WO2021143661A1 - 一种高耐蚀带钢及其制造方法 - Google Patents

一种高耐蚀带钢及其制造方法 Download PDF

Info

Publication number
WO2021143661A1
WO2021143661A1 PCT/CN2021/071186 CN2021071186W WO2021143661A1 WO 2021143661 A1 WO2021143661 A1 WO 2021143661A1 CN 2021071186 W CN2021071186 W CN 2021071186W WO 2021143661 A1 WO2021143661 A1 WO 2021143661A1
Authority
WO
WIPO (PCT)
Prior art keywords
corrosion
steel
resistant
base layer
layer
Prior art date
Application number
PCT/CN2021/071186
Other languages
English (en)
French (fr)
Inventor
闫博
焦四海
Original Assignee
宝山钢铁股份有限公司
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by 宝山钢铁股份有限公司 filed Critical 宝山钢铁股份有限公司
Priority to EP21741882.1A priority Critical patent/EP4092151A4/en
Priority to US17/790,590 priority patent/US20220396054A1/en
Priority to AU2021207953A priority patent/AU2021207953A1/en
Priority to KR1020227021503A priority patent/KR20220127234A/ko
Priority to JP2022542049A priority patent/JP2023510288A/ja
Publication of WO2021143661A1 publication Critical patent/WO2021143661A1/zh

Links

Images

Classifications

    • 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
    • B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
    • 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
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
    • B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or welding
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • 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
    • 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
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/04—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
    • C22C38/08—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/42—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C23G1/08—Iron or steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/18—Sheet panels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/34—Coated articles, e.g. plated or painted; Surface treated articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys
    • B23K2103/05—Stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/08—Non-ferrous metals or alloys
    • B23K2103/14—Titanium or alloys thereof
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/18—Dissimilar materials
    • 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
    • B32B2250/00—Layers arrangement
    • B32B2250/02—2 layers
    • 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
    • B32B2307/00—Properties of the layers or laminate
    • B32B2307/70—Other properties
    • B32B2307/714—Inert, i.e. inert to chemical degradation, corrosion
    • 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
    • B32B2307/00—Properties of the layers or laminate
    • B32B2307/70—Other properties
    • B32B2307/732—Dimensional properties
    • 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
    • B32B2311/00—Metals, their alloys or their compounds
    • B32B2311/18—Titanium
    • 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
    • B32B2311/00—Metals, their alloys or their compounds
    • B32B2311/30—Iron, e.g. steel
    • 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
    • B32B2413/00—Belts
    • 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
    • C21D2211/005—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
    • C21D2211/009—Pearlite
    • 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
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material

Definitions

  • the invention relates to a steel grade and a manufacturing method thereof, in particular to a corrosion-resistant strip steel and a manufacturing method thereof.
  • the ratio of the high corrosion resistance layer to the carbon steel sheet as the base metal is quite different. Usually, the ratio exceeds 1:50, which will cause huge differences in material properties, which will lead to difficult control of the heating process, rolling process or heat treatment process. These difficulties are specifically, such as: the temperature is not uniform during the heating process, which causes the deformation and bulging, resulting in the high corrosion resistance layer and the base metal can not be combined; another example: the high corrosion resistance layer is easily separated from the base metal during the rolling process , Cracking, resulting in the difficulty of ensuring the uniformity of the thickness of the final steel plate,
  • the thickness of the high corrosion resistance layer is only 20-100 ⁇ m. If the previous compounding is not completed and the bonding quality is not good, it will undergo subsequent pickling, forming, etc. After processing, the continuity and uniformity of the corrosion-resistant layer of the finished product cannot be guaranteed, which will cause huge problems for later use.
  • One of the objectives of the present invention is to provide a high corrosion-resistant steel strip, which through reasonable composition design, thickness design and process design finally makes the obtained steel plate or steel strip have high corrosion-resistant surface and interlayer
  • the bonding performance is good, and the mechanical properties of the steel plate or the steel strip are excellent, and the workability is good.
  • the present invention proposes a high corrosion-resistant steel strip, which includes a carbon steel base layer and a corrosion-resistant coating layer rolled and composited with the carbon steel base layer, wherein the corrosion-resistant coating layer is austenitic stainless steel or pure titanium,
  • the thickness of the corrosion-resistant coating is 0.5 to 5% of the total thickness of the strip steel.
  • the thickness of the corrosion-resistant coating has a crucial impact on the performance of the final strip steel product. If the thickness of the corrosion-resistant coating is too thick, it will affect the strip steel product. The mechanical properties increase the cost. If the thickness of the corrosion-resistant coating is too thin, the corrosion resistance and service life of the high corrosion-resistant steel strip will be reduced. Based on this, in the technical solution of the present invention, the thickness of the corrosion-resistant coating is controlled to be 0.5-5% of the total thickness of the strip steel.
  • the corrosion-resistant coating in this case is an ultra-thin corrosion-resistant coating whose thickness is only 0.5-5% of the total strip thickness, which is much thinner than the conventional coating in the prior art.
  • the austenitic stainless steel or pure titanium used in the corrosion-resistant coating can only meet the national or international standards. According to the working conditions, choose different corrosion-resistant grades of austenitic stainless steel or pure titanium. Titanium, such as austenitic stainless steel, can be 304, 304L, 316, 316L, and pure titanium can be TA2.
  • the carbon steel base layer can be a carbon steel base layer with higher strength and better workability.
  • the mass percentage of chemical elements in the carbon steel base layer is:
  • the balance is Fe and other unavoidable impurities.
  • the content of C, Si, Mn, Al, Ti and Nb satisfies at least one of the following items:
  • C is an austenite stabilizing element, which plays a role of solid solution strengthening in steel, and can significantly improve the strength of steel.
  • the mass percentage of C is too high, which can affect the welding performance. It is unfavorable to toughness, and it is easy to increase the hard-phase structure such as pearlite and Maio, which has an adverse effect on the corrosion resistance of steel. Therefore, considering the strength and toughness matching of the steel plate and the requirements for the corrosion resistance of carbon steel materials, the mass percentage of C can be controlled in the range of 0.01 to 0.20% in this case, which is beneficial to ensure that the high corrosion resistance strip steel in this case is air-cooled after rolling.
  • the mass percentage of C should not be too high, otherwise it will deteriorate the welding performance of the carbon steel base layer, especially for this case, because the thickness of the corrosion-resistant coating in this case is strip steel 0.5 to 5% of the total thickness, therefore, the mass percentage of C needs to be controlled within the above range to avoid adverse effects on welding performance.
  • the mass percentage of C can be further controlled at 0.01-0.18%.
  • the mass percentage of C is further controlled at 0.10 to 0.20%, more preferably 0.10 to 0.18%.
  • Si In the technical scheme of the present invention, adding Si to the steel can improve the purity of the steel and has a deoxidizing effect. Si plays a solid solution strengthening effect in steel, but Si with a high mass percentage is not conducive to welding performance. Therefore, the mass percentage of Si in the high corrosion-resistant steel strip of the present invention can be controlled to be between 0.10 and 0.5%, so as to The corrosion resistance of the corrosion-resistant coating will not have adverse effects, and it can ensure that the carbon steel base layer has good welding performance. In some preferred embodiments, the mass percentage of Si can be further controlled at 0.10 to 0.3%. In some preferred embodiments, the mass percentage of Si is 0.15 to 0.35%.
  • Mn For the high corrosion-resistant strip steel of the present invention, Mn can delay the pearlite transformation, reduce the critical cooling rate, improve the hardenability of the steel, and at the same time has the effect of solid solution strengthening on the steel. It is the main part of the steel. Solid solution strengthening element. However, if the mass percentage of Mn is too high, segregation zones and martensite structures are likely to appear, which will adversely affect the toughness of the steel. In addition, the appearance of segregation zone will also reduce the corrosion resistance of steel. Based on this, in the technical solution of the present invention, the mass percentage of Mn can be controlled to be 0.5-2.0%. In some preferred embodiments, the mass percentage of Mn can be further controlled to 0.5 to 1.5%.
  • Al is a strong deoxidizing element.
  • the mass percentage of Al is controlled to be 0.02-0.04%. After deoxidation, the excess Al and nitrogen in the steel can form AlN precipitates, which can improve the strength of the final strip steel product, and can refine the austenite grain size of the steel during heat treatment.
  • the mass percentage of Al can be further controlled to be 0.02-0.03%.
  • Ti is a strong carbide forming element.
  • the addition of a small amount of Ti to the steel is beneficial to fix the N in the steel, and the formed TiN can make the high corrosion resistance strip steel
  • Ti can also be combined with carbon and sulfide in steel to form TiC, TiS, Ti4C2S2, which exist in the form of inclusions and second phase particles.
  • the above-mentioned carbonitride precipitates of Ti can also prevent the heat-affected zone grains from growing during welding and improve the welding performance. Therefore, in the technical solution of the present invention, the mass percentage of Ti is controlled to be 0.005 to 0.018%. In some preferred embodiments, the mass percentage of Ti can be further controlled to 0.005 to 0.015%.
  • Nb is a strong carbide forming element. Adding a small amount of Nb to the carbon steel base layer is mainly to increase the recrystallization temperature. With a higher finishing temperature, it can be As a result, the high-corrosion-resistant steel strip in this case is refined after rolling in the recrystallized and unrecrystallized zone, which is beneficial to the improvement of the low-temperature impact toughness of the carbon steel base layer. Therefore, in the technical solution of the present invention, the mass percentage of Nb is controlled to be 0.005 to 0.020%. In some preferred embodiments, the mass percentage of Nb can be further controlled to 0.005 to 0.015%.
  • the high corrosion-resistant steel strip of the present invention also contains at least one of the following chemical elements: 0 ⁇ B ⁇ 0.0003%; 0 ⁇ N ⁇ 0.006%; 0 ⁇ Ni ⁇ 0.20%; 0 ⁇ Cr ⁇ 0.20%; 0 ⁇ Mo ⁇ 0.10%; 0 ⁇ Sb ⁇ 0.30%; 0 ⁇ V ⁇ 0.30%; 0 ⁇ W ⁇ 0.30%; 0 ⁇ Cu ⁇ 0.30%; 0 ⁇ Sn ⁇ 0.30%; 0 ⁇ Bi ⁇ 0.30%; 0 ⁇ Se ⁇ 0.30%; 0 ⁇ Te ⁇ 0.30%; 0 ⁇ Ge ⁇ 0.30%; 0 ⁇ As ⁇ 0.30%; 0 ⁇ Ca ⁇ 0.30%; 0 ⁇ Mg ⁇ 0.30%; 0 ⁇ Zr ⁇ 0.30%; 0 ⁇ Hf ⁇ 0.30%; 0 ⁇ rare earth elements ⁇ 0.50%.
  • B can play a role: B can greatly improve the hardenability of steel.
  • B can greatly improve the hardenability of steel.
  • the thickness of the corrosion-resistant coating of the high corrosion-resistant steel strip in this case is within the range of 0.5% to 5% of the total thickness.
  • the mass percentage of B added in this case can be limited to 0 ⁇ B ⁇ 0.0003%.
  • Ni is an element that stabilizes austenite and has a certain effect on improving strength. Adding Ni to steel, especially adding Ni to quenched and tempered steel, can greatly improve the low-temperature impact toughness of steel.
  • the mass percentage of Ni added can be limited to 0 ⁇ Ni ⁇ 0.20%. In some embodiments, the mass percentage of Ni added is 0 ⁇ Ni ⁇ 0.10%.
  • the segregation tendency of Cr is lower than that of Mn.
  • the mass percentage of Mn in the carbon steel base layer is higher, so that there are obvious segregation bands and band-like structures in the steel, the mass percentage of Mn can be appropriately reduced, and Cr can be added. conduct.
  • the addition of Cr to the carbon steel base layer is also beneficial to inhibit the diffusion of Cr in the corrosion-resistant coating to the carbon steel base layer. Therefore, in the technical solution of the present invention, the mass percentage of Cr added can be limited to: 0 ⁇ Cr ⁇ 0.20% .
  • Mo can significantly refine grains, improve strength and toughness, Mo can reduce the temper brittleness of steel, and at the same time, it can also precipitate very fine carbides during tempering, which can significantly strengthen the steel matrix.
  • the addition of Mo It is beneficial to suppress the self-tempering brittleness that is easily generated during the air cooling of the steel plate. Therefore, in the technical solution of the present invention, the mass percentage of added Mo can be limited to: 0 ⁇ Mo ⁇ 0.10%.
  • the mass percentage of chemical elements in the carbon steel base layer is: C: 0.01 to 0.20%, preferably 0.01 to 0.18%, more preferably 0.10 to 0.18 %; Si: 0.10 to 0.5%, preferably 0.10 to 0.3% or 0.15 to 0.35%; Mn: 0.5 to 2.0%, preferably 0.5 to 1.5%; Al: 0.02 to 0.04%, preferably 0.02 to 0.03%; Ti: 0.005 to 0.018%, preferably 0.005 to 0.015%; Nb: 0.005 to 0.020%, preferably 0.005 to 0.015%; N:0 ⁇ N ⁇ 0.006%, preferably 0.0035 to 0.0055%; Mo: ⁇ 0.10%; Cr: ⁇ 0.20%; Ni : ⁇ 0.20%, preferably ⁇ 0.10%; the balance is Fe and other unavoidable impurities.
  • the microstructure of the carbon steel base layer is ferrite and pearlite
  • the microstructure of the austenitic stainless steel corrosion-resistant coating is austenite
  • the carbon steel base layer and The transition layer between the corrosion-resistant coatings is pearlite and ferrite.
  • the tensile strength is ⁇ 500MPa, preferably ⁇ 530MPa, the yield strength is 370-510MPa, and the elongation is ⁇ 30%.
  • the tensile strength is ⁇ 600MPa
  • the yield strength is 470-510MPa
  • the elongation is ⁇ 35%.
  • the high corrosion-resistant steel strip of the present invention has a tensile strength of 600-650 MPa, a yield strength of 470-510 MPa, and an elongation of 35-40%.
  • the high corrosion-resistant steel strip of the present invention is a hot-rolled steel strip or a cold-rolled steel strip.
  • another object of the present invention is to provide a method for manufacturing high corrosion-resistant steel strip, by which high-corrosion-resistant steel strip can be obtained.
  • the present invention proposes a method for manufacturing high corrosion-resistant strip steel, which includes the steps:
  • Pre-heating Pre-heat the billet at a temperature of 1150 to 1250°C, so that the elements of the corrosion-resistant coating and the carbon steel base layer diffuse at the interface to form a stable transition layer, and then slowly cool to room temperature;
  • Secondary heating and rolling Perform secondary heating at a temperature of 1100 to 1200°C, and then perform multiple passes of rolling, and control the final rolling temperature to be no less than 900°C;
  • the preheating can make the corrosion-resistant coating on the surface of the blank obtain a uniform austenitized structure, so that the carbides that may have existed before can be completely dissolved, and can also make the carbon steel base layer
  • the compounds of alloying elements are completely or partially dissolved, so that the elements of the corrosion-resistant coating and the carbon steel base layer are diffused at the interface to form a stable transition layer, and then slowly cooled to room temperature.
  • the thickness of each layer of cladding material is 5-20 mm, preferably 8-15 mm.
  • the thickness of the base layer material is 300-370 mm.
  • the total reduction rate of the control rolling is not less than 70%. In some embodiments, the total reduction of controlled rolling is not less than 90%.
  • step (4) the final rolling temperature is controlled to be 920-1000°C.
  • the coiling temperature is controlled to be 500 to 650°C, preferably 550 to 650°C.
  • step (5) it further includes: a surface treatment step or a cold rolling step.
  • step of surface treatment includes pickling or mechanical descaling.
  • the cold rolling annealing temperature is controlled to be 600-750°C.
  • the high corrosion-resistant steel strip and the manufacturing method thereof according to the present invention have the following advantages and beneficial effects:
  • the high-corrosion-resistant steel strip of the present invention is provided with a corrosion-resistant coating of a suitable thickness and a carbon steel base layer, thereby obtaining a strip with high corrosion resistance and good mechanical properties.
  • the corrosion-resistant coating and the carbon steel base layer form a transition layer structure with a certain thickness, so as to excellently realize the complete metallurgical combination of the corrosion-resistant coating and the carbon steel base layer, ensuring corrosion resistance and mechanical properties.
  • improving the applicability and economy of materials can solve the essential pain points of current carbon steel materials. It has corrosion resistance, bonding strength and durability that current coated plate products are difficult to match, and it is more energy-saving, environmentally friendly, and maintenance-free. Important meaning and broad prospects.
  • the present invention also includes the high corrosion-resistant steel strip prepared by the method described in any embodiment of the present invention.
  • the corrosion resistance of the high corrosion-resistant steel strip of the present invention can reach the corrosion resistance of the material used for the cladding material.
  • the manufacturing method of the present invention also has the above-mentioned advantages and beneficial effects.
  • Fig. 1 schematically shows the structure of the high corrosion-resistant steel strip according to the present invention in some embodiments.
  • Fig. 2 schematically shows the structure of the high corrosion-resistant steel strip according to the present invention in other embodiments.
  • Fig. 3 is a photo of a typical structure at the upper surface of the high corrosion-resistant steel strip of Example 1.
  • Fig. 4 is a typical microstructure photo at the lower surface of the high corrosion-resistant steel strip of Example 1.
  • Fig. 5 is a typical microstructure photo of the high corrosion-resistant steel strip of Example 2.
  • Fig. 6 is a typical microstructure photograph of the high corrosion-resistant steel strip of Example 6.
  • the high corrosion-resistant steel strips of Examples 1-6 were prepared by the following steps:
  • the thickness of the high corrosion-resistant steel strip shall be 0.5% to 5% of the total thickness of the blanks for forming blanks.
  • the base material layer and the cladding material can be pre-treated before the blank assembly, and then the bonding surface between the base material layer and the cladding material is welded and sealed around, and the joint surface after welding and sealing is performed Vacuum treatment.
  • Pre-heating Pre-heat the billet at a temperature of 1150 to 1250°C to diffuse the elements of the corrosion-resistant coating and the carbon steel base layer at the interface to form a stable transition layer, and then slowly cool to room temperature.
  • Secondary heating and rolling Perform secondary heating at a temperature of 1100 to 1200°C, and then perform multiple passes of rolling, and control the final rolling temperature to not less than 900°C.
  • the total rolling reduction ratio in step (4), can be controlled not to be less than 70%.
  • the final rolling temperature in step (4), can be controlled to be 920-1000°C.
  • the coiling temperature in step (5), can be controlled to be 500-650°C.
  • the hot-rolled high-corrosion-resistant steel strip coil may be subjected to surface treatment, including pickling or mechanical dephosphorization.
  • cold-rolling annealing may be performed to obtain cold-rolled high-corrosion-resistant steel strip coils.
  • Table 1 lists the mass percentages of the chemical elements of the high corrosion-resistant steel strips of Examples 1-6.
  • Table 2 lists the specific process parameters of the high corrosion-resistant steel strips of Examples 1-6.
  • this case tested the high corrosion-resistant steel strips of Examples 1-6, and the test results are listed in Table 3.
  • Fig. 1 schematically shows the structure of the high corrosion-resistant steel strip according to the present invention in some embodiments.
  • the high corrosion-resistant steel strip includes a carbon steel base layer 1 and a corrosion-resistant coating layer 2 rolled and composited with the upper and lower surfaces of the carbon steel base layer 1.
  • the corrosion-resistant coating layer 2 may be austenite Stainless steel or pure titanium, the thickness of the corrosion-resistant coating is 0.5 to 5% of the total thickness of the strip.
  • Fig. 2 schematically shows the structure of the high corrosion-resistant steel strip according to the present invention in other embodiments.
  • the high corrosion-resistant steel strip includes a carbon steel base layer 1 and a corrosion-resistant coating 2 that is rolled and composited with the upper surface of the carbon steel base layer 1 (of course, in some other embodiments, The corrosion-resistant coating 2 can also be rolled and compounded with the lower surface of the carbon steel base layer 1), the corrosion-resistant coating 2 can be austenitic stainless steel or pure titanium, and the thickness of the corrosion-resistant coating is 0.5 to 5% of the total thickness of the strip. .
  • Fig. 3 is a photo of a typical structure at the upper surface of the high corrosion-resistant steel strip of Example 1.
  • Fig. 4 is a photo of a typical structure at the lower surface of the high corrosion-resistant steel strip of Example 1.
  • Fig. 5 is a typical microstructure photo of the high corrosion-resistant steel strip of Example 2.
  • the microstructure of the carbon steel base layer 1 is ferrite and pearlite
  • the corrosion-resistant coating 2 is austenitic stainless steel corrosion-resistant coating.
  • the microstructure of the coating layer 2 is austenite
  • the transition layer between the carbon steel base layer 1 and the corrosion-resistant coating layer 2 is ferrite and pearlite. It should be pointed out that, as can be seen from FIG. 5, the thickness of the high corrosion-resistant steel strip of Example 2 is 3.5 mm, and the thickness of the corrosion-resistant coating 2 is 40 ⁇ m.
  • Fig. 6 is a typical microstructure photograph of the high corrosion-resistant steel strip of Example 6.
  • the microstructure of the carbon steel base layer 1 is ferrite and pearlite
  • the corrosion-resistant coating 2 is a pure titanium corrosion-resistant coating, and its microstructure is ⁇ -Ti, the transition layer between the carbon steel base layer 1 and the corrosion-resistant coating 2 is ferrite and pearlite.
  • the thickness of the high corrosion-resistant steel strip of Example 6 is 0.5 mm, and the thickness of each layer of the corrosion-resistant coating 2 is 20 ⁇ m.
  • the high corrosion-resistant steel strip of the present invention is provided with a suitable thickness of the corrosion-resistant coating and a carbon steel base layer, thereby obtaining a strip with high corrosion resistance and good mechanical properties.
  • the corrosion-resistant coating and the carbon steel base layer form a transition layer structure with a certain thickness, so as to excellently realize the complete metallurgical combination of the corrosion-resistant coating and the carbon steel base layer, ensuring corrosion resistance and mechanical properties.
  • improving the applicability and economy of materials can solve the essential pain points of current carbon steel materials. It has corrosion resistance, bonding strength and durability that current coated plate products are difficult to match, and it is more energy-saving, environmentally friendly, and maintenance-free. Important meaning and broad prospects.
  • the manufacturing method of the present invention also has the above-mentioned advantages and beneficial effects.

Abstract

本发明公开了一种高耐蚀带钢，其包括碳钢基层以及与碳钢基层轧制复合的耐蚀覆层，其中耐蚀覆层为奥氏体不锈钢或纯钛，耐蚀覆层的厚度为带钢总厚度的0.5～5％。此外，本发明还公开了上述的高耐蚀带钢的制造方法，其包括步骤：(1)获得基层材和覆层材；(2)组坯；(3)预加热：将坯料在1150～1250℃的温度下进行预加热，以使耐蚀覆层与碳钢基层的各元素在界面发生扩散，形成稳定的过渡层，之后缓冷至室温；(4)二次加热和轧制；(5)水冷后进行卷取。该高耐蚀带钢通过合理的成分设计、厚度设计以及工艺设计最终使得获得的钢板或是钢带具有高耐蚀表面、层间结合性能好，且钢板或是钢带的力学性能优良，可加工性能好。

Description

一种高耐蚀带钢及其制造方法 技术领域
本发明涉及一种钢种及其制造方法，尤其涉及一种耐蚀带钢及其制造方法。
背景技术
现有技术中，除了对钢板产品表面镀锌或锌合金从而提高其耐蚀性外，还有一种提高碳钢耐蚀性的方式，即通过轧制复合方式，在碳钢板表面形成高耐蚀层，该方式不需要在轧后进行涂镀工序，且高耐蚀层的耐蚀性远高于通过镀锌工艺所获得的锌层，这是因为：轧制复合的高耐蚀层与碳钢之间为冶金结合，因而，既能够保证钢板强度与可加工性能，又具有良好的耐蚀性，达到产品升级的目的。但是现有技术中，轧制复合工艺受到高耐蚀层厚度的限制，想要进一步减小高耐蚀层的厚度，则组坯、加热、轧制的难度迅速增高，目前行业内没有成功的事例。
而若是需要获得高耐蚀层的厚度在总厚度5％内的钢板或钢带，其难度极高，难度主要包括：
(1)高耐蚀层与作为基体金属的碳钢板的比例相差较大，通常该比例超过1：50，会使得材料特性的差异巨大，进而导致加热工序、轧制工序或热处理工序难以控制。这些难度具体来说，比如：在加热过程中温度不均匀，引起的变形鼓包，导致高耐蚀层与基体金属无法结合；又比如：在轧制过程中，高耐蚀层容易与基体金属分离、开裂，导致最终钢板的厚度的均匀性难以保证，
(2)对于总厚度在0.2～2mm的热冷轧带钢而言，其高耐蚀层厚度只有20-100μm，若前期的复合未完成，结合质量不佳，则经过后续酸洗、成型等加工后，成品的耐蚀层的连续性、均匀性无法保证，对于后期使用带来巨大问题。
(3)在一些钢板中，当碳钢板层中碳含量较高时，若缺少稳定化元素，则高耐蚀层与碳钢板层之间的界面结合处的碳钢板一侧会存在明显脱碳层，导致碳钢板层的基材组织不均匀，进而导致加工后容易产生表面缺陷，使得最终产品的力学性能也难以满足需要。
基于此，期望获得一种高耐蚀带钢，该高耐蚀带钢通过合理的成分设计、厚度 设计以及工艺设计最终使得获得的钢板或是钢带具有高耐蚀表面、层间结合性能好，且钢板或是钢带的力学性能优良，可加工性能好。
发明内容
本发明的目的之一在于提供一种高耐蚀带钢，该高耐蚀带钢通过合理的成分设计、厚度设计以及工艺设计最终使得获得的钢板或是钢带具有高耐蚀表面、层间结合性能好，且钢板或是钢带的力学性能优良，可加工性能好。
为了实现上述目的，本发明提出了一种高耐蚀带钢，其包括碳钢基层以及与碳钢基层轧制复合的耐蚀覆层，其中耐蚀覆层为奥氏体不锈钢或纯钛，耐蚀覆层的厚度为带钢总厚度的0.5～5％。
在本发明所述的高耐蚀带钢中，耐蚀覆层的厚度对于最终的带钢产品的性能有着至关重要的影响，若耐蚀覆层的厚度过厚，则会影响带钢产品的力学性能，提高成本。而若耐蚀覆层的厚度过薄，则会降低高耐蚀带钢的耐蚀性和使用寿命。基于此，在本发明所述的技术方案中，控制耐蚀覆层的厚度为带钢总厚度的0.5～5％。
需要说明的是，本案的耐蚀覆层是超薄的耐蚀覆层，其厚度仅为带钢总厚度0.5～5％，其较之现有技术中的常规覆层的厚度要薄很多。
另外，需要指出的是，耐蚀覆层所采用的奥氏体不锈钢或是纯钛可以只需满足国家或国际标准即可，根据使用工况条件选择不同耐蚀级别的奥氏体不锈钢或纯钛，例如奥氏体不锈钢可以采用304、304L、316、316L，纯钛可以采用TA2。
此外，考虑到最终的带钢成品需要具有较高的力学性能，因此，碳钢基层可以采用较高强度且可以保证较好的可加工性能的碳钢基层。
进一步地，在本发明所述的高耐蚀带钢中，碳钢基层的化学元素质量百分比为：
C：0.01～0.20％；
Si：0.10～0.5％；
Mn：0.5～2.0％；
Al：0.02～0.04％；
Ti：0.005～0.018％；
Nb：0.005～0.020％；
余量为Fe和其他不可避免的杂质。
进一步地，在本发明所述的高耐蚀带钢中，其中C、Si、Mn、Al、Ti和Nb的 含量满足下列各项的至少其中之一：
C：0.01～0.18％；
Si：0.10～0.3％；
Mn：0.5～1.5％；
Al：0.02～0.03％；
Ti：0.005～0.015％；
Nb：0.005～0.015％。
在上述方案中，碳钢基层的各化学元素的设计原理如下所述：
C：在本发明所述的技术方案中，C是奥氏体稳定化元素，在钢中起到固溶强化的作用，可明显提高钢的强度，但是C的质量百分比太高，对焊接性能和韧性不利，也容易增加诸如珠光体组织及马奥岛的硬相组织，对钢的耐腐蚀性能有不利影响。因此，考虑到钢板的强韧性匹配以及对碳钢材料耐腐蚀性的要求，本案中可以控制C的质量百分比范围为0.01～0.20％，从而有利于保证本案的高耐蚀带钢轧制后空冷的情况下获得一定的硬度和强度，但C的质量百分比又不能太高，否则就会恶化碳钢基层的焊接性能，尤其是对于本案而言，由于本案的耐蚀覆层的厚度为带钢总厚度的0.5～5％，因此，C的质量百分比更需要控制在上述范围内，以避免焊接性能的不利影响。当然，在一些优选的实施方式中，C的质量百分比可以进一步控制在0.01～0.18％。在一些优选的实施方式中，将C的质量百分比进一步控制在0.10～0.20％，更优选0.10～0.18％。
Si：在本发明所述的技术方案中，钢中加Si能提高钢质纯净度，并且起到脱氧作用。Si在钢中起固溶强化作用，但质量百分比过高的Si不利于焊接性能，因此，在本发明所述的高耐蚀带钢中可以控制Si的质量百分比在0.10～0.5％，从而对耐蚀覆层的耐蚀性不会有不良影响，且可以保证碳钢基层具有良好的焊接性能。在一些优选的实施方式中，Si的质量百分比可以进一步控制在0.10～0.3％。在一些优选的实施方式中，Si的质量百分比为0.15～0.35％。
Mn：对于本发明所述的高耐蚀带钢而言，Mn可以推迟珠光体转变，降低临界冷却速度，提高钢的淬透性，同时对钢具有固溶强化的作用，是钢中的主要固溶强化元素。但若是Mn的质量百分比太高，则容易出现偏析带以及马氏体组织，对钢的韧性有不利影响。此外，偏析带的出现对钢的耐腐蚀性能也会有所降低。基于此，在本发明所述的技术方案中，可以控制Mn的质量百分比在0.5～2.0％。在一些优选 的实施方式中，Mn的质量百分比可以进一步控制为0.5～1.5％。
Al：对于本发明所述的高耐蚀带钢中，Al是强脱氧元素。为了保证钢中的氧含量尽量地低，因而，在本发明所述的技术方案中控制Al的质量百分比控制在0.02～0.04％。脱氧后多余的Al和钢中的氮元素能形成AlN析出物，从而可以提高最终带钢产品的强度，并且在热处理加热时能细化钢的元素奥氏体晶粒度。在一些优选的实施方式中，Al的质量百分比可以进一步控制为0.02～0.03％。
Ti：对于本发明所述的高耐蚀带钢而言，Ti是强碳化物形成元素，钢中加入微量的Ti有利于固定钢中的N，形成的TiN能使高耐蚀板带钢的碳钢继承的坯料加热时基体奥氏体晶粒不过分长大，细化原始奥氏体晶粒度。此外，Ti在钢中还可分别与碳和硫化合生成TiC、TiS、Ti4C2S2，其以夹杂物和第二相粒子的形式存在。Ti的上述碳氮化物析出物在焊接时还可阻止热影响区晶粒长大，改善焊接性能。因此，在本发明所述的技术方案中控制Ti的质量百分比在0.005～0.018％。在一些优选的实施方式中，Ti的质量百分比可以进一步控制为0.005～0.015％。
Nb：对于本发明所述的高耐蚀带钢而言，Nb是强碳化物形成元素，将碳钢基层中加入少量的Nb主要是为了提高再结晶温度，配合较高的终轧温度，可以使得本案的高耐蚀带钢在再结晶及未再结晶区轧制结束后晶粒细化，有利于碳钢基层的低温冲击韧性的提高。因此，在本发明所述的技术方案中控制Nb的质量百分比为0.005～0.020％。在一些优选的实施方式中，Nb的质量百分比可以进一步控制为0.005～0.015％。
进一步地，在本发明所述的高耐蚀带钢中，其还含有下述化学元素的至少其中之一：0＜B≤0.0003％；0＜N≤0.006％；0＜Ni≤0.20％；0＜Cr≤0.20％；0＜Mo≤0.10％；0＜Sb≤0.30％；0＜V≤0.30％；0＜W≤0.30％；0＜Cu≤0.30％；0＜Sn≤0.30％；0＜Bi≤0.30％；0＜Se≤0.30％；0＜Te≤0.30％；0＜Ge≤0.30％；0＜As≤0.30％；0＜Ca≤0.30％；0＜Mg≤0.30％；0＜Zr≤0.30％；0＜Hf≤0.30％；0＜稀土元素≤0.50％。
上述元素中，例如B可以起到的作用为：B能极大地提高钢的淬透性，针对生产轧后空冷情况，为了获得更好的微观组织，例如全部得到铁素体+珠光体组织，抑制贝氏体的形成，针对本案的高耐蚀带钢的耐蚀覆层厚度在总厚度的0.5％-5％范围内，本案可以限定添加B的质量百分比为0＜B≤0.0003％。
而对于Ni而言，Ni是稳定奥氏体的元素，对提高强度有一定的作用，钢中加 Ni，尤其是在调质钢中加Ni可以大幅提高钢的低温冲击韧性，因此，在本发明所述的技术方案中，可以限定添加Ni的质量百分比为0＜Ni≤0.20％。在一些实施方案中，添加的Ni的质量百分比为0＜Ni≤0.10％。
对于Cr而言，Cr的偏析倾向较Mn小，当碳钢基层中Mn的质量百分比较高，使得钢中有明显的偏析带及带状组织的时，可以适当降低Mn的质量百分比，添加Cr进行。此外，碳钢基层添加Cr还有利于抑制耐蚀覆层的Cr向碳钢基层扩散，因此，在本发明所述的技术方案中，可以限定添加Cr的质量百分比为：0＜Cr≤0.20％。
对于Mo而言，Mo能显著地细化晶粒，提高强度和韧性，Mo能减少钢的回火脆性，同时回火时还能析出非常细小的碳化物，显著强化钢的基体，Mo的添加有利于抑制钢板空冷过程中容易产生的自回火脆性，因此，在本发明所述的技术方案中，可以限定添加Mo的质量百分比为：0＜Mo≤0.10％。
进一步地，在本发明所述的高耐蚀带钢中，在其他不可避免的杂质中：P≤0.015％；并且/或者S≤0.010％。
在本发明所述的技术方案中，S在钢中与Mn化合形成塑性夹杂物MnS，其对钢的横向塑性和韧性不利，因此S的质量百分比应尽可能地低。P也是钢中的有害元素，严重损害钢板的塑性和韧性。因此，需要控制P、S的质量百分比越低越好，考虑到钢厂实际的炼钢水平，因此，限定P≤0.015％并且/或者S≤0.010％。
在本发明的一些实施方案中，在本发明所述的高耐蚀带钢中，碳钢基层的化学元素质量百分比为：C：0.01～0.20％，优选0.01～0.18％，更优选0.10～0.18％；Si：0.10～0.5％，优选0.10～0.3％或0.15～0.35％；Mn：0.5～2.0％，优选0.5～1.5％；Al：0.02～0.04％，优选0.02～0.03％；Ti：0.005～0.018％，优选0.005～0.015％；Nb：0.005～0.020％，优选0.005～0.015％；N：0＜N≤0.006％，优选0.0035～0.0055％；Mo：≤0.10％；Cr：≤0.20％；Ni：≤0.20％，优选≤0.10％；余量为Fe和其他不可避免的杂质。进一步地，在本发明所述的高耐蚀带钢中，碳钢基层的微观组织为铁素体和珠光体，奥氏体不锈钢耐蚀覆层的微观组织为奥氏体，碳钢基层和耐蚀覆层之间的过渡层为珠光体和铁素体。
进一步地，在本发明所述的高耐蚀带钢中，其抗拉强度≥500MPa、优选≥530MPa，屈服强度为370～510MPa，延伸率≥30％。
进一步地，在本发明所述的高耐蚀带钢中，其抗拉强度≥600MPa，屈服强度为470～510MPa，延伸率≥35％。在一些实施方案中，本发明所述的高耐蚀带钢的抗拉 强度为600～650MPa，屈服强度为470～510MPa，延伸率为35～40％。
进一步地，本发明的高耐蚀带钢为热轧带钢或冷轧带钢。
相应地，本发明的另一目的在于提供一种高耐蚀带钢的制造方法，通过该制造方法可以获得高耐蚀带钢。
为了实现上述目的，本发明提出了一种高耐蚀带钢的制造方法，其包括步骤：
(1)获得碳钢基层作为基层材和耐蚀覆层作为覆层材；
(2)组坯；
(3)预加热：将坯料在1150～1250℃的温度下进行预加热，以使耐蚀覆层与碳钢基层的各元素在界面发生扩散，形成稳定的过渡层，之后缓冷至室温；
(4)二次加热和轧制：在1100～1200℃的温度下进行二次加热，然后进行多道次轧制，控制终轧温度不低于900℃；
(5)水冷后进行卷取。
在本发明所述的技术方案中，预加热可以使得坯料表面的耐蚀覆层获得均匀的奥氏体化组织，以使得原先可能存在的碳化物完全溶解，并且还可以使得碳钢基层中的合金元素的化合物全部或部分溶解，以使耐蚀覆层与碳钢基层的各元素在界面发生扩散，形成稳定的过渡层，之后缓冷至室温。
进一步地，在本发明所述的制造方法中，在步骤(1)中，每一层覆层材的厚度为5～20mm，优选8～15mm。
进一步地，在本发明所述的制造方法中，在步骤(1)中，基层材的厚度为300～370mm。
进一步地，在本发明所述的制造方法中，在步骤(4)中，控制轧制的总压下率不低于70％。在一些实施方案中，控制轧制的总压下率不低于90％。
进一步地，在本发明所述的制造方法中，在步骤(4)中，控制终轧温度为920～1000℃。
进一步地，在本发明所述的制造方法中，在步骤(5)中，控制卷取温度为500～650℃，优选550～650℃。
进一步地，在本发明所述的制造方法中，在步骤(5)之后还包括：表面处理的步骤或者冷轧步骤。
需要说明的是，所述表面处理的步骤包括酸洗或机械法除鳞。
进一步地，所述冷轧步骤中，控制冷轧退火温度为600～750℃。
本发明所述的高耐蚀带钢及其制造方法相较于现有技术具有如下所述的优点以及有益效果：
本发明所述的高耐蚀带钢通过设置合适厚度的耐蚀覆层以及碳钢基层，从而获得了具有高耐蚀性、良好力学性能的板带。
在一些实施方式中，耐蚀覆层与碳钢基层形成了一定厚度的过渡层组织，从而极好地实现了耐蚀覆层与碳钢基层的完全冶金结合，在保证耐蚀性和力学性能的同时，提升材料的适用性与经济性，能够解决目前碳钢材料的本质痛点，具有目前镀层板产品难以企及的耐蚀性、结合强度和耐用性，并且更加节能、环保、免维护，具有重要的意义与广阔的前景。
本发明还包括采用本发明任一实施方案所述的方法制备得到的高耐蚀带钢。本发明的高耐蚀带钢的耐蚀性能可达到覆层材所用材料的耐蚀性能。
此外，本发明所述的制造方法也同样具有上述的优点以及有益效果。
附图说明
图1示意性地显示了本发明所述的高耐蚀带钢在一些实施方式中的结构。
图2示意性地显示了本发明所述的高耐蚀带钢在另一些实施方式中的结构。
图3为实施例1的高耐蚀带钢的上表面处的典型组织照片。
图4为实施例1的高耐蚀带钢的下表面处的典型组织照片。
图5为实施例2的高耐蚀带钢的典型组织照片。
图6为实施例6的高耐蚀带钢的典型组织照片。
具体实施方式
下面将结合说明书附图和具体的实施例对本发明所述的高耐蚀带钢及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-6
实施例1-6的高耐蚀带钢采用以下步骤制得：
(1)获得基层材和覆层材，其中基材层与覆层材的各化学成分配比可以参见表1。
(2)组坯：组坯时按照高耐蚀带钢的厚度为坯料总厚度的0.5％～5％以进行组坯。 在一些实施方式中，组坯前可以对基材层与覆层材进行预处理，随后对基材层与覆层材之间的贴合面进行四周焊接密封，对焊接密封后的结合面进行抽真空处理。
(3)预加热：将坯料在1150～1250℃的温度下进行预加热，以使耐蚀覆层与碳钢基层的各元素在界面发生扩散，形成稳定的过渡层，之后缓冷至室温。
(4)二次加热和轧制：在1100～1200℃的温度下进行二次加热，然后进行多道次轧制，控制终轧温度不低于900℃。
(5)水冷后进行卷取。
在一些实施方式中，在步骤(4)中，可以控制轧制的总压下率不低于70％。
在一些优选的实施方式中，在步骤(4)中，可以控制终轧温度为920～1000℃。
在一些其他的实施方式中，在步骤(5)中，可以控制卷取温度为500～650℃。
需要说明的是，在一些实施方式中，可以在步骤(5)之后，对热轧高耐蚀带钢卷进行表面处理，包括酸洗或机械法除磷。
在一些其他的实施方式中，也可以在步骤(5)之后，进行冷轧退火，以获得冷轧高耐蚀带钢卷。
表1列出了实施例1-6的高耐蚀带钢的各化学元素的质量百分配比。
表1.(wt％，余量为Fe和除了P以及S以外的其他不可避免的杂质)
Figure PCTCN2021071186-appb-000001
表2列出了实施例1-6的高耐蚀带钢的具体工艺参数。
Figure PCTCN2021071186-appb-000002
为了验证本案的实施效果，同时证明本案较之现有技术的优异效果，本案将实施例1-6的高耐蚀带钢进行测试，测试结果列于表3中。
表3
Figure PCTCN2021071186-appb-000003
图1示意性地显示了本发明所述的高耐蚀带钢在一些实施方式中的结构。
如图1所示，在本实施方式中，高耐蚀带钢包括碳钢基层1以及与碳钢基层1上下表面轧制复合的耐蚀覆层2，耐蚀覆层2可以为奥氏体不锈钢或纯钛，耐蚀覆层的厚度为带钢总厚度的0.5～5％。
图2示意性地显示了本发明所述的高耐蚀带钢在另一些实施方式中的结构。
如图2所示，在本实施方式中，高耐蚀带钢包括碳钢基层1以及与碳钢基层1上表面轧制复合的耐蚀覆层2(当然在一些其他的实施方式中，耐蚀覆层2也可以与碳钢基层1的下表面轧制复合)，耐蚀覆层2可以为奥氏体不锈钢或纯钛，耐蚀覆层的厚度为带钢总厚度的0.5～5％。
图3为实施例1的高耐蚀带钢的上表面处的典型组织照片。图4为实施例1的高耐蚀带钢的下表面处的典型组织照片。
结合图3和图4可以看出，在实施例1的高耐蚀带钢中，碳钢基层1的微观组织为铁素体和珠光体，耐蚀覆层2为奥氏体不锈钢耐蚀覆层，耐蚀覆层2的微观组织为奥氏体，碳钢基层1和耐蚀覆层2之间的过渡层为铁素体和珠光体。
图5为实施例2的高耐蚀带钢的典型组织照片。
如图5所示，在实施例2的高耐蚀带钢中，碳钢基层1的微观组织为铁素体和珠光体，耐蚀覆层2为奥氏体不锈钢耐蚀覆层，耐蚀覆层2的微观组织为奥氏体，碳钢基层1和耐蚀覆层2之间的过渡层为铁素体和珠光体。需要指出的是，由图5可以看出，实施例2的高耐蚀带钢的厚度为3.5mm，耐蚀覆层2的厚度为40μm。
图6为实施例6的高耐蚀带钢的典型组织照片。
如图6所示，在实施例6的高耐蚀带钢中，碳钢基层1的微观组织为铁素体和珠光体，耐蚀覆层2为纯钛耐蚀覆层，其微观组织为α-Ti，碳钢基层1和耐蚀覆层2之间的过渡层为铁素体和珠光体。实施例6的高耐蚀带钢的厚度为0.5mm，每一层耐蚀覆层2的厚度为20μm。
综上所述，本发明所述的高耐蚀带钢通过设置合适厚度的耐蚀覆层以及碳钢基层，从而获得了具有高耐蚀性、良好力学性能的板带。
在一些实施方式中，耐蚀覆层与碳钢基层形成了一定厚度的过渡层组织，从而极好地实现了耐蚀覆层与碳钢基层的完全冶金结合，在保证耐蚀性和力学性能的同时，提升材料的适用性与经济性，能够解决目前碳钢材料的本质痛点，具有目前镀层板产品难以企及的耐蚀性、结合强度和耐用性，并且更加节能、环保、免维护，具有重要的意义与广阔的前景。
此外，本发明所述的制造方法也同样具有上述的优点以及有益效果。
需要说明的是，本发明的保护范围中现有技术部分并不局限于本申请文件所给出的实施例，所有不与本发明的方案相矛盾的现有技术，包括但不局限于在先专利文献、在先公开出版物，在先公开使用等等，都可纳入本发明的保护范围。
此外，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (15)

  1. 一种耐蚀带钢，其特征在于，其包括碳钢基层以及与碳钢基层轧制复合的耐蚀覆层，其中耐蚀覆层为奥氏体不锈钢或纯钛，耐蚀覆层的厚度为带钢总厚度的0.5～5％。
  2. 如权利要求1所述的耐蚀带钢，其特征在于，所述碳钢基层的化学元素质量百分比为：
    C：0.01～0.20％；
    Si：0.10～0.5％；
    Mn：0.5～2.0％；
    Al：0.02～0.04％；
    Ti：0.005～0.018％；
    Nb：0.005～0.020％；
    余量为Fe和其他不可避免的杂质。
  3. 如权利要求2所述的耐蚀带钢，其特征在于，其中C、Si、Mn、Al、Ti和Nb的含量满足下列各项的至少其中之一：
    C：0.01～0.18％；
    Si：0.10～0.3％；
    Mn：0.5～1.5％；
    Al：0.02～0.03％；
    Ti：0.005～0.015％；
    Nb：0.005～0.015％。
  4. 如权利要求1所述的耐蚀带钢，其特征在于，其还含有下述化学元素的至少其中之一：0＜B≤0.0003％；0＜N≤0.006％；0＜Ni≤0.20％；0＜Cr≤0.20％；0＜Mo≤0.10％；0＜Sb≤0.30％；0＜V≤0.30％；0＜W≤0.30％；0＜Cu≤0.30％；0＜Sn≤0.30％；0＜Bi≤0.30％；0＜Se≤0.30％；0＜Te≤0.30％；0＜Ge≤0.30％；0＜As≤0.30％；0＜Ca≤0.30％；0＜Mg≤0.30％；0＜Zr≤0.30％；0＜Hf≤0.30％；0＜稀土元素≤0.50％。
  5. 如权利要求1所述的耐蚀带钢，其特征在于，在其他不可避免的杂质中：P≤0.015％；并且/或者S≤0.010％。
  6. 如权利要求1所述的耐蚀带钢，其特征在于，所述耐蚀带钢碳钢基层的化学元素质量百分比为：C：0.01～0.20％；Si：0.10～0.5％；Mn：0.5～2.0％；Al：0.02～0.04％；Ti：0.005～0.018％；Nb：0.005～0.020％；N：0＜N≤0.006％；Mo：≤0.10％；Cr：≤0.20％；Ni：≤0.20％，优选≤0.10％；余量为Fe和其他不可避免的杂质。
  7. 如权利要求1所述的耐蚀带钢，其特征在于，碳钢基层的微观组织为铁素体和珠光体，奥氏体不锈钢耐蚀覆层的微观组织为奥氏体，碳钢基层和耐蚀覆层之间的过渡层为珠光体和铁素体。
  8. 如权利要求1所述的耐蚀带钢，其特征在于，其抗拉强度≥500MPa，屈服强度为370～510MPa，延伸率≥30％。
  9. 如权利要求1-8中任意一项所述的耐蚀带钢的制造方法，其特征在于，其包括步骤：
    (1)获得碳钢基层作为基层材和耐蚀覆层作为覆层材；
    (2)组坯；
    (3)预加热：将坯料在1150～1250℃的温度下进行预加热，以使耐蚀覆层与碳钢基层的各元素在界面发生扩散，形成稳定的过渡层，之后缓冷至室温；
    (4)二次加热和轧制：在1100～1200℃的温度下进行二次加热，然后进行多道次轧制，控制终轧温度不低于900℃；
    (5)水冷后进行卷取。
  10. 如权利要求8所述的制造方法，其特征在于，在步骤(4)中，控制轧制的总压下率不低于70％。
  11. 如权利要求8所述的制造方法，其特征在于，在步骤(4)中，控制终轧温度为920～1000℃。
  12. 如权利要求8所述的制造方法，其特征在于，在步骤(5)中，控制卷取温度为500～650℃。
  13. 如权利要求8所述的制造方法，其特征在于，在步骤(5)之后还包括步骤表面处理的步骤或者冷轧步骤。
  14. 如权利要求13所述的制造方法，其特征在于，所述表面处理的步骤包括酸洗或机械法除鳞，所述冷轧步骤中，控制冷轧退火温度为600～750℃。
  15. 如权利要求8所述的制造方法，其特征在于，在步骤(1)中，每一层 覆层材的厚度为5～20mm，基层材的厚度为300～370mm。
PCT/CN2021/071186 2020-01-13 2021-01-12 一种高耐蚀带钢及其制造方法 WO2021143661A1 (zh)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP21741882.1A EP4092151A4 (en) 2020-01-13 2021-01-12 HIGH CORROSION RESISTANCE STRIP STEEL AND METHOD OF MANUFACTURING THEREOF
US17/790,590 US20220396054A1 (en) 2020-01-13 2021-01-12 High corrosion-resistance strip steel and manufacturing method therefor
AU2021207953A AU2021207953A1 (en) 2020-01-13 2021-01-12 High corrosion-resistance strip steel and manufacturing method therefor
KR1020227021503A KR20220127234A (ko) 2020-01-13 2021-01-12 고내식성 띠강 및 이의 제조 방법
JP2022542049A JP2023510288A (ja) 2020-01-13 2021-01-12 高耐食性ストリップ鋼およびその製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN202010031109.7 2020-01-13
CN202010031109.7A CN113106327B (zh) 2020-01-13 2020-01-13 一种高耐蚀带钢及其制造方法

Publications (1)

Publication Number Publication Date
WO2021143661A1 true WO2021143661A1 (zh) 2021-07-22

Family

ID=76708854

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2021/071186 WO2021143661A1 (zh) 2020-01-13 2021-01-12 一种高耐蚀带钢及其制造方法

Country Status (7)

Country Link
US (1) US20220396054A1 (zh)
EP (1) EP4092151A4 (zh)
JP (1) JP2023510288A (zh)
KR (1) KR20220127234A (zh)
CN (1) CN113106327B (zh)
AU (1) AU2021207953A1 (zh)
WO (1) WO2021143661A1 (zh)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113667894B (zh) * 2021-08-13 2022-07-15 北京首钢冷轧薄板有限公司 一种具有优良扩孔性能800MPa级双相钢及其制备方法
CN116516244A (zh) * 2022-01-21 2023-08-01 宝山钢铁股份有限公司 一种耐氢氧化钠腐蚀高强度管道及其制造方法
CN116536573A (zh) * 2022-01-26 2023-08-04 宝山钢铁股份有限公司 一种耐硫酸铝腐蚀高强度管道及其制造方法
CN115341210B (zh) * 2022-08-16 2023-12-19 泰尔(安徽)工业科技服务有限公司 一种轧机用复合阶梯垫及其加工方法
CN117418169B (zh) * 2023-12-15 2024-03-08 北京科技大学 一种抗点蚀316l不锈钢及其制备方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06235050A (ja) * 1993-02-10 1994-08-23 Nippon Steel Corp 接合強度の高いステンレスクラッド鋼材
CN108085585A (zh) * 2016-11-23 2018-05-29 宝山钢铁股份有限公司 一种高强耐蚀复合花纹钢及其制造方法
CN108580555A (zh) * 2018-05-11 2018-09-28 中冶南方工程技术有限公司 一种复合带材生产方法及生产系统
CN109108071A (zh) * 2017-06-26 2019-01-01 宝山钢铁股份有限公司 一种高强耐蚀用单面不锈钢复合板及其制造方法
CN109306436A (zh) * 2017-07-28 2019-02-05 宝山钢铁股份有限公司 一种具有耐腐蚀性的抗酸管线用复合钢板及其制造方法
CN110499453A (zh) * 2018-05-16 2019-11-26 宝山钢铁股份有限公司 一种高强双面不锈钢复合板及其制造方法

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5927676B2 (ja) * 1980-02-29 1984-07-07 株式会社日本製鋼所 圧延圧着によるチタン又はチタン合金クラッド鋼板の製造方法
JPH06207249A (ja) * 1993-01-06 1994-07-26 Nippon Steel Corp 耐食性、耐摩耗性に優れた鋼板
WO2012048844A1 (en) * 2010-10-11 2012-04-19 Tata Steel Ijmuiden B.V. A steel strip composite and a method for making the same
CN103143566B (zh) * 2013-03-06 2015-11-04 攀钢集团攀枝花钢铁研究院有限公司 一种钛钢复合板卷及其生产方法
CN103695816A (zh) * 2013-12-25 2014-04-02 无锡帝圣金属制品有限公司 金属复合板的制备方法
CN105506478B (zh) * 2014-09-26 2017-10-31 宝山钢铁股份有限公司 一种高成形性的冷轧超高强度钢板、钢带及其制造方法
JP6168131B2 (ja) * 2014-12-09 2017-07-26 Ｊｆｅスチール株式会社 ステンレスクラッド鋼板
US10786974B2 (en) * 2015-08-19 2020-09-29 Nippon Steel Chemical & Material Co., Ltd. Stainless steel foil
KR101758567B1 (ko) * 2016-06-23 2017-07-17 주식회사 포스코 강도 및 성형성이 우수한 클래드 강판 및 그 제조방법
US11130161B2 (en) * 2016-11-23 2021-09-28 Baoshan Iron & Steel Co., Ltd. High-strength corrosion-resistant composite chequered iron and manufacturing method therefor
CN108116006A (zh) * 2016-11-30 2018-06-05 宝山钢铁股份有限公司 一种超级奥氏体不锈钢轧制复合钢板及其制造方法
CN109695000B (zh) * 2017-10-20 2021-01-08 鞍钢股份有限公司 以if钢为过渡层的双面钛钢复合板及其高温制备方法
CN109835014B (zh) * 2017-11-28 2021-03-12 宝山钢铁股份有限公司 一种高强高韧耐磨复合钢板及其制造方法
CN109835015B (zh) * 2017-11-28 2021-03-12 宝山钢铁股份有限公司 一种耐磨复合钢板及其制造方法
CN109835013B (zh) * 2017-11-28 2021-03-12 宝山钢铁股份有限公司 一种高强耐磨复合钢板及其制造方法
CN108995323B (zh) * 2018-08-07 2020-10-27 鞍钢股份有限公司 一种三代核电站高剪切强度特厚复合钢板及其制造方法
CN109570257A (zh) * 2018-11-08 2019-04-05 南京工业大学 一种双金属复合扁钢、带钢及其制备方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06235050A (ja) * 1993-02-10 1994-08-23 Nippon Steel Corp 接合強度の高いステンレスクラッド鋼材
CN108085585A (zh) * 2016-11-23 2018-05-29 宝山钢铁股份有限公司 一种高强耐蚀复合花纹钢及其制造方法
CN109108071A (zh) * 2017-06-26 2019-01-01 宝山钢铁股份有限公司 一种高强耐蚀用单面不锈钢复合板及其制造方法
CN109306436A (zh) * 2017-07-28 2019-02-05 宝山钢铁股份有限公司 一种具有耐腐蚀性的抗酸管线用复合钢板及其制造方法
CN108580555A (zh) * 2018-05-11 2018-09-28 中冶南方工程技术有限公司 一种复合带材生产方法及生产系统
CN110499453A (zh) * 2018-05-16 2019-11-26 宝山钢铁股份有限公司 一种高强双面不锈钢复合板及其制造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4092151A4 *

Also Published As

Publication number Publication date
AU2021207953A1 (en) 2022-07-14
KR20220127234A (ko) 2022-09-19
US20220396054A1 (en) 2022-12-15
CN113106327B (zh) 2022-06-24
EP4092151A1 (en) 2022-11-23
CN113106327A (zh) 2021-07-13
EP4092151A4 (en) 2022-11-23
JP2023510288A (ja) 2023-03-13

Similar Documents

Publication Publication Date Title
CN108796375B (zh) 一种抗拉强度1000MPa级热镀锌高强钢及其减量化生产方法
WO2021143661A1 (zh) 一种高耐蚀带钢及其制造方法
JP5135868B2 (ja) 缶用鋼板およびその製造方法
US7959747B2 (en) Method of making cold rolled dual phase steel sheet
JP6285462B2 (ja) ７８０ＭＰａ級冷間圧延二相帯鋼及びその製造方法
CN111748745A (zh) 780MPa级具有较高成形性的冷轧热镀锌双相钢及其制造方法
EP1969148B1 (en) Method for manufacturing high strength steel strips with superior formability and excellent coatability
JP7274505B2 (ja) 高強度両面ステンレス鋼クラッド板およびその製造方法
KR101461740B1 (ko) 재질 및 두께 편차가 작고 내도금박리성이 우수한 열연강판 및 그 제조방법
WO2011118421A1 (ja) 深絞り性に優れた高強度鋼板の製造方法
US20190218639A1 (en) Twip steel sheet having an austenitic matrix
JP2008308732A (ja) 焼入れ鋼板部材および焼入れ用鋼板とそれらの製造方法
EP4180547A1 (en) Hot-pressed member and manufacturing method therefor
KR20140013333A (ko) 굽힘 가공성과 연신율이 우수한 고강도 고망간 강판 및 그 제조방법
JPH03277741A (ja) 加工性、常温非時効性及び焼付け硬化性に優れる複合組織冷延鋼板とその製造方法
CN114807737B (zh) 一种热镀锌钢及其制造方法
EP3708691B1 (en) Manufacturing method for ultrahigh-strength and high-ductility steel sheet having excellent cold formability
CN114207172A (zh) 高强度钢板、高强度部件及其制造方法
JP3282887B2 (ja) 深絞り性、溶接性に優れた薄鋼板およびその製造方法
WO2023138595A1 (zh) 一种耐氢氧化钠腐蚀的高强度管道及其制造方法
WO2023143290A1 (zh) 一种耐硫酸铝腐蚀的高强度管道及其制造方法
KR102606996B1 (ko) 굽힘 가공성이 우수한 고강도 강판 및 그 제조방법
JPH09310149A (ja) 深絞り性、スポット溶接性、および打抜き性に優れた冷延鋼板及びその製造方法
WO2023134616A1 (zh) 一种耐臭氧腐蚀高强度管道及其制造方法
KR100554760B1 (ko) 용접성과 도장특성이 우수한 고가공성 고강도 냉연강판 및그 제조방법

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 21741882

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2022542049

Country of ref document: JP

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 2021207953

Country of ref document: AU

Date of ref document: 20210112

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2021741882

Country of ref document: EP

Effective date: 20220816