CN113227429A - 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
- CN113227429A CN113227429A CN201980086542.6A CN201980086542A CN113227429A CN 113227429 A CN113227429 A CN 113227429A CN 201980086542 A CN201980086542 A CN 201980086542A CN 113227429 A CN113227429 A CN 113227429A
- Authority
- CN
- China
- Prior art keywords
- steel sheet
- hot
- less
- dip galvanized
- content
- 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
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
-
- 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
- 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
- C21D8/0221—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
- C22C38/02—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—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
- C22C38/18—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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- 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
- 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
- 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
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
-
- 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
- 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
- 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
- C22C38/08—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
- C22C38/38—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
- C22C38/60—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)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- General Chemical & Material Sciences (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Coating With Molten Metal (AREA)
Abstract
本发明提供一种高强度且从剪切端面的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;上述钢组织中,在从钢板表层至板厚方向上300~400μm的范围中,以面积率计马氏体和包含碳化物的贝氏体的合计为90~100%,残余奥氏体为0~10%,旧奥氏体粒的长径比为2.0以下;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0.2~0.8;在从钢板表层至板厚方向上300~400μm的范围中,以FE‑EPMA进行分析时的C量的标准差与平均C量的比为0.40以下;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热浸镀锌钢板及其制造方法。
背景技术
从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。这样的汽车用零件会暴露在腐蚀环境中,因此,对高防锈性能的要求也日益提高。然而,对于暴露在腐蚀环境中的零件而言,如果进行高强度化,则可能会由于来自环境的氢侵入而导致延迟断裂,会对高强度化产生极大的阻碍。特别是在具有剪切端面的零件中,抑制以剪切端面为起点的延迟断裂非常重要,需要高强度和抗延迟断裂特性优异的镀覆钢板。作为这样的延迟断裂特性优异的镀覆钢板,在专利文献1和专利文献2中,公开了控制钢板中夹杂物的量和形状、分布的钢板。
现有技术文献
专利文献
专利文献1:日本特表2018-62380号公报
专利文献2:日本特表2018-62381号公报
发明内容
然而,在专利文献1和专利文献2中,主要是控制了夹杂物和微米级的组织,并没有公开控制纳米级的C分布、以及通过控制晶粒形状而提高抗延迟断裂特性。也没有公开由剪断刀的状态引起的延迟断裂特性的降低。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从剪切端面的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。
本发明人等重复进行了深入研究,结果发现了以下内容。即,发现了:从剪切端面的延迟断裂对剪切端面的形成具有深远的影响,在剪断刀被倒圆到R为0.2mm左右的条件下所形成的、从剪切端面的延迟断裂特性会显著降低,但是,如果进行如下的设定,那么即使是在TS为1300~1750MPa钢板中,从剪切端面的抗延迟断裂特性(以下记为耐端面断裂性)也仍然优异;即,使钢板具有特定的成分组成和钢组织;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、S:0.02%以下、Al:0.01~1.50%,剩余部分由Fe和不可避免的杂质构成;上述钢组织中,在钢板表层至300~400μm位置中,以通过组织观察求出的面积率计马氏体和包含碳化物的贝氏体的合计为90~100%,残余奥氏体为0~10%,旧奥氏体粒的长径比为2.0以下;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;在从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比为0.40以下。
本发明中,高强度是指TS为1300MPa以上。耐端面断裂性优异是指,在以具有剪切端面的试验片的毛刺外侧为弯折外侧、且对弯折外侧施加1000MPa的拉伸应力的状态下浸渍在pH3的塩酸中24小时,此时在弯折表面上,没有产生以端面为起点的1mm以上的龟裂。在此,剪切端面是指以剪切角2°、间隙15%、剪断刀的R为0.2mm以下的条件进行剪切而形成的剪切端面。剪切角是指由剪断刀与钢板形成的角。
本发明正是基于这样的看法而完成的,其要旨如下所述。
[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;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;上述钢组织中,在从钢板表层至板厚方向上300~400μm的范围中,以面积率计,马氏体和包含碳化物的贝氏体的合计为90~100%,残余奥氏体为0~10%,旧奥氏体粒的长径比为2.0以下;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;在从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比为0.40以下;并且,在钢板表面具有热浸镀锌层。
[2]根据[1]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1种以上。
[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1种以上。
[4]根据[1]至[3]中任1项所述的高强度热浸镀锌钢板,其中,上述热浸镀锌层为合金化热浸镀锌层。
[5]一种高强度热浸镀锌钢板的制造方法,其中,对具有[1]至[3]中任1项所述成分组成的坯材实施热轧,之后进行冷却,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400以上且小于600℃、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,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。
18500>(273+T1)×Log10(t/3600)···(1)
上述(1)式中,T1为最高到达温度(℃),t为保持时间(s)。
[6]根据[5]所述的高强度热浸镀锌钢板的制造方法,其中,在上述实施热浸镀锌处理或进一步实施合金化处理,其后冷却至室温的工序中,以满足下述(2)式的方式进行冷却。
上述(2)式中,T2为50℃~Ms点的范围的温度(℃),C为T2时的冷却速度(℃/s)。
根据本发明,可以得到适合作为汽车零件用坯材的、耐端面断裂性优异的高强度镀锌钢板。
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的元素,是为了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耐端面断裂性。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,使耐端面断裂性劣化。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使夹杂物增加而使耐端面断裂性劣化。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是形成微细碳化物、对高强度化有效的元素。为了得到这样的效果,优选使选自Ti、Nb、V、Mo中的1种以上为上述下限量以上。另一方面,如果它们的含量大于各自上述的上限量,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%。
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,会有耐端面断裂性降低的情况。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耐端面断裂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,会有耐端面断裂性降低的情况。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
在本实施方式涉及的钢板中,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,从而可以抑制端面的表层附近的龟裂生成、得到优异的耐端面断裂性。因此,从板厚表层至板厚方向上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。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(3)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)···(3)
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位置的飞溅时间中的C的检测强度的比。
在从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比:0.40以下
在本实施方式涉及的钢板中,钢板的极小区域的C量的不均匀会使耐端面断裂性大幅度降低。因此,在以FE-EPMA进行分析时的C量的标准差与平均C量的比就极其重要。通过使该比为0.40以下,从而可以得到优异的耐端面断裂性。因此,在从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比必须为0.40以下。在从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比优选为0.36以下,更优选为0.32以下。
在从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比可以按照下述(4)式而算出。
(从钢板表层至板厚方向上300~400μm的范围的C量的标准差)/(从钢板表层至板厚方向上300~400μm的范围的平均C量)···(4)
FE-EPMA的测定条件为加速电压9.0kV、照射电流7.0×10-8A、测定间隔0.065μm。以FE-EPMA测定的平均C量与通过燃烧法而测定的钢中C量在±20%以内就认为是一致的。钢板表层是指热浸镀锌层与钢板的界面。
接下来,对本实施方式涉及的钢板的钢组织进行说明。本实施方式涉及的钢板中,在从钢板表层至板厚方向上300~400μm的范围中,以面积率计,马氏体和包含碳化物的贝氏体合计为90~100%,残余奥氏体为0~10%,旧奥氏体粒的长径比为2.0以下。
马氏体和包含碳化物的贝氏体的合计:90~100%
马氏体和包含碳化物的贝氏体是实现TS上升和优异的耐端面断裂特性所必需的组织。为了得到这样的效果,马氏体和包含碳化物的贝氏体的面积率的合计必须为90%以上。马氏体和包含碳化物的贝氏体的合计优选为92%以上,更优选为94%以上。马氏体和包含碳化物的贝氏体的合计的上限为100%。
残余奥氏体:0~10%
残余奥氏体可以出于提高延展性等目的而被包含,但由于容易导致C量的不均匀,因此优选使其减少。在本实施方式涉及的钢板中,可以容许至以面积率计为10%。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%。
旧奥氏体粒的长径比:2.0以下
如果旧奥氏体粒的长径比变大,则会助长产自端面的龟裂进展,使耐端面断裂性降低。因此,旧奥氏体粒的长径比必须为2.0以下。
本实施方式涉及的钢板中,基本上不优选铁素体、不含碳化物的贝氏体和珠光体,因此其合计量以面积率计为5%以下。
本实施方式中,包含碳化物的贝氏体、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研磨后,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,将这些视野的平均面积率作为各组织的面积率。
该图像数据中,包含碳化物的贝氏体为包含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。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。碳化物为白色的点或线状,由此可以进行区别。铁素体和不含碳化物的贝氏体为黑色或暗灰色,由此可以进行区别。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。
旧奥氏体粒的长径比如下求出:与上述同样地进行,将切出的样品在600℃热处理10min后,对与轧制方向平行的板厚剖面进行研磨,之后,浸渍于苦味酸水溶液中,接下来,用氯化铁水溶液进行腐蚀,使旧奥氏体粒界出现,然后,用光学显微镜以400倍的倍率对从钢板表面至板厚方向上300~400μm的范围拍摄3~10个视野,对于各视野内的各旧奥氏体粒,使轧制方向的最大长度除以板厚方向的最大长度,算出所有的粒的平均值,将其作为旧奥氏体粒的长径比。
残余奥氏体的面积率可如下求出:将退火后的钢板研磨至板厚的1/4后,利用化学研磨进一步研磨0.1mm,对于研磨后的面,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。
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400℃以上且小于600℃、且最高到达温度T(℃)和保持时间t(s)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A3~950℃,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。制造条件所示的各温度均为钢板的表面温度。
18500>(273+T1)×Log10(t/3600)···(1)
上述(1)式中,T1为最高到达温度(℃),t为保持时间(s)。t是指T1~T1-20℃的温度范围中的保持时间。
在上述退火后的、实施镀锌处理或进一步实施合金化处理后冷却至室温的工序中,以满足下述(2)式的方式进行冷却。
上述(2)式中,T2为50℃~Ms点的范围的温度(℃),C为T2时的冷却速度(℃/s)。Ms点是马氏体转变开始的温度,可以通过全自动相变仪(Formastor)求出。以下详细说明。
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分布。因此,将卷绕温度设为590℃以下。下限温度没有规定,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。
最高到达温度为400℃以上且小于600℃、并且、最高到达温度T与保持时间t:满足下述(1)式
18500>(273+T1)×Log10(t/3600)···(1)
上述(1)式中,T1为最高到达温度(℃),t为保持时间(s)。t是指T1~T1-20℃的温度范围中的保持时间。
在热轧板的热处理中,如果最高到达温度为600℃以上或(1)式的右边为18500以上,则渗碳体会粗大化,在退火后会以未溶解的状态残留,由此,C量的微观不均匀会变大。其结果是,本实施方式涉及的钢板的C量的标准差与平均C量的比无法为0.40以下。因此,最高到达温度必须小于600℃,最高到达温度T1与保持时间t必须满足上述(1)式。另一方面,如果小于400℃,则热轧板中生成的马氏体的回火软化会不充分,冷轧时形变分布会不均匀,容易产生C量的微观不均匀。因此,最高到达温度必须为400℃以上。
冷轧压下率:20%以上
如果冷轧压下率小于20%,则在轧制方向上会生成伸长的旧奥氏体粒,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。
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℃,则会不均匀地粗粒化,使C量的不均匀增大。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℃
如果保持温度大于550℃,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,保持温度必须为550℃以下。另一方面,如果保持温度小于400℃,则钢板表层的贝氏体转变会过剩地进行,无法得到本实施方式涉及的钢板的钢板表层的C量分布。因此,保持温度必须为400℃以上。
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。
合金化处理后的冷却条件:满足下述(2)式
上述(2)式中,T2为50℃~Ms点的范围的温度(℃),C为T2时的冷却速度(℃/s)。在上述(2)式的左边的计算时,将T2=50、51、52、···、Ms点分别进行计算,求出它们的总和。
在合金化处理后,以符合上述(2)式的条件进行冷却,从而可以进一步抑制C量的不均匀。因此,合金化处理后的冷却的T2和C优选符合上述(2)式。
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。也可以根据需要进一步实施回火处理,该温度优选为200℃以下。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)1~33。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,冷却至室温,其后实施伸长率0.1%的调质轧制。对一部分还会进一步实施回火热处理。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、耐端面断裂性。
<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TS。本实施例中,将TS为1300MPa以上作为合格。
<耐端面断裂>
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。此时,以110mm剖面的内侧为研削端面,另一侧为剪切端面。该剪切端面是通过在以剪切角2゜、间隙15%、剪断刀的R为0.2mm以下的条件进行剪切而形成的。将该试验片以棱线与轧制方向平行且在毛刺外的方式、以7mm的弯折半径进行90゜V弯折加工,用螺栓以弯折顶点为1000MPa的拉伸应力的方式拧紧,浸渍在pH值为3的盐酸中,保持24hr后,调查有无裂纹产生。在本实施例中,将无法确认到产自端面的长度为1mm以上的龟裂的情况判定为耐端面断裂性合格,将产自端面的龟裂的长度为0.5mm以上且小于1mm的情况判定为“○”,将小于0.5mm的情况判定为“◎”,将龟裂横跨整个宽度的情况判定为“×”,将产自端面的龟裂的长度为1mm以上但未横跨整个宽度的情况判定为“△”。
钢板的钢组织、旧奥氏体粒的长径比、从钢板表层至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、以及从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比按照前述方法进行测定。它们的评价结果与钢板的钢组织等示于表3。
[表3]
*1V(H):表示包含碳化物的贝氏体和马氏体的合计面积率
*2V(γ):残余奥氏体的面积率。
*3V(O):铁素体、不含碳化物的贝氏体、珠光体的面积率的合计。
*4C比:从钢板表层至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。
*5σ(C)/C:从钢板表层至板厚方向上300~400μm的范围中的、以FE-EPMA进行分析时的C量的标准差与平均C量的比。
发明例中,可以得到TS为1300MPa以上且具有优异的耐端面断裂性的高强度镀锌钢板。另一方面,在本发明的范围外的比较例无法得到期望的TS和耐端面断裂性中的1者以上。
Claims (6)
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;
所述钢组织是在从钢板表层至板厚方向300~400μm的范围中,以面积率计,马氏体和包含碳化物的贝氏体的合计为90~100%,残余奥氏体为0~10%,旧奥氏体粒的长径比为2.0以下;
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上70μm的位置的平均C量的比为0.20~0.80,
在从钢板表层至板厚方向300~400μm的范围中,以FE-EPMA进行分析时的C量的标准差与平均C量的比为0.40以下,
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,
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1种以上。
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
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1种以上。
4.根据权利要求1至3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。
5.一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至3中任一项所述的成分组成的坯材实施热轧之后进行冷却,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400以上且小于600℃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℃,以该温度区域中的露点为-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,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;
18500>(273+T1)×Log10(t/3600)···(1)
所述(1)式中,T1为最高到达温度(℃),t为保持时间(s)。
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2018-242711 | 2018-12-26 | ||
JP2018242711 | 2018-12-26 | ||
PCT/JP2019/033081 WO2020136989A1 (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 |
---|---|
CN113227429A true CN113227429A (zh) | 2021-08-06 |
CN113227429B CN113227429B (zh) | 2023-02-07 |
Family
ID=71127021
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN201980086542.6A Active CN113227429B (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) | US20220098687A1 (zh) |
EP (1) | EP3904553B1 (zh) |
JP (1) | JP6760523B1 (zh) |
KR (1) | KR102544887B1 (zh) |
CN (1) | CN113227429B (zh) |
MX (1) | MX2021007713A (zh) |
WO (1) | WO2020136989A1 (zh) |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP4339309A1 (en) * | 2021-06-24 | 2024-03-20 | JFE Steel Corporation | Hot-dip galvanized steel sheet and method for producing same, and member |
WO2024150820A1 (ja) * | 2023-01-13 | 2024-07-18 | 日本製鉄株式会社 | 溶接継手 |
WO2024150822A1 (ja) * | 2023-01-13 | 2024-07-18 | 日本製鉄株式会社 | 鋼板及びめっき鋼板 |
WO2024150824A1 (ja) * | 2023-01-13 | 2024-07-18 | 日本製鉄株式会社 | 溶接継手 |
WO2024150817A1 (ja) * | 2023-01-13 | 2024-07-18 | 日本製鉄株式会社 | 鋼板及びめっき鋼板 |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102770568A (zh) * | 2010-02-26 | 2012-11-07 | 杰富意钢铁株式会社 | 弯曲性优良的超高强度冷轧钢板 |
JP2014009377A (ja) * | 2012-06-29 | 2014-01-20 | Jfe Steel Corp | 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
JP5884210B1 (ja) * | 2014-07-25 | 2016-03-15 | Jfeスチール株式会社 | 高強度溶融亜鉛めっき鋼板の製造方法 |
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 |
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 |
CN106471147A (zh) * | 2014-06-06 | 2017-03-01 | 安赛乐米塔尔公司 | 高强度多相钢、生产方法和用途 |
WO2018146828A1 (ja) * | 2017-02-10 | 2018-08-16 | Jfeスチール株式会社 | 高強度亜鉛めっき鋼板及びその製造方法 |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CA2850094C (en) * | 2011-09-30 | 2015-10-13 | Nippon Steel & Sumitomo Metal Corporation | High-strength hot-dip galvanized steel sheet |
MX2017009203A (es) * | 2015-01-15 | 2017-11-17 | Jfe Steel Corp | Lamina de acero galvanizada de alta resistencia y metodo para producir la misma. |
JP6749818B2 (ja) * | 2016-02-29 | 2020-09-02 | 株式会社神戸製鋼所 | 高強度鋼板およびその製造方法 |
WO2017169869A1 (ja) * | 2016-03-31 | 2017-10-05 | Jfeスチール株式会社 | 薄鋼板およびめっき鋼板、並びに熱延鋼板の製造方法、冷延フルハード鋼板の製造方法、薄鋼板の製造方法およびめっき鋼板の製造方法 |
WO2018055425A1 (en) | 2016-09-22 | 2018-03-29 | Arcelormittal | High strength and high formability steel sheet and manufacturing method |
JP6887236B2 (ja) | 2016-10-14 | 2021-06-16 | 株式会社ダイゾー | 吐出容器 |
JP2018062380A (ja) | 2016-10-14 | 2018-04-19 | 株式会社ディスコ | テープ貼着用器具 |
-
2019
- 2019-08-23 JP JP2019568114A patent/JP6760523B1/ja active Active
- 2019-08-23 US US17/417,865 patent/US20220098687A1/en active Pending
- 2019-08-23 KR KR1020217019656A patent/KR102544887B1/ko active IP Right Grant
- 2019-08-23 CN CN201980086542.6A patent/CN113227429B/zh active Active
- 2019-08-23 WO PCT/JP2019/033081 patent/WO2020136989A1/ja unknown
- 2019-08-23 EP EP19906059.1A patent/EP3904553B1/en active Active
- 2019-08-23 MX MX2021007713A patent/MX2021007713A/es unknown
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102770568A (zh) * | 2010-02-26 | 2012-11-07 | 杰富意钢铁株式会社 | 弯曲性优良的超高强度冷轧钢板 |
JP2014009377A (ja) * | 2012-06-29 | 2014-01-20 | Jfe Steel Corp | 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
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 |
CN106471147A (zh) * | 2014-06-06 | 2017-03-01 | 安赛乐米塔尔公司 | 高强度多相钢、生产方法和用途 |
JP5884210B1 (ja) * | 2014-07-25 | 2016-03-15 | Jfeスチール株式会社 | 高強度溶融亜鉛めっき鋼板の製造方法 |
CN106661658A (zh) * | 2014-07-25 | 2017-05-10 | 杰富意钢铁株式会社 | 高强度热浸镀锌钢板的制造方法 |
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 |
WO2018146828A1 (ja) * | 2017-02-10 | 2018-08-16 | Jfeスチール株式会社 | 高強度亜鉛めっき鋼板及びその製造方法 |
Also Published As
Publication number | Publication date |
---|---|
EP3904553A1 (en) | 2021-11-03 |
US20220098687A1 (en) | 2022-03-31 |
CN113227429B (zh) | 2023-02-07 |
EP3904553B1 (en) | 2023-12-13 |
KR102544887B1 (ko) | 2023-06-19 |
EP3904553A4 (en) | 2021-12-01 |
MX2021007713A (es) | 2021-08-05 |
JP6760523B1 (ja) | 2020-09-23 |
WO2020136989A1 (ja) | 2020-07-02 |
KR20210094620A (ko) | 2021-07-29 |
JPWO2020136989A1 (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 | |
US10745775B2 (en) | Galvannealed steel sheet and method for producing the same | |
CN108884537B (zh) | 薄钢板和镀覆钢板、以及热轧钢板的制造方法、冷轧全硬钢板的制造方法、薄钢板的制造方法和镀覆钢板的制造方法 | |
EP2813595B1 (en) | High-strength cold-rolled steel sheet and process for manufacturing same | |
CN113227429B (zh) | 高强度热浸镀锌钢板及其制造方法 | |
CN111527224B (zh) | 高强度钢板及其制造方法 | |
JP2017048412A (ja) | 溶融亜鉛めっき鋼板、合金化溶融亜鉛めっき鋼板、およびそれらの製造方法 | |
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 | |
CN113227415B (zh) | 钢板、构件和它们的制造方法 | |
JP2009215616A (ja) | 溶融亜鉛めっき鋼板およびその製造方法 | |
CN114667360A (zh) | 钢板及其制造方法 | |
CN109072375B (zh) | 薄钢板和镀覆钢板、以及热轧钢板的制造方法、冷轧全硬钢板的制造方法、薄钢板的制造方法和镀覆钢板的制造方法 | |
CN117545867A (zh) | 热浸镀锌钢板及其制造方法和部件 | |
CN113227430B (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 | |
CN114761596B (zh) | 钢板及其制造方法 | |
CN113166837B (zh) | 高强度钢板及其制造方法 | |
CN115698361A (zh) | 钢板、构件及它们的制造方法 | |
JP7493132B1 (ja) | 高強度鋼板、高強度めっき鋼板、及びそれらの製造方法、並びに部材 | |
JP7311069B1 (ja) | 鋼板および部材、ならびに、それらの製造方法 | |
WO2024157552A1 (ja) | 亜鉛めっき鋼板および部材、ならびに、それらの製造方法 | |
WO2024127766A1 (ja) | 高強度鋼板、高強度めっき鋼板、及びそれらの製造方法、並びに部材 | |
JP2022024998A (ja) | 高強度鋼板およびその製造方法 | |
CN115698362A (zh) | 钢板、构件及它们的制造方法 | |
CN118679274A (zh) | 钢板、构件和它们的制造方法 |
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 |