finish temperature was 900C. After temporary cooling, the sheet was equally heated at 700C for an hour according to the heat history obtained after it was coiled. The sheet was then cold rolled under a rolling reduction of 75~ after it was cooled and pickled with acid.
Table 1 shows the components of the specimen steel sheet, the condition for plating and the composition of a ..... . ... . . . . . .... . . . . ...
21~698~
plated layer provided before alloying treatment. Table 2 shows the characteristics of the plated steel sheet after the alloying treatment was performed. The material of the steel sheet was obtained by heat treatment according to CGL(Continuous Galvanizing Line) in an alloyed hot dip galvanizing cycle after which cold rolling was performed.
The steel sheet was then annealed at 850C for 20 seconds and cooled at 500C for 30 seconds. Table 1 shows the components of the steel sheet as well.
The measurement of the amount of Al-Fe shown in Table 2 was performed by immersing a plated steel sheet before it was subjected to alloying processing in fuming nitric acid to remove zinc (~) phase, solving the Al-Fe alloy layer which was left unsolved in the passive state in hydrochloric acid and then measuring the amount of Al according to the atomic absorption method.
The elongation percentage tEl) and r values of the steel sheet were obtained by tensile testing to evaluate the characteristics of the plated steel sheet. Powdering resistance and flaking resistance were obtained to investigate the characteristics of the plated layer.
..
Powdering resistance was evaluated according to a five-step evaluation system by bending a plated steel sheet which had been sub~ected to alloying processing at 90 degrees, restoring it, and collecting separated plating particles using a preliminarily attached cellophane tape to measure the amount thereof. "1" indicated acceptable and "5" indicated unacceptable in the test.
Flaking resistance was measured by means of the bead type drawing test apparatus shown in Fig. 1 by using 10 mm wide cut pieces of the steel sheet which had undergone alloying processing. In the bead type drawing test apparatus, a test piece 2 was drawn through a bent path between an indented member 1 and a protruded member 3.
The test piece coated with no oil was drawn under the condition in which the pressing load was lOOkgf and that the drawing velocity was 500mm/min. Separated plated particles were collected using a cellophane tape to visually recognize whether flaking had occurred according to a two-level (yes/no) evaluation system.
As is evident from Tables 1 and 2, the present invention has succeeded in realizing production of alloyed hot dip galvanized steel sheet which has high workability and excellent platiny separation resistance.
Consequently, according to the present invention, it is possible to produce an alloyed hot dip galvanized steel 8heet which has high workabLlity and excellent plating separation resistance.
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BACKGROUND OF THE INVENTION
Field of the Invention The present invention relates to an alloyed hot dip galvanized steel sheet which is used for external vehicle body plates having excellent pressing workability and plating separation resistance.
Descri~tion of Related Art Recently, increased anticorrosive properties for vehicle bodies have been demanded. Industry has therefore been trying to develop adequate galvanized surface treatment steel sheets to meet these demands.
One development has been hot dip galvanized steel sheets, which are economically excellent. Further, it has become possible to improve weldability and corrosion resistance after coating steel sheets by composing a plating layer of Fe-Zn (alloyed hot dip galvanized steel plate) and sub~ecting it to heat treatment.
Higher ductility (elongation El) and higher drawabil~ty (Lankford value, r value) have also been demanded because alloyed hot dip galvanized steel sheets used for external vehicle body sheets (hereinafter sometimes referred to as "GA") are subjected to high-level press processing to improve their design characteristics... To solve problems associated with achieving high ductility and high drawability, a variety of methods for reducing the content of C, N, P, S and the like contained in steels from the viewpoint of the property of the steel sheet as a material have been `. 5; r . ~ "
developed. Optimum hot rolling and cold rolling processes have also been developed.
In conjunction with the demands for the steel sheet, the characteristics demanded for the plating layer of GA
steel sheets are that the plating layer must not exhibit ~ powdering~ in which the structure thereof is powdered and iseparated because it cannot follow the deformation of the steel sheet during processing, and 2) "flaking" in which the structure is separated in the form of scales when it is ironed by means of pressing dies. If such phenomena occur, separated plated particles are collected in the pressing dies, thereby causing highly undesirable indentations on the surface of steel sheets. Also, the corrosion resistance of the plating itself may be lost.
Generally, the plating layer of GA steel sheet is said to be composed of three Zn-Fe alloy phases ~, ~I r r from the viewpoint of low percentage content of Fe. The reason for powdering is believed to originate from the r phase and the reason for flaking is believed to originate from the ~ phase. If GA steel sheet is produced by hot-dip galvanizing the C, N, P, S reduced material, the ductility and r value are satisfied. However, if such a treatment is performed, alloying in the grain boundary of the s~eel sheet is excessively accelerated and increases the amount of r phase formation, thereby reducing powdering resistance. To secure a satisfactory powderlng resistance, it is necessary to restrict the degree of alloying to the level (concentration of Fe) in which substantially no r phase is generated. However, in this case, as disclosed in Japanese Patent Laid-Open No.2-11745, if only the percentage content of Fe is restricted to cause no r phase, the ~ phase may form in a thick layer on the surface of the plating layer depending on production conditions, so that flaking becomes likely to occur when the layer is strongly flattened during pressing.
SUMMARY OF THE INVENTION
Accordingly, it is an object of the present invention to obtain an alloyed hot dip galvanized steel sheet in which the powdering resistance and flaking resistance can be satisfied at the same time by using a :
steel sheet obtained by reducing the content of C, N, P, S contained in the steel plate.
According to the present invention, there is provided an alloyed hot dip galvanized steel sheet having excellent press workability and plating separation resistance, wherein an alloyed hot dip galvanized layer which contains about 9 weight % or more and about 12 weight % or less of Fe, about 0.3 weight % or more and : ::
about 1.5 weight % or less of Al, about 0.1 weight % or less of Pb is formed on the surface of a steel sheet :
which contains about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % or more and about 0.3 weight % or less of Mn, about 0.01 weight % : ;
or more and about 0.1 weight % or less of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, ~1698~
about 0.005 weight % or less of O, about 0.005 weight %
or less of N and further contains at least one of about 0.03 weight 'i~ or less of Ti or about 0.03 weight % or less of Nb in the range in which C/12<Ti*/48 + Nb/93~C/2, the layer being in the thickness of about 25g/m2or more and about 70g/m2or less.
In this case, it is assumed that T* is Ti - (48N/14 + 48S/32) when Ti - (48N/14 + 48S/32)20 and Ti* is 0 when Ti - (48N/14 + 48S/32)~0. Additionally, the steel sheet having the aforementioned composition may contain about 0.001 weight % or less of B.
BRIEF DESCRIPTION OF THE DRAWINGS
Fig. 1 is a schematic, explanatory drawing of a bead type pulling testing apparatus.
pETAILED DESCRIPTION OF THE INVENTION
The alloyed hot dip galvanized steel sheet which has excellent press workability and plating separation resistance which is an object of the present invention will be described below. However, it will be appreciated that the following description is intended to refer to specific embodiments of the invention selected for illustration in the drawing and is not intended to define or limit the invention, other than in the appended claims.
First, the components contained in steel sheet which is to be used as the material for plating are determined ~
as follows in order to satisfy necessary properties and achieve efficient economic production.
211 ~98~
C: C is an element which directly determines the strength of steel. To obtain an extremely high workability (high El, r value) which is an object of the present invention, a smaller content thereof is better.
The content thereof should be about 0.0015 weight % or less.
N, P and S: N, P and S are in the structure of steel to reduce the El and r values. As in the case of C, a smaller content of these elements is better. It is considered that N, P and S must be about 0.005 weight %
or less, about 0.01 weight ~ or less, and about 0.005 weight % or less, respectively.
O: O is precipitated as an oxide if it is excessively contained in steel, thereby reducing the El and r values. Therefore, the content thereof must be about 0.005 weight % maximum.
Mn: If Mn is added into steel, it is combined with S and then precipitated to become non-effective. Thus, when a small amount of Mn is added, there is no remarkable effect from the viewpoint of the material.
However, if the content thereof exceeds about 0.3 weight %, the El and r values decrease gradually. Thus, the content of Mn must be about 0.03 weight ~ or more and about 0.3 weight % or less.
Si: As in the case of Mn, a large amount of Si contain0d in steel reduces the El and r values and blocks the wettability of plating. Thus, the amount of Si is about 0.1 weight % maximum.
r~ :. ::: t.,. - : . '' ' .' ' . " '' ' 2~1 ~98~
Ti and Nb: Ti and Nb are combined with C and precipitated in the form of TiC and NbC, thereby improving workability. Thus, the atomic ratio of Ti and Nb with respect to C needs to be more than about 1.
However, because excessive addition of the elements increases cost, the maximum atomic ratio is about 6.
Additionally, it is desirable that the maximum amount of each component is about 0.03 weight ~. However, because Ti is more likely to be combined with N or S than C, it is necessary to determine the amount of Ti so that it is minus N and S equivalents. Specifically, it is assumed that the amounts of Ti and Nb satisfy the expression described below:
C/12~Ti*/48 + Nb/93<C/2 (where Ti* is Ti - (48N/14 + 48S/32) when Ti -(48N/14 + 48S/32)~0 and Ti* is 0 when (Ti - 48N/14 +
48S/32)<0) Al: The amount of Al needs to be about 0.01 weight % or more to prevent Ti and Nb from being oxidized and lost when Ti and Nb are added. Al is combined with N and S contained in steel, thereby eliminating the effects thereof. However, if the amount of added Al exceeds about 0.1 weight %, the effect is saturated, so that excessive addition of Al is economically meaningless.
B: In the steel sheet according to the present invention, besides the basic composition described above, it is preferable that the amount of B is less than about 0.001 weight %. The reason is that B is effective in strengthening the grain boundary and improving spot weldability and cold working embrittlement. However, if the amount of added B exceeds 0.001 weight %, the drawability is lost. Thus, the maximum amount is about 0.001 weight %.
Next, the reasons for the components of plating layer will be described below.
The alloyed hot dip galvanized steel sheet is produced by immersing a steel sheet in a molten zinc bath and then heating the steel sheet to diffuse Fe contained in the steel sheet into plated layers, thereby forming a Zn-Fe alloy layer. Consequently, the corrosion resistance, phosphatability and spot weldability thereof are markedly better than ordinary galvanized steel plates. These functions are preferably achieved by adjusting the content of Fe to about 9 weight % or more.
Additionally, the amou~t of Fe needs to be about 9 weight % or more to prevent a ~ phase layer from growing. On the other hand, if the content of Fe exceeds about 12 weight %, a hard, brittle r phase layer is developed even if the content of Al in the plating layer is controlled in a range described later, thereby blocking press workability. Thus, the content of Fe contained in the plating layer must be about 9-12 weight %.
~he content of Al contained in the plating layer affects the phase composition of the Zn-Fe alloy which is formed at the time of alloying. If the amount of Al is less than about 0.3 weight %, the r phase layer is developed so that undesirable powdering becomes likely.
If the amount of Al exceeds about 1.5 weight %, insufficient alloying is achieved. ~hus, the amount of Al contained in the plating layer is about 0.3 weight % -about 1.5 weight ~.
Pb contained in the plating layer is restricted to about 0.2 weight % or less because it badly affects the corrosion resistance of the plating layer.
The amount of the plating layer applied needs to be about 25g/m2 from the viewpoint of corrosion resistance.
However, if the plating layer is too thick, the layer cannot follow the deformation of the steel sheet when pressing is performed, thereby resulting in powdering.
Thus, the maximum amount of plating applied to the steel plate i8 determined to be about 70g/cm2.
Although the steel sheet production method according to the present invention is not particularly restricted to a specific method, a preferred production example will be described below.
Molten steel which is adjusted to the aforementioned composition i8 processed into a slab by means of a continuous casting method. The slab is then processed into cold finished steel plates through hot rolling and cold rolling. In hot rolling, it is desirable that the finishing temperature is about 850C - 920C which is near the Ar3 transformation point to obtain high processing properties. It is desirable that the winding temperature is about 600C or more. Further, in the cold rolling step, it is desirable that the rolling reduction is about 50% or more.
In hot dip galvanizing, the surface of a steel sheet is purified before annealing reduction is performed.
Degreasing, pickling or burning are permissible methods.
The steel sheet is then subjected to annealing reduction.
It is appropriate to use an H2 atmosphere containing between several % and several tens ~ of N2. It is also desirable that the dew point be 0C or less. Although the annealing reduction temperature needs to be higher than the recrystallization temperature to secure a preferred material, it is desirable that the annealing ~, reduction temperature is about 780C or more.
After annealing reduction is performed, the steel sheet is cooled in reducing gas and introduced to a hot dip galvanizing bath. The components and the temperature of the bath are determined as follows.
Concentration of Al in the bath: One purpose of the present invention is to secure powdering resistance and flaking resistance by controlling the amount of the Al-Fe alloy layer generated in the galvanizing bath to achieve alloying of mainly ~1 phase. The amount of the Al-Fe alloy layer should be ad~usted so that the amount of Al contained in the alloy is 0.15g/m2 or more for this purpose. Thus, the amount of Al in the bath needs to be about 0.13 weight % or more. To form the Al-Fe alloy layer effectively, it is desirable that the amount of Al is about 0.145 weight % or more. On the other hand, if ---, .. ' "' :' ', ' ~ ' ."' '' '' ' .' . `'` :
211698~
the amount of the Al-Fe layer is increased so that the amount of Al exceeds about O.Sg/m2, alloying is excessively restricted, so that productivity may be blocked. Namely, in the plating layer after alloying is S performed, it is desirable that the amount of Al including Al contained in layers other than the Al-Fe layer is about 1.5 weight % at most. Thus, the maximum concentration of Al contained in the bath is about 0.2 weight %.
Concentration of Pb in the bath: Unlike Al, Pb in the bath is not concentrated on the plating during hot dipping. However, if the concentration of Pb in the ~ ~
plating layer exceeds about 0.1 weight %, corrosion ~ r ' resistance may drop. Thus, the upper limit of the lS concentration of Pb in the bath is about 0.1 weight %.
The steel sheet of the present invention can be used for various applications including automobiles, household electric appliances, construction materials, and the like in bare condition and/or in a condition which undergoes pre-coating, po~t-coating, laminating, chromate ~;
treatment, phosphate treatment or the like. Moreover, if the top layer of the alloyed hot dip galvanized plating layer is further coated with a plating layer containing at least one of Fe, Zn and Ni, the corrosion resistance is further improved.
After the steel sheet is immersed in the plating bath, it is subjected to alloying processing to obtain a GA steel sheet in which the degree of alloying (Fe) is 2~ 16984 9 - 12~.
In the process described above, alloyed hot dip galvanized steel sheet which has excellent press processing and plating separation resistance can be obtained.
EXAMPLES:
Advantages of the present invention will be described with reference to examples thereof. Using a vertical type hot dip galvanizing experimental apparatus as a plating apparatus, a steel of 70mm x 200 mm was ;
plated in an atmosphere containing an-annealing reduction gas of 5%-hydrogen containing nitrogen. A heating oven which controlled the amount of heat generated by resistance by directly feeding power to a plated steel sheet was used for the alloying treatment of the plating.
A specimen of steel sheet wa~ softened by means of a vacuum melting furnace, and hot rolled and cold rolled to adjust the thickness of the sheet to 0.7 mm. The sheet wa~ sub~ected to electrolytic degreasing and pickling with hydrochloric acid before it was inserted into a plating apparatus. The hot rolling finish temperature was 900C. After temporary cooling, the sheet was equally heated at 700C for an hour according to the heat history obtained after it was coiled. The sheet was then cold rolled under a rolling reduction of 75~ after it was cooled and pickled with acid.
Table 1 shows the components of the specimen steel sheet, the condition for plating and the composition of a ..... . ... . . . . . .... . . . . ...
21~698~
plated layer provided before alloying treatment. Table 2 shows the characteristics of the plated steel sheet after the alloying treatment was performed. The material of the steel sheet was obtained by heat treatment according to CGL(Continuous Galvanizing Line) in an alloyed hot dip galvanizing cycle after which cold rolling was performed.
The steel sheet was then annealed at 850C for 20 seconds and cooled at 500C for 30 seconds. Table 1 shows the components of the steel sheet as well.
The measurement of the amount of Al-Fe shown in Table 2 was performed by immersing a plated steel sheet before it was subjected to alloying processing in fuming nitric acid to remove zinc (~) phase, solving the Al-Fe alloy layer which was left unsolved in the passive state in hydrochloric acid and then measuring the amount of Al according to the atomic absorption method.
The elongation percentage tEl) and r values of the steel sheet were obtained by tensile testing to evaluate the characteristics of the plated steel sheet. Powdering resistance and flaking resistance were obtained to investigate the characteristics of the plated layer.
..
Powdering resistance was evaluated according to a five-step evaluation system by bending a plated steel sheet which had been sub~ected to alloying processing at 90 degrees, restoring it, and collecting separated plating particles using a preliminarily attached cellophane tape to measure the amount thereof. "1" indicated acceptable and "5" indicated unacceptable in the test.
Flaking resistance was measured by means of the bead type drawing test apparatus shown in Fig. 1 by using 10 mm wide cut pieces of the steel sheet which had undergone alloying processing. In the bead type drawing test apparatus, a test piece 2 was drawn through a bent path between an indented member 1 and a protruded member 3.
The test piece coated with no oil was drawn under the condition in which the pressing load was lOOkgf and that the drawing velocity was 500mm/min. Separated plated particles were collected using a cellophane tape to visually recognize whether flaking had occurred according to a two-level (yes/no) evaluation system.
As is evident from Tables 1 and 2, the present invention has succeeded in realizing production of alloyed hot dip galvanized steel sheet which has high workability and excellent platiny separation resistance.
Consequently, according to the present invention, it is possible to produce an alloyed hot dip galvanized steel 8heet which has high workabLlity and excellent plating separation resistance.
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Claims (4)
1. An alloyed hot dip galvanized steel sheet having excellent press workability and plating separation resistance, wherein an alloyed hot dip galvanized layer containing about 9 weight % or more and about 12 weight %
or less of Fe, about 0.3 weight % or more and about 1.5 weight % or less of Al, and about 0.1 weight % or less of Pb is formed on the surface of a steel plate containing about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % or more and about 0.3 weight % or less of Mn, about 0.01 weight % or more and about 0.1 weight % or less of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, about 0.005 weight % or less of 0, about 0.005 weight % or less of N, and at least one of about 0.03 weight % or less of Ti or about 0.03 weight % or less of Nb in the range in which C/12?Ti*/48 + Nb/93?C/2, the layer having a thickness of about 25g/m2 or more and about 70g/m2 or less; where T* is Ti - (48N/14 + 48S/32) when Ti - (48N/14 +
48S/32)?0 and Ti* is 0 when Ti - (48N/14 + 48S/32)<0.
or less of Fe, about 0.3 weight % or more and about 1.5 weight % or less of Al, and about 0.1 weight % or less of Pb is formed on the surface of a steel plate containing about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % or more and about 0.3 weight % or less of Mn, about 0.01 weight % or more and about 0.1 weight % or less of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, about 0.005 weight % or less of 0, about 0.005 weight % or less of N, and at least one of about 0.03 weight % or less of Ti or about 0.03 weight % or less of Nb in the range in which C/12?Ti*/48 + Nb/93?C/2, the layer having a thickness of about 25g/m2 or more and about 70g/m2 or less; where T* is Ti - (48N/14 + 48S/32) when Ti - (48N/14 +
48S/32)?0 and Ti* is 0 when Ti - (48N/14 + 48S/32)<0.
2. An alloyed hot dip galvanized steel sheet according to Claim 1, wherein said steel plate further contains about 0.001 weight % or less of B, said steel plate having excellent press workability and plating separation resistance.
3. An alloyed hot dip galvanized steel sheet having excellent press workability and plating separation resistance comprising:
a steel plate containing about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % or more and about 0.3 weight % or less of Mn, about 0.01 weight % or more and about 0.1 weight % or less of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, about 0.005 weight % or less of O, about 0.005 weight % or less of N, and at least one of about 0.03 weight % or less of Ti or about 0.03 weight %
or less of Nb in the range in which C/12?Ti*/48 +
Nb/93?C/2; and an alloyed hot dip galvanized layer formed on said steel plate at a thickness of between about 25g/m2 and about 70 g/m2, said layer containing about 9 weight % or more and about 12 weight % or less of Fe, about 0.3 weight % or more and about 1.5 weight % or less of Al, and about 0.1 weight % or less of Pb.
a steel plate containing about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % or more and about 0.3 weight % or less of Mn, about 0.01 weight % or more and about 0.1 weight % or less of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, about 0.005 weight % or less of O, about 0.005 weight % or less of N, and at least one of about 0.03 weight % or less of Ti or about 0.03 weight %
or less of Nb in the range in which C/12?Ti*/48 +
Nb/93?C/2; and an alloyed hot dip galvanized layer formed on said steel plate at a thickness of between about 25g/m2 and about 70 g/m2, said layer containing about 9 weight % or more and about 12 weight % or less of Fe, about 0.3 weight % or more and about 1.5 weight % or less of Al, and about 0.1 weight % or less of Pb.
4. An alloyed hot dip galvanized steel sheet comprising:
a steel plate containing about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % to about 0.3 weight % of Mn, 0.01 weight % to about 0.1 weight % of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, about 0.005 weight % or less of O, about 0.005 weight % or less of N, and at least one of about 0.03 weight % or less of Ti or about 0.03 weight % or less of Nb in the range in which C/12?Ti*/48 + Nb/93?C/2; and an alloyed hot dip galvanized layer formed on said steel plate having a thickness of between about 25g/m2 and about 70 g/m2, said layer containing about 9 weight % to about 12 weight % of Fe, about 0.3 weight % to about 1.5 weight % of Al, and about 0.1 weight % or less of Pb.
a steel plate containing about 0.0015 weight % or less of C, about 0.1 weight % or less of Si, about 0.03 weight % to about 0.3 weight % of Mn, 0.01 weight % to about 0.1 weight % of Al, about 0.01 weight % or less of P, about 0.005 weight % or less of S, about 0.005 weight % or less of O, about 0.005 weight % or less of N, and at least one of about 0.03 weight % or less of Ti or about 0.03 weight % or less of Nb in the range in which C/12?Ti*/48 + Nb/93?C/2; and an alloyed hot dip galvanized layer formed on said steel plate having a thickness of between about 25g/m2 and about 70 g/m2, said layer containing about 9 weight % to about 12 weight % of Fe, about 0.3 weight % to about 1.5 weight % of Al, and about 0.1 weight % or less of Pb.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP043122/93 | 1993-03-04 | ||
| JP04312293A JP3318385B2 (en) | 1993-03-04 | 1993-03-04 | Alloyed hot-dip galvanized steel sheet with excellent press workability and plating resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2116984A1 true CA2116984A1 (en) | 1994-09-05 |
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| CA002116984A Abandoned CA2116984A1 (en) | 1993-03-04 | 1994-03-04 | Alloyed hot dip galvanized steel sheet |
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|---|---|
| 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) |
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| BR0107195B1 (en) * | 2000-09-12 | 2011-04-05 | hot-dip steel plate with high tensile strength and method for producing it. | |
| WO2005021823A1 (en) * | 2003-08-29 | 2005-03-10 | Jfe Steel Corporation | 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 |
| 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 |
| 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 |
| KR101614230B1 (en) * | 2011-09-30 | 2016-04-20 | 신닛테츠스미킨 카부시키카이샤 | High-strength galvannealed steel sheet of high bake hardenability, high-strength alloyed galvannealed steel sheet, and method for manufacturing same |
| 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 |
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| 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
Also Published As
| Publication number | Publication date |
|---|---|
| EP0613961A1 (en) | 1994-09-07 |
| JP3318385B2 (en) | 2002-08-26 |
| JPH06256903A (en) | 1994-09-13 |
| CN1096060A (en) | 1994-12-07 |
| CN1125188C (en) | 2003-10-22 |
| TW380165B (en) | 2000-01-21 |
| DE69404338T2 (en) | 1997-11-13 |
| DE69404338D1 (en) | 1997-09-04 |
| KR100261522B1 (en) | 2000-07-15 |
| KR940021750A (en) | 1994-10-19 |
| EP0613961B1 (en) | 1997-07-23 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EEER | Examination request | ||
| FZDE | Discontinued |