CN113227428A - 高强度热浸镀锌钢板及其制造方法 - Google Patents
高强度热浸镀锌钢板及其制造方法 Download PDFInfo
- Publication number
- CN113227428A CN113227428A CN201980086541.1A CN201980086541A CN113227428A CN 113227428 A CN113227428 A CN 113227428A CN 201980086541 A CN201980086541 A CN 201980086541A CN 113227428 A CN113227428 A CN 113227428A
- Authority
- CN
- China
- Prior art keywords
- steel sheet
- hot
- dip galvanized
- less
- precipitates
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- 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
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
- B21C47/02—Winding-up or coiling
-
- 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
- B32B15/013—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 a metal other than iron or aluminium
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/76—Adjusting the composition of the atmosphere
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/001—Heat treatment of ferrous alloys containing Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
-
- 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
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- 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
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment
-
- 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
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
-
- 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
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
-
- 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
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
-
- 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
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—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
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
本发明提供一种高强度且扩孔性和抗延迟断裂特性优异的高强度热浸镀锌钢板及其制造方法。一种高强度热浸镀锌钢板,其具有特定的成分组成和钢组织;上述钢组织是以面积率计铁素体与上贝氏体的合计为0~15%,下贝氏体与马氏体合计为80~100%,残余奥氏体为0~10%,在从钢板表层至板厚方向上100~300μm的范围中,以等效圆直径计粒径100~2000nm的析出物为109~1012个/m2;并且,从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比为0.20~0.80,并且,在钢板表面具有热浸镀锌层。
Description
技术领域
本发明涉及适用于汽车用构件的高强度镀锌钢板及其制造方法。
背景技术
从改善汽车的碰撞安全性和提高燃油经济性的观点出发,对可用于汽车用零件的钢板要求高强度化。特别是从确保乘车人的安全性的观点出发,用于包围驾驶室的钢板需要较高的YS。这样的零件会暴露在腐蚀环境中,因此,也要求高防锈性能和腐蚀环境下的抗延迟断裂特性。而且,这些零件大多被实施了拉伸法兰加工,因而也需要拉伸法兰性优异,要求以高水平兼顾这些多个特性。
作为具有高强度和高加工性的镀覆钢板,专利文献1中公开了耐氢脆化(具有与抗延迟断裂特性相同的意义)、弯折性优异的拉伸强度为770MPa以上的热浸镀锌钢板。专利文献1中还公开了如下热浸镀锌钢板:在该热浸镀锌钢板中,与镀覆层的界面直接接触的软质层的厚度D与存在与钢板表层部的包含Si、Mn中的一种以上的氧化物到镀覆/铁基界面的深度d满足d/4≤D≤2d。
专利文献2中公开了一种高强度热浸镀锌钢板,其在延展性和强度不受损的情况下使抗延迟断裂特性变优异且即使是薄板状态下抗延迟断裂特性的各向异性也少。专利文献2中还公开了如下高强度热浸镀锌钢板:为了防止以母材钢板的表层部为起点的延迟断裂,将母材钢板的表层部制成硬质组织少的脱碳层,并且,在该脱碳层中高密度地分散作为氢阱位点发挥功能的微细的氧化物。
现有技术文献
专利文献
专利文献1:国际公开2011/025042号
专利文献2:国际公开2013/047760号
发明内容
但是,专利文献1和专利文献2中,尚不存在以高水平同时实现屈服强度(YS)、拉伸强度(TS)、扩孔性、抗延迟断裂特性的例子。本发明正是鉴于上述课题而完成的,其目的在于提供高强度且扩孔性和抗延迟断裂特性优异的高强度热浸镀锌钢板及其制造方法。在本发明中,高强度是指YS为1000MPa以上且TS为1300MPa以上。优异的扩孔性是指,在TS为1300MPa以上且小于1450MPa时扩孔率为40%以上,在TS为1450MPa以上且小于1600MPa时扩孔率为30%以上,在TS为1600MPa以上且小于1750MPa时扩孔率为25%以上。而优异的抗延迟断裂特性是指,即使在pH3的盐酸中浸渍96小时,也不会产生断裂。
本发明人等为了解决上述课题,进行了深入研究。其结果是,发现通过下述的钢组织能够以高水平同时实现YS、TS、扩孔性、抗延迟断裂特性,该钢组织为:将从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比调节到适当的范围,使之为0.20~0.80;并且,以面积率计,铁素体与上贝氏体的合计为0~15%,下贝氏体与马氏体的合计为80~100%,残余奥氏体为0~10%,在从钢板表层至板厚方向上100~300μm的范围中,以等效圆直径计,粒径100~2000nm的析出物为109~1012个/m2。
本发明正是基于上述见解而完成,其特征如下所述。
[1]一种高强度热浸镀锌钢板,具有下述的成分组成和下述的钢组织,并在钢板表面具有热浸镀锌层;所述成分组成是以质量%计含有C:0.12~0.35%、Si:0.01~3.0%、Mn:2.0~4.0%、P:0.100%以下(不含0)、S:0.02%以下(不含0)、Al:0.01~1.50%,剩余部分由Fe和不可避免的杂质构成;所述钢组织是,以面积率计,铁素体与上贝氏体的合计为0~15%,下贝氏体与马氏体的合计为80~100%,残余奥氏体为0~10%,在从钢板表层至板厚方向上100~300μm的范围中,以等效圆直径计,粒径100~2000nm的析出物为109~1012个/m2;并且,从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比为0.20~0.80。
[2]根据[1]所述的高强度热浸镀锌钢板,其中,在上述粒径100~2000nm的析出物之中,存在于旧奥氏体晶界上的析出物的个数N1与存在于其他位置的析出物的个数N2的比N1/N2为1/3以下。
[3]根据[1]或[2]所述的高强度热浸镀锌钢板,其中,上述成分组成进一步以质量%计含有选自Ti:0.005~0.20%、Nb:0.005~0.20%、V:0.005~2.0%、Mo:0.005~2.0%中的一种以上的元素。
[4]根据[1]至[3]中任1项所述的高强度热浸镀锌钢板,其中,上述成分组成进一步以质量%计含有选自Cr:0.005~2.0%、Ni:0.005~2.0%、Cu:0.005~2.0%、B:0.0002~0.0050%、Ca:0.001~0.005%、REM:0.001~0.005%、Sn:0.001~0.05%、Sb:0.001~0.05%中的一种以上的元素。
[5]根据[1]至[4]中任1项所述的高强度热浸镀锌钢板,其中,上述热浸镀锌层为合金化热浸镀锌层。
[6]一种高强度热浸镀锌钢板的制造方法,其中,对具有[1]、[3]或[4]中任1项所述成分组成的坯材实施热轧后进行冷却,实施在590℃以下的温度卷绕的热轧,制造热轧板,对上述热轧板进行酸洗;接下来,在O2≤1体积%且O2/H2≤0.2(体积%比)的气氛中,以最高到达温度为600~750℃、且最高到达温度和保持时间满足下述(1)式的条件实施热处理;接下来,以20%以上的压下率实施冷轧;接下来进行退火,即加热至Ac3~950℃,在该温度区域中以露点为-35~+20℃保持10~600s后,以3℃/s以上的平均冷却速度冷却至550℃,在400~550℃保持5~300s;接下来,进行热浸镀锌处理或进一步实施合金化处理,其后冷却至室温。
21000≥(273+T)×[20+log10(t/3600)]···(1)
上述(1)式中,T为最高到达温度(℃),t为保持时间(s)。
[7]根据[6]所述的高强度热浸镀锌钢板的制造方法,其中,在上述加热至Ac3~950℃的工序中,在500~700℃以10℃/s以上的平均加热速度进行加热。
根据本发明,可以得到扩孔性和抗延迟断裂特性优异的高强度热浸镀锌钢板。具有这样的特性的高强度热浸镀锌钢板可以很好地用作汽车零件用坯材。
附图说明
图1是用硝酸酒精溶液进行了腐蚀处理的钢板剖面的SEM图像。
具体实施方式
以下,对本发明的实施方式进行说明。本发明不限定于以下的实施方式。首先,对本实施方式涉及的高强度热浸镀锌钢板(以下有时也称为“钢板”)的成分组成进行说明。成分组成的说明中的元素的含量的单位的“%”是指“质量%”。
C:0.12~0.35%
C是使马氏体和包含碳化物的贝氏体生成从而有效地使TS上升的元素。如果C量小于0.12%,则无法得到使TS上升的效果,无法提高钢板的强度,不能得到本实施方式涉及的钢板的钢组织。因此,C量必须为0.12%以上。C量优选为0.13%以上。另一方面,如果C量大于0.35%,则马氏体会硬化,抗延迟断裂特性会降低。因此,C量必须为0.35%以下。C量优选为0.32%以下,更优选为0.30%以下。
Si:0.01~3.0%
Si是通过固溶强化和马氏体的回火的抑制而提高TS,得到优异的抗延迟断裂特性所必需的元素。为了得到这样的效果,Si量必须为0.01%以上。Si量优选为0.1%以上,更优选为0.2%以上。另一方面,如果Si量大于3.0%,则会导致铁素体生成过剩,无法得到本实施方式涉及的钢板的钢组织。因此,Si量必须为3.0%以下。Si量优选为2.5%以下,更优选为2.0%以下。
Mn:2.0~4.0%
Mn是使马氏体和包含碳化物的贝氏体生成而有效地使TS上升的元素。为了得到这样的效果,Mn量必须为2.0%以上。Mn量优选为2.1%以上,更优选为2.2%以上。另一方面,如果Mn量大于4.0%,则钢会脆化,无法得到本实施方式涉及的钢板的抗延迟断裂特性。因此,Mn量必须为4.0%以下。Mn量优选为3.7%以下,更优选为3.4%以下。
P:0.100%以下(不含0)
P会使晶界脆化,使抗延迟断裂特性劣化。因此,优选尽可能地减少P量,但在本实施方式涉及的钢板中可容许至0.100%。P量的下限无需规定,但是如果钢板的P量小于0.0005%,则在精炼中会产生巨大的负荷,生产效率会降低。因此,P量的下限优选为0.0005%。
S:0.02%以下(不含0)
S使夹杂物增加而使抗延迟断裂特性劣化。因此,优选尽可能地减少S量,但在本实施方式涉及的钢板中可容许至0.02%。S量的下限无需规定,但是如果钢板的S量小于0.0001%,则在精炼中会产生巨大的负荷,生产效率会降低。因此,S量的下限优选为0.0001%。
Al:0.01~1.50%
Al作为脱氧剂而发挥作用,因此,优选在脱氧工序中进行添加。为了得到这样的效果,Al量必须为0.01%以上。Al量优选为0.015%以上。另一方面,如果Al量大于1.50%,则会导致铁素体生成过剩,无法得到本实施方式涉及的钢板的钢组织。因此,Al量必须为1.50%以下。Al量优选为1.00%以下,更优选为0.70%以下。
进而,本实施方式涉及的钢板根据需要,也可以含有选自以下的元素中的1种以上。
Ti:0.005~0.20%、Nb:0.005~0.20%、V:0.005~2.0%、Mo:0.005~2.0%
Ti、Nb、V、Mo通过形成微细碳化物,从而抑制在热轧后的热处理时的粗粒化。由此,退火后的粒径会微细化,可以进一步提高钢板的扩孔性。这样的效果可以通过使选自Ti、Nb、V、Mo中的1种以上为上述下限量以上而得到。另一方面,如果它们的含量大于各自的上限值,则钢中的固溶碳量会降低,铁素体会大量生成,因此,会有无法得到钢板的钢组织的情况。因此,选自Ti、Nb、V、Mo中的1种以上优选为Ti:0.005%~0.20%、Nb:0.005%~0.20%、V:0.005%~2.0%、Mo:0.005%~2.0%的范围。
Cr:0.005~2.0%、Ni:0.005~2.0%、Cu:0.005~2.0%、B:0.0002~0.0050%、Ca:0.001~0.005%、REM:0.001~0.005%、Sn:0.001~0.05%、Sb:0.001~0.05%
Cr、Ni、Cu是使马氏体、贝氏体生成而对高强度化有效的元素。为了得到这样的效果,Cr、Ni、Cu量优选为0.005%以上。另一方面,如果Cr、Ni、Cu量大于2.0%,则残留γ会大量的生成,会有无法得到钢板的钢组织的情况。因此,Cr、Ni、Cu量优选为2.0%以下。
B是提高钢板的淬硬性,使马氏体、贝氏体生成,对高强度化有效的元素。为了得到这样的效果,B量优选为0.0002%以上。另一方面,如果B量大于0.0050%,则夹杂物会增加,会有抗延迟断裂特性降低的情况。因此,B量优选为0.0050%以下。
Ca、REM是通过夹杂物的形态控制而对抗延迟断裂特性的提高有效的元素。为了得到这样的效果,Ca、REM量优选为0.001%以上。另一方面,如果Ca、REM量大于0.005%,则夹杂物量会增加,会有抗延迟断裂特性降低的情况。因此,Ca、REM量优选为0.005%以下。
Sn、Sb是抑制脱氮、脱硼等而对钢的强度降低抑制有效的元素。为了得到这样的效果,Sn、Sb量优选为0.001%以上。另一方面,如果Sn、Sb量大于0.05%,则会有无法得到钢板表层的C量分布的情况。因此,Sn、Sb量优选为0.05%以下。
因此,选自Cr、Ni、Cu、B、Ca、REM、Sn、Sb中的1种以上优选为Cr:0.005~2.0%、Ni:0.005~2.0%、Cu:0.005~2.0%、B:0.0002~0.0050%、Ca:0.001~0.005%、REM:0.001~0.005%、Sb:0.001~0.05%、Sn:0.001~0.05%。
本实施方式涉及的钢板含有上述成分组成,上述成分组成以外的剩余部分包含Fe(铁)和不可避免的杂质。上述剩余部分优选为Fe和不可避免的杂质。在以小于下限值而包含上述任意成分的情况下,将该成分视为不可避免的杂质。作为不可避免的杂质,可以包含0.01%以下的N。进而,可以包含合计0.002%以下的其他元素即Zr、Mg、La、Ce。
从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比:0.20~0.80
本实施方式中,钢板表层的C量分布极其重要,通过使钢板表层附近的C量少、且使从表层至70μm的区域的C量的比在一定的范围,从而可以使表层附近的应力得到缓和、得到优异的抗延迟断裂特性。因此,从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比必须为0.20~0.80。从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比优选为0.25以上。从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比优选为0.70以下,更优选为0.60以下。从钢板表层至板厚方向上5μm的位置的平均C量和从钢板表层至板厚方向上70μm的位置的平均C量可以使用辉光放电发光分光分析法(GDS)进行测定。钢板表层是指热浸镀锌层与钢板的界面。从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比是使板厚方向上5μm的位置的平均C量除以从钢板表层至板厚方向上70μm的位置的平均C量而算出的。即,从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比可按照下述(2)式而算出。
(从钢板表层至板厚方向上5μm的位置的平均C量)/(从钢板表层至板厚方向上70μm的位置的平均C量)···(2)
接下来,对本实施方式涉及的钢板的钢组织进行说明。在钢板的钢组织中,以面积率计,铁素体与上贝氏体的合计为0~15%,下贝氏体与马氏体合计为80~100%,残余奥氏体为0~10%,在从钢板表层至板厚方向上100~300μm的范围中,以等效圆直径计,粒径100~2000nm的析出物为109~1012个/m2。
铁素体与上贝氏体的合计:0~15%
铁素体与上贝氏体会使YS和扩孔性降低,因此优选使它们减少。在本实施方式涉及的钢板中,可以容许至以面积率计为15%。因此,铁素体和上贝氏体的合计必须为15%以下。铁素体和上贝氏体的合计优选为10%以下,更优选为5%以下。铁素体和上贝氏体的合计的下限为0%。
下贝氏体与马氏体的合计:80~100%
从兼顾TS和优异的抗延迟断裂特性的观点出发,下贝氏体与马氏体是必需的组织。为了得到这样的效果,下贝氏体与马氏体的合计以面积率计必须为80%以上。下贝氏体与马氏体的合计优选为85%以上,更优选为90%以上。下贝氏体与马氏体的合计的上限为100%。
残余奥氏体:0~10%
以提高延展性为目的,可以含有残余奥氏体,但如果以面积率计大于10%,则抗延迟断裂特性会降低。因此,残余奥氏体以面积率计必须为10%以下。残余奥氏体优选为8%以下,更优选为6%以下。残余奥氏体的下限为0%。
在从钢板表层至板厚方向上100~300μm的范围中的、以等效圆直径计的、粒径100~2000nm的析出物:109~1012个/m2
本实施方式涉及的钢板中,析出物极其重要,在钢板表层附近100~300μm的范围中,以等效圆直径计,粒径100~2000nm的析出物的个数密度必须为109个/m2以上,必须为1012个/m2以下。由此,可以得到钢板的优异的抗延迟断裂特性。其机制尚不明确,但可推测为析出物导致的氢阱效果。钢板表层是指热浸镀锌层与钢板的界面。
另一方面,如果以等效圆直径计粒径小于100nm的析出物或该析出物的个数密度小于109个/m2,则无法得到该效果。以等效圆直径计粒径大于2000nm的析出物会产生以该析出物为起点的延迟断裂,因此,析出物的大小的上限设为以等效圆直径计2000nm。因此,在从钢板表层至板厚方向上100~300μm的范围中,以等效圆直径计粒径100~2000nm的析出物的个数密度必须为109个/m2以上。该析出物的个数密度优选为5×109以上。另一方面,如果析出物的个数密度大于1012个/m2,则扩孔性会降低。因此,在从钢板表层至板厚方向上100~300μm的范围中,以等效圆直径计粒径100~2000nm的析出物的个数密度必须为1012个/m2以下。该析出物的个数密度优选为5×1011以下。该析出物优选为渗碳体。
在粒径为100~2000nm的析出物之中的、旧奥氏体晶界上的析出物的个数N1与存在于其他位置的析出物的个数N2的比N1/N2:1/3以下
通过使以等效圆直径计粒径为100nm~2000nm的析出物在旧奥氏体的晶粒内大量生成,从而可以进一步提高钢板的扩孔性。因此,在粒径100nm~2000nm的析出物之中,旧奥氏体晶界上的析出物的个数N1与存在于其他位置的析出物的个数N2的比N1/N2优选为1/3以下。由此,可以进一步提高钢板的扩孔性。该比N1/N2更优选为1/4以下。
图1是用硝酸酒精溶液进行了腐蚀处理的钢板剖面的SEM图像。图1中,符号10表示旧奥氏体晶界上的析出物,符号12表示旧奥氏体晶界内的析出物。如图1所示,在旧奥氏体晶界上和晶粒内,析出物可以作为黑点被观察到。
本实施方式中,铁素体、上贝氏体、下贝氏体、马氏体的面积率是指各组织的面积占观察面积的比例。这些面积率是如下求出的:从退火后的钢板切出样品,对与轧制方向平行的板厚剖面进行抛光后,用1质量%硝酸酒精溶液(nital)进行腐蚀,用SEM(扫描型电子显微镜)以1500倍的倍率分别对钢板表面附近和从钢板表面至沿板厚方向上300μm~400μm的范围拍摄3~10个视野,使用Media Cybernetics公司制的Image-Pro,根据得到的图像数据求出各组织的面积率,将这些视野的面积率的平均值作为各组织的面积率。
该图像数据中,铁素体为黑、上贝氏体为不含碳化物的暗灰色、下贝氏体为包含107个/mm2以上的取向碳化物的灰色或暗灰色,由此可以进行区别。碳化物为白色的点或线状,由此可以进行区别。马氏体为包含未取向的碳化物的暗灰色、灰色、明灰色,或不包含碳化物的块状的白色,由此可以进行区别。残余奥氏体虽然同为白色,但可以通过后述的方法与马氏体进行区别。虽然本实施方式涉及的钢板基本上不含有珠光体,但其为黑色和白色的层状组织,由此可以进行区别。
残余奥氏体的体积率可如下求出:将退火后的钢板研磨至板厚的1/4后,利用化学抛光进一步抛光0.1mm,对于抛光后的面,利用X射线衍射装置,使用Mo的Kα线测定fcc铁(奥氏体)的(200)面、(220)面、(311)面以及bcc铁(铁素体)的(200)面、(211)面、(220)面的积分反射强度,根据来自fcc铁的各面的积分反射强度的强度与来自bcc铁的各面的积分反射强度的比,求出残余奥氏体的体积率,将其作为残余奥氏体的面积率。通过这样的方式算出残余奥氏体的面积率,从而可以区别残余奥氏体与马氏体。
以等效圆直径计粒径为100~2000nm的析出物的个数与钢组织的面积率的测定相同,对从钢板表层至板厚方向上100~300μm的范围内的剖面进行抛光,使用SEM以1500倍的倍率对用1质量%硝酸酒精溶液腐蚀过的面拍照3~10个视野,根据得到的图像数据,对析出物的等效圆直径和个数进行计数,将这些视野的平均值作为钢板中析出物的个数的代表值,算出1m2的析出物的个数。进而,旧奥氏体晶界上的析出物的个数(N1)与其它位置的旧奥氏体晶界内的析出物的个数(N2)的比N1/N2也是根据SEM图像数据对旧奥氏体晶界上的析出物的个数(N1)和旧奥氏体晶界内的析出物的个数(N2)进行计数,基于这些视野的平均值算出N1/N2。
从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量通过GDS而测定。利用盐酸酸洗等除去镀锌层,露出钢板表层,之后,对于钢板表面,以等离子用气体为Ar、气体压力为600Pa、高频输出为35W、测定间隔为0.1s的条件进行GDS测定。测定从表面直至80μm以上的深度位置为止,求出对应于5μm位置和70μm位置的溅射时间中的C的检测强度的比。
接下来,对本实施方式涉及的钢板的制造方法进行说明。本实施方式涉及的钢板可如下制造:对具有上述成分的坯材实施热轧,之后进行冷却,在590℃以下的温度实施卷绕热轧,制造热轧板,对上述热轧板进行酸洗;接下来,在O2≤1体积%且O2/H2≤0.2的气氛中,以最高到达温度为600~750℃、且最高到达温度T和保持时间t满足下述(1)式的条件实施热处理;接下来,以20%以上的压下率实施冷轧;接下来进行退火,即加热至Ac3~950℃,在该温度区域中以露点为-35~+20℃保持10~600s后,以3℃/s以上的平均冷却速度冷却至550℃以下,在400~550℃保持5~300s;接下来,实施热浸镀锌处理或进一步实施合金化处理,其后冷却至室温。在上述退火中的、加热至Ac3~950℃的加热工序中,优选500~700℃的平均加热速度为10℃/s以上。以下,对高强度热浸镀锌钢板的制造方法进行详细说明。制造条件所示的温度均为钢板的表面温度。
21000≥(273+T)×[20+log10(t/3600)]···(1)
(1)式中,T为最高到达温度(℃),t为保持时间(s)。t是指T~T-20℃的温度范围中的保持时间。
卷绕温度:590℃以下
如果卷绕温度大于590℃,则内部氧化会过剩,无法得到退火后的钢板表层的C量分布。因此,将卷绕温度设为590℃以下。下限没有规定,但从形状稳定性的的观点出发,优选为400℃。
气氛:O2≤1体积%且O2/H2≤0.2(体积%比)
热轧板的热处理中,将气氛中的氧设为O2≤1体积%且O2/H2≤0.2(体积%比)。由此,内部氧化得到抑制,可以得到退火后的钢板表层的C量分布。因此,热轧板的热处理的气氛必须为O2≤1体积%且O2/H2≤0.2。该气氛中除O2、H2以外的剩余部分优选为N2或氩。
最高到达温度:600~750℃、并且最高到达温度T与保持时间T:满足下述(1)式
21000≥(273+T)×[20+log10(t/3600)]···(1)
上述(1)式中,T为最高到达温度(℃),t为保持时间(s)。
热轧板的热处理中,如果最高到达温度小于600℃,则渗碳体等析出物的成长会不充分,在退火后无法得到100nm~2000nm的析出物。因此,最高到达温度必须为600℃以上。另一方面,如果最高到达温度大于750℃、或最高到达温度T与保持时间t不满足上述(1)式,则析出物会粗大化,在退火后无法得到100nm~2000nm的析出物。因此,最高到达温度必须为750℃以下,并且最高到达温度T(℃)与保持时间t(s)必须为满足上述(1)式的值。
冷轧压下率:20%以上
如果冷轧压下率小于20%,则铁素体会生成,无法得到本实施方式涉及的钢板的钢组织。因此,冷轧压下率必须为20%以上。冷轧压下率优选为30%以上。冷轧压下率的上限没有规定,但从形状稳定性的的观点出发,优选为90%以下。
500~700℃的平均加热速度:10℃/s以上
通过在退火中于500℃~700℃时以10℃/s以上的平均加热速度进行升温,从而晶界的析出物会减少,可以进一步提高扩孔性。因此,500℃~700℃的平均加热速度优选为10℃/s以上。平均加热速度是使500℃至700℃的温度差200℃除以从500℃加热到700℃所需的时间来算出的。
退火温度:Ac3~950℃
如果退火温度小于Ac3,则奥氏体的生成不充分,无法得到本实施方式涉及的钢板的钢组织。因此,退火温度必须为Ac3以上。另一方面,如果退火温度大于950℃,则析出物会溶解,无法得到本实施方式涉及的钢板的钢组织。因此,退火温度必须为950℃以下。
退火保持时间:10~600s
如果退火保持时间小于10s,则奥氏体的生成不充分,无法得到本实施方式涉及的钢板的钢组织。因此,退火保持时间必须为10s以上。退火保持时间优选为20s以上,更优选为30s以上。另一方面,如果退火保持时间大于600s,则内部氧化会过剩,无法得到本实施方式涉及的钢板的强度和表层的C量分布。因此,退火保持时间必须为600s以下。退火保持时间优选为500s以下,更优选为400s以下。
退火温度中的露点:-35~+20℃
如果退火时的露点小于-35℃,则钢板表层的C的氧化反应会不充分,无法得到本实施方式涉及的钢板的表层的C量分布。因此,退火温度中的露点必须为-35℃以上。另一方面,如果露点大于+20℃,则内部氧化会过剩,无法得到本实施方式涉及的钢板的强度和表层的C量分布。因此,退火温度中的露点必须为+20℃以下。退火温度中的露点优选为+15℃以下,更优选为+10℃以下。
从退火温度至550℃为止的平均冷却速度:3℃/s以上
如果从退火温度至550℃为止的平均冷却速度小于3℃/s,则铁素体的生成会过剩,无法得到本实施方式涉及的钢板的钢组织。因此,从退火温度至550℃为止的平均冷却速度必须为3℃/s以上。从退火温度至550℃为止的平均冷却速度优选为5℃/s以上。从退火温度至550℃为止的平均冷却速度的上限可以没有规定,但是从形状稳定性的观点出发,优选小于100℃/s。平均冷却速度通过使退火温度与550℃的温度差除以从退火温度至550℃的冷却所需的时间而算出。
保持温度:400~550℃
如果保持温度小于400℃,则会产生包含碳化物的贝氏体、回火马氏体,在之后的镀覆处理、镀覆合金化处理时会导致碳化物的粗大化,无法得到本实施方式涉及的钢板的微观组织。因此,保持温度必须为400℃以上。另一方面,如果保持温度大于550℃,则会过剩地生成铁素体、珠光体,无法得到本实施方式涉及的钢板的钢组织。因此,保持温度必须为550℃以下。
400~550℃的保持时间:5~300s
通过在400℃~550℃保持5秒以上,从而进行钢板表层的贝氏体转变,可以得到本实施方式涉及的钢板的表层的C量分布。另一方面,如果保持时间小于5s,则这样的效果不充分,无法得到本实施方式涉及的钢板的表层的C量分布。因此,400℃~550℃的保持时间必须为5s以上。400℃~550℃的保持时间优选为10s以上。如果400℃~550℃的保持时间大于300s,则贝氏体的生成会过剩,无法得到本实施方式涉及的钢板的钢组织。因此,400℃~550℃的保持时间必须为300s以下。400℃~550℃的保持时间优选为200s以下,更优选为120s以下。在保持中,只要在400℃~550℃的范围即可,温度不必恒定,可以冷却、加热。
其它制造条件没有特别限定,例如可以按以下的条件进行。为了防止宏观偏析,坯材优选以连续铸造法进行制造。也可以用造块法、薄坯材铸造法进行制造。对坯材进行热轧可以将坯材暂时冷却至室温,之后再加热,进行热轧。或者,也可以不将坯材冷却至室温,而是装入加热炉中进行热轧。或者,也可以适用在进行了些许的保热后直接热轧的节能工艺。在加热坯材的情况下,优选以坯材温度为1100℃以上1300℃以下的方式进行加热。通过将坯材温度加热至1100℃以上,可以使碳化物融解,抑制轧制负荷的增大。通过使坯材温度为1300℃以下,可以抑制氧化烧损的增大。坯材温度为坯材表面的温度。
在对坯材进行热轧时,可以对粗轧后的粗块进行加热。或使粗块彼此接合,连续进行精轧,即,也可以适用连续轧制工艺。进而,在热轧中,为了轧制负荷的降低、形状·材质的均匀化,优选在精轧的整个流程或一部分流程中,进行摩擦系数为0.10~0.25的润滑轧制。
对于卷绕后的钢板,通过酸洗等除去鳞片,然后可以实施冷轧、退火、热浸镀锌。镀覆后冷却至室温,为了控制表面、屈服强度(YS),优选以伸长率1%以下实施调质轧制。为了调节形状、YS,可以实施校平。
实施例
以下,基于实施例对本发明进行具体的说明。将钢(剩余部分为Fe和不可避免的杂质)在实验室的真空融解炉中熔制,轧制,制成钢坯材。钢的成分组成示于表1。
[表1]
将这些钢坯材加热至1250℃后进行粗轧、热轧,实施热轧板的热处理。接下来,冷轧至1.4mm,制成冷轧板。将得到的冷轧板供给于退火。在退火中,于实验室中使用热处理和镀覆处理装置,制作热浸镀锌钢板(GI)和合金化热浸镀锌钢板(GA)1~2。热浸镀锌钢板是通过浸渍在465℃的镀覆浴中,在钢板两面形成每个单面的附着量为40~60g/m2的镀覆层而制作的。合金化热浸镀锌钢板是通过在上述镀覆后进一步进行于540℃保持1~60s的合金化处理而制作的。在镀覆处理后,以8℃/s冷却至室温,其后实施伸长率0.1%的调质轧制。热浸镀锌钢板和合金化热浸镀锌钢板的制造条件示于表2。
对于得到的热浸镀锌钢板和合金化热浸镀锌钢板,按照以下的试验方法评价拉伸特性、扩孔性、抗延迟断裂特性。
<拉伸试验>
在相对于轧制方向为直角方向上,从退火板采取JIS(日本工业标准)5号拉伸试验片(JIS Z2201:1998),依据形变速度为10-3/s的JIS(日本工业标准)Z 2241:2011的规定进行拉伸试验,求出YS和TS。YS在0.2%耐力评价下评价。本实施例中,将YS为1000MPa以上、TS为1300MPa以上作为合格。
<扩孔试验>
依据日本钢铁联盟标准JFST1001,实施扩孔试验,测定λ。详细而言,在镀覆钢板上冲压出直径10mm的孔后,以固定周围的状态将60°圆锥的冲头挤压到孔中,测定产生龟裂的极限时的孔的直径。根据下述(3)式,求出极限扩孔率λ(%)。
极限扩孔率λ(%)={(Df-D0)/D0}×100···(3)
上述(3)式中,Df为龟裂发生极限时的孔的直径(mm),D0为初期孔的直径(mm)。在该扩孔试验中,在TS为1300MPa以上且小于1450MPa时扩孔率为40%以上,在TS为1450MPa以上且小于1600MPa时扩孔率为30%以上,在TS为1600MPa以上且小于1750MPa时扩孔率为25%以上这几种情况,判定为扩孔性优异。
<抗延迟断裂特性>
将与轧制方向平行的方向作为宽度方向,从退火板采取宽度为30mm、长度为110mm的试验片。将该试验片以棱线与轧制方向平行的方式、以7mm的弯折半径进行90゜V弯折加工,用螺栓按回弹量的多少拧紧,浸渍在pH值为3的盐酸中,保持96hr后,调查有无裂纹产生。本实施例中,将无法确认到裂纹的情况判定为抗延迟断裂特性优异,在表3的抗延迟断裂特性一列中记为“优”。另一方面,将确认到裂纹的情况判定为抗延迟断裂特性差,在表3的抗延迟断裂特性一列中记为“劣”。
钢板的钢组织、从表层至100~300μm的范围中的以等效圆直径计的粒径为100~2000nm的析出物的个数、从钢板表层至板厚方向上5μm的位置的平均C量与从钢板表层至板厚方向上70μm的位置的平均C量的比、以及粒径100~2000nm的析出物中存在于旧奥氏体晶界上的析出物的个数N1与存在于其他位置的析出物的个数N2的比N1/N2按照前述的方法进行测定。它们的评价结果与钢板的钢组织等示于表3。
[表3]
*1V(F+UB):铁素体和上贝氏体的合计面积率、V(M+LB):马氏体和下贝氏体的的合计面积率、V(RA):残余奥氏体的面积率、V(O):上述以外的组织的合计面积率
*2ρ(i):存在于从表层至100~300μm位置的以等效圆直径计的粒径为100~2000m的析出物的个数密度
*3表层C比:从表层至5μm位置的平均C量与从表层至70μm位置的平均C量的比
如表3所示,可以确认:在发明例中,可以得到YS为1000MPa以上、TS为1300MPa以上且具有优异的扩孔性和优异的抗延迟断裂特性的高强度镀锌钢板和合金化热浸镀锌钢板。另一方面,在本发明的范围外的比较例无法得到优异的YS、TS、扩孔性、抗延迟断裂特性中的1者以上。
附图标记说明
10 旧奥氏体晶界上的析出物
12 旧奥氏体晶界内的析出物
Claims (7)
1.一种高强度热浸镀锌钢板,具有下述的成分组成和下述的钢组织;
所述成分组成是以质量%计含有
C:0.12~0.35%、
Si:0.01~3.0%、
Mn:2.0~4.0%、
P:0.100%以下且不含0、
S:0.02%以下且不含0、
Al:0.01~1.50%,剩余部分由Fe和不可避免的杂质构成;
所述钢组织是以面积率计,铁素体与上贝氏体的合计为0~15%,下贝氏体与马氏体的合计为80~100%,残余奥氏体为0~10%,在从钢板表层至板厚方向100~300μm的范围中,以等效圆直径计粒径为100~2000nm的析出物为109~1012个/m2;
并且,从钢板表层至板厚方向5μm的位置的平均C量与从钢板表层至板厚方向70μm的位置的平均C量的比为0.20~0.80;
并且,在钢板表面具有热浸镀锌层。
2.根据权利要求1所述的高强度热浸镀锌钢板,其中,在所述粒径为100~2000nm的析出物中,存在于旧奥氏体晶界上的析出物的个数N1与存在于其他位置的析出物的个数N2的比N1/N2为1/3以下。
3.根据权利要求1或2所述的高强度热浸镀锌钢板,其中,
所述成分组成进一步以质量%计含有选自
Ti:0.005~0.20%、
Nb:0.005~0.20%、
V:0.005~2.0%、
Mo:0.005~2.0%
中的一种以上的元素。
4.根据权利要求1~3中任一项所述的高强度热浸镀锌钢板,其中,
所述成分组成进一步以质量%计含有选自
Cr:0.005~2.0%、
Ni:0.005~2.0%、
Cu:0.005~2.0%、
B:0.0002~0.0050%、
Ca:0.001~0.005%、
REM:0.001~0.005%、
Sn:0.001~0.05%、
Sb:0.001~0.05%
中的一种以上的元素。
5.根据权利要求1~4中任一项所述的高强度热浸镀锌钢板,其中,所述热浸镀锌层为合金化热浸镀锌层。
6.一种高强度热浸镀锌钢板的制造方法,其中,对具有权利要求1、3或4中任一项所述的成分组成的坯材实施热轧后进行冷却,实施在590℃以下的温度卷绕的热轧,制造热轧板,对所述热轧板进行酸洗,接下来,在O2≤1体积%且O2/H2≤0.2(体积%比)的气氛中,以最高到达温度为600~750℃且最高到达温度和保持时间满足下述(1)式的条件实施热处理,接下来,以20%以上的压下率实施冷轧,接下来,加热至Ac3~950℃,以该温度区域的露点为-35~+20℃条件下保持10~600s后,以3℃/s以上的平均冷却速度冷却至550℃,在400~550℃保持5~300s而进行退火,接下来,进行热浸镀锌处理或进一步实施合金化处理,其后冷却至室温;
21000≥(273+T)×[20+log 10(t/3600)]···(1)
所述(1)式中,T为最高到达温度(℃),t为保持时间(s)。
7.根据权利要求6所述的高强度热浸镀锌钢板的制造方法,其中,在所述加热至Ac3~950℃的工序中,在500~700℃以10℃/s以上的平均加热速度进行加热。
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2018-242710 | 2018-12-26 | ||
JP2018242710 | 2018-12-26 | ||
PCT/JP2019/033080 WO2020136988A1 (ja) | 2018-12-26 | 2019-08-23 | 高強度溶融亜鉛めっき鋼板およびその製造方法 |
Publications (2)
Publication Number | Publication Date |
---|---|
CN113227428A true CN113227428A (zh) | 2021-08-06 |
CN113227428B CN113227428B (zh) | 2022-12-27 |
Family
ID=71127087
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN201980086541.1A Active CN113227428B (zh) | 2018-12-26 | 2019-08-23 | 高强度热浸镀锌钢板及其制造方法 |
Country Status (7)
Country | Link |
---|---|
US (1) | US11390932B2 (zh) |
EP (1) | EP3904552B1 (zh) |
JP (1) | JP6760524B1 (zh) |
KR (1) | KR102544884B1 (zh) |
CN (1) | CN113227428B (zh) |
MX (1) | MX2021007759A (zh) |
WO (1) | WO2020136988A1 (zh) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN116043120A (zh) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | 一种成型性能优异的1000MPa级冷轧复相钢及其制备方法 |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20230161507A (ko) * | 2021-06-24 | 2023-11-27 | 제이에프이 스틸 가부시키가이샤 | 용융 아연 도금 강판 및 그 제조 방법, 그리고 부재 |
KR20240036626A (ko) * | 2021-08-31 | 2024-03-20 | 제이에프이 스틸 가부시키가이샤 | 강판, 부재 및 그들의 제조 방법 |
CN117836458A (zh) * | 2021-08-31 | 2024-04-05 | 杰富意钢铁株式会社 | 钢板、构件和它们的制造方法 |
WO2023182279A1 (ja) * | 2022-03-25 | 2023-09-28 | 日本製鉄株式会社 | 冷延鋼板及び冷延鋼板の製造方法 |
WO2024122122A1 (ja) * | 2022-12-09 | 2024-06-13 | 日本製鉄株式会社 | 鋼板及びホットスタンプ成形体 |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2011025042A1 (ja) * | 2009-08-31 | 2011-03-03 | 新日本製鐵株式会社 | 高強度溶融亜鉛めっき鋼板及びその製造方法 |
EP2540854A1 (en) * | 2010-02-26 | 2013-01-02 | JFE Steel Corporation | Super-high strength cold-rolled steel sheet having excellent bending properties |
CN105814227A (zh) * | 2013-12-18 | 2016-07-27 | 杰富意钢铁株式会社 | 高强度热浸镀锌钢板及其制造方法 |
KR101726090B1 (ko) * | 2015-12-22 | 2017-04-12 | 주식회사 포스코 | 표면품질 및 도금밀착성이 우수한 고강도 용융아연도금강판 및 그 제조방법 |
WO2018055425A1 (en) * | 2016-09-22 | 2018-03-29 | Arcelormittal | High strength and high formability steel sheet and manufacturing method |
CN108603269A (zh) * | 2016-02-10 | 2018-09-28 | 杰富意钢铁株式会社 | 高强度镀锌钢板及其制造方法 |
WO2018186335A1 (ja) * | 2017-04-05 | 2018-10-11 | Jfeスチール株式会社 | 高強度冷延鋼板およびその製造方法 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5207480B2 (ja) | 2008-05-30 | 2013-06-12 | 株式会社ナントー精密 | インプラント体及びその製造方法並びに歯科用インプラント |
KR20110025042A (ko) | 2009-09-03 | 2011-03-09 | 주식회사 신영 | 프레스 라인의 공용화 그리퍼 |
JP5765092B2 (ja) * | 2010-07-15 | 2015-08-19 | Jfeスチール株式会社 | 延性と穴広げ性に優れた高降伏比高強度溶融亜鉛めっき鋼板およびその製造方法 |
CA2850462C (en) | 2011-09-30 | 2016-10-11 | Nippon Steel & Sumitomo Metal Corporation | High-strength hot-dip galvanized steel sheet having excellent delayed fracture resistance and manufacturing method thereof |
KR101601001B1 (ko) * | 2011-09-30 | 2016-03-08 | 신닛테츠스미킨 카부시키카이샤 | 고강도 용융 아연 도금 강판 |
KR101930185B1 (ko) * | 2015-01-15 | 2018-12-17 | 제이에프이 스틸 가부시키가이샤 | 고강도 용융 아연 도금 강판 및 그 제조 방법 |
WO2016129550A1 (ja) * | 2015-02-13 | 2016-08-18 | 株式会社神戸製鋼所 | 切断端部での耐遅れ破壊特性に優れた超高強度鋼板 |
JP2016153524A (ja) | 2015-02-13 | 2016-08-25 | 株式会社神戸製鋼所 | 切断端部での耐遅れ破壊特性に優れた超高強度鋼板 |
MX2018011754A (es) | 2016-03-31 | 2019-02-18 | Jfe Steel Corp | Lamina de acero, lamina de acero recubierta, metodo para la produccion de lamina de acero laminada en caliente, metodo para la produccion de lamina de acero laminada en frio extra-dura, metodo para la produccion de lamina de acero, y metodo para la produccion de lamina de acero recubierta. |
MX2019009513A (es) | 2017-02-10 | 2019-11-05 | Jfe Steel Corp | Lamina de acero galvanizada de alta resistencia y metodo para producir la misma. |
-
2019
- 2019-08-23 WO PCT/JP2019/033080 patent/WO2020136988A1/ja unknown
- 2019-08-23 MX MX2021007759A patent/MX2021007759A/es unknown
- 2019-08-23 JP JP2019568129A patent/JP6760524B1/ja active Active
- 2019-08-23 CN CN201980086541.1A patent/CN113227428B/zh active Active
- 2019-08-23 EP EP19902584.2A patent/EP3904552B1/en active Active
- 2019-08-23 US US17/417,858 patent/US11390932B2/en active Active
- 2019-08-23 KR KR1020217019655A patent/KR102544884B1/ko active IP Right Grant
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2011025042A1 (ja) * | 2009-08-31 | 2011-03-03 | 新日本製鐵株式会社 | 高強度溶融亜鉛めっき鋼板及びその製造方法 |
EP2540854A1 (en) * | 2010-02-26 | 2013-01-02 | JFE Steel Corporation | Super-high strength cold-rolled steel sheet having excellent bending properties |
CN105814227A (zh) * | 2013-12-18 | 2016-07-27 | 杰富意钢铁株式会社 | 高强度热浸镀锌钢板及其制造方法 |
KR101726090B1 (ko) * | 2015-12-22 | 2017-04-12 | 주식회사 포스코 | 표면품질 및 도금밀착성이 우수한 고강도 용융아연도금강판 및 그 제조방법 |
CN108603269A (zh) * | 2016-02-10 | 2018-09-28 | 杰富意钢铁株式会社 | 高强度镀锌钢板及其制造方法 |
WO2018055425A1 (en) * | 2016-09-22 | 2018-03-29 | Arcelormittal | High strength and high formability steel sheet and manufacturing method |
WO2018186335A1 (ja) * | 2017-04-05 | 2018-10-11 | Jfeスチール株式会社 | 高強度冷延鋼板およびその製造方法 |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN116043120A (zh) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | 一种成型性能优异的1000MPa级冷轧复相钢及其制备方法 |
CN116043120B (zh) * | 2023-01-19 | 2023-10-27 | 鞍钢股份有限公司 | 一种成型性能优异的1000MPa级冷轧复相钢及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
MX2021007759A (es) | 2021-08-05 |
US20220074013A1 (en) | 2022-03-10 |
CN113227428B (zh) | 2022-12-27 |
EP3904552B1 (en) | 2023-11-01 |
JP6760524B1 (ja) | 2020-09-23 |
KR102544884B1 (ko) | 2023-06-19 |
KR20210095189A (ko) | 2021-07-30 |
EP3904552A1 (en) | 2021-11-03 |
EP3904552A4 (en) | 2021-12-01 |
WO2020136988A1 (ja) | 2020-07-02 |
US11390932B2 (en) | 2022-07-19 |
JPWO2020136988A1 (ja) | 2021-02-18 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
CN113227428B (zh) | 高强度热浸镀锌钢板及其制造方法 | |
WO2020080553A9 (ja) | 熱延鋼板およびその製造方法 | |
WO2022149502A1 (ja) | 鋼板及びその製造方法 | |
US20190112682A1 (en) | Steel sheet, coated steel sheet, method for producing hot-rolled steel sheet, method for producing full-hard cold-rolled steel sheet, method for producing heat-treated sheet, method for producing steel sheet, and method for producing coated steel sheet | |
CN112955575B (zh) | 高强度构件、高强度构件的制造方法和高强度构件用钢板的制造方法 | |
CN113227430B (zh) | 高强度热浸镀锌钢板及其制造方法 | |
JP7136335B2 (ja) | 高強度鋼板及びその製造方法 | |
CN115244204B (zh) | 热轧钢板 | |
CN113227429B (zh) | 高强度热浸镀锌钢板及其制造方法 | |
CN115087754B (zh) | 高强度钢板及其制造方法 | |
JP7136336B2 (ja) | 高強度鋼板及びその製造方法 | |
CN115151672A (zh) | 钢板、构件和它们的制造方法 | |
WO2021141006A1 (ja) | 鋼板およびその製造方法 | |
CN115151673A (zh) | 钢板、构件和它们的制造方法 | |
CN115210398A (zh) | 钢板、构件和它们的制造方法 | |
JP7401826B2 (ja) | 鋼板、及び鋼板の製造方法 | |
CN114945690B (zh) | 钢板及其制造方法 | |
CN114761596B (zh) | 钢板及其制造方法 | |
CN113544301B (zh) | 钢板 | |
WO2022079970A1 (ja) | 溶融亜鉛めっき鋼板 | |
WO2023190867A1 (ja) | 鋼部材及び鋼板 | |
WO2023132344A1 (ja) | 鋼板およびその製造方法 | |
EP4269644A1 (en) | Cold-rolled steel sheet and method for manufacturing same | |
WO2023135983A1 (ja) | 高強度鋼板およびその製造方法 | |
CN116997671A (zh) | 热冲压用钢板及热冲压成型体 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PB01 | Publication | ||
PB01 | Publication | ||
SE01 | Entry into force of request for substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
GR01 | Patent grant | ||
GR01 | Patent grant |