AU2002309283B2 - High-strength Alloyed Aluminum-system Plated Steel Sheet and High-strength Automotive Part Excellent in Heat Resistance and After-painting Corrosion Resistance - Google Patents
High-strength Alloyed Aluminum-system Plated Steel Sheet and High-strength Automotive Part Excellent in Heat Resistance and After-painting Corrosion Resistance Download PDFInfo
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- AU2002309283B2 AU2002309283B2 AU2002309283A AU2002309283A AU2002309283B2 AU 2002309283 B2 AU2002309283 B2 AU 2002309283B2 AU 2002309283 A AU2002309283 A AU 2002309283A AU 2002309283 A AU2002309283 A AU 2002309283A AU 2002309283 B2 AU2002309283 B2 AU 2002309283B2
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- 229910000831 Steel Inorganic materials 0.000 claims description 292
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- 238000000034 method Methods 0.000 claims description 77
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- 238000004519 manufacturing process Methods 0.000 claims description 13
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- 238000012360 testing method Methods 0.000 description 12
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- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
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- -1 FeAl1 Substances 0.000 description 1
- 229910019142 PO4 Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- 229910009378 Zn Ca Inorganic materials 0.000 description 1
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- 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
- OXNIZHLAWKMVMX-UHFFFAOYSA-N picric acid Chemical compound OC1=C([N+]([O-])=O)C=C([N+]([O-])=O)C=C1[N+]([O-])=O OXNIZHLAWKMVMX-UHFFFAOYSA-N 0.000 description 1
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Classifications
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- 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
- C23C2/12—Aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
- C21D1/673—Quenching devices for die quenching
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
-
- 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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Crystallography & Structural Chemistry (AREA)
- Coating With Molten Metal (AREA)
Description
WO 02/103073 PCT/JP02/05978 1
DESCRIPTION
HIGH-STRENGTH ALLOYED ALUMINUM-SYSTEM PLATED STEEL SHEET AND HIGH-STRENGTH AUTOMOTIVE PART EXCELLENT IN HEAT RESISTANCE AND AFTER-PAINTING CORROSION RESISTANCE Technical Field The present invention relates to an alloyed aluminum-system plated steel sheet suitable for a member, which is produced by a high-temperature press and requires strength, as represented by a structural member for an automotive part, and a method of producing the same and, in particular, to a member which requires high strength such as an undercarriage component of an automobile or the like, and a steel material used for producing the same.
Background Art For pursuing the weight reduction of an automobile, originating from global environmental problems, a steel sheet used for an automobile is required to have the highest possible strength. However, in general, when the strengthening of a steel sheet is enhanced, elongation and an r-value are lowered and thus formability is deteriorated. Therefore, a steel sheet is desired to have high-strength, high formability and shape fixability simultaneously.
One solution to the problem is a TRIP (Transformation Induced Plasticity) steel produced by using the martensite transformation of retained austenite and the application of a TRIP steel is increasing recently. However, though it is possible to produce a li000 MPa class high-strength steel sheet excellent in formability using a TRIP steel, it is difficult to secure good formability in a higher-strength steel sheet, for example, an ultra-high-strength steel sheet having a WO 02/103073 PCT/JP02/05978 2 strength of not lower than 1,500 MPa. Moreover, it is difficult to solve the problem of the shape fixability by that technology.
To cope with the problems, there is a warm press technology which is a technology attracting attention recently as another means which reconciles high-strength and high formability. A technology of increasing strength by forming a steel sheet while warm and making use of the heat generated during the forming is disclosed in Japanese Unexamined Patent Publication No. 2000- 234153. This technology aims at increasing strength by controlling components in a steel appropriately, heating the steel sheet in the temperature range of ferrite and making use of the precipitation strengthening in the temperature range.
In Japanese Unexamined Patent Publication No. 2000- 87183, proposed is a high-strength steel sheet wherein the yield strength at a temperature during forming is decreased far lower than the yield strength at the room temperature, aiming at improving the accuracy of press forming. However, there may be a limitation in the strength obtained by this technology.
As a technology which overcomes this drawback, a technology of heating a steel sheet to the temperature range where austenite single phase is formed and then cooling it during press forming is disclosed in the literature (SAE, 2001-01-0078).
This is a technology of obtaining desired material properties by forming a steel sheet in the state of heating it to a high temperature of not lower than 800'C, by so doing, solving the forming problem of a highstrength steel sheet, and then quenching it in the cooling after forming. However, as the technology involves heating in the atmosphere, oxides are generated on the surface of a steel sheet and it is required to remove the oxides in a downstream process. A technology of applying aluminum plating for suppressing the WO 02/103073 PCT/JP02/05978 3 oxidation during heating is also disclosed in the aforementioned literature (SAE, 2001-01-0078).
As another means, a means of obtaining high strength by, after forming a steel sheet at the room temperature, heating rapidly and cooling rapidly a part of the steel sheet and thus quenching it can be adopted. In this case, by heating the steel sheet locally, it is possible to enhance the strength of only the portion where high strength is required. Japanese Unexamined Patent Publication No. 2000-83640 discloses such a technology and a steel sheet containing carbon at 0.15 to 0.5% is used therefor.
A hot forming technology and a technology of applying an aluminum plated steel sheet in the hot forming are disclosed in the aforementioned prior arts.
However, in the prior arts, when a steel sheet is heated to a high temperature of not lower than 800 0 C, Fe diffuses up to the surface for a short period of time and an aluminum plated layer changes to an intermetallic compound, hereinafter called "alloyed aluminum-system plated layer". Since the alloyed aluminum-system plated layer is very hard and brittle, sometimes it generates cracks and peels off in the state of powder, and therefore the deterioration of corrosion resistance after painting has been a concern. Even when cracks are not generated, there have been cases where an aluminum plated steel sheet is inferior to another surface treated steel sheet, for example, a hot-dip galvanized steel sheet or a hot-dip galvannealed steel sheet, in after-painting corrosion resistance. More specifically, after-painting corrosion resistance is evaluated after a forming at a high temperature and, when scratches, such as cutting in a cross shape, are provided, the corrosion of the base steel has been apt to propagate from the portion in the direction of the depth and to advance more than the case of a hot-dip galvanized or hot-dip galvannealed steel sheet of a sacrificial corrosion prevention type.
WO 02/103073 PCT/JP02/05978 4 -4- Further, there also is the possibility that the exfoliated plated layer piles up on dies and causes flaws during pressing. This is because, though the plated layer can withstand the working of a hot forming, it is practically difficult to work the whole part while it is hot and there is the problem of the plated layer being apt to peel off at the portion where the working has been delayed and the temperature has dropped. Another problem here is that, when the temperature drops, the base steel constitutes a hard structure mainly composed of martensite as a result of quenching, and therefore the stress is apt to escalate.
Disclosure of the Invention The present inventors conducted a basic study for solving the aforementioned problems, and found that a plated steel sheet excellent in after-painting corrosion resistance could be produced by applying an Fe-Al-system coating containing Mn and Cr of more than 0.1% in total on the surface of a steel sheet after a high temperature forming. An aluminum-system plated layer after being subjected to a hot forming and being rapidly heated locally is transformed into an alloyed aluminum-system plated layer up to its surface, and the compound is very brittle and thus tends to generate cracks during working.
The aluminum-system plated steel sheet defined in the present invention means a plated steel sheet having a plated layer composed of Al and Fe content of at least Further, since the layer has a nobler electric potential than the base steel sheet, the corrosion of the base steel is initiated starting from the cracks and after-painting corrosion resistance is apt to deteriorate. For avoiding the deterioration of the after-painting corrosion resistance, Mn addition to the alloyed aluminum-system plated layer is very effective.
Though the function of Mn is not clarified yet, it is said that Mn plays the roll of bringing the electric WO 02/103073 PCT/JP02/05978 5 potential of an Fe-Al-system plated layer close to that of the steel sheet by controlling the electric potential of the alloy layer, and, in addition to the function, there is also the possibility that Mn controls also the shape of phosphate crystals in a phosphating treatment which is a pre-painting treatment.
Extremely excellent heat resistance, in particular, heat resistance after working, can be obtained by specifying the amounts of C, Si, Mn, P, S and Al as base steel components and by adding Ti, Cr and Mo, which addition was effective, so as to satisfy the following equation 1: Ti 0.5xMn Cr 0.5xMo 0.4 1 It is estimated that those elements accelerate the diffusion between Al and Fe, and, by so doing, even when cracks are generated in a plated layer, the reaction between Fe and Al proceeds from the circumference of the cracks and therefore the base steel is hardly exposed.
Further, the present inventors also obtained the knowledge that, by adding N, Nb, V, Ni, Cu, B, Sn and Sb as steel components, further excellent after-painting corrosion resistance could be obtained.
In the meantime, it is advantageous for a plated layer after alloying treatment to contain Si further, and furthermore, better corrosion resistance is obtained by adding Zn, Mg, etc. It is important that Al content in an alloy layer is not more than 35% in view of suppressing cracks in the alloy layer. Further, it is desirable that the thickness of an Fe-Al-system alloy layer is 3 to 35 Vm from the viewpoint of after-painting corrosion resistance.
Further, for overcoming the above-mentioned problems, the present inventors studied in detail the factors influencing the workability of an aluminum-system plated steel sheet after alloying treatment, and obtained WO 02/103073 PCT/JP02/05978 6 the following knowledge. That is, since both an alloyed aluminum-system plated layer and a base steel are hard, the internal stress increases, but, since a soft layer exists between the alloyed aluminum-system plated layer and the base steel, the stress is mitigated and therefore exfoliation resistance is improved markedly. The soft layer is composed of a ferrite phase, and it is estimated that the fact that the thickness of the soft layer is not less than 1 Rm prevents the cracks in the alloyed layer propagating up to the base steel.
In addition, for overcoming the above-mentioned problems, the present inventors studied in detail the factors influencing the workability of an aluminum-system plated steel sheet after alloying treatment, and obtained the following knowledge. That is, it is possible to prevent the exfoliation of a plated layer by optimizing the heating conditions. The reason is not clear but it is estimated that a plated layer is alloyed according to heating conditions, the phase structure changes complicatedly, and there is an appropriate phase structure for securing workability. The gist of the present invention is as follows: A high-strength alloyed aluminum-system plated steel sheet excellent in after-painting corrosion resistance, characterized by having an Fe-Al-system coating containing Mn and Cr of more than 0.1% in total on the surface of the steel sheet.
A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and afterpainting corrosion resistance, characterized by having an Fe-Al-system coating containing, in mass, Mn and Cr of more than 0.i% in total on the surface of the steel containing, in mass, C: 0.05 to Si: 0.05 to Mn: 0.5 to P: not more than S: not more than 0.1% and Al: not more than and, in addition, one or more element(s) selected from among Ti: 0.01 to Cr: not WO 02/103073 PCT/JP02/05978 7 more than 3% and Mo: not more than so as to satisfy the following equation 1: Ti 0.5xMn Cr 0.5xMo 0.4 1 A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and afterpainting corrosion resistance according to the item characterized in that the steel further contains, in mass, one or more element(s) selected from among N: not more than Nb: not more than V: not more than Ni: not more than Cu: not more than B: 0.0003 to 0.03%, Sn: not more than 0.1% and Sb: not more than 0.1%.
A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and afterpainting corrosion resistance according to the item characterized in that the steel contains, in mass, C: 0.15 to 0.55%, Si: not more than Mn: 0.2 to P: not more than S: not more than 0.04%, Al: 0.01 to 0.1% and N: not more than 0.01%, and also one or more element(s) selected from among B: 0.0002 to 0.0050%, Ti: 0.01 to Cr: not more than Mo: not more than 1%, Ni: not more than Cu: not more than 0.5% and Sn: not more than 0.2%.
A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and afterpainting corrosion resistance according to any one of the items to characterized in that the Fe-Al-system coating further contains Si of 1 to An alloyed aluminum-system plated steel sheet for high-strength automotive members according to any one of the items to characterized in that Al concentration in the Fe-Al-system coating layer is not more than 35% in weight.
O
A high-strength alloyed aluminum-system plated steel sheet excellent in heat Sresistance and after-painting corrosion resistance according to any one of the items to 00 characterized in that the Fe-Al-system coating further contains either one or both of O Zn: 1 to 50% and Mg: 0.1 to 5 An alloyed high-strength aluminum-system plated steel sheet excellent in heat e¢3 00 resistance and after-painting corrosion resistance according to any one of the items to characterized in that the thickness of the Fe-Al-system coating layer is 3 to 35 Ctm.
Cc A high strength alloyed aluminum-system plated steel sheet according to any one of the items 1-8, wherein a coating layer mainly composed of Fe-A1 on the surface of 10 the steel sheet; a ferrite layer having a thickness from not less than 2 /m to not more than one tenth of the steel sheet thickness at the underside of the coating layer; and the base steel mainly composed of martensite at the underside of the ferrite layer.
An alloyed aluminum-system plated steel sheet for high-strength automotive members according to the item characterized in that the alloyed aluminum-system plated layer on the surface of the steel sheet and the ferrite layer at the underside of the intermetallic compound layer contain Si.
(11) An alloyed aluminum-system plated steel sheet for high-strength automotive members according to the item or characterized in that the hardness of the ferrite phase is not higher than 200.
(12) A high-strength automotive part formed by press forming, at least a portion of which is composed of a steel according to any one of the items to (11).
(13) A high-strength automotive part according to the item characterized by having a coated film 1 to 200 jm in thickness on at least a part of the surface.
(14) A method for producing an automotive part according to item 13, comprising the steps of; plating an aluminum-system coating on a steel sheet containing C of not less than 0.05 wt%, heating the plated steel sheet for a longer time period than the following regions, A, B, C and D, wherein A is (800 0 C x 13 min), B is (900 0 C x 6 min), C is (1050C x 1.5 min) and D is (1200 0 C x 0.3 min), hot pressing the heated plated steel sheet, and cooling the hot pressed plated steel sheet with a cooling rate of not lower than 1 OO0C/sec.
[R:\LIBZZ]658812speci.doc:GYM cBrief Description of the Drawings Fig. 1 is a graph showing the influence of the total amount of Mn and Cr in an 00 alloyed aluminum-system plated layer on an after-painting corrosion resistance.
o Fig. 2 is a graph showing the relation between the addition amount of Ni, Cu and Sn and bare corrosion resistance.
00 Fig. 3 is a graph showing the relation between the addition of Ni, Cu and Sn and 0after-painting corrosion resistance.
r< Fig. 4 is a graph showing the relation between the addition amount of Cr and Mo Sand bare corrosion resistance.
C1 to Fig. 5 is a graph showing the relation between the addition amount of Cr and Mo and after-painting corrosion resistance.
Fig. 6 is the Fe-Al-Si-system ternary phase diagram rR:\LIBZZj65881 2speci.doc:GYM WO 02/103073 PCT/JP02/05978 10 at the temperature of 950 0
C.
Fig. 7 is a photograph (back scattered election image) showing an example of structures according to the present invention, taken by an optical microscope.
Fig. 8 is a graph showing the relation between the thickness of an outer layer and the workability of a plated layer.
Fig. 9 is a photograph (back scattered electron image) showing an example of metallic structures according to the present invention, taken by a microscope.
Fig. 10 is a view showing a shape obtained by forming a steel sheet according to the present invention.
Fig. 11 is a graph showing the relation between a heating time and a heating temperature according to the present invention.
Best Mode for Carrying out the Invention Embodiment 1 Chemical compositions of steel sheets used in the present invention will be explained hereunder.
C: A steel sheet according to the present invention has a high-strength of not lower than 1,000 MPa after forming and is obtained by rapidly cooling it after a high temperature press and thus transforming the structure thereof into a structure mainly composed of martensite. In that sense, a C content of not less than 0.05% is desirable, and, for obtaining a high-strength stably, the content of not less than 0.1% is more desirable. On the other hand, even though C content is increased to not less than the strength is saturated and also weld cracking tends to be generated, and therefore the upper limit is set at 0.7%.
Si: Since too low an Si content causes fatigue property to deteriorate, the addition amount of not less than 0.05% is desirable. However, Si is also an element which forms a stable oxide film on the surface of a steel WO 02/103073 PCT/JP02/05978 11 sheet during recrystallizing annealing and hinders aluminum plating properties. For that reason, the upper limit of Si is set at 1%.
Mn: Mn is well known as an element which enhances the hardenability of a steel sheet. Also, Mn is an element which is necessary for preventing hot embrittlement caused by S which is an unavoidable impurity. For that reason, the addition amount of not less than 0.5% is preferable. Further, Mn also enhances heat resistance after aluminum plating. However, since Mn addition amount exceeding 3% causes the impact property after quenching to deteriorate, the value is determined to be the upper limit.
Ti: Ti affects the heat resistance of an aluminum plated layer most. In the case where a steel sheet is used in such a temperature range as exceeding 900 0 C, as is the case of the present invention, Ti addition is preferable from the viewpoint of heat resistance, and an addition amount of not less than 0.01% is desirable for achieving the effect. However, since Ti forms TiC with C and decreases the amount of C which contributes to strength, it is necessary to increase C amount corresponding to the Ti addition amount. Further, the effect of Ti is saturated in the amount of about 0.8%, and therefore this value is determined to be the upper limit.
Cr: Cr, like Mn and Ti, contribute to the improvement of the heat resistance after aluminum plating. However, Mn deteriorates aluminum plating properties by forming a stable oxide film on the surface of a steel sheet, in the same way as Si. Further, Cr is a relatively expensive element, and therefore the upper limit is set at 3% when it is added.
Mo: Mo, like Mn, Ti and Cr, also contributes to the improvement of the heat resistance after aluminum plating and its addition is desirable. However, since Mo is a relatively expensive element and the effect is saturated, WO 02/103073 PCT/JP02/05978 12 the upper limit is set at 1%.
In the present invention, it is preferable to add the elements which improve the heat resistance after aluminum plating, such as Ti, Mn, Cr and Mo, in a manner of satisfying the following expression: Ti+0.5xMn+Cr+0.5xMo 0.4.
In particular, Ti and Cr have an effect against the exfoliation of a plated layer during heating. Further, Mn may be added relatively abundantly and greatly contributes to heat resistance.
The present invention prescribes that P, S and Al are further added in a steel. However, since P and Al deteriorate the ductility and fatigue strength of a steel and S deteriorates toughness thereof, an upper limit is determined for each of them. In addition, one or more of Ni, Nb, V, N, Cu, B, Sn and Sb can be contained in a steel as occasion demands. Ni and Cu contribute to the corrosion resistance of a steel and B improves hardenability.
On many occasions, a steel sheet is used after an aluminum plated layer is alloyed and then it is painted.
On those occasions, after-painting corrosion resistance is affected by the amounts of Mn and Cr in an alloyed aluminum-system plated layer. When the amount of these elements is not less than good after-painting corrosion resistance is obtained. As the methods of adding Mn and Cr, there are a method of diffusing steel components and a method of adding them in a plating bath, and either of the methods can achieve the effect as long as the addition amount is not less than It is known that one to five phases can coexist in an alloyed aluminum-system plated layer depending on the deposit amount of plating, the steel composition, the heating conditions and the like. Since the influence of phases in the vicinity of a surface is particularly large, when analyzing them, it is preferable to judge by measuring them at about 5 portions on a cross-section in the region WO 02/103073 PCT/JP02/05978 13 within 5 [m in depth from the surface using a means such as the EPMA quantitative analysis or the like, and by calculating the average thereof. As is stated later, in case of hot dip aluminum plating, it is common to add Si and, at that time, Si is further contained in the alloyed aluminum-system plated layer. The amount is about 1 to and the Si amount in the alloyed aluminum-system plated layer of one to five phases may vary considerably.
Though an Fe-Al-system coating of one to five phases can have various compositions, such as an Fe-Al-Si-system alloyed aluminum-system plated layer, Fe 2 Al 5 FeA1 3 Fe 3 Al, FeAl, Al dissolved ferrite, or the like, in any of the compositions, stable after-painting corrosion resistance can be obtained as long as the total amount of Mn and Cr is not less than With regard to which phase should be analyzed when a plurality of phases exist, since the knowledge that Mn and Cr contribute to the improvement of after-painting corrosion resistance was obtained and the corrosion phenomenon is a macroscopic phenomenon, the present inventors think that; general information can be obtained by analyzing them at about 5 portions at random, even when a plurality of phases exist, and calculating the average thereof and, by so doing, the judgement can be made. Further, it is prescribed that a cross-section is etched with nitral of 2 to 3% for observing the cross-section of a structure after heating. This is because the interface between a base metal and Al dissolved ferrite, which is formed particularly when the heating time is longer, cannot be observed without etching.
The deposit amount of aluminum plating affects corrosion resistance, weldability, workability and the like. If the deposit amount is too small, after-painting corrosion resistance is insufficient, and if it is too large, weldability and workability deteriorate. With regard to workability, it is because a brittle alloyed aluminum-system plated layer tends to peel off during the WO 02/103073 PCT/JP02/05978 14 press after heating.
A method of aluminum plating is not specifically restricted, and the hot dip plating method, the electroplating method, the vacuum deposition method, the clad method or the like can be employed. The method most widely employed industrially at present is the hot dip plating method, and usually AI-10%Si is frequently used in a plating bath and Fe is contained therein as an unavoidable impurity. It was already described before that, in addition to those, the addition of Cr and Mn improves after-painting corrosion resistance. As other additional elements, Mg, Ti, Zn, Sb, Sn, Cu, Ni, Co, In, Bi, misch metal, etc. are nominated, and those elements may be applied as long as the plated layer is mainly composed of Al.
The present invention does not specifically define a pre-treatment and a post-treatment of aluminum plating.
As a plating pre-treatment, a pre-plating of Ni, Cu, Cr, or Fe, or the like is nominated, and any of those can be adopted. As a plating post-treatment, a chromate treatment, a resin coating treatment or the like is nominated aiming at primary rust prevention and lubricity, but an organic resin is not preferable because it disappears when heated. With regard to a chromate treatment, considering the recent regulation against hexavalent chrome, a treatment film containing trivalent chrome, such as electrolytic chromate or the like, is preferable. Another post-treatment other than an inorganic-system chromate treatment can be applied. It is also possible to apply a treatment of alumina, silica, MoS 2 or the like, beforehand, aiming at lubricity.
Embodiment 2 The reason why the steel components are regulated in Embodiment 2 according to the present invention will be described hereunder.
N is an element unavoidably included and is not WO 02/103073 PCT/JP02/05978 15 specifically prescribed when B is not added, but, when B is added and the amount is excessively large, the addition amount of Ti must be increased. As a result, there is a problem that the amount of resultantly generated TiN increases and hot cracking occurs, and that costs increase also. Therefore, the upper limit is set at 0.1%.
B is added for enhancing hardenability at cooling during or after press forming, and, for achieving the effect, the addition of not less than 0.0002% is necessary. However, when the addition amount is excessive, there is a problem of hot cracking and the effect is saturated. Therefore, the upper limit is set at 0.03%.
Ni, Cu and Sn have the effect of changing the state of surface cracking during press forming after high temperature heating by changing the state of alloying an aluminum plated layer during the high temperature heating, and are important since they lead to an improvement of after-painting corrosion resistance of a formed product. With regard to those elements, from the results shown in Figs. 2 and 3 which were obtained by measuring the addition amounts of Ni, Cu and Sn, and bare corrosion resistance and after-painting corrosion resistance of the samples after high temperature forming in a laboratory test, the present inventors found that, for obtaining above-mentioned effects, Ni, Cu and Sn had to be added so that they might satisfy the equation 3.
Here, the bare corrosion resistance and the afterpainting corrosion resistance were evaluated by the method examined under the conditions shown in Example, using samples taken from the portions to which working was applied after high temperature forming.
(Ni+0.5xCu+3xSn) 0.012 3 With regard to each of Ni, Cu and Sn, an excessive addition of Ni makes the effects saturated and causes a WO 02/103073 PCT/JP02/05978 16 cost increase, Cu and Sn have the problem of generating surface cracking and, therefore, the upper limit of each element is set at 1% and respectively.
The production conditions of a steel sheet according to the present invention is not specifically prescribed, but preferable production conditions will be explained hereunder.
A steel having components as described above was cast, and the obtained hot slab, directly or after heated, or the slab once cooled and reheated, was hotrolled. Here, the difference in the properties of the steel between the direct rolling of the hot slab and the rolling after reheating is scarcely recognized. Further, the reheating temperature is not specified, but it is preferable to regulate it in the range from 1,000 to 1,300 0 C, taking productivity into consideration.
With regard to hot-rolling, either a regular hotrolling process or a continuous hot-rolling process wherein slabs are connected with each other and rolled at the finish rolling can be adopted. It is preferable to control the finishing temperature at the hot-rolling to not lower than Ar3 transformation temperature taking the productivity and the accuracy of the sheet thickness into consideration.
The cooling after hot-rolling is carried out by a usual method. In that case, it is preferable to control the coiling temperature to not lower than 550 0 C from the viewpoint of productivity. On the other hand, if the coiling temperature is too high, pickling capability deteriorates, and therefore it is preferable to control the coiling temperature to not higher than 750 0
C.
For a pickling process or a cold-rolling process, a usual method may be employed, and, for a subsequent aluminum plating process or a subsequent aluminum-zinc plating process, a usual method may be employed too.
That is, in case of an aluminum plating process, Si concentration of 5 to 12% in a plating bath is WO 02/103073 PCT/JP02/05978 17 appropriate, and, in case of an aluminum-zinc plating process, Zn concentration of 40 to 50% in a plating bath is appropriate.
Here, with regard to the atmosphere in a plating process, plating can be carried out using either a continuous plating equipment having a non-oxidizing furnace or a continuous plating equipment not having a non-oxidizing furnace as long as usual conditions are preserved. Therefore, no specific control is required in the production of a product according to the present invention and thus the productivity is not hindered.
In the above production conditions, metal preplating is not applied to the surface of a steel sheet before plating, but no specific problem arises even when Ni pre-plating, Fe pre-plating, or another metal preplating which improves plating properties is employed.
Further, even when Mg and Zn are included in an aluminum plated layer or Mg is included in an aluminumzinc plated layer, no specific problem occurs and a steel sheet having similar properties can be produced.
Embodiment 3 Firstly, the reason why the steel components are regulated in Embodiment 3 according to the present invention will be described hereunder.
C is an element which is added for making a structure after cooling composed of martensite and securing material quality, and the addition amount of not less than 0.15% is required for securing a strength of not lower than 1,200 MPa. On the other hand, if the addition amount is excessive, the strength against impact deformation is hardly secured and, therefore, the upper limit is set at 0.55%.
Si is a solute strengthening element and can increase the strength of a steel sheet at a relatively low cost. However, if it is added excessively, plating properties are deteriorated, and therefore the upper WO 02/103073 PCT/JP02/05978 18 limit is set at Mn is added for making it possible to secure the strength after cooling in a wide range of cooling rates.
When the C amount is large but the addition amount of Mn is small, a martensite structure cannot be obtained in a usual range of cooling rate, which range can be obtained during press forming, and therefore the strength is hardly secured. The range of cooling rates cited here is not higher than 500 0 C/sec. in the case of the sheet thickness of 1.4 mm. To demonstrate such function, the addition amount of not less than 0.2% is required. On the other hand, if the Mn amount is too large, not only the cost increases but also the effect is saturated.
Therefore, the upper limit is set at 3%.
S is an element which is included unavoidably and causes the deterioration of workability. Therefore, it is necessary to decrease the amount as much as possible.
By decreasing the amount to not more than 0.04%, the problem of the workability is eliminated and therefore the range is determined to be not more than 0.04%.
P is a solute strengthening element and can increase the strength of a steel sheet at a relatively low cost.
However, if the addition amount increases too much, cracks are generated during hot-rolling or cold-rolling caused by the embrittlement, and therefore the upper limit is set at 0.1%.
Al is used as a deoxidizing agent and, for demonstrating the effect, an Al content of not less than 0.005% in a steel is required. On the other hand, the addition amount exceeding 0.1% causes the increase of oxide-system inclusions and a problem of the deterioration of surface quality, and therefore the upper limit is set at 0.10%.
Cr and Mo have the effect of changing the state of surface cracking during press forming after a high temperature heating by changing the state of alloying an aluminum plated layer during the high temperature WO 02/103073 PCT/JP02/05978 19 heating, and are important since they lead to the improvement of after-painting corrosion resistance of a formed product. With regard to those elements, from the results shown in Figs. 2 and 3, which were obtained by measuring the addition amounts of Cr and Mo, and bare corrosion resistance and after-painting corrosion resistance of the samples after high temperature forming in a laboratory test, the present inventors found that Cr and Mo had to be added. Here, the bare corrosion resistance and the after-painting corrosion resistance were evaluated by the method examined under the conditions shown in Example, using samples taken from the portions to which working was applied after high temperature forming.
With regard to each of Cr and Mo, an excessive addition of Cr causes problems in plating properties and cost increase and Mo makes the effects saturated and causes cost increase. Therefore, the upper limit of each element is set at 2.0% and respectively.
Other components are not specifically prescribed.
Ni is included unavoidably, and, if the amount is within the usual range, no problem arises.
The production conditions of a steel sheet according to the present invention are not specifically prescribed, but preferable production conditions will be explained hereunder.
A steel having components as described above was cast, and the obtained hot slab, directly or after being heated, or the slab once cooled and reheated, was hotrolled. Here, the difference in the properties of the steel between the direct rolling of the hot slab and the rolling after reheating is scarcely recognized. Further, the reheating temperature is not specified, but it is preferable to regulate it in the range from 1,000 to 1,300 0 C taking the productivity into consideration.
With regard to hot-rolling, either a regular hotrolling process or a continuous hot-rolling process WO 02/103073 PCT/JP02/05978 20 wherein slabs are connected with each other and rolled at the finish rolling can be adopted. It is preferable to control the finishing temperature at the hot-rolling to not lower than Ar3 transformation temperature taking the productivity and the accuracy of the sheet thickness into consideration.
The cooling after hot-rolling is carried out by a usual method. In that case, it is preferable to control the coiling temperature to not lower than 550cC from the viewpoint of productivity. On the other hand, if the coiling temperature is too high, pickling capability deteriorates, and therefore it is preferable to control the coiling temperature to not higher than 750 0
C.
For a pickling process or a cold-rolling process, a usual method may be employed, and, for a subsequent aluminum plating process or a subsequent aluminum-zinc plating process, a usual method may be employed too.
That is, in case of an aluminum plating process, Si concentration of 5 to 12% in a plating bath is appropriate and, in case of an aluminum-zinc plating process, Zn concentration of 40 to 50% in a plating bath is appropriate.
Here, with regard to the atmosphere in a plating process, plating can be carried out using either a continuous plating equipment having a non-oxidizing furnace or a continuous plating equipment not having a non-oxidizing furnace as long as usual conditions are preserved. Therefore, no specific control is required in the production of a product according to the present invention and thus the productivity is not hindered.
In the above production conditions, metal preplating is not applied to the surface of a steel sheet before plating, but no specific problem arises even when Ni pre-plating, Fe pre-plating, or another metal preplating which improves plating properties is employed.
Further, even when Mg and Zn are included in an aluminum plated layer or Mg is included in an aluminum-zinc plated WO 02/103073 PCT/JP02/05978 21 layer, no specific problem occurs and a steel sheet having similar properties can be produced.
Embodiment 4 By heating an aluminum plated layer and thus converting it into an alloy layer, namely an Fe-Al-system coating layer, and also by controlling the Al amount to not more than 35% and thus converting the Fe-Al-system coating layer into Fe+Fe 3 Al wherein Al and Si are dissolved, obtained are far more excellent workability and corrosion resistance at a portion which is subjected to working than those of a plated layer which contains other phases than Fe+Fe 3 Al.
C: A steel sheet according to the present invention has a high-strength of not lower than 1,000 MPa after forming and is obtained by rapidly cooling it after a hot press and thus transforming the structure thereof into a structure mainly composed of martensite. To do so, a C content of not less than 0.05% is necessary. On the other hand, even though the C content is increased to not less than the strength is saturated and also weld cracking tends to be generated, and therefore the upper limit is set at 0.7%.
Steel components except C are not specifically prescribed, but elements such as Si, Mn, P, Al, N, Cr, Mo, Ti, Nb, B, Ni, Cu, V, Sn, Sb, etc., are nominated as addition elements or unavoidable impurity elements.
Those elements may be added as occasion demands.
Examples are: Mn and B are effective in hardenability; Cr, Ti and Mo are effective in the heat resistance of an aluminum plated layer; and Ni and Cu improve corrosion resistance. The desirable ranges of their addition are Mn: 0.5 to Si: not more than P: not more than S: not more than Al: not more than N: not more than 0.01%, Cr: not more than Mo: not more than Ti: not more than Nb: not more than B: not more than 0.05%, Ni: not more than Cu: WO 02/103073 PCT/JP02/05978 22 not more than V: not more than Sn: not more than 0.1% and Sb; not more than 0.1%.
As stated above, the smaller the deposit amount of aluminum plating is, the more easily an Fe+Fe 3 Al region is formed. In that sense, it is desirable that the deposit amount is not more than 120 g/m 2 per both sides.
A method of aluminum plating is not specifically restricted, and the hot dip plating method, the electroplating method, the vacuum deposition method, the clad method or the like can be employed. The method most widely employed industrially at present is the hot dip plating method, and usually Al-10%Si is frequently used in a plating bath and Fe is contained therein as an unavoidable impurity. In this case, Si enters into an alloy layer after heating and the Si amount may vary depending on the phase structure. However, the Si amount in the Fe+Fe.Al region is not more than 15% and therefore the value is determined to be the upper limit of Si. As other additional elements, Mn, Cr, Mg, Ti, Zn, Sb, Sn, Cu, Ni, Co, In, Bi, misch metal, etc. are nominated, and those elements may be applied as long as the plated layer is mainly composed of Al. The addition of Zn and Mg is effective in making red rust hardly generated. However, the excessive addition of those elements, whose vapor pressures are high, causes the generation of fumes containing Zn and Mg, the generation of powdery substances on the surface caused by Zn and Mg, and the like. Therefore, a Zn addition of not less than 60% and a Mg addition of not less than 10% are not desirable.
The present invention does not specifically define a pre-treatment and a post-treatment of aluminum plating.
As a plating pre-treatment, a pre-plating of Ni, Cu, Cr, or Fe, or the like is nominated, and any of these can be adopted. As a plating post-treatment, a chromate treatment, a resin coating treatment or the like is nominated aiming at primary rust prevention and lubricity, but an organic resin is not preferable because WO 02/103073 PCT/JP02/05978 23 it disappears when heated. With regard to a chromate treatment, considering the recent regulation against hexavalent chrome, a treatment film containing trivalent chrome, such as electrolytic chromate or the like, is preferable. Another post-treatment other than an inorganic-system chromate treatment can be applied. It is also possible to apply a treatment of alumina, silica, MoS 2 or the like beforehand aiming at lubricity.
Embodiment In Embodiment 5, the restriction of the composition of an aluminum-system plated layer will be explained.
The aluminum-system plated layer cited here means a plated layer which is not heated yet and thus not alloyed yet.
Si: Si is effective in decreasing the thickness of an alloy layer (a layer composed of an intermetallic compound formed at an interface between a plated layer and a steel sheet) of aluminum-system plating. Further, Si forms Mg 2 Si by adding Mg complexly and is effective in improving corrosion resistance. To enjoy the effects, the addition of not less than 1% is effective. An excessive addition of Si causes the rise of a melting point and, when Si single phase crystallizes at the plated layer, it causes the deterioration of corrosion resistance. Therefore, the upper limit is set at Mg: It is known that Mg is effective in improving corrosion resistance particularly under a salt damage environment. By forming Mg 2 Si particularly, a emission efficiency into an environment is increased and corrosion resistance is improved. For securing corrosion resistance, a Mg amount of not less than 0.5% is added.
Since an excessive addition causes fierce oxidation at the surface of a plating bath and a rise in the melting point of the plating bath, the addition amount is determined to be not more than 10%. For suppressing the oxidation of the surface of a plating bath, the addition WO 02/103073 PCT/JP02/05978 24 of a small amount of Ca (not more than is effective, and about this amount of Ca may be added.
Zn: Zn has an electric potential more basic than that of Al or steel and a function of suppressing the corrosion of a base steel. The effects begin to appear when Zn addition amount is not less than 1% and the best properties are obtained when Zn amount is 20 to However, with the addition amount exceeding corrosion resistance is rather deteriorated. Therefore, the lower limit and the upper limit of Zn amount are set at 1% and 60%, respectively.
When a part is practically produced using an aluminum-system plated steel sheet according to the present invention, quenching is carried out by rapidly cooling the part with the dies after press, and thus the structure is mainly composed of martensite. For securing a sufficient strength as a member, the percentage of martensite is determined to be not less than 60% in volume. Here, the percentage of martensite is calculated by polishing and etching a specimen and, after that, observing it with an optical microscope and using image analysis.
Embodiment 6 The reason why the components of a steel sheet and the like are regulated in Embodiment 6 will be described hereunder.
A steel sheet according to the present invention has a soft ferrite layer having a thickness from not less than 2 iim to not more than one tenth of a steel sheet thickness at the interface between an intermetallic compound layer formed by alloying an aluminum plated layer and a base steel mainly composed of martensite.
Usually, Al of about 1 to 10% exists in the ferrite layer. The ferrite phase can also contain Si, in addition to Al. The thickness is limited to not less WO 02/103073 PCT/JP02/05978 25 than 1 tm. The reason is that, if the thickness of the soft ferrite layer is not more than the above thickness, the exfoliation resistance of the plated layer is not sufficiently obtained. On the other hand, this layer is soft and, if it is too thick, the strength of the whole steel sheet is deteriorated. For that reason, the upper limit is determined to be not more than one tenth of the steel sheet thickness. Usually, an aluminum plated steel sheet is often produced by the hot dip plating method, and, in this case, an alloyed aluminum-system plated layer (called "alloy layer") at the interface between the steel sheet and the plated layer tends to grow. If the layer grows excessively, the workability of the steel sheet is deteriorated and, therefore, the aluminum plated steel sheet is produced in a plating bath wherein Si of about 10% is added. In the present invention, as an aluminum plated steel sheet is worked in the hot after the whole plated layer is alloyed by heating, Si is not necessarily required to be added in the plating bath, but there is no specific problem even when Si is added.
In the present invention, it is desirable that the hardness of a ferrite layer is not higher than 200 in terms of Vickers hardness. As stated above, the layer plays a role of preventing a hard alloy layer from peeling off during working. For that reason, it is preferable that the layer is soft. However, as the layer contains solute strengthening elements such as Al, Si, etc., it is harder than a usual ferrite layer.
Next, other components related to the present invention will be described hereunder. Firstly, with regard to steel components, as the present invention aims at a high-strength region which cannot be obtained with a regular TRIP steel or the like and the enhancement of strength by quenching, it is desirable that C amount is not less than 0.05%, preferably not less than With regard to other elements in a steel, the elements of Sii Mn, Ti, B, Cr, Mo, Al, P, S, N, etc. are used usually.
WO 02/103073 PCT/JP02/05978 26 Si is effective in fatigue property, and Mn and B contribute to the improvement of hardenability. Ti, Si, Cr, Mo and Al are elements which improve heat resistance after aluminum plating.
With regard to the construction of an aluminum plated layer, an aluminum plated layer is mainly composed of Al and may contain Si as stated above. As other addition elements, Cr, Mg, Ti, Sb, Sn, Zn, etc. are nominated, and those are applicable as long as the plated layer is mainly composed of Al. However, Zn has a low boiling point and, when added excessively, Zn generates zinc powder on the surface during heating and that causes galling during pressing. Therefore, the addition amount of not less than 60% is not desirable.
FeAl 3 Fe 2 Al 5 Fe 3 Al, Fe 2 AlSi, etc. are generated as an element of the alloyed aluminum-system plated layer.
Those phases tend to form a multi-layered structure in a laminar manner, but the structures of the phases are not specifically regulated. When the composition is mainly composed of Al and Fe, and Si is added in an aluminum plating bath, Si of about 5 to 10% is contained. Those elements account for not less than 90% of the composition in total. Further, a small amount of not-alloyed Al may remain, but it does not affect the properties of an aluminum plated steel sheet as long as the amount is small.
The thickness of a ferrite layer is measured with an optical microscope. The thickness of a ferrite layer is clearly observed by polishing a cross-section and, after that, etching it with nital at about However, there is a case where the boundary with an intermetallic compound layer is hardly observed, and, in that case, EPMA analysis is additionally adopted. By so doing, a ferrite layer can easily be identified from the difference between the radiation strength of Fe and that of Al. It is determined that the measurement of the thickness of a ferrite layer is carried out by measuring WO 02/103073 PCT/JP02/05978 27 the thickness at about 5 portions at random and calculating the average value. Further, a base steel consists of a structure mainly composed of martensite, and the structure can be observed, for example, by etching it with picral and using an optical microscope.
Fig. 7 shows an example of structures according to the present invention. Two layers are recognized at the interface, and, as a result of quantitative analysis with an EPMA, the lower layer is a ferrite layer about 5 pm in thickness. Here, in Fig. 7, the reference numeral 1 shows the layer composed of Al: 26.85%, Si: 9.83%, Fe: 59.92%; the reference numeral 2 the layer composed of Al: 49.54%, Si: 3.11%, Fe: 44.89%; the reference numeral 3 the layer composed of Al: 30.75%, Si: 8.88%, Fe: 56.91%; and the reference numeral 4 the layer composed of Al: 9.59%, Si: 2.92%, Fe: 84.02%.
Finally, with regard to the heating and cooling conditions of a plated steel sheet, a method of heating and cooling is not specifically defined. For obtaining a hardened structure, a cooling rate affects it largely as a matter of course, and a cooling rate of not lower than about 30 0 C/sec. is desirable. This depends on steel components, and, in case of a steel having good hardenability, a desired structure mainly composed of martensite can be obtained even at a cooling rate of about 10 0 C/sec., or, in another case, a cooling rate of not lower than 100 0 C/sec. is required depending on a steel grade. For obtaining a desired thickness of a ferrite layer, the optimization of heating conditions is required.
Embodiment 7 The reason why the components of a steel sheet and the like are regulated in Embodiment 7 will be described hereunder.
The present invention is a high-strength steel sheet having a high-strength of not lower than about 1,000 MPa WO 02/103073 PCT/JP02/05978 28 after forming, and is the steel sheet obtained by rapidly cooling it after it is subjected to hot press or partial rapid heating, thus quenching it and, by so doing, transforming it into a structure mainly composed of martensite. Therefore, the hardness of a base steel is determined to be not lower than 250. The hardness is measured in terms of Vickers hardness. For obtaining the hardness, a C amount of 0.05% is desirable. With regard to other elements in a steel, no specific restriction is determined, but the elements of Si, Mn, Ti, B, Cr, Mo, Al, P, S, N, etc. are used usually. Si is effective in fatigue property, and Mn and B contribute to the improvement of hardenability. Ti, Si, Cr, Mo and Al are elements which improve heat resistance after aluminum plating.
Further, in the present invention, a steel sheet has an alloyed aluminum-system plated layer mainly composed of Al and Fe on the surface of the base steel and the thickness of the alloyed aluminum-system plated layer is limited to 3 to 35 pm, preferably 3 to 18 [im. The restriction is determined considering the balance among weldability, after-painting corrosion resistance and heat resistance, as described above. That is, when the thickness of a layer is less than 3 tm, sufficient afterpainting corrosion resistance and heat resistance cannot be obtained. In case of not adding Si to an aluminum plated layer in particular, the deterioration of heat resistance is remarkable. The upper limit of the thickness is determined by spot weldability. A spot weldability (electrode life) identical with a galvanized steel sheet can be obtained when the plating thickness is not more than 35 Vm, and a spot weldability identical with a hot dip alloyed zinc-coated steel sheet can be obtained when the plating thickness is not more than 18 Am. FeA1 3 Fe 2 Al 5 Fe 3 A1, Fe 2 A1lSi, etc. can be formed as alloyed layers. Further, the formation of a ferrite WO 02/103073 PCT/JP02/05978 29 layer containing Al is recognized very often at the interface between the alloyed layer and the base steel.
Usually, in an aluminum plated steel sheet, an Fe- Al-system ally layer tends to grow and deteriorate workability. Therefore, it often happens that Si is added for suppressing the growth of the alloy layer and improving workability. In case of hot press, since a steel sheet is worked in the hot after the aluminum plated layer is heated and alloyed up to the surface, Si is not particularly required to be added. However, Si may be added as a matter of course. In case of rapidly heating a part of a steel sheet, since working is applied at the room temperature, Si addition is indispensable.
Cr, Mg, Ti, Sb, Sn, Zn, etc. are nominated as other addition elements in an aluminum plated layer, and those elements are applicable as long as the plated layer is mainly composed of Al. However, Zn has a low boiling point and, when added excessively, Zn generates zinc powder on the surface during heating and that causes galling during press. Therefore, the addition amount of not less than 60% is not desirable.
The present invention does not specifically define a pre-treatment and a post-treatment of plating, a heating method of a steel sheet during pressing and a cooling method thereof. As a plating post-treatment, a chromate treatment, a resin coating treatment or the like is nominated aiming at primary rust prevention and lubricity. However, with regard to a chromate treatment, considering the recent regulation against hexavalent chrome, a treatment film containing trivalent chrome, such as electrolytic chromate or the like, is preferable.
A resin coating treatment is effective in improving formability in general and it is particularly effective when a part of a steel sheet is rapidly heated after forming. When a steel sheet is heated and then formed, a resin film is decomposed and therefore has no effect.
A method of producing an aluminum plated steel sheet WO 02/103073 PCT/JP02/05978 30 is not prescribed either. Regular steelmaking conditions and hot-rolling conditions may be applied. An aluminum plating is carried out by the hot dip plating method usually, but a method is not limited to it and an electroplating in nonaqueous solvent, a vapor deposition treatment or the like can be used. As a pre-treatment before plating, Ni pre-plating or the like is nominated, and it can be adopted.
A method of heating or cooling a steel sheet is not particularly prescribed either. A heating means such as electric heating, heating in a furnace, high-frequency heating or the like may be adopted. Among those means, high-frequency heating is appropriate for rapidly heating a part of a steel sheet.
Embodiment 8 The reason why the components of a steel sheet and the like are regulated in Embodiment 8 will be described hereunder.
As stated above, the present invention is a technology which secures a desired strength by forming an aluminum plated steel sheet while hot after heating it, cooling it immediately after that, and thus quenching it, and the components of the steel sheet are required to grant excellent hardenability to the steel sheet. To meet the requirement, a C amount of not less than 0.05%, preferably not less than is required. With regard to other elements in a steel, the elements of Si, Mn, Ti, B, Cr, Mo, Al, P, S, N, etc. are used as usual. Si is effective in fatigue property, and Mn and B contribute to the improvement of hardenability. Ti, Si, Cr, Mo and Al are elements which improve heat resistance after aluminum plating.
An element of an alloyed aluminum-system plated layer, such as FeAl1, Fe 2 Al_, Fe 3 A1, Fe,A1,Si, etc. can be generated on a surface after heating. Those phases tend to form a multi-layered structure in a laminar manner, WO 02/103073 PCT/JP02/05978 31 but the structures of the phases are not specifically regulated. When the composition is mainly composed of Al and Fe and, Si is added in an aluminum plating bath, Si of about 5 to 10% is contained. Those elements account for not less than 90% of the composition in total.
Further, it is determined that an aluminum plated steel sheet is subjected to press working after the plated layer is transformed into an alloyed aluminum-system plated layer up to the surface by heating. This is because, when Al remains abundantly on the surface, weldability and after-painting corrosion resistance are deteriorated.
With regard to the heating and cooling conditions in the present invention, a method of heating and that of cooling are not particularly restricted. Any one of heating in an atmospheric furnace, induction heating, electric heating or the like may be used. A heating rate at this time is not restricted either. The heating rate largely depends on the thickness and shape of a steel sheet as a matter of course. New knowledge was obtained that, the longer the retention time in a furnace was, the better the plating adhesiveness during subsequent forming was. The heating temperature is in the range roughly from 800 to 1,200 0 C, preferably 900 to 1,000 0 C, and it is important to retain a steel sheet within this temperature range for about several minutes. However, the retention time depends on temperature, and it is determined that the retention time must be longer than the four points of A (800 0 C, 13 min.), B (900 0 C, 6 min.), C (1,050 0 C, min.) and D (1,200 0 C, 0.3 min.).
However, a longer retention time causes the deterioration of the productivity in press forming. A practically sufficient plating adhesiveness can be obtained by a heating at 950 0 C for 5 to 8 min., which condition is determined as a point of compromise. A hardened structure is largely affected by a cooling rate as a matter of course, and, to obtain the hardened WO 02/103073 PCT/JP02/05978 32 structure, a cooling rate of not lower than 10 0 C/sec. is required. This depends on steel components, and, in case of a steel sheet having good hardenability, a desired structure mainly composed of martensite can be obtained even at a cooling rate of about 10 0 C/sec., or, in another case, a cooling rate of about 30°C/sec. is required depending on the steel grade.
Next, the present invention will hereunder be explained in detail based on Examples.
Example 1 Hot dip aluminum plating was applied to pickled steel sheets (1.8 mm in thickness) and cold-rolled steel sheets (1.2 mm in thickness) as the materials, having steel compositions shown in Table 1 and being produced through regular hot-rolling and cold-rolling processes.
Nos. 1, 3, 5, 7 and 9 in Table 1 are cold-rolled steel sheets, and the rests are hot-rolled steel sheets. In the hot dip aluminum plating, a line of non-oxidizing furnace-reducing furnace type was used, a deposit amount of plating was adjusted to 40 g/m 2 per one side by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-10%Si-2%Fe. Fe in the bath is a component unavoidably supplied by the plating apparatus and the steel sheets in the bath. The plating appearance was good without having non-plating defects or the like. The hardenability and heat resistance of the hot dip aluminum plated steel sheets thus produced were evaluated. The evaluation methods are shown below.
As substantial alloying process, an aluminum plated steel sheet was heated at 950 0 C for 30 minutes and thereafter cooled while inserted between dies made of steel under a nitrogen atmosphere. The cooling rate was 100°C/sec. The exfoliation of a plated later of a steel sheet was evaluated visually. Further, Vickers hardness WO 02/103073 PCT/JP02/05978 33 at the cross-section of a steel sheet was measured imposing a load of 100 g. Thereafter, a steel sheet was subjected to a chemical treatment which was commonly used for aluminum plating, a steel sheet and zinc plating, coated with a cationic electrodeposition paint (Nippon Paint Co., Ltd.; powernix 110) in the thickness of 20 Rm, baked, and subjected to a salt spray test (JIS-Z2371) for days after being cut in a cross shape, and the corrosion depth from the portion cut in a cross shape was measured. Here, the depth of the cut in a cross shape was about 50 pm. Therefore, a value obtained by subtracting 50 [tm from a recorded value is a true corrosion depth. Further, for obtaining the concentrations of Mn and Cr in an Fe-Al intermetallic compound, the amounts of Mn and Cr were measured by quantitatively analyzing a specimen after quenched at portions in a cross-section after polished in the region from the surface to the depth of 5 ym, using an EPMA.
The evaluation results are shown in Table 2.
Evaluation criteria of heat resistance 0: No exfoliation z: Partial exfoliation from edges X: Exfoliation generated Evaluation criteria of after-painting corrosion resistance O: Corrosion depth not more than 80 pm X: Corrosion depth more than 80 tm (Each value includes the depth of a cut in a cross shape.) [Tables 1 and 2] WO 02/103073 PCT/JP02/05978 34 Table 1 No. Chemical composition (mass%) Si Mn P S Al N Ti Cr M, B Ti* 1 0.23 0.12 1.21 0.02 0.009 0.03 0.004 0.02 0.13 -0.002 0.76 2 0.21 0.20 0.81 0.02 0.007 0.05 0.004 0.22 0.20 0.83 3 0.17 0.15 1.24 0.01 0.008 0.03 0.003 0.01 1.10 -0.0008 1.73 4 0.42 0.7 2.41 0.01 0.009 0.01 0.003 0.66 0.21 -0.001 2.08 0.23 0.31 1.54 0.02 0.007 0.05 0.003 0,02 0.44 -0.002 1.23 6 .0.25, 0.18 1.22.0.01 0.01 0.04 0.003 0.02 0.66 0.20 0.005 1.29 7 0.24 0.2 0.41 0.01 0.02 0.05 0.004 0.09 0.10 0.15 0.0. 0.47 8 0.2 0.2 2.43 0.01 0.01 0.04 0.003 0.09 0.21 0.0008 1.52 9 0,03 0.1 1.4 0.02 0.01. 0.03 0.004 0.25 0.15 0.0003 1.1 0.23 0.12 0.3 0.01 0.008 0.05 0.003 0.03 0.23 0.41 1.1 0.24 0.10 0.51 0.01 0.008 0.03 0.00410.05 10. 0:3 002 0.34 Note 1) Ti*: Ti 0.5Mn Cr +i 0.514o Table 2 No. Mn Cr amount Heat Vickers After-painting resistance hardness corrosion resistance 1 0.4 0 515 0 2 0.22 0 480 0 3 0.96 0 405 0 4 0.85 0 766 0 0.30 0 513. 0 6 0.30 0 548 0 7 0.15 0 539 0 8 0.78 0 466 0 90.44 0 200 0 0.19 0 311 0 11 0.21 A522 0 When the C amount is excessively low as in the No. 9 steel sheet, the strength lowers. In general, a value close to material strength (MPa) is obtained by multiply a Vickers hardness by 3, and, in this case, a strength of only 600 MPa class at the most is obtained. When the addition amounts of the elements effective in quenching, such as Mn, B, etc., are small like No. 10 steel sheet, quenching effect is not obtained even though the C amount is large and the strength tends to decrease to some WO 02/103073 PCT/JP02/05978 35 extent. Further, in the case where the value of Ti*: Ti 0.5xMn Cr 0.5xMo is low like No. 11 steel sheet, the plated layer peels off after heating and the heat resistance tends to deteriorate to some extent. In case of Nos. 1 to 8 steel sheets wherein the addition amounts of the elements in the steels are properly controlled, all of strength, heat resistance and after-painting corrosion resistance show good results.
Next, No. 7 steel sheet of this Example in Table 1 was plated in a plating bath which mainly contained Al- 10%Si-2%Fe and in which Mn and Cr were added. The deposit amount of the plating was 60 g/m 2 per one side, and good plating appearance was obtained. The steel sheet was quenched with dies after heated at 900 0 C for 2 minutes. The cooling rate was about 100°C/sec. The amounts of Mn and Cr in the bath at this time and the evaluation results are shown in Table 3. When the amounts ;of Mn and Cr in the intermetallic compound are small like No 1 steel sheet, after-painting corrosion resistance is inferior, but the corrosion resistance improves with the increase of the addition amounts of Mn and Cr in the plating bath. The relation between the amounts of Mn and Cr in the intermetallic compound and the after-painting corrosion resistance at this time are shown in Fig. 3. It is understood that the afterpainting corrosion resistance improves with the increase of the amounts of Mn and Cr.
[Table 3] WO 02/103073 PCT/JP02/05978 36 Table 3 No. Amount of element Amount of element in Afterin bath intermetallic compound painting corrosion Mn Cr Mn Cr resistance 1 0 0 0.08 0 X 2 0.1 0 0.11 0 0 3 0.2 0 0.24 0 0 4 0.4 0.05 0.51 0.08 O 0.6 0 0.73 0 0 6 0.8 0.1 0.75 0.14 O Example 2 The steels having various chemical compositions as shown in Table 4 were cast, heated again to a temperature of 1,050 to 1,250°C, thereafter hot-rolled, pickled, cold-rolled, annealed, subjected to a plating treatment (aluminum plating or aluminum-zinc plating: "Galvalium®" plating), and thereafter subjected to temper rolling at the reduction rate of Further, as alloying process, these steel sheets were heated to a temperature of 900 to 1,000 0 C, retained for 5 minutes at the temperature, thereafter subjected to press forming with dies of the room temperature, and then subjected to the investigation on the properties. The investigation on material properties was carried out by cutting out the specimens from the portions which were rapidly cooled at the press and applying a tensile test thereto. The test was carried out by cutting the specimens into No. 5 test pieces according to JIS-Z2201 and following the test method described in JIS-Z2241. The evaluation results are shown in Table [Tables 4 and Steel No.
Table 4 Ti Al Ti-3.42*N 1 0.22 0.20 1.05 0.020 0.020 0.025 0.020 0.0024 0.02 0.02 0.0030 0.012 2 0.21 0.15 0.94 0.018 0.023 0.024 0.022 0.0035 0.25 0.10 0.0027 0.010 3 0.22 0.15 0.94 0.018 0.023 0.024 0.022 0.0025 0.01 0.01 0.0027 0.01 0.013 4 0.16 0.48 1.70 0.009 0.015 0.021 0.017 0.0025 0.80 0.02 0.0002 0.008 0.35 0.05 1.00 0.015 0.012 0.030 0.020 0.0028 0.01 0.01 0.0020 0.010 6 0.53 0.10 1.10 0.010 0.020 0.026 0.200 0.0021 0.02 0.01 0.0010 0.05 0.193 7 0.53 0.10 0.30 0.010 0.020 0.030 0.020 0.0020 0.90 0.02 0.0047 0.013 8 0.22 0.20 1.00 0.002 0.015 0.035 0.005 0.0034 0.02 0.02 0.0005 -0.007 9 0.21 0.20 1.10 0.022 0.021 0.028 0.020 0.0026 0.00 0.02 0.0020 0.011 0.22 0.20 2.00 0.010 0.010 0.030 0.020 0.0033 0.01 0.01 0.009 11 0.35 0.15 2.10 0.012 0.013 0.023 0.018 0.0028 0.05 0.01 0.01 0.008 12 0.24 0.20 2.50 0.008 0.009 0.035 0.026 0.0035 0.02 0.01 0.014 WO 02/103073 PCT/JP02/05978 38 Table Steel Coiling Anneal- Kind of TS Heating YP TS Bare After- No. temper- ing plating before temper- (MPa) (MPa) corro- paintature temper- forming ature sion ing ature before resis- corroforming tance sion resist- (Mpa) (CC) ance 1 630 780 Aluminum 560 950 1250 1580 O O platin 610 775 Galvalium 550 950 1255 1600 O O lating 2 680 760 Aluminum 550 950 1220 1610 O O plating 650 780 Galvalium 558 950 1210 1590 O O plating 3 620 730 Aluminum 570 950 1280 1550 O O plating 630 730 Galvalium 564 950 1270 1540 O O platin 4 650 830 Aluminum 500 980 1110 1310 O O plating 660 840 Galvalium 508 980 1100 1320 O O plating 630 770 Aluminum 603 950 1480 1830 O O plating 640 770 Galvalium 605 950 1490 1820 O O plating 6 650 775 Aluminum 654 940 1610 1990 O O plating 660 .780 Galvalium 660 940 1620 1980 O O plating 7 650 760 Aluminum 780 910 1850 2100 O O plating 650 760 Galvalium 774 910 1820 2120 O O plating 8 650 790 Aluminum 553 950 750 980 O O plating 9 630 800 Aluminum 558 950 1210 1540 X O lating 640 780 Aluminum 554 950 1240 1580 O O plating 630 775 Galvalium 550 950 1230 1575 O O plating 11 650 760 Aluminum 572 950 1200 1510 O O plating 650 760 Galvalium 563 950 1205 1520 O O plating 12 620 730 Aluminum 595 950 1270 1560 O O plating 630 730 Galvalium 598 950 1275 1570 O O plating WO 02/103073 PCT/JP02/05978 39 Specimens were cut out from the portions which underwent working during press forming and bare corrosion resistance and after-painting corrosion resistance were evaluated as the surface properties after high temperature forming. The bare corrosion resistance was evaluated by subjecting the specimens to a moisture tank test (relative humidity: 95%, temperature: 40 0 C) for 3 days, and the after-painting corrosion resistance was evaluated by subjecting the specimens to a salt spray test (JIS-Z2134) for 30 days after the specimens were cut in a cross shape. A cationic electrodeposition paint was adopted as the painting in this case and the painting thickness was 15 Vm. The bare corrosion resistance was judged from the appearance using a mark O or X, and the evaluation criteria were: X for the occurrence of red rust and O for no red rust. Likewise, the afterpainting corrosion resistance was judged from the appearance using a mark O, L or X, and the evaluation criteria were: 0 for blistering of not more than 2 mm, A for blistering from more than 2 mm to not more than 4 mm, and X for blistering of more than 4 mm. Nos. 1 to 7 steels are the steels having the components within the range specified in the present invention, and all steel sheets produced on the conditions within the range specified in the present invention can secure high strength after high temperature forming and, moreover, have no problem with respect to both the bare corrosion resistance and the after-painting corrosion resistance.
Here, in case of No. 7 steel, the results of the steel sheet produced on the conditions where the annealing temperature deviates from the range specified in the present invention is also shown, and, in this case, as the strength of the steel sheet is too high, the evaluation of the properties is not carried out thereafter. In case of Nos. 8 and 9 steels, the steel WO 02/103073 PCT/JP02/05978 40 compositions deviate from the range specified in the present invention. As a result, in case of No. 8 steel, the strength after high temperature forming, which is one of the targets of the present invention, is low, and, in the case of No. 9 steel, the bare corrosion resistance and the after-painting corrosion resistance are not secured.
Example 3 The steels having various chemical compositions as shown in Table 6 were cast, heated again to a temperature of 1,050 to 1,250 0 C, thereafter hot-rolled, pickled, cold-rolled, annealed, subjected to a plating treatment (aluminum plating or aluminum-zinc plating), and thereafter subjected to temper rolling at the reduction rate of Further, as substantial alloying process, these steel sheets were heated to a temperature of 900 to 1,000 0 C, retained for 5 minutes at this temperature, thereafter subjected to press forming with dies of the room temperature, and then subjected to the investigation on the properties. The investigation on material properties was Carried out by cutting out specimens from the portions which were rapidly cooled at the press and applying a tensile test thereto. The test was carried out by cutting the specimens into No. 5 test pieces according to JIS-Z2201 and following the test method described in JIS-Z2241. The evaluation results are shown in Table 7.
[Tables 6 and 7] Table 6 Steel C Si Mn S P Al N Cr Mo Cr+7xMo Remarks No.
Invented 1 0.16 0.20 0.72 0.006 0.020 0.035 0.0025 1.00 0.18 2.260 Invented example Invented 2 0.21 0.21 0.68 0.008 0.018 0.032 0.0030 0.95 0.15 2.000 I e e example Invented 3 0.50 0.25 0.75 0.006 0.020 0.026 0.0028 0.98 0.17 2.170 I e e example Invented 4 0.23 0.20 1.50 0.010 0.015 0.030 0.0030 0.32 0.00 0.320 Invented example Invented 0.22 0.45 2.20 0.009 0.010 0.038 0.0035 0.00 0.05 0.350 Invented example Invented 6 0.23 0.15 0.30 0.008 0.012 0.032 0.0026 1.90 0.00 1.900 example Invented 7 0.21 0.20 0.50 0.008 0.010 0.033 0.0028 0.00 0.80 5.600 Invented example Invented 8 0.22 0.21 0.65 0.006 0.015 0.032 0.0030 0.10 0.02 0.240 Invented example Invented 9 0.22 0.20 0.70 0.008 0.014 0.025 0.0025 0.25 0.00 0.250 I e e example 0.21 0.18 0.45 0.010 0.012 0.028 0.0025 0.00 0.03 0.210 Comparative S____example WO 02/103073 PCT/JP02/05978 42 Table 7 Steel Coiling Anneal- Kind of TS Heating YP TS Bare After- Remarks No. temper- ing plating before temper- (MPa) (MPa) corro- paintature temper- forming ature sion ing ature before resis- corroforming tance sion resist- (Mpa) (OC) ance 1 630 780 Aluminum 565 980 1080 1280 o 0 Invented plating example 620 780 Aluminum- 560 980 1090 1270 o O Invented zinc plating example 2 650 770 Aluminum 605 950 1290 1560 0 o Invented plating example 650 765 Aluminum- 600 950 1285 1580 o o Invented zinc plating ,example 3 635 740 Aluminum 725 930 1705 1890 0 o Invented plating example 630 750 Aluminum- 750 930 1700 1900 0 O Invented zinc plating example 4 645 775 Aluminum 500 950 1390 1610 o o Invented plating example 650 780 Aluminum- 508 950 1400 1600 0 o Invented zinc plating example 630 770 Aluminum 603 950 1300 1550 0 0 Invented plating example 630 770 Aluminum- 605 950 1320 1555 0 0 Invented zinc plating example 6 650 770 Aluminum 654 950 1390 1620 0 0 Invented plating example 640 760 Aluminum- 660 950 1380 1620 0 o Invented zinc plating example 7 640 770 Aluminum 780 950 1320 1510 0 a Invented plating example 650 760 Aluminum- 774 950 1325 1520 0 a Invented zinc plating example 8 630 765 Aluminum 553 950 1320 1580 0 a Invented plating example 635 760 Aluminum- 555 950 1310 1570 O a Invented zinc plating _example 9 640 770 Aluminum 558 950 1340 1575 0 0 Invented plating example 645 770 Aluminum- 562 950 1350 1585 0 0 Invented zinc plating example 630 765 Aluminum 554 950 1350 1595 X X Comparative plating I __II example 640 760 Aluminum- 550 950 1330 1530 X X Comparative zinc plating example WO 02/103073 PCT/JP02/05978 43 Specimens were cut out from the portions which underwent working during press forming and bare corrosion resistance and after-painting corrosion resistance were evaluated as the surface properties after high temperature forming. The bare corrosion resistance was evaluated by subjecting the specimens to a moisture tank test (relative humidity: 95%, temperature: 40 0 C) for 3 days, and the after-painting corrosion resistance was evaluated by subjecting the specimens to a salt spray test (JIS-Z2134) for 30 days after the specimens were cut in a cross shape. A cationic electrodeposition paint was adopted as the painting in this case and the painting thickness was 15 pm. The bare corrosion resistance was judged from the appearance using a mark O or X, and the evaluation criteria were: X for the occurrence of red rust and O for no red rust. Likewise, the afterpainting corrosion resistance was judged from the appearance using a mark O, or X, and the evaluation criteria were: 0 for blistering of not more than 2 mm, A for blistering from more than 2 mm to not more than 4 mm, and X for blistering of more than 4 mm. Nos. 1 to 9 steels are the steels having the components within the range specified in the present invention, and all steel sheets produced on the conditions within the range specified in the present invention can secure high strength after high temperature forming, and moreover have no problem with respect to both the bare corrosion resistance and the after-painting corrosion resistance.
In case of the No. 10 steel, the steel composition deviates from the range specified in the present invention and therefore the bare corrosion resistance and the after-painting corrosion resistance are not secured.
Example 4 Hot dip aluminum plating was applied to pickled steel sheets (1.8 mm in thickness) and cold-rolled steel WO 02/103073 PCT/JP02/05978 44 sheets (1.2 mm in thickness) as the materials having steel compositions shown in Table 8 and being produced through regular hot-rolling and cold-rolling processes.
Nos. 1, 3, 5 and 7 in Table 8 are cold-rolled steel sheets, and the rest are hot-rolled steel sheets. In the hot dip aluminum plating, a line of non-oxidizing furnace-reducing furnace type was used, a deposit amount of plating was adjusted to 80 g/m 2 per both sides by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-10%Si-2%Fe. Fe in the bath is a component unavoidably supplied from the plating apparatus and the steel sheets in the bath. Plating appearance was good without having non-plating defects or the like. The properties are shown in Table 9.
The hardenability and workability of the hot dip aluminum plated steel sheets thus produced were evaluated. The workability was evaluated by heating an aluminum plated steel sheet at 950 0 C for 10 minutes under the atmosphere, as substantial alloying process, thereafter cooling it while inserting it between dies made of steel (cooling rate: about 30°C/sec.), cooling it to the room temperature, and thereafter subjecting it to an impact test. Further, Vickers hardness at the crosssection of a steel sheet was measured by imposing a load of 100 g.
Evaluation criteria of workability 0: No exfoliation A: Cracks generated X: Powdery exfoliation generated [Tables 8 and 9] WO 02/103073 PCT/JP02/05978 45 Table 8 No. Chemical composition (wt% C Si Mn P S Al N Ti Cr Mo B 1 0.23 0.12 1.21 0.02 0.009 0.03 0.004 0.02 0.13 0.002 2 0.21 0.20 0.81 0.02 0.007 0.05 0.004 0.22 0.20 3 0.17 0.15 1.24 0.01 0.008 0.03 0.003 0.01 1.10 0.0008 4 0.23 0.31 1.54 0.02 0.007 0.05 0.003 0.02 0.44 0.002 0.25 0.18 1.22 0.01 0.01 0.04 0.003 0.02 0.66 0.20 0.005 6 0.24 0.2 0.95 0.01 0.02 0.05 0.004 0.09 0.5 0.15 0.01 7 0.2 0.2 2.43 0.01 0.01 0.04 0.003 0.09 0.21 0.0008 8 0.04 0.1 1.4 0.02 0.01 0.03 0.004 0.25 0.15 0.0003 Table 9 No. Workability Al amount in Fe-Al coating Vickers hardness 1 0 15 515 2 0 15 480 3 0 15 405 4 0 15 511 0 15 548 6 0 15 539 7 0 15 466 8 0 15 209 When the C amount is rather low as in the No. 8 steel, the strength is rather low. In general, a value close to the tensile strength (MPa) of a material is obtained by multiplying a Vickers hardness by 3, and, in this case, a strength of only 600 MPa class at the most is obtained. In case of Nos. 1 to 7 steels, both strength and workability show good results. The Al amount in the Fe-Al coating layer in this case is quantitatively analyzed using an EPMA, and the value is around 15%. Here, the value is obtained by analyzing portions in a cross-section of a specimen after quenching in the range from the surface to the depth of 10 Am and averaging the analysis data.
Next, No. 1 steel sheet of this Example in Table 8 was plated with a metal mainly composed of Al-10%Si-2%Fe and the deposit amount of the plating was varied from WO 02/103073 PCT/JP02/05978 46 to 200 g/m 2 per both sides. The samples thus obtained were heated at 950 0 C under the atmosphere with the retention time being changed, the workability was evaluated with an impact test, and the Al amount in the Fe-Al coating layer was measured by the method described in the item 1 of Example 4. As shown in Table 10, the workability depends on the Al amount in the Fe-A1 coating layer, and, when the Al amount is not more than 35%, good workability is obtained. Further, the Al amount in the Fe-Al coating layer depends on the deposit amount and the retention time, and it can be understood that, the smaller the deposit amount is and the longer the retention time is, the more the diffusion proceeds and the smaller the Al amount in the Fe-Al coating layer is.
[Table Table No. Deposit amount Retention Al amount in Workability (g/m 2 time Fe-Al coating 1 60 0 36 A 2 60 1 29 O 3 60 2 17 0 4 80 0 38 X 80 1 35 A 6 80 2 20 O 7 120 2 42 X 8 120 4 36 X 9 120 6 15 O 200 5 44 X 11 200 10 38 X 12 200 15 377 X Example Hot dip Al-Si-Mg plating was applied to pickled steel sheets (1.8 mm in thickness) and cold-rolled steel sheets (1.2 mm in thickness) as the materials, having steel compositions shown in Table 11 and being produced through regular hot-rolling and cold-rolling processes.
WO 02/103073 PCT/JP02/05978 47 A, C, E and G in Table 11 are cold-rolled steel sheets, and the rest are hot-rolled steel sheets. In the hot dip plating, a line of non-oxidizing furnace-reducing furnace type was used, a deposit amount of plating was adjusted to 40 g/m 2 per one side by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-8%Si-6%Mg-l%Fe- 0.1%Ca. Fe in the bath is a component unavoidably supplied from the plating apparatus and the steel sheets in the bath. Plating appearance showed a spangle pattern and was good without having non-plating defects or the like. The production conditions in this case are shown in Table 12.
The hardenability and corrosion resistance of the hot dip plated steel sheets thus produced were evaluated.
The evaluation methods are described below. The hot dip plated steel sheets were subjected to 5% tensile stress, then heated at 950 0 C for 5 minutes, and, as substantial alloying process, thereafter cooled while inserted between steel sheets. The cooling rate was about The heat resistance was evaluated by visually observing the specimens after cooling. Then, the bare corrosion resistance was evaluated by subjecting the specimens to a moisture tank test (relative humidity: temperature: 40 0 C) for 3 days, and the afterpainting corrosion resistance was evaluated by subjecting the specimens to a salt spray test (JIS-Z2134) for days after the specimens were cut in a cross shape. A cationic electrodeposition paint was adopted as the painting in this case and the painting thickness was m. Further, the Vickers hardness of a steel sheet was measured by imposing a load of 100 g.
Evaluation criteria of heat resistance 0: Good A: Crack-shaped patterns generated on the WO 02/103073 PCT/JP02/05978 48 surface X: Red scales generated Evaluation criteria of bare corrosion resistance 0: Good A: Red rust generated Evaluation criteria of after-painting corrosion resistance Paint blister not more than 1 mm O: Paint blister not more than 2 mm A: Paint blister 2 to 4 mm X: Paint blister more than 4 mm [Tables 11 and 12] Table 11 Steel C Si Mn P S Al N Ti Cr Mo Ni B code A 0.21 0.20 0.81 0.02 0.007 0.05 0.004 0.05 0.20 0.0005 B 0.17 0.15 1.24 0.01 0.008 0.03 0.003 0.15 1.10 0.0008 C 0.42 0.7 2.41 0,01 0.009 0.01 0.003 0.46 0.21 0.001 D 0.23 0.31 1.54 0,02 0.007 0.4 0.003 0.24 0.44 0.002 E 0.25 0.18 1.22 0.01 0.01 0.04 0.003 0.003 0.66 0.20 0.005 F 0.24 0.2 0.95 0.01 0.02 0.05 0.004 0.001 0.15 0.33 0.01 G 0.08 0.1 1.4 0.02 0.01 0.03 0.004 0.25 0.15 0.0003 H 0.24 0.10 0.31 0.01 0.008 0.03 0.004 0.21 0.03 0.0001 Table 12 No. Code of Bare After-painting Vickers applied steel corrosion corrosion hardness resistance resistance 1 A O O 485 (0) 2 B O O 401 (0) 3 C O O 769 (0) 4 D O O 509 (0) E O O 544 (0) 6 F 0 0 540 (0) 7 G O O 289 (X) 8 H O O 301 (X) When the C amount is too small as in the No. 7 steel sheet, sufficient strength is not obtained. In general, WO 02/103073 PCT/JP02/05978 49 a value close to material strength (MPa) is obtained by multiplying a Vickers hardness by 3, and, in this case, a strength of only 800 MPa class at the most is obtained.
Further, when the amounts of the elements effective in quenching, such as Mn, B, etc., are small as in No. 8 steel sheet, the quenching effect is not obtained even though the C amount is large. In case of Nos. 1 to 6 steel sheets wherein the addition amounts of the elements in the steels are properly controlled, both strength and corrosion resistance show good results in either the case of the Mn-B-system or the Mo-Cr-Ni-system.
Then, using steel E in Table 11, the relation between the plating compositions and the properties of the plated steel sheets was investigated with the compositions in the plating bath of the hot dip plating line being varied. The relation between the compositions of the plated layers and the properties thereof after plating is summarized in Table 13. Here, the Vickers hardness was in the range from 470 to 510 in each case.
In case of a No. 8 steel sheet, which is of Mg-Znsystem, corrosion resistance is poor. On the other hand, Nos. 4 to 7 steel sheets, which are of Si-Mg-system, show excellent corrosion resistance. Likewise, Nos. 1 to 3 steel sheets, which are of Si-Mg-Zn-system, show excellent corrosion resistance.
[Table 13] WO 02/103073 PCT/JP02/05978 50 Table 13 No. Composition of plated Bare corrosion After-painting layer (mass resistance corrosion Si Mq Zn Ca resistance 1 2 3 40 0.1 0 2 5 7 20 0.1 0 3 8 6 10 0 4 12 8 0.1 0 8 6 0.1 0 6 6 3 O@0 7 9 0.5 0 8 1 3 X X Example 6 Hot dip aluminum plating was applied to cold-rolled steel sheets (1.2 mm in thickness) as the materials, having a steel composition shown in Table 14 and being produced through regular hot-rolling and cold-rolling processes. In the hot dip aluminum plating, a line of non-oxidizing furnace-reducing furnace type was used, a deposit amount of plating was adjusted to 60 g/m 2 per one side by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-10%Si-2%Fe. Fe in the bath is a component unavoidably supplied from the plating apparatus and the steel sheets in the bath. The plating appearance was good without having non-plating defects or the like.
The aluminum plated steel sheets thus produced were heated to 950 0 C, and, as substantial alloying process, the workability (exfoliation resistance) of the plated layers during air-cooling was evaluated.
At this time, the thickness of the ferrite layers was varied by varying the heating times and heating patterns. Working was applied by an impact test, the exfoliation state was visually judged with the working temperature being varied during cooling, and the workability of the plated layers was evaluated at the WO 02/103073 PCT/JP02/05978 51 lowest temperature where the exfoliation of a plated layer did not occur. Here, in case of this steel, the hardenability was good even at the cooling rate of 0 C/sec. and a structure mainly composed of martensite was obtained even in case of air-cooling. The relation between the thickness of the intermediate ferrite layer and the lowest temperature where good working can be obtained in this case is shown in Fig. 8.
As shown in Fig. 8, it is understood that, when the thickness of a ferrite layer is not less than 2 pm, preferably not less than 4 m, the exfoliation resistance of a plated layer improves. When the thickness of a ferrite layer is about 0.5 pm, powdery exfoliation of a plated layer is observed even in the case of the working at 800 0 C. Further, as substantial alloying process, the workability of a plated layer depends on the deposit amount of plating. Even though the thickness of a ferrite layer is 2 tm, when the deposit amount is 30 g/m 2 per one side, the lowest temperature where good working is obtained is about 500 0 C. Further, the structure of the base steel at the time was analyzed by the observation with an optical microscope and the subsequent image analysis, and not less than 80% of the structure was composed of martensite under all conditions.
[Table 14] Table 14 C Si Mn P S Al N Ti Cr Mo B 0.36 0.21 0.65 0.02 0.006 0.027 0.003 0.002 1.01 0.16 0.0001 Example 7 Hot dip aluminum plating was applied to pickled steel sheets (1.8 mm in thickness) and cold-rolled steel sheets (1.2 mm in thickness) as the materials, having steel compositions shown in Table 15 and being produced through regular hot-rolling and cold-rolling processes.
WO 02/103073 PCT/JP02/05978 52 Nos. 1, 3 and 5 in Table 15 are cold-rolled steel sheets, and the rests are hot-rolled steel sheets. In the hot dip aluminum plating, a line of non-oxidizing furnacereducing furnace type was used, a deposit amount of plating was adjusted to 60 g/M 2 per one side by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-10%Si-2%Fe. Plating appearance was good without having non-plating defects or the like. The hot dip aluminum plated steel sheets thus produced were heated to 950 0 C, and, as substantial alloying process, thereafter subjected to press forming at the time when the temperature reached about 600 0 C while cooled by watercooled dies. The exfoliation state of a plated layer at the portion to which bending working was applied was visually judged and the exfoliation of a plated layer was not observed for all steel sheets. At the time, the thickness of the ferrite layers was 10 to 20 IRm, and the martensite percentage in all base steels was not less than 80%. Here, the cooling rate was about 150 0 C/sec.
[Table Table No. C Si Mn P s Al N Ti Cr MO 3 1 0.22 0.20 0.94 0.02 0.0C07 0.025 0.003 0.22 0.05 0.002 0.0017 2 0.16 0.17 0. 69 0.02 0.007 0.037 0.004 0.002 0. 98 0.17 0.000 1 3 0.20 0.20 0. 67 0.02 0.006 0.033 0.003 0.002 0.96 0.17 0.0002 4 0.22 0.15 0.88 10.03 0.0C07 0.022 0 .004 0.55 0.12 110.01 0n.000oo .0.25 0.55 0.72 10.02 0.009 0.025 10.003,0.31 0.581 0.12 0.0020 Example 8 Hot dip aluminum plating was applied to cold-rolled steel sheets (1.2 mm in thickness) as the materials, having a steel composition shown in Table 16 and being produced through regular hot-rolling and cold-rolling processes. in the hot dip aluminum plating, a line of non-oxidizing furnace-reducing furnace type was used, the WO 02/103073 PCT/JP02/05978 53 deposit amounts of plating were adjusted to 30 to 80 g/m 2 per one side by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-10%Si-2%Fe. Fe in the bath is a component unavoidably supplied from the plating apparatus and the steel sheets in the bath. Plating appearance was good without having non-plating defects or the like.
The hardness after quenching, the thickness of the intermetallic compounds, weldability, heat resistance and after-painting corrosion resistance of the aluminum plated steel sheets thus produced were evaluated. The quenching was applied by heating a steel sheet at 950 0
C
for 0.5 to 20 minutes in the atmosphere, and, as substantial alloying process, thereafter pressing the steel sheet in the state of a plane sheet with dies and cooling it. At the time, the cooling rate was about 300°C/sec. By so doing, quenched steel sheets having alloy layers different in thickness and alloyed up to the surface were obtained by changing the deposit amounts and heating times. Here, the appearance of all steel sheets was almost homogenous. The evaluation methods and the evaluation criteria of the properties are shown below.
[Table 16] Table 16 Number C Si Mn P S Al N Ti Cr Mo B 1 0.22 0.20 0.94 0.02 0.007 0.025 0.003 0.22 0.05 0.002 0.0017 [Hardness] Vickers hardness was measured at the center portion in the cross-section of a steel sheet by imposing a load of 100 g.
[Thickness of intermetallic compound] The thickness of an intermetallic compound was measured by observing the cross-section of a steel sheet using a microscope, then etching it with 2% nitral, and WO 02/103073 PCT/JP02/05978 54 thereafter analyzing the structure using an EPMA. An example of the analysis is shown in Fig. 9. The reference numeral 1 shows the layer composed of Al: 26.85%, Si: 9.83%, Fe: 59.92%; the reference numeral 2 the layer composed of Al: 49.54%, Si: 3.11%, Fe: 44.87%; the reference numeral 3 the layer composed of Al: 30.75%, Si: 8.88%, Fe: 56.91%; and the reference numeral 4 the layer composed of Al: 9.59%, Si: 2.92%, Fe: 84.02%.
[Weldability] Spot weldability was evaluated on the following conditions: Electrode; Dome electrode made of alumina dispersed copper and having an electrode tip of 6 Pressure; 600 kgf, welding current; 10 kA, Welding time; 12 cycles (60 Hz).
Evaluation criteria 0: Consecutive spot welding of more than 2,000 cycles A: Consecutive spot welding of 1,200 to 2,000 cycles X: Consecutive spot welding of less than 1,200 cycles [After-painting corrosion resistance] A steel sheet was subjected to a chemical treatment for about 2 minutes in a chemical treatment liquid, which was commonly used for aluminum plating a steel sheet and zinc plating, then coated with a cationic electrodeposition paint of 20 Vm in thickness, baked at 140°C for 20 minutes, and thereafter subjected to a salt spray test for 20 days after cut in a cross shape, and the after-painting corrosion resistance was judged by the corrosion depth at the portion cut in a cross shape.
Here, the depth of the cut in a cross shape with a cutter was about 50 Am. Therefore, a value obtained by subtracting 50 am from a measured value is a true WO 02/103073 PCT/JP02/05978 55 corrosion depth.
The evaluation results are summarized in Table 17.
Evaluation criteria 0: Corrosion depth not more than 80 pm X: Corrosion depth more than 80 [m [Table 17] Table 17 No. Thickness of Hardness of Spot After-painting alloy layer base material weldability corrosion (Mm) (Hv) resistance 1 2 397 O X 2 5 395 O O 3 10 399 O O 4 17 401 O O 25 398 0 O 6 32 399 0 7 38 397 X 0 As shown in Table 17, when the thickness of an alloy layer is small, the steel sheet tends to be excellent in spot weldability but to be inferior in after-painting corrosion resistance. When the thickness is too thin like No. 1 steel sheet, the steel sheet is inferior in after-painting corrosion resistance, and when the thickness is too heavy like No. 7 steel sheet, the steel sheet is inferior in spot weldability. In case of Nos. and 6 steel sheets too, the steel sheets tend to be inferior in spot weldability. Therefore, when spot weldability is regarded as important, it is desirable to make the thickness of an alloy layer rather thin.
Example 9 Steel sheets made of the steels shown in Table 18 were plated with a metal mainly composed of 2%Fe, and good plating appearance was obtained. The thickness of the alloyed layers after quenched on the same conditions as the item 1 of Example 7 was measured WO 02/103073 PCT/JP02/05978 56 and the values were within the range from 8 to 15 R~m.
With respect to those steel sheets, the same evaluation items as the item 1 of Example 7 were evaluated. As a result, all of the steel sheets obtained the evaluation results which correspond to the evaluation rank 0 of Example 1, and showed good weldability and good afterpainting corrosion resistance.
[Table 18] Table 18 No. C Si Mn P S Al N Ti Cr Mo B 1 0.22 0.20 0.94 0.02 0.007 0.025 0.003 0.22 0.05 0.002 0.0017 2 0.16 0.7 0.69 0.02 0.007 0.037 0.004 0.002 0.98 0.17 0.0001 3 0.20 0.20 0.67 0.02 0.006 0.033 0.003 0.002 0.96 0.17 0.0002 4 10.36 0.21, 0.65 0.02 0.006 0.027 ,0.003 0.002,1.01 0.16 0.0002 ,201 .80.03 0.007 0.022 0.004 0.55 0.12 0.01 0.0005 6 .505 .20.02 0.009 0.052 0.003 0.31 0.58 0.12 0.0020 7 .301 .10.03 0.007 0.025 0.003 0.27 0.03 0.01 0.0022 Example Hot dip aluminum plating was applied to cold-rolled steel sheets (1.2 mm in thickness) as the materials having a steel composition shown in Table 19 and being produced through regular hot-rolling and cold-rolling processes. In the hot dip aluminum plating, a line of non-oxidizing furnace-reducing furnace type was used, a deposit amount of plating was adjusted to 60 g/m 2 per one side by the gas wiping method after plating, and, after that, the steel sheets were cooled and subjected to a zero-spangle treatment. The plating bath composition at the time was Al-1O%Si-2%Fe. Fe in the bath is a component unavoidably supplied from the plating apparatus and the steel sheets in the bath. The plating appearance was good without having non-plating defects or the like.
The hot dip aluminum plated steel sheets thus produced were heated in the atmosphere, then retained at various temperatures, and formed into the shape shown in Fig. At the time, the steel sheets were cooled with water- WO 02/103073 PCT/JP02/05978 57 cooled dies. The heating rate was about 5 to 10 0 C/sec., and the cooling rate was, though it varied with the portions, about 100 0 C/sec. at a portion where cooling rate was high and about 20 0 C/sec. at a portion where cooling rate was low. The workability (exfoliation resistance) of a plated layer at the time was evaluated.
The exfoliation of the plated layers was formed in a shape of streak or in a shape of spot on the compressed surface. The relation between the heating conditions and the state of the exfoliation of the plated layers is shown in Table 20. Further, the heating conditions according to the present invention are shown in Fig. 11.
[Tables 19 and Table 19 C Si Mn P S Al N Ti Cr Mo B 0.24 0.21 0.95 0.02 0.006 0.027 0.003 0.002 1.01 0.16 0.0018 Table No. Heating temperature Heating time Adhesiveness (min.) 1 800. 20 A 2 850 15 O 3 900 13 O 4 950 8 O 1000 6 0 6 1050 4 O 7 1100 2 O 8 900 5 X 9 1000 2 X Evaluation criteria of adhesiveness 0: No exfoliation of plated layer A: Cracks generated partially in plated layer X: Exfoliation of plated layer generated As shown in Table 20, the adhesiveness is not regarded yet as perfect even after heating for 20 minutes when the temperature is as low as 800°C as substantial WO 02/103073 PCT/JP02/05978 58 alloying process. When a heating temperature rises, good adhesiveness is obtained with a retention time of not more than 10 minutes. Adhesiveness is still insufficient when the retention time is 5 minutes at 9000C, or 2 minutes at 1,0000C as substantial alloying process.
Industrial Applicability As stated above, the present invention provides a hot press method for forming a high-strength automotive part, and will greatly contribute to the weight reduction of an automobile in the future.
Claims (12)
1. A high-strength alloyed aluminum-system plated steel sheet excellent in after- painting corrosion resistance and worked by hot forming, characterized by having an Fe- Al-system coating containing Mn and Cr of more than 0.1% in total on the surface of the steel sheet. c 2. A high-strength alloyed aluminum-system plated steel sheet excellent in heat 00 0, resistance and after-painting corrosion resistance, characterized by having an Fe-A1- system coating containing, in mass, Mn and Cr of more than 0.1% in total on the surface C€3 N, of the steel containing, in mass, C: 0.05 to Si: 0.05 to Mn: 0.5 to P: not more than S: not more than 0.1% and Al: not more than and, in addition, one or more element(s) selected from among Ti: 0.01 to Cr: not more than 3% and Mo: not more than so as to satisfy the following expression Ti 0.5xMn Cr 0.SxMo 0.4
3. A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and after-painting corrosion resistance according to claim 2, wherein the steel further contains, in mass, one or more element(s) selected from among N: not more than Nb: not more than V: not more than Ni: not more than Cu: not more than B: 0.0003 to 0.03%, Sn: not more than 0.1% and Sb: not more than 0.1%.
4. A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and after-painting corrosion resistance according to claim 1, wherein the steel contains, in mass, C: 0.15 to 0.55%, Si: not more than Mn: 0.2 to P: not more than S: not more than 0.04%, Al: 0.01 to 0.1% and N: not more than 0.01%, and also one or more element(s) selected from among B: 0.0002 to 0.0050%, Ti: 0.01 to 0.8%, Cr: not more than Mo: not more than Ni: not more than Cu: not more than 0.5% and Sn: not more than 0.2%. A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and after-painting corrosion resistance according to any one of claims 1 to 4, wherein the Fe-Al-system coating further contains Si of 1 to
6. An alloyed aluminum-system plated steel sheet for high-strength automotive members according to any one of claims 1 to 5, wherein Al concentration in the Fe-A1- system coating layer is not more than 35% in weight.
7. A high-strength alloyed aluminum-system plated steel sheet excellent in heat resistance and after-painting corrosion resistance according to any one of claims 1 to 6, wherein the Fe-Al-system coating further contains either one or both of Zn: 1 to 50% and Mg: 0.1 to [R:\LIBZZ]658812speci.doc:GYM t8. A high-strength alloyed aluminum-system plated steel sheet excellent in heat Sresistance and after-painting corrosion resistance according to any one of claims 1 to 7, 00 wherein the thickness of the Fe-Al-system coating layer is 3 to 35 pm. O 9. A high-strength alloyed aluminum-system plated steel sheet according to any 5 one of claims 1-8, wherein a coating layer mainly composed of Fe-Al on the surface of C€3 00 the steel sheet; a ferrite layer having a thickness from not less than 2 /m to not more than one tenth of the steel sheet thickness at the underside of the coating layer; and the base c steel mainly composed of martensite at the underside of the ferrite layer. A high-strength alloyed aluminum-system plated steel sheet for high-strength S 10o automotive members according to claim 9, wherein the alloyed aluminum-system plated layer on the surface of the steel sheet and the ferrite layer at the underside of the intermetallic compound layer contain Si.
11. A high-strength alloyed aluminum-system plated steel sheet for high-strength automotive members according to claim 9 or 10, wherein the hardness of the ferrite phase is not higher than 200.
12. A high-strength alloyed aluminum-system plated steel sheet substantially as hereinbefore described with reference to any one of the examples or accompanying drawings.
13. A high-strength automotive part formed by press forming, at least a portion of which is composed of a steel according to any one of claims 1 to 12.
14. A high-strength automotive part according to claim 13, characterized by having a coated film 1 to 200 pm in thickness on at least a part of the surface. A method for producing an automotive part according to claim 13, comprising the steps of; plating an aluminum-system coating on a steel sheet containing C of not less than 0.05 wt%, heating the plated steel sheet for a longer time period than the following regions, A, B, C and D, wherein A is (800 0 C x 13 min), B is (900 0 C x 6 min), C is (1050 0 C x min) and D is (1200 0 C x 0.3 min), hot pressing the heated plated steel sheet, and cooling the hot pressed plated steel sheet with a cooling rate of not lower than 1 0°C/sec.
16. A method for producing a high-strength alloyed aluminum-system plated steel sheet comprising the steps substantially as hereinbefore described with reference to any one of the examples or accompanying drawings. [R:\LIBZZ]65881 2speci.doc:GYM
17. A high-strength alloyed aluminum-system plated steel sheet produced by the Smethod of claim 16. o 18. A method for producing an automotive part comprising the steps substantially O as hereinbefore described with reference to any one of the examples or accompanying drawings. 0 0
19. An automotive part produced by the method of claim 18. N SDated 7 December, 2004 SNippon Steel Corporation Patent Attorneys for the Applicant/Nominated Person SPRUSON FERGUSON [R:\LIBZZ658812speci.doc:GYM
Applications Claiming Priority (23)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001181833A JP3845271B2 (en) | 2001-06-15 | 2001-06-15 | Aluminum or aluminum-galvanized steel sheet suitable for high temperature forming and having high strength after high temperature forming and method for producing the same |
| JP2001-181833 | 2001-06-15 | ||
| JP2001-190707 | 2001-06-25 | ||
| JP2001-190708 | 2001-06-25 | ||
| JP2001190707A JP4023710B2 (en) | 2001-06-25 | 2001-06-25 | Aluminum-plated steel sheet for hot press with excellent corrosion resistance and heat resistance, and automotive parts using the same |
| JP2001190709A JP4564207B2 (en) | 2001-06-25 | 2001-06-25 | Hot-pressed hot-dip aluminized steel sheet that is heated to 800 ° C or higher |
| JP2001-190709 | 2001-06-25 | ||
| JP2001190708A JP4634655B2 (en) | 2001-06-25 | 2001-06-25 | Aluminized steel sheet for hot press with excellent heat resistance |
| JP2001198431 | 2001-06-29 | ||
| JP2001-198431 | 2001-06-29 | ||
| JP2001220807A JP4612240B2 (en) | 2001-07-23 | 2001-07-23 | High-strength aluminized steel sheet with excellent corrosion resistance after painting and automotive parts using it |
| JP2001-220807 | 2001-07-23 | ||
| JP2001-228431 | 2001-07-27 | ||
| JP2001228431A JP4990449B2 (en) | 2001-07-27 | 2001-07-27 | Aluminum-coated steel sheet for high-strength automotive parts and automotive parts using the same |
| JP2001-241633 | 2001-08-09 | ||
| JP2001241633A JP4551034B2 (en) | 2001-08-09 | 2001-08-09 | High-strength aluminum plated steel sheet for automobile parts with excellent weldability and post-painting corrosion resistance, and automobile parts using the same |
| JP2001-264727 | 2001-08-31 | ||
| JP2001264727 | 2001-08-31 | ||
| JP2001383852A JP2003183802A (en) | 2001-12-18 | 2001-12-18 | High-strength aluminum-plated steel sheet excellent in heat resistance and after-coating corrosion resistance, and high-strength automotive part |
| JP2001-383852 | 2001-12-18 | ||
| JP2001390842A JP4022063B2 (en) | 2001-12-25 | 2001-12-25 | High-strength aluminum-plated steel sheet and high-strength automotive parts with excellent workability and corrosion resistance |
| JP2001-390842 | 2001-12-25 | ||
| PCT/JP2002/005978 WO2002103073A2 (en) | 2001-06-15 | 2002-06-14 | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
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| AU2002309283A1 AU2002309283A1 (en) | 2003-05-15 |
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-
2002
- 2002-06-14 KR KR1020077017549A patent/KR20070087240A/en not_active Application Discontinuation
- 2002-06-14 KR KR1020087029007A patent/KR20080108163A/en not_active Application Discontinuation
- 2002-06-14 AU AU2002309283A patent/AU2002309283B2/en not_active Ceased
- 2002-06-14 KR KR1020077027723A patent/KR20070119096A/en not_active Application Discontinuation
- 2002-06-14 KR KR1020037016351A patent/KR100836282B1/en active IP Right Review Request
- 2002-06-14 TW TW091113018A patent/TWI317383B/en not_active IP Right Cessation
- 2002-06-14 WO PCT/JP2002/005978 patent/WO2002103073A2/en active Application Filing
- 2002-06-14 CN CNB028120361A patent/CN100370054C/en not_active Ceased
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| Publication number | Publication date |
|---|---|
| KR20070087240A (en) | 2007-08-27 |
| WO2002103073A3 (en) | 2004-05-21 |
| KR20080108163A (en) | 2008-12-11 |
| KR100836282B1 (en) | 2008-06-09 |
| CN100370054C (en) | 2008-02-20 |
| TWI317383B (en) | 2009-11-21 |
| WO2002103073A2 (en) | 2002-12-27 |
| KR20040007718A (en) | 2004-01-24 |
| CN1531604A (en) | 2004-09-22 |
| KR20070119096A (en) | 2007-12-18 |
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Owner name: NIPPON STEEL CORPORATION Free format text: FORMER NAME(S): NIPPON STEEL & SUMITOMO METAL CORPORATION |
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