WO2016059742A1 - 高強度溶融亜鉛めっき鋼板 - Google Patents
高強度溶融亜鉛めっき鋼板 Download PDFInfo
- Publication number
- WO2016059742A1 WO2016059742A1 PCT/JP2015/004137 JP2015004137W WO2016059742A1 WO 2016059742 A1 WO2016059742 A1 WO 2016059742A1 JP 2015004137 W JP2015004137 W JP 2015004137W WO 2016059742 A1 WO2016059742 A1 WO 2016059742A1
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- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel sheet
- hot
- dip galvanized
- plating
- Prior art date
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
- C22C18/04—Alloys based on zinc with aluminium as the next major constituent
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- 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
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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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- C22C—ALLOYS
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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- 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
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- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12951—Fe-base component
- Y10T428/12958—Next to Fe-base component
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12951—Fe-base component
- Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12993—Surface feature [e.g., rough, mirror]
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
- Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
- Y10T428/264—Up to 3 mils
- Y10T428/265—1 mil or less
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/27—Web or sheet containing structurally defined element or component, the element or component having a specified weight per unit area [e.g., gms/sq cm, lbs/sq ft, etc.]
Definitions
- the present invention relates to a high-strength hot-dip galvanized steel sheet used for an inner plate of an automobile.
- so-called high-strength steel sheets used as strength members are required to have strict workability and rust prevention of the processed parts, and therefore, excellent plating quality is required for the processed parts. Further, in such a high strength steel plate, spot weldability is also required from the viewpoint of assembling a steel plate formed by an automobile manufacturer, particularly a high strength steel plate used for reducing the weight of the vehicle body.
- Patent Document 1 discloses a method for producing a hot-dip galvanized steel sheet having excellent slidability at the time of press work that regulates the amount of Al in the plating layer and the amount of Al at the interface between the plating layer and the steel sheet.
- the plating quality such as impact resistance adhesion of the processed portion and corrosion resistance after coating, plating appearance and spot weldability have not yet been sufficiently considered, and further improvement is required. It was.
- the present invention has been made in view of such circumstances, and an object thereof is to provide a high-strength hot-dip galvanized steel sheet excellent in plating quality, plating appearance and spot weldability of a processed part.
- the present inventors do not simply perform hot dip galvanizing treatment as in the prior art, but (1) form an FeAl intermetallic compound at the interface between the plating layer and the steel plate with a predetermined property (2 ) Controlling the solidification structure of the plating, (3) Controlling the texture of the surface, and (4) Controlling the state of internal oxidation in the surface layer of the steel sheet, so that the plating quality, plating appearance and spot weldability of the processed part
- the present inventors have found that a high-strength hot-dip galvanized steel sheet can be provided, and have completed the present invention.
- the present invention has been made based on the above findings, and the gist thereof is as follows.
- a high-strength hot-dip galvanized steel sheet comprising: a hot-dip galvanized layer having a thickness of 30% to 60%.
- the high strength molten steel sheet means a steel sheet having a tensile strength (TS) of 590 to 690 MPa.
- a high-strength hot-dip galvanized steel sheet excellent in plating quality, plating appearance and spot weldability of a processed part is provided.
- the high-strength hot-dip galvanized steel sheet of the present invention has a hot-dip galvanized layer having a specific structure on a cold-rolled steel sheet having a specific structure.
- an intermetallic compound having a specific configuration is formed between the cold-rolled steel sheet and the hot-dip galvanized layer.
- the high-strength hot-dip galvanized steel sheet of the present invention is excellent in the plating quality, plating appearance and spot weldability of the processed part.
- the cold-rolled steel sheet constituting the high-strength hot-dip galvanized steel sheet of the present invention is C: 0.06% or more and 0.09% or less, Si: 0.30% or less, Mn: 1.7% or more and 2.3% or less.
- the reasons for limiting the components of this cold-rolled steel sheet will be described.
- “%” of each component in the steel sheet of the present invention indicates “mass%” unless otherwise specified.
- C is one of the important basic components of steel.
- the volume fraction of the austenite ( ⁇ ) phase when heated in the ( ⁇ (ferrite) + ⁇ (austenite)) region and thus martensite after transformation.
- ⁇ austenite
- Mechanical properties such as strength are greatly influenced by the martensite fraction and the hardness of the martensite phase. If the C content is less than 0.06%, the martensite phase is difficult to be generated. On the other hand, if it exceeds 0.09%, the spot weldability deteriorates, so the C content is 0.06% or more and 0.09%. The following.
- Si 0.30% or less
- Si is an element that improves the workability such as elongation by reducing the amount of solid solution C in the ferrite ( ⁇ ) phase, but the inclusion of Si amount exceeding 0.30% improves spot weldability and plating quality. Therefore, the upper limit of the Si content is 0.30%.
- Mn 1.7% to 2.3%
- Mn is an important element as a basic component because it concentrates in the austenite ( ⁇ ) phase and promotes martensitic transformation.
- the Mn content is less than 1.7%, the effect is not obtained.
- the Mn content exceeds 2.3%, spot weldability and plating quality are remarkably impaired. Therefore, the Mn content is 1.7% or more and 2.3%. The following.
- P 0.001% to 0.020%
- P is an element effective in achieving high strength at a low cost. In order to achieve high strength, the P content is set to 0.001% or more. On the other hand, if P is contained in excess of 0.020%, spot weldability is remarkably impaired, so the upper limit is made 0.020%.
- S not only causes hot cracking during hot rolling, but also induces breakage in the nugget of the spot weld, so it is desirable to reduce it as much as possible. Therefore, in the present invention, the S content is suppressed to 0.010% or less.
- Mo 0.05% or more and 0.30% or less
- Mo is an important element for obtaining a composite structure of ferrite and martensite without impairing the plating quality, and at least the Mo content needs to be 0.05%.
- Mo contains Mo exceeding 0.30%, there is little further effect and the rise of manufacturing cost is caused, so 0.30% is made the upper limit.
- N 0.005% or less
- Al 0.01% or more and 0.10% or less
- Al is an effective element that fixes N as AlN as a deoxidizer in the steelmaking process and causes aging deterioration, and in order to fully exhibit the effect, the Al content is 0.01% or more. To do. On the other hand, if the Al content exceeds 0.10%, the production cost increases, so the Al content must be suppressed to 0.10% or less.
- the balance consists of Fe and inevitable impurities.
- the cold-rolled steel sheet constituting the high-strength hot-dip galvanized steel sheet of the present invention described above has a specific structure and physical properties, and details thereof will be described below.
- the area ratio of martensite mainly controls the C content in steel to 0.06% or more and 0.09% or less, and the heating temperature during annealing (the annealing temperature, which means the highest steel sheet temperature) Can be adjusted to 730 ° C. or higher and 880 ° C. or lower.
- the area ratio of ferrite is 50% or more.
- the area ratio of this ferrite is preferably 60% or more.
- the area ratio of ferrite can be adjusted mainly by controlling the C content in the steel to 0.06% or more and 0.09% or less.
- the area ratio of ferrite is the ratio of the area of the ferrite phase in the observation area
- the area ratio of martensite is the ratio of the area of the martensite phase in the observation area.
- the actual ferrite area ratio and martensite area ratio can be calculated as follows. That is, after the plate thickness direction cross section of the obtained steel plate is polished, it is corroded with 3% nital (alcohol solution containing 3% nitric acid). Then, the vicinity of the 1 ⁇ 4 position in the plate thickness direction is observed at a magnification of about 1500 times using an SEM (scanning electron microscope), and the obtained image is analyzed using general image analysis software. The area ratio can be obtained. In the obtained gray scale image, ferrite is gray (underlying structure), and martensite can be identified as a white structure.
- the remaining structure other than the aforementioned martensite and ferrite is not particularly limited.
- the amount of internal oxidation of the surface layer of the steel sheet on the surface of the cold-rolled steel sheet is 0.05 g / m 2 or less per side.
- oxidizable elements such as Si, Mn, Al, and P contained in the steel sheet are oxidized in a hot rolling process, an annealing process in a CGL (continuous hot dip galvanizing line), or the like.
- the coiling temperature at the time of hot rolling should not be increased excessively or in the annealing atmosphere in CGL It is necessary not to raise the dew point excessively.
- winding-up temperature does not exceed 700 degreeC for the descalability improvement.
- the base metal surface layer part on the surface of the cold-rolled steel sheet refers to a surface layer part in contact with the hot dip galvanized layer, and can be said to be a steel sheet surface layer part directly under the plated layer after removing the plated layer.
- the surface iron surface layer portion in which the internal oxidation amount is defined refers to a range from the interface between the hot dip galvanized layer and the steel plate to 50 ⁇ m in the thickness direction of the steel plate.
- This amount of internal oxidation can be obtained by measuring the amount of oxygen in the steel after the plating layer is removed.
- the method for removing the plating layer is not particularly limited, but any removal by acid or alkali is possible. However, care should be taken not to remove the base iron and to oxidize the surface after the removal by using an inhibitor (base iron dissolution inhibitor) together.
- the plating layer can be removed with 195 cc of a 20 mass% NaOH-10 mass% triethanolamine aqueous solution and 7 cc of a 35 mass% H 2 O 2 aqueous solution.
- the plating layer can be removed with a dilute HCl solution containing an inhibitor.
- the amount of oxide in steel is measured, for example, by “impulse furnace melting-infrared absorption method”.
- the high-strength hot-dip galvanized steel sheet of the present invention can improve the adhesion at the impact test of the processed part by containing an intermetallic compound at the interface between the plating layer and the steel sheet.
- This intermetallic compound contains Fe 2 Al 5 having an Al of 0.03 g / m 2 or more and 0.12 g / m 2 or less and an average particle size of less than 0.7 ⁇ m.
- the FeAl intermetallic compound can be formed at the interface between the plating layer and the steel sheet with a fine and dense property.
- the amount of intermetallic compound produced depends on the activity of Al in the molten zinc bath, it can be increased mainly by increasing the Al concentration. However, if there is too much Al, impact resistance characteristics deteriorate, so it is necessary to control to an appropriate amount.
- Average particle size of Fe 2 Al 5 is less than 0.7 ⁇ m
- the average particle diameter of Fe 2 Al 5 is 0.7 ⁇ m or more, since the hard FeAl intermetallic compound is excessively grown, it is difficult to ensure the plating appearance of the high-strength hot-dip galvanized steel sheet of the present invention.
- the average particle size of Fe 2 Al 5 is less than 0.7 ⁇ m, the formation of FeAl intermetallic compounds at the interface between the plating layer and the steel sheet is suppressed, so that spot weldability is improved. Therefore, the average particle size is set to less than 0.7 ⁇ m.
- the average particle diameter of this Fe 2 Al 5 can be adjusted by controlling the Al concentration in the plating bath.
- the average particle diameter is not particularly limited, but can be measured by a measuring method set to a predetermined magnification using a scanning electron microscope (SEM).
- SEM scanning electron microscope
- the hot-dip galvanized layer constituting the high-strength hot-dip galvanized steel sheet of the present invention contains Zn and 0.15% ⁇ Al% ⁇ 0.30%.
- Al% indicates the Al content (mass%) of the hot-dip galvanized layer.
- Al concentration in the hot dip zinc bath of plating. If this Al concentration is too low, Fe elution will occur and dross will precipitate. As a result, the appearance deteriorates.
- Al exceeds 0.30%, a large amount of an oxide film of Al is formed on the surface of the plating layer, and spot weldability deteriorates.
- the hot-dip galvanized layer can also contain Pb, Sb, Mg, Ni, Mn, Si, Ti, Cr, Sr, and Ca.
- Ra of hot dip galvanized layer surface 0.8 ⁇ m or more and 1.6 ⁇ m or less
- surface roughness Ra of the hot dip galvanized layer surface is less than 0.8 ⁇ m, oil is not retained during pressing, and press formability during processing is poor.
- Ra is set to 0.8 ⁇ m or more and 1.6 ⁇ m or less.
- ⁇ Ra is adjusted by using a dull roll that has been processed with high roughness in the skin pass process to ensure an appropriate amount.
- shot dull EDT (Electron discharged texture), EBT (Electron beam texturing), or a scratch dull processed dull roll is used.
- said Ra is not specifically limited, Based on JISB0601 (2001), it can measure with a roughness meter.
- Zinc base bottom surface orientation ratio: Zn (002) / (004) is 30% or more and 60% or less
- the glossiness (G value) is set to 750 or more and 850 or less
- the rate Zn (002) / (004) is 30% or more and 60% or less.
- the solidification structure of the above plating mainly when the Al concentration in the bath reaches a predetermined value, an Fe-Al intermetallic compound is formed at the interface between the plating phase and the steel sheet, and the solidification structure of zinc develops soundly.
- the Al concentration is too high, the solidified structure is formed in a dendritic shape, so that the surface is uneven and the glossiness (G value) is reduced to less than 750.
- the Al concentration is low, the formation of the Fe—Al intermetallic compound at the interface is suppressed, and at the same time, the Fe—Zn alloy layer develops.
- the solidification structure is refined and smoothed, whereby the glossiness (G value) increases more than necessary and exceeds 850.
- the gloss level (G value) is less than 750, the beauty cannot be ensured and the appearance deteriorates.
- the glossiness (G value) exceeds 850, the inner plate member is too smooth and oil is not retained in the inner plate member at the time of pressing, resulting in poor moldability.
- the glossiness (G value) is not particularly limited, but can be measured with a glossometer based on JIS Z 8741 (1997).
- the desired surface texture can be ensured by controlling the texture with a skin pass or the like.
- the zinc base bottom surface orientation ratio Zn (002) / (004) is less than 30%, the crystal size when the zinc solidifies immediately after plating becomes small when the orientation of the zinc crystal is relatively random. Since it is too smooth and oil is not held in the inner plate member during pressing, the moldability is poor. When the orientation ratio of the basal plane of the zinc base exceeds 60%, the orientation of the basal plane of the Zn crystal is too high and the crystal grains are likely to grow. As a result, the dendritic arm develops. Deteriorate.
- the zinc base bottom surface orientation ratio Zn (002) / (004) is not particularly limited, but can be obtained by measuring the X-ray diffraction intensity.
- Zn has an hcp structure and is usually easily oriented on the basal plane, but the measurement of the zinc basal plane orientation ratio shown by the formula (1) shows how much the crystals are randomly oriented.
- the gloss, crystal size, and surface roughness are affected by the degree of orientation of the solidified structure, so accurate control of the zinc base orientation ratio is not only the surface properties of high-strength hot-dip galvanized steel sheets, but also press workability. It is extremely important when controlling.
- the orientation is adjusted by securing an appropriate amount of the Fe—Al alloy layer at the plating phase / steel plate interface and suppressing the formation of the Fe—Zn alloy layer that serves as a precipitation nucleus of the zinc solidified structure.
- the tensile strength (TS) is set to 590 MPa or more and 690 MPa or less in order to mainly secure the strength of the inner plate.
- a high-strength hot-dip galvanized steel sheet having a tensile strength (TS) of 590 MPa or more and 690 MPa or less can be obtained by passing the CGL under appropriate annealing conditions for the material of the steel sheet component in the present invention.
- the annealing temperature is preferably about 800 to 850 ° C. because annealing in a two-phase region is necessary.
- a high-strength hot-dip galvanized steel sheet can be produced by the following method. First, steel having the above component composition is made into a slab by continuous casting, the slab is heated, and scale removal and rough rolling are performed. Next, after cooling, finish rolling, cooling, winding, pickling, and cold rolling are performed. Next, the steel sheet is annealed and hot-dip galvanized in a continuous hot-dip galvanizing facility.
- the heating time, heating temperature, rough rolling conditions, cooling conditions, finish rolling conditions, winding conditions, etc. when heating the slab can be appropriately set based on common technical knowledge.
- the annealing conditions of the steel sheet affect the tensile strength of the high-strength hot-dip galvanized steel sheet.
- the heating temperature during annealing (the annealing temperature, which means the highest steel sheet temperature) is set to 730 ° C. or higher and 880 ° C. or lower, preferably 750 It sets to 850 degreeC or more.
- the annealing atmosphere may be adjusted as appropriate, but in the present invention, it is preferable to adjust the dew point to 0 ° C. or lower. Exceeding 0 ° C. is not preferable because the surface of the furnace body tends to become brittle.
- the hydrogen concentration in the annealing atmosphere is preferably 1 vol% or more and 50 vol% or less. If the hydrogen concentration is 1 vol or more, it is preferable because the surface of the steel sheet is activated, and if the hydrogen concentration exceeds 50 vol%, it is not preferable because it is economically disadvantageous.
- Normally containing N 2 is other than hydrogen. Inevitable components include CO 2 , CO, O 2 and the like.
- the intrusion plate temperature which is the temperature of the steel plate when the annealed steel plate enters the plating bath, is not particularly limited, but is preferably a plating bath temperature (bath temperature) of ⁇ 20 ° C. or higher and a bath temperature of + 20 ° C. or lower. If the infiltration plate temperature is in the above range, the change in bath temperature is small, and it is easy to perform desired hot dip galvanization continuously.
- the Al content in the hot-dip galvanized layer and the Al content in the intermetallic compound tend to decrease by increasing the bath temperature. Moreover, the glossiness of the surface of the hot dip galvanized layer tends to increase as the bath temperature is increased.
- the composition of the plating bath into which the annealed steel sheet enters is not limited as long as it contains Al in addition to Zn, and may contain other components as necessary.
- the concentration of Al in the plating bath is not particularly limited, but is preferably 0.16% by mass or more and 0.25% by mass or less. It is preferable that the Al concentration is in the above range because an Fe—Al alloy phase is formed and the Fe—Zn alloy phase is suppressed.
- the glossiness can be adjusted by the Al concentration in the plating bath. When the Al concentration in the plating bath is lowered, Fe—Zn crystals are formed slightly at the interface instead of Fe—Al, and they become Zn solidification nucleation sites, so that a large number of zinc crystals are generated, and the zinc crystal orientation is random.
- a more preferable Al concentration is 0.19% by mass or more and 0.22% by mass or less. Since the Al concentration also affects the Al content in the hot-dip galvanized layer and the Al content in the intermetallic compound, it is preferable to determine the Al concentration in consideration of these contents.
- the temperature of the plating bath is not particularly limited, but is preferably 430 ° C. or higher and 470 ° C. or lower.
- a bath temperature of 430 ° C. or higher is preferred for the reason that the zinc bath dissolves stably without solidification, and a bath temperature of 470 ° C. or lower is preferred for the reason that Fe elution is small and dross defects are reduced.
- a more preferable range of the bath temperature is 450 ° C. or higher and 465 ° C. or lower.
- the immersion time when the steel sheet is immersed in the plating bath is not particularly limited, but is preferably 0.1 second or more and 5 seconds or less. When the immersion time is in the above range, a desired hot dip galvanized layer is easily formed on the surface of the steel plate.
- the amount of plating adhesion is adjusted by gas jet wiping or the like.
- the plating adhesion amount is not particularly limited, but is preferably in the range of 20 g / m 2 or more and 120 g / m 2 or less. If it is less than 20 g / m 2 , it may be difficult to ensure corrosion resistance. On the other hand, if it exceeds 120 g / m 2 , the plating peel resistance may deteriorate.
- temper rolling is performed.
- the type of roll used for the SK treatment is not particularly limited, and an Electro-Discharge Texture roll (EDT roll), an Electron Beam Texture roll (EBT roll), a shotdal roll, a topochrome roll, or the like can be used.
- the rolling reduction rate during SK treatment is not particularly limited, but is preferably 0.7 to 0.9%. If the SK rolling reduction is in the above range, the surface roughness can be easily adjusted to the above preferable range. Further, if it is outside the above range, the press workability may be deteriorated without forming a dull eye that holds the rolling oil, and the yield strength may also be lowered.
- the cooling rate after the steel sheet is lifted from the plating bath is preferably ⁇ 5 ° C./second or more and ⁇ 30 ° C./second or less.
- the high-strength hot-dip galvanized steel sheet of the present invention is preferably used for applications in which a coating film is formed on the surface of a hot-dip galvanized layer because it has excellent post-painting corrosion resistance after press working.
- the high-strength hot-dip galvanized steel sheet of the present invention is excellent in plating adhesion even when applied to applications requiring strict workability, and does not significantly reduce corrosion resistance and mechanical properties. Examples of applications in which strict processability is required and a coating film is formed include automotive steel plates such as automobile outer plates and inner plates.
- the formation method of a coating film is not specifically limited, After performing a chemical conversion treatment to the surface of a hot-dip galvanized layer and forming a chemical conversion film, it is preferable to form a coating film on this chemical conversion film.
- Either a coating type or a reaction type can be used as the chemical conversion treatment liquid.
- the component contained in a chemical conversion liquid is not specifically limited, either a chromate processing liquid may be used and a chromium free chemical conversion liquid may be used.
- the chemical conversion film may be a single layer or a multilayer.
- the coating method for forming the coating film is not particularly limited, but examples of the coating method include electrodeposition coating, roll coater coating, curtain flow coating, and spray coating.
- the coating method include electrodeposition coating, roll coater coating, curtain flow coating, and spray coating.
- means such as hot air drying, infrared heating, induction heating and the like can be used.
- the high-strength hot-dip galvanized steel sheet of the present invention is excellent in spot weldability, and is therefore suitable for welding with super high tensile strength of 980 MPa class or higher, which is difficult to weld.
- the steel sheet as shown in Table 1 was removed by pickling the hot-rolled steel sheet produced by winding at a coiling temperature of 650 ° C. or less, and cold rolled at a cold rolling reduction of 50%.
- a cold-rolled material having a thickness of 1.2 mm or 2.3 mm was produced.
- the line speed (LS) was 60 mpm or 100 mpm.
- the bath temperature and the Al concentration in the bath were appropriately changed.
- temper rolling SK treatment
- the amount of adhesion was 55 g / m 2 per side. The results are shown in Table 2.
- the obtained high-strength hot-dip galvanized steel sheet was first visually judged as good ( ⁇ ) when there was no poor appearance such as uneven plating as the appearance (plating appearance), and poor ( ⁇ ) when there was.
- the Zn crystal orientation on the (002) plane and the (004) plane on X-ray were measured, and the zinc base surface orientation ratio on the surface of the hot-dip galvanized layer Zn (002) / (004) was measured.
- the Al content of the hot-dip galvanized layer was peeled off with dilute hydrochloric acid containing an inhibitor, and quantified by ICP emission analysis.
- the FeAl-enriched layer amount (total mass of the Fe 2 Al 5 alloy layer) was determined by peeling the galvanized layer with fuming nitric acid and quantifying the FeAl-enriched layer amount as Al by ICP emission analysis.
- the average particle diameter of Fe 2 Al 5 constituting the intermetallic compound was measured by observing it at a magnification of 5000 using a scanning electron microscope (SEM).
- composition of the intermetallic compound was Fe 2 Al 5 was determined by thin film X-ray diffraction.
- the amount of internal oxidation was obtained by measuring the amount of oxygen in the steel after the plating layer was removed.
- the amount of oxide in steel was measured by “impulse furnace melting-infrared absorption method”.
- the steel of the sample obtained by mechanically polishing the front and back surface portions of the sample from which the plating layer has been removed 100 ⁇ m or more. Separately measure the amount of oxygen in the medium, and subtract from the amount of oxygen in the sample with the plating layer removed to calculate the amount of increase in oxidation only on the surface layer, and convert it to the amount per unit area to obtain the value of internal oxidation It was.
- the cross section in the plate thickness direction of the obtained steel plate was polished and then corroded with 3% nital (3% nitric acid alcohol solution). Then, the vicinity of the 1 ⁇ 4 position in the plate thickness direction is observed at a magnification of about 1500 times using an SEM (scanning electron microscope), and the obtained image is analyzed using image analysis software, and the area ratio of each phase. Asked. In the obtained gray scale image, ferrite was gray (underlying structure), and martensite was identified as a white structure.
- ⁇ ⁇ ⁇ ⁇ Spot weldability was evaluated by spot welding continuous dots. Specifically, after degreasing the steel plate first, using a DR electrode having a tip diameter of 6 mm, a pressing force of 250 kgf, an initial pressurizing time of 35 cy / 60 Hz, an energizing time of 18 cy / 60 Hz, a holding time of 1 cy / 60 Hz, a resting time of 16 cy / 60 Hz, Under the conditions of a welding current of 10 kA and a nugget diameter ⁇ 4 ⁇ tmm (t is the plate thickness), the number of continuous hit points during spot welding was investigated for a 0.8 mm material. The number of continuous hit points ⁇ 2000 points was good ( ⁇ ), and less than 2000 was bad ( ⁇ ).
- An impact resistance test was performed in which a punch with a hit diameter of 5/8 inch was dropped from a height of 1 m, and peeling with a Nichiban tape was observed. Those with peeling were marked with x, and those without peeling were marked with ⁇ .
- a JIS No. 5 tensile test piece is taken from the sample in a direction 90 ° with respect to the rolling direction, and a tensile test is performed at a constant crosshead speed of 10 mm / min in accordance with the provisions of JIS Z 2241 to obtain a tensile strength (TS (MPa)).
- TS tensile strength
- the high-strength hot-dip galvanized steel sheet of the present invention had very good characteristics despite the press work, no plating peeling, and excellent impact resistance adhesion. Moreover, the corrosion resistance after coating was also good. Moreover, spot weldability and plating appearance were also good.
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Abstract
Description
[1]質量%で、C:0.06%以上0.09%以下、Si:0.30%以下、Mn:1.7%以上2.3%以下、P:0.001%以上0.020%以下、S:0.010%以下、Mo:0.05%以上0.30%以下、N:0.005%以下及びAl:0.01%以上0.10%以下を含有し、残部がFe及び不可避不純物の組成からなり、マルテンサイト面積率が7%以上25%未満、フェライト面積率が50%以上の組織を有し、地鉄表層部の内部酸化量が片面当たり0.05g/m2以下である冷延鋼板と、
該冷延鋼板上に形成された0.03g/m2以上0.12g/m2以下のAlを含み、かつ平均粒径1μm未満のFe2Al5を含む金属間化合物と、
該金属間化合物上に形成され、0.15%≦Al%≦0.30%(Al%は、溶融亜鉛めっき層のAlの含有量(質量%)を示す。)を含有し、表面粗さRaが0.8μm以上1.6μm以下であり、光沢度(G値)が750以上850以下であり、以下の式(1)で規定される亜鉛基底面配向率Zn(002)/(004)が30%以上60%以下である溶融亜鉛めっき層と、を有することを特徴とする高強度溶融亜鉛めっき鋼板。
本発明の高強度溶融亜鉛めっき鋼板を構成する冷延鋼板は、C:0.06%以上0.09%以下、Si:0.30%以下、Mn:1.7%以上2.3%以下、P:0.001%以上0.020%以下、S:0.010%以下、Mo:0.05%以上0.30%以下、N:0.005%以下、Al:0.01%以上0.10%以下を含有し、残部がFe及び不可避不純物の組成からなる。ここでは、まず、この冷延鋼板の成分限定理由について説明する。なお、本発明の鋼板中の各成分の「%」は、特に説明のない限り、「質量%」を示す。
Cは鋼の重要な基本成分の一つであり、とくに本発明では、(α(フェライト)+γ(オーステナイト))域に加熱したときのオーステナイト(γ)相の体積率、ひいては変態後のマルテンサイトの量に影響するために重要な元素である。そして、強度などの機械的特性は、このマルテンサイト分率とマルテンサイト相の硬度によって大きく左右される。C含有量が、0.06%未満ではマルテンサイト相が生成しにくく、一方、0.09%超ではスポット溶接性が劣化することから、C含有量は、0.06%以上0.09%以下とする。
Siはフェライト(α)相中の固溶C量を減少させることにより、伸びなどの加工性を向上させる元素であるが、0.30%超のSi量の含有はスポット溶接性およびめっき品質を損ねるので、Si含有量は上限を0.30%とする。
Mnは、本発明においてはオーステナイト(γ)相に濃化し、マルテンサイト変態を促す効果があり、基本成分として重要な元素である。ただし、Mn含有量が1.7%未満ではその効果がなく、一方、2.3%を超えるとスポット溶接性およびめっき品質を著しく損なうので、Mn含有量は1.7%以上2.3%以下とする。
Pは、高強度化を安価に達成するうえで有効な元素であり、高強度化を実現するために、P含有量は、0.001%以上とする。一方、Pを0.020%超えて含有するとスポット溶接性を著しく損なうので上限を0.020%とする。
Sは熱延時の熱間割れを引き起こすもとになるほか、スポット溶接部のナゲット内破断を誘発するので、極力低減することが望ましい。よって、本発明では、S含有量は0.010%以下に抑制する。
Moはめっき品質を損なうことなく、フェライト+マルテンサイトの複合組織を得るのに重要な元素であり、少なくともMo含有量を0.05%とすることは必要である。しかし、0.30%を超えてMoを含有しても、さらなる効果が少なく、製造コストの上昇を招くので0.30%を上限とする。
Nは時効劣化をもたらすほか、降伏点(降伏比)の上昇、降伏伸びの発生を招くことから、N含有量は0.005%以下に抑制する必要がある。
Alは製鋼工程での脱酸剤として、また時効劣化を引き起こすNをAlNとして固定する有効な元素であり、その効果を十分に発揮するためにも、Al含有量は、0.01%以上とする。一方、0.10%を超えてAlを含有すると製造コストの上昇を招くので、Al含有量は0.10%以下に抑える必要がある。
本発明の高強度溶融亜鉛めっき鋼板を構成する冷延鋼板では、マルテンサイトの面積率が7%未満になると、降伏比YRが顕著に上昇する。一方、マルテンサイトの面積率が25%以上になると、局部延性が低下するために全伸びELが低下する。したがって、本発明の高強度溶融亜鉛めっき鋼板を構成する冷延鋼板では、マルテンサイトの面積率は、7%以上25%未満とする。このマルテンサイトの面積率は、好ましくは7%以上22%以下、より好ましくは7%以上20%以下である。マルテンサイトの面積率は、主に鋼中のC含有量を0.06%以上0.09%以下に制御することと共に、焼鈍の際の加熱温度(焼鈍温度であり、鋼板最高到達温度を意味する。)を730℃以上880℃以下に設定することで調整することができる。
本発明の高強度溶融亜鉛めっき鋼板を構成する冷延鋼板では、フェライトの面積率が50%未満になると、全伸びELの低下が顕著になる。したがって、フェライトの面積率は、50%以上とする。このフェライトの面積率は、好ましくは60%以上である。フェライトの面積率は、主に鋼中のC含有量を0.06%以上0.09%以下に制御することで調整することができる。
鋼板表層部(地鉄表層部)における内部酸化の状態を制御することで、高強度溶融亜鉛めっき鋼板における加工部の耐衝撃性試験時のめっき密着性と塗装後耐食性を優れたものとすることができると共に、スポット溶接性も優れたものとすることができる。良好なめっき密着性の確保のためには、冷延鋼板の表面における地鉄表層部の内部酸化量が片面当たり0.05g/m2以下であることが必要である。
次に、前述した冷延鋼板上に形成される金属間化合物の構成について説明する。
本発明の高強度溶融亜鉛めっき鋼板は、めっき層と鋼板との界面に金属間化合物を含有することで、加工部の耐衝撃性試験時の密着性を向上させることができる。この金属間化合物は、0.03g/m2以上0.12g/m2以下のAlを有し、かつ平均粒径0.7μm未満のFe2Al5を含有する。これにより、本発明の高強度溶融亜鉛めっき鋼板では、FeAl金属間化合物をめっき層と鋼板の界面に微細かつ緻密な性状で形成させることができる。
Fe2Al5の平均粒径が0.7μm以上の場合は硬質のFeAl金属間化合物が過剰成長しているため、本発明の高強度溶融亜鉛めっき鋼板のめっき外観性の確保が難しくなる。一方、Fe2Al5の平均粒径が0.7μm未満であれば、めっき層と鋼板の界面のFeAl金属間化合物の生成が抑制されるため、スポット溶接性は向上する。そのため、平均粒径は0.7μm未満にする。
次に、冷延鋼板の表面に溶融亜鉛めっき処理を行うことによって形成され、前述した金属間化合物上に形成される溶融亜鉛めっき層の構成について説明する。
本発明の高強度溶融亜鉛めっき鋼板を構成する溶融亜鉛めっき層は、Znおよび0.15%≦Al%≦0.30%を含有する。ここで、Al%は、溶融亜鉛めっき層のAlの含有量(質量%)を示す。Alが0.15%未満であるようにするためには、めっきの溶融亜鉛浴中のAl濃度を低くする必要があり、このAl濃度が低過ぎると、Feの溶出があるため、ドロスが析出して外観性が劣化する。Alが0.30%超えであるとめっき層表面にAlの酸化皮膜が多量に形成されてスポット溶接性が劣化する。また、溶融亜鉛めっき層は、Pb、Sb、Mg、Ni、Mn、Si、Ti、Cr、Sr、Caを含有することもできる。
溶融亜鉛めっき層表面の表面粗さRaが0.8μm未満であると、プレス時に油が保持されずに加工時のプレス成形性が劣る。一方、Raが1.6μm超えであると、塗装後鮮映性や密着性が劣る。そのため、Raは、0.8μm以上1.6μm以下とする。
本発明の高強度溶融亜鉛めっき鋼板では、めっきの凝固組織を制御するために、まず、光沢度(G値)を750以上850以下とし、以下の式(1)で規定される亜鉛基底面配向率Zn(002)/(004)を30%以上60%以下とする。これにより、hcp(hexagonal close-packed:六方最密充填構造)の亜鉛を凝固する際に基底面に配向し易くすることができる。
本発明の高強度溶融亜鉛めっき鋼板では、引張強度(TS)は主に内板の強度を確保するため、590MPa以上690MPa以下とする。このような引張強度(TS)が590MPa以上690MPa以下の高強度溶融亜鉛めっき鋼板は、本発明での鋼板成分の材料について適正な焼鈍条件でCGL通板することで得ることが出来る。焼鈍温度としては、2相域での焼鈍が必要であるため、800~850℃程度の温度とすることが好ましい。
自動車のサイドメンバーなどの加工部が自動車の衝突時の衝撃による加工を模擬するため、90°曲げした部分を対象とする。この部分をいわゆるデュポン試験器で耐衝撃性を調査し、テープ剥離して評価する。塗装後耐食性はこの曲げた部分を化成処理・電着塗装を実施し、クロスカットを施しSST試験で膨れ腐食幅で評価する。上述のように界面のFe-Al金属間化合物の量が必要以上に確保出来ていれば、良好なめっき密着性(耐衝撃密着性)を確保出来る。
続いて、高強度溶融亜鉛めっき鋼板の製造方法について説明する。例えば、以下の方法で高強度溶融亜鉛めっき鋼板を製造可能である。先ず、上記のような成分組成を有する鋼を連続鋳造によりスラブとし、該スラブを加熱し、スケール除去および粗圧延を施す。次いで、冷却した後、仕上げ圧延し、冷却し、巻取り、次いで、酸洗、冷間圧延を行う。次いで、連続式溶融亜鉛めっき設備において、鋼板の焼鈍および溶融亜鉛めっき処理を行う。
×:密着不良
不良(×):膨れ有り
Claims (1)
- 質量%で、C:0.06%以上0.09%以下、Si:0.30%以下、Mn:1.7%以上2.3%以下、P:0.001%以上0.020%以下、S:0.010%以下、Mo:0.05%以上0.30%以下、N:0.005%以下、Al:0.01%以上0.10%以下を含有し、残部がFe及び不可避不純物の組成からなり、
マルテンサイト面積率が7%以上25%未満、フェライト面積率が50%以上の組織を有し、
地鉄表層部の内部酸化量が片面当たり0.05g/m2以下である冷延鋼板と、
該冷延鋼板上に形成され、0.03g/m2以上0.12g/m2以下のAlを含み、かつ平均粒径0.7μm未満のFe2Al5を含む金属間化合物と、
該金属間化合物上に形成され、
0.15%≦Al%≦0.30%(Al%は、溶融亜鉛めっき層のAlの含有量(質量%)を示す。)を含有し、
表面粗さRaが0.8μm以上1.6μm以下であり、
光沢度(G値)が750以上850以下であり、
以下の式(1)で規定される亜鉛基底面配向率Zn(002)/(004)が30%以上60%以下である溶融亜鉛めっき層と、
を有する高強度溶融亜鉛めっき鋼板。
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