WO2014054141A1 - 合金化溶融亜鉛めっき鋼板およびその製造方法 - Google Patents

合金化溶融亜鉛めっき鋼板およびその製造方法 Download PDF

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Publication number
WO2014054141A1
WO2014054141A1 PCT/JP2012/075708 JP2012075708W WO2014054141A1 WO 2014054141 A1 WO2014054141 A1 WO 2014054141A1 JP 2012075708 W JP2012075708 W JP 2012075708W WO 2014054141 A1 WO2014054141 A1 WO 2014054141A1
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WIPO (PCT)
Prior art keywords
steel sheet
rolled steel
hot
descaling
dip galvanized
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.)
Ceased
Application number
PCT/JP2012/075708
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English (en)
French (fr)
Japanese (ja)
Inventor
寛哲 佐藤
真木　純
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel and Sumitomo Metal Corp
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 Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Priority to CN201280076196.1A priority Critical patent/CN104685091B/zh
Priority to PCT/JP2012/075708 priority patent/WO2014054141A1/ja
Priority to KR1020157010234A priority patent/KR101720891B1/ko
Priority to JP2013513873A priority patent/JP5825343B2/ja
Priority to US14/429,520 priority patent/US9850565B2/en
Priority to BR112015007044-2A priority patent/BR112015007044B1/pt
Priority to IN2193DEN2015 priority patent/IN2015DN02193A/en
Priority to MX2015004208A priority patent/MX380570B/es
Publication of WO2014054141A1 publication Critical patent/WO2014054141A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C21D8/0284—Application of a separating or insulating coating
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C23C2/34—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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the present invention relates to an alloyed hot-dip galvanized steel sheet for press working mainly applied to the automobile field and a method for producing the same, and relates to an alloyed hot-dip galvanized steel sheet for press work excellent in surface appearance and a method for producing the same.
  • automobile body steel sheets pressed into complex shapes are also required to have excellent surface corrosion resistance, electrodeposition coating properties, and excellent surface appearance.
  • a solid solution strengthening element such as Si (silicon), Mn (manganese), or P (phosphorus) is contained in the steel.
  • the alloyed hot-dip galvanized steel sheet manufactured with the component composition containing elements such as Si, Mn, and P described above often shows surface defects such as lines and streaks on the surface after pressing, and traces after coating. Is unfavorable in appearance and is a problem.
  • P is added to steel in order to increase the strength of the steel sheet, but P is an element that is very easily segregated, and P segregated on the slab surface is the longitudinal direction of the steel sheet by hot rolling and cold rolling. And a concentrated layer of P is formed on the coil surface. In the enriched layer of P, alloying is delayed at the time of plating, which causes generation of linear wrinkles in the galvannealed steel sheet.
  • Patent Document 4 In order to prevent the formation of chevron patterns on the surface of the steel sheet after pickling, there is also a technology in which the hot-rolled steel sheet is further pickled after ordinary pickling to dissolve the surface layer by 1.0 ⁇ m or more. It has been proposed (Patent Document 4).
  • One aspect of the present invention is an alloyed hot-dip galvanized steel sheet based on a high-tensile steel sheet containing, as a basic component, an ultra-low carbon steel and a strengthening element P in order to improve workability, It is an object of the present invention to provide an alloyed hot-dip galvanized steel sheet for press working that exhibits a beautiful surface appearance even after processing and a method for producing the same. In addition, it reduces the amount of surface defects such as linear patterns and obtains a beautiful surface appearance. It reduces the amount of steel sheet surface removal, and makes it possible to optimize the removal amount.
  • An object is to provide a hot-dip galvanized steel sheet and a method for producing the same. That is, the steel sheet according to one embodiment of the present invention has an object of being excellent in manufacturing cost.
  • the present inventor has earnestly studied the cause of the occurrence of P concentration unevenness that causes surface defects such as a linear pattern in a high-tensile alloyed hot-dip galvanized steel sheet containing P as a strengthening element, with ultra-low carbon steel as a basic component. Studied. As a result, the following was found.
  • the alloying rate during the alloying process is reduced at the part where P on the surface of the steel sheet is segregated. Due to this difference in alloying speed, the plating thickness varies. This variation in plating thickness becomes a surface defect of a vertically long pattern (linear pattern) that is whitish or blackish in appearance.
  • the pattern becomes more prominent because the convex portions forming the linear pattern on the surface of the steel sheet are scraped. Furthermore, when P, Ni (nickel), and Cu (copper) segregate at the same location on the interface between the scale (oxide film) and steel in a hot-rolled steel sheet, the segregated portion is acid even if the pickling process is performed. It remains without being washed. As a result, surface defects such as a linear pattern become conspicuous.
  • the surface of the surface can be removed by removing the segregated portion of these elements that segregate at the interface between the scale and steel after hot rolling.
  • the P segregation part harmful to the properties is also removed and rendered harmless.
  • the gist of the present invention is as follows.
  • the alloyed hot-dip galvanized steel sheet according to one aspect of the present invention has chemical components in mass%: C: 0.0005% to 0.01%; Si: 0.001% to 1.0%; Mn: 0.01% to 2.0%; P: 0.005% to 0.1%; Al: 0.01% to 0.10%; S: 0.02% or less; Ni: 0.1% or less; Cu: 0.1% or less; N: 0.01% or less; and the descaling rolled steel sheet with the balance being Fe and inevitable impurities, and the descaling rolled steel sheet.
  • the minimum value of the P content of the plating layer at the 10 measurement points is P Compared to the maximum value of the chromatic amount, 50% or more.
  • the chemical component of the descaling rolled steel sheet is further in mass%, B: 0.0001% to 0.0050%; Nb: 0 It may contain at least one of 0.001% to 0.1%; Ti: 0.001% to 0.1%; Mo: 0.001% to 0.1%.
  • 10 measurement points are provided by dividing a line segment section having a reference length of 50 mm into 10 equal parts in the sheet width direction of the descaling rolled steel sheet.
  • a method for producing an alloyed hot-dip galvanized steel sheet according to one aspect of the present invention is as follows: the chemical component is mass%, C: 0.0005% to 0.01%, Si: 0.001% to 1.
  • the chemical component of the molten steel is further in mass%, B: 0.0001% to 0.0050%, Nb: 0 It may contain at least one of 0.001% to 0.1%, Ti: 0.001% to 0.1%, Mo: 0.001% to 0.1%.
  • the surface of the descaling rolled steel sheet is acidified at least one of before the surface removal step or after the surface removal step.
  • the pickling process to wash In the method for producing an galvannealed steel sheet according to (5) above, the surface of the descaled rolled steel sheet is acidified at least one of before the surface removal step or after the surface removal step. You may have the pickling process to wash. (9) In the method for producing an alloyed hot-dip galvanized steel sheet according to (5) to (8) above, the descaling rolled steel sheet before the plating step is further applied at a cold rolling rate of 50% or more and 95% or less. A cold rolling step of cold rolling; and an annealing step of annealing the descaling rolled steel sheet after the cold rolling step at a temperature equal to or higher than a recrystallization temperature.
  • the alloyed hot-dip galvanized steel sheet according to the above aspect of the present invention has a plating layer having excellent workability and having few surface defects such as linear patterns while satisfying mechanical properties such as tensile strength. Even when pressed, a beautiful surface appearance can be maintained.
  • the surface removal amount of hot-rolled steel sheets to reduce surface defects such as linear patterns can be reduced compared to the prior art, and the removal amount can be optimized to produce alloyed hot-dip galvanized steel sheets, steel materials It is possible to reduce the loss, and to achieve a remarkable effect such as excellent cost.
  • An alloyed hot-dip galvanized steel sheet has an alloyed hot-dip galvanized layer disposed on a descaling rolled steel sheet.
  • the descaling rolled steel sheet is defined as a rolled steel sheet that has been subjected to surface removal by a surface removal process described later.
  • variation in the P content in the plating layer is small.
  • 10 measurement points that are equally spaced are provided by dividing the line segment section having a reference length of 50 mm into 10 equal parts in the sheet width direction of the galvannealed steel sheet, these 10 measurement points are provided.
  • the minimum value of the P content of the plating layer is required to be 50% or more (and 100% or less) as compared with the maximum value of the P content.
  • the minimum value of the P content of the plating layer at the above 10 measurement points is less than 50% compared to the maximum value of the P content of the plating layer, the alloying rate is reduced during the alloying heat treatment after the plating step. The difference is noticeable. As a result, the surface defect of the linear pattern of the galvannealed steel sheet becomes remarkable. Therefore, the P content in the plating layer needs to satisfy the above conditions. More preferably, the minimum value of the P content of the plating layer at the 10 measurement points is 60% or more as compared with the maximum value of the P content of the plating layer.
  • the P content in the plating layer can be measured using a glow discharge emission spectrometer (GDS: Glow Discharge Spectroscopy) or the like.
  • GDS glow discharge emission spectrometer
  • the thickness variation of the alloyed hot-dip galvanized layer is small.
  • the minimum value of the thickness of the plating layer at the 10 measurement points is preferably 50% or more (and 100% or less) as compared with the maximum value of the thickness.
  • the thickness of the plating layer preferably satisfies the above conditions. More preferably, the minimum value of the thickness of the plating layer at the 10 measurement points is 60% or more as compared with the maximum value of the thickness of the plating layer.
  • the thickness of the plating layer is measured so that the surface width is perpendicular to the rolling direction of the galvannealed steel sheet in view of the occurrence of the surface defects linearly in parallel with the rolling direction. What is necessary is just to carry out by the cut surface cut
  • the descaling rolled steel sheet that is the base material of the galvannealed steel sheet has P, Ni, and Cu on the steel sheet surface. Is preferably not segregated. Specifically, when 10 measurement points that are equally spaced are provided by dividing a line segment section having a reference length of 50 mm into 10 equal parts in the width direction of the descaling rolled steel sheet, each of the 10 measurement points is provided. At the measurement point, the contents of P, Ni, and Cu in the surface portion of the descaling rolled steel sheet having a depth of 0.1 ⁇ m from the surface in the thickness direction of the descaling rolled steel sheet are 2 ⁇ m from the surface in the thickness direction. Each component is preferably 105% or more and 150% or less as compared with the contents of P, Ni, and Cu in the base material part of the descaling rolled steel sheet that is an extremely deep depth.
  • the contents of P, Ni and Cu in the surface portion of the descaled rolled steel sheet are 150% for each component as compared with the contents of P, Ni and Cu in the base material part of the descaled rolled steel sheet. If it is super, segregation parts of P, Ni, and Cu remain on the surface of the descaling rolled steel sheet even after pickling of the descaling rolled steel sheet, and surface defects of the linear pattern of the galvannealed steel sheet are remarkable. It becomes. Moreover, when the said value is less than 105%, since the surface removal amount of a descaling rolled steel plate is excessive, it takes a burden to the time and equipment for surface removal, and also leads to the yield reduction of steel materials. Therefore, the content of P, Ni, and Cu in the surface portion of the descaling rolled steel sheet needs to satisfy the above conditions. More preferably, the range is 110% or more and 130% or less.
  • the measurement of the P, Ni, and Cu contents of the descaling rolled steel sheet can be performed by GDS.
  • the measurement average value from the surface to 0.1 ⁇ m in the thickness direction of the descaling rolled steel sheet is taken as the measurement result of the descaling rolled steel sheet surface, and the measurement average value exceeding 2 ⁇ m from the surface is the descaling rolled steel plate base material part.
  • the measurement result of it is preferable that the measurement depth of GDS of a descaling rolled steel plate base material shall be more than 2 micrometers and 4 micrometers or less.
  • steel plates for automobile bodies are required to have an excellent surface appearance and good press formability.
  • a steel sheet containing P is used as the steel sheet to be plated.
  • P is an element that is very easily segregated, and P segregated on the surface of the slab is stretched in the longitudinal direction of the steel sheet by hot rolling or cold rolling to form a linear P segregation portion on the steel sheet surface.
  • alloyed hot dip galvanizing is applied to this steel plate, the P segregation part becomes uneven in the plating alloying rate, which causes unevenness on the surface of the alloyed hot dip galvanized steel plate. As a result, a surface defect of a linear pattern occurs.
  • this plated steel sheet is press-worked, the above-mentioned convex part is scraped, so that the linear pattern becomes more prominent.
  • the inventor of the present invention is the cause of generating surface defects such as a linear pattern in an alloyed hot-dip galvanized steel sheet using a high-tensile hot-rolled steel sheet containing P as a strengthening element, with an extremely low carbon steel as a basic component.
  • Researched earnestly.
  • P, Ni, and Cu are segregated at the same location at the interface between the scale of the hot-rolled steel sheet and the steel, this segregated portion remains even after the pickling process, and after plating It has been found that the plating thickness varies at the segregated portion during the alloying process, and surface defects of a linear pattern occur.
  • an alloyed hot-dip galvanized steel sheet is obtained by heating a continuously cast slab in a heating furnace, hot-rolling it after descaling, winding it as a hot-rolled coil, and cooling the hot-rolled steel sheet as necessary. It is manufactured by subjecting it to hot rolling and annealing and applying an alloying hot dip galvanizing treatment.
  • the primary scale is removed by descaling as necessary, but Ni and Cu segregated on the steel surface remain without being removed.
  • the Ni and Cu segregation parts are stretched in the longitudinal direction of the steel sheet, and the thicknesses of the Ni and Cu segregation parts are reduced.
  • secondary scale is generated by oxidation of the steel sheet surface during hot rolling, and Ni and Cu are further segregated on the steel surface.
  • this hot-rolled steel sheet is cold-rolled and annealed as necessary, and then subjected to alloying hot-dip galvanizing treatment, surface defects with a linear pattern are generated.
  • the site where this surface defect occurs is a site where P, Ni, and Cu are mixed and segregated. From this, it can be judged that the occurrence of the surface defect of the linear pattern is caused not only by the segregation of P but also by the segregation of Ni, Cu and P in the surface portion.
  • the descaled rolled steel sheet with the surface removed as the base material it has a plated layer that has no surface defects such as linear patterns by applying galvanizing, and maintains a beautiful surface appearance even when pressed.
  • An alloyed hot-dip galvanized steel sheet can be obtained. Note that the descaling rolled steel sheet after the surface removal is subjected to a cold rolling process or an annealing process, if necessary, and then subjected to alloying hot dip galvanizing, the same effect as above can be obtained. .
  • the component elements of the descaling rolled steel sheet that is the base material of the galvannealed steel sheet according to this embodiment will be described.
  • the described% is mass%.
  • the descaling rolled steel sheet used as the base material of the galvannealed steel sheet according to the present embodiment is composed of extremely low carbon steel as a basic component and contains Si, Mn, P, etc., which are strengthening elements. Use added high strength steel sheet. The reason for adding the basic component elements and the reason for the limitation will be described below.
  • C 0.0005 to 0.01%
  • C (carbon) is an element that reduces the elongation and the r value (Rankford value) related to press workability.
  • the C content is small, in order to reduce it to less than 0.0005%, the cost of the steelmaking process is increased and it is not practical in operation.
  • the r value which is an index of workability, is impaired, so the upper limit was made 0.01%.
  • the upper limit is 0.008%.
  • Si 0.001 to 1.0%
  • Si is an element that increases the strength of steel and is used in combination with other strengthening elements. If the Si content is less than 0.001%, the above effect cannot be obtained. On the other hand, if the Si content exceeds 1.0%, Si oxide is formed on the surface of the steel sheet, resulting in a decrease in non-plating and plating adhesion during hot dip galvanization. Reduce the r value. In order to further increase the tensile strength, the content is preferably 0.1% or more.
  • Mn 0.01 to 2.0%
  • Mn manganese
  • the content is preferably 0.15% or more.
  • P 0.005 to 0.1%
  • P phosphorus
  • the content is preferably 0.01% or more.
  • P is an element that slows the alloying reaction of hot dip galvanizing, and is an element that generates a linear pattern on the plating surface, deteriorates surface properties, and adversely affects spot weldability. Therefore, the upper limit of the P content is set to 0.1%.
  • Al 0.01 to 0.10%
  • Al (aluminum) is contained as a deoxidizing element for steel and is an element that increases the strength of steel. If the Al content is less than 0.01%, the above effect cannot be obtained, the deoxidation is insufficient, the oxide remains, and the workability of the steel cannot be obtained. Further, if the Al content exceeds 0.10%, the r value, which is an index of workability, is reduced, so the upper limit was made 0.10%.
  • At least one of B, Nb, Ti, and Mo may be further contained as a selective element.
  • the reason for adding the selective element and the reason for the limitation will be described.
  • the described% is mass%.
  • B 0.0001 to 0.0050%
  • B has a strong affinity with N (nitrogen), forms a nitride during solidification or hot rolling, reduces N dissolved in the steel, improves workability, and steel There is an effect to increase the strength of.
  • the B content is preferably 0.0001% or more.
  • the B content exceeds 0.0050%, the welded part and its heat-affected zone become hard during welding and the toughness deteriorates.
  • the strength of the hot-rolled steel sheet increases, and the load during cold rolling increases.
  • the in-plane anisotropy of the r value which is an index of workability, increases and press formability deteriorates. Therefore, the B content is preferably 0.0001 to 0.0050%. If the B content is 0% to 0.0050%, each characteristic value of the galvannealed steel sheet will not be adversely affected.
  • Nb 0.001 to 0.1%
  • Nb niobium
  • the Nb content is preferably 0.001% or more.
  • the Nb content is preferably 0.001 to 0.1%. If the Nb content is 0% to 0.1%, each characteristic value of the galvannealed steel sheet is not adversely affected.
  • Ti 0.001 to 0.1%
  • Ti is an element that improves the workability and increases the strength of the steel by fixing N in the steel as TiN and reducing the amount of solute N.
  • the Ti content is preferably 0.001% or more.
  • the Ti content is preferably 0.001 to 0.1%. More preferably, the content is 0.015% to 0.09%. If the Ti content is 0% to 0.1%, each characteristic value of the galvannealed steel sheet is not adversely affected.
  • Mo 0.001 to 0.1%
  • Mo is an element capable of obtaining delayed aging by suppressing the aging by adding a small amount.
  • the Mo content is preferably 0.001% or more.
  • the Mo content is preferably 0.001 to 0.1%. If the Mo content is 0% to 0.1%, each characteristic value of the galvannealed steel sheet is not adversely affected.
  • inevitable impurities are contained in the descaling rolled steel sheet as the base material of the galvannealed steel sheet according to the present embodiment.
  • the inevitable impurities mean auxiliary materials such as scrap and elements such as S, Ni, Cu, N, Mg, Pb, Sb, Sn, and Cd that are inevitably mixed in from the plating step.
  • S, Ni, Cu, and N are preferably limited as follows in order to sufficiently exhibit the effects of the present invention. Since these impurity contents are preferably as small as possible, the limit range of these impurity contents includes 0%.
  • the described% is mass%.
  • S 0.02% or less S (sulfur) is an impurity inevitably contained in steel. If the S content exceeds 0.02%, the r value, which is an index of deep drawability, is reduced. If the S content is limited to 0% or more and 0.02% or less, there is no substantial adverse effect, and the allowable range.
  • Ni 0.1% or less Ni is an element that is difficult to remove when the steel composition is adjusted by steelmaking, and is contained in a trace amount (for example, 0.001% or more). Therefore, the pattern is easily generated, so the content is limited to 0% or more and 0.1% or less. In addition, when adding a large amount, it is necessary to dare to add expensive Ni, which increases the cost, so the upper limit is made 0.1%.
  • Cu 0.1% or less Cu is also an element that is difficult to remove when adjusting the steel composition by steelmaking in the same manner as Ni, and is contained in a trace amount (for example, 0.001% or more), but when it exceeds 0.1% Since the pattern is likely to occur in the hot dip galvanized steel sheet, and also leads to grain boundary embrittlement and cost increase, the content is limited to 0% or more and 0.1% or less.
  • N 0.01% or less N is an impurity inevitably contained in steel. When the N content exceeds 0.01%, the r value, which is an index of deep drawability, is reduced. If the N content is limited to 0% or more and 0.01% or less, there is no substantial adverse effect, and this is an acceptable range.
  • a slab is obtained by casting molten steel that satisfies the above chemical components.
  • the casting method is not particularly limited, but a vacuum casting method, a continuous casting method, or the like may be used.
  • this slab is heated at 1100-1300 ° C.
  • the reason for heating the slab at 1100 to 1300 ° C. is that if it is less than 1100 ° C., the load in hot rolling becomes high and the desired hot rolling finishing temperature cannot be ensured.
  • heating exceeding 1300 ° C. uses excessive energy and causes an increase in cost.
  • the heated slab is hot-rolled under conditions of a finishing temperature of 800 ° C. or higher and 1050 ° C. or lower and a winding temperature of 500 ° C. or higher and 800 ° C. or lower to obtain a hot rolled steel sheet.
  • a finishing temperature 800 ° C. or higher and 1050 ° C. or lower and a winding temperature of 500 ° C. or higher and 800 ° C. or lower.
  • the hot rolling finishing temperature is set to 800 ° C. or higher and 1050 ° C. or lower.
  • the coiling temperature is set to 500 ° C. or higher and 800 ° C. or lower. Moreover, you may perform the pickling which pickles and removes the scale on the surface of a hot-rolled steel plate as a pickling process after this hot-rolling process and before the surface removal process mentioned later.
  • the surface of the hot-rolled steel sheet is removed. Specifically, 10 measurement points that are equally spaced are provided by dividing a line segment section having a reference length of 50 mm into 10 equal parts in the sheet width direction of the hot-rolled steel sheet, and the scale of the hot-rolled steel sheet and the steel When the maximum value at the above 10 measurement points of the Ni and Cu contents of the steel surface part having a depth of 2 ⁇ m on the steel side from the interface to the steel thickness direction is Ni max and Cu max in mass%.
  • the surface of the hot-rolled steel sheet is removed within the range of not less than GL represented by the following formula C and not more than GU represented by the following formula D, in units of ⁇ m, on the steel side in the thickness direction with respect to the interface. To obtain a descaled rolled steel sheet.
  • GL (Ni max + 0.8 ⁇ Cu max ) ⁇ 0.2
  • GU (Ni max + 0.8 ⁇ Cu max ) ⁇ 4 (Formula D)
  • a method of removing the surface it is easy to carry out by machining, and for example, a wire brush roll, an abrasive belt, a shot blast, or the like is preferably used, but any means can be used as long as the above amount can be removed. The method is also acceptable.
  • the surface removal amount is in units of ⁇ m and less than GL, segregated parts of P, Ni, and Cu remain on the steel surface part. If it exceeds GU in a unit of ⁇ m, it takes a burden on the time and equipment for the removal and causes an increase in cost, and further leads to a decrease in the yield of the steel material.
  • the measurement of the Ni and Cu contents in the steel surface part can be performed using a glow discharge emission spectrometer (GDS), an electron probe X-ray microanalysis (EPMA), or the like.
  • GDS glow discharge emission spectrometer
  • EPMA electron probe X-ray microanalysis
  • Ten measurement points that are equally spaced are provided by dividing a line segment section having a reference length of 50 mm in the plate width direction of the hot-rolled steel sheet into 10 equal parts, and each of these measurement points contains Ni and Cu by GDS or EPMA. What is necessary is just to measure quantity.
  • GDS glow discharge emission spectrometer
  • EPMA electron probe X-ray microanalysis
  • EPMA measurement may be performed.
  • the surface of the descaled rolled steel sheet after the surface removal step may be pickled and removed as a pickling step.
  • the pickling method is not particularly limited, and may be a regular pickling method using sulfuric acid or hydrochloric acid.
  • the pickling process for pickling the surface of the descaling rolled steel sheet is performed at least one of after the hot rolling process and before the surface removing process or after the surface removing process and before the plating process described later. It is preferable. Since the segregation part of P, Ni, and Cu cannot be removed in the pickling process, it is necessary to perform surface removal with the removal amount within the above range in order to remove the segregation part. . However, it is preferable to perform the pickling step because adhesion between the descaling rolled steel sheet and the galvannealed layer is increased.
  • P, Ni, and Cu are segregated at the interface between the scale of the steel sheet and the steel during the heating process and the hot rolling process. And this segregation part is extended
  • the surface of the hot-rolled steel sheet is optimally removed, so that P existing in the Ni and Cu segregation portions is removed and rendered harmless.
  • This surface removal amount is optimized, and the P segregation part can be reliably removed although it is less than the conventional removal amount.
  • Cold rolling at 50% or more and 95% or less is preferable because the descaling rolled steel sheet can be controlled to a target thickness while securing the r value and ensuring workability. If the cold rolling rate is less than 50%, it is necessary to increase the coil length of the hot-rolled steel sheet in the hot rolling process, which may lead to an increase in cost in terms of equipment.
  • the descaling rolled steel sheet after the cold rolling process may be annealed at a temperature higher than the recrystallization temperature as an annealing process.
  • annealing at a temperature equal to or higher than the recrystallization temperature, distortion caused by rolling can be removed and softened to improve workability. Note that the effect of one embodiment of the present invention can be obtained without change even if the descaling rolled steel sheet is subjected to a cold rolling process or an annealing process as necessary, as described above.
  • hot-dip galvanized steel sheet is obtained by performing hot dip galvanizing on the descaled rolled steel sheet after the surface removal process, after the pickling process, after the cold rolling process, or after the annealing process.
  • an alloyed hot-dip galvanized steel sheet is obtained by subjecting the hot-dip galvanized steel sheet after the plating process to an alloying heat treatment. Under the present circumstances, it is preferable to process continuously, without cooling a hot-dip galvanized steel plate between a plating process and an alloying process.
  • the conditions in the examples are one example of conditions adopted for confirming the feasibility and effects of the present invention.
  • the invention is not limited to this one condition example.
  • the present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.
  • Alloyed hot-dip galvanized steel sheets were manufactured under the steel compositions shown in Table 1 and the manufacturing conditions shown in Tables 2 and 3. Specifically, specimen slabs (slabs) having the steel compositions shown in Table 1 were produced by continuous casting. This slab was heated and held in a heating furnace (heating process), extracted, descaled (deske), and subjected to hot rolling under the conditions of hot rolling finishing temperature and coiling temperature shown in Table 2 ( Hot rolling process). The surface of the hot rolled steel sheet after hot rolling was pickled as necessary (pickling process), and then the surface of the hot rolled steel sheet was removed to obtain a descaling rolled steel sheet (surface removing process). Thereafter, the surface was cleaned by pickling as necessary (pickling step).
  • the descaled rolled steel sheet was cold-rolled and adjusted to a predetermined thickness as needed (cold rolling process), and then annealed in a continuous annealing furnace (annealing process). And it immersed in the hot dip galvanizing bath, hot dip galvanization (plating process), and alloying process (alloying process) were performed, and the galvannealed steel plate was obtained.
  • the case where pickling is performed is C.I. O. (Carrying Out) and the case where pickling is not performed O. (Not Carrying Out).
  • Other processes are also shown in the same manner.
  • Table 2 the process conditions in the surface removal (surface removal process) of an above-described hot-rolled steel plate are shown.
  • the surface is removed.
  • GL and GU which are appropriate ranges, were calculated in units of ⁇ m.
  • Table 2 also shows the actual surface removal amount.
  • the Ni max and Cu max contents were measured using EPMA (Electron Probe Micro Analyzer).
  • Ten measurement points were provided by dividing a line segment section having a reference length of 50 mm in the plate width direction of the hot-rolled steel sheet into 10 equal parts, and the Ni and Cu contents were measured by EPMA at each measurement point. At this time, the measurement average value from the surface to 2 ⁇ m from the surface to the steel side in the thickness direction with the interface of the hot rolled steel sheet as a reference was taken as the measurement result of the steel surface portion. Then, the maximum value of the 10 measurement points Ni and Cu contents, in mass%, and the Ni max and Cu max.
  • the P, Ni, and Cu contents in the surface portion and base material portion of the descaled rolled steel sheet after the surface removal were also measured, and the segregation state was confirmed.
  • the measurement of P, Ni, and Cu contents is performed by dividing 10 line segments of a reference length of 50 mm in the plate width direction of the descaling rolled steel sheet, and providing 10 measurement points. Measurement was performed using GDS at each measurement point.
  • the measurement average value from the surface to 0.1 ⁇ m in the thickness direction of the descaling rolled steel sheet is taken as the measurement result of the descaling rolled steel sheet surface
  • the measurement result from 2 ⁇ m to 4 ⁇ m from the surface is taken as the descaling rolled steel sheet mother It was set as the measurement result of the material part.
  • the contents of P, Ni, and Cu in the surface portion of the descaling rolled steel sheet are compared with P, Ni, and Cu in the base material part of the descaling rolled steel plate for each component, and the segregation state is expressed as a percentage. expressed. This result passes when each component is 105% or more and 150% or less.
  • Table 5 the measurement result of the segregation state of P, Ni, and Cu represented by ratio of a descaling rolling steel plate surface part and descaling rolling steel plate base material part is shown.
  • the value is farthest from 127.5% (intermediate value between 105% and 150%). Only one measurement point result is shown.
  • Tensile properties are, for example, in accordance with JIS Z 2241: 2011 or ISO 6892-1: 2009, JIS No. 5 test taken from each galvannealed steel sheet so that the tensile direction is perpendicular to the rolling direction and the plate thickness direction. Tensile tests were performed using the pieces, and tensile strength (TS) was evaluated in units of MPa, and elongation (El) was evaluated in units of%. And the case where tensile strength was 320 Mpa or more and elongation was 25% or more was set as the pass.
  • TS tensile strength
  • El elongation
  • Evaluation of the r value that is an index of deep drawing is, for example, in accordance with JIS Z 2254: 2008 or ISO 10113-1: 2006 from each alloyed hot-dip galvanized steel sheet in the direction parallel to the rolling direction, 45 ° direction, and perpendicular direction.
  • JIS No. 5 tensile test specimens were collected, and the r value of each specimen was measured.
  • the r value is measured by measuring the change in the plate thickness and the change in the plate width at the time when the tensile deformation of about 10% is performed in the above-described tensile test. Find the ratio.
  • the surface property was evaluated by investigating the P content in the alloyed hot dip galvanized layer, investigating the dispersion of the plating thickness, and observing the presence or absence of the surface pattern.
  • the P content in the plating layer was measured using GDS. Ten measurement points are provided by dividing a line segment section having a reference length of 50 mm in the plate width direction of the alloyed hot-dip galvanized steel sheet into 10 equal parts. At each measurement point, the P content in the plating layer is determined by GDS. Was measured. The minimum value of the P content of the plated layer of the galvannealed steel sheet at these 10 measurement points was compared with the maximum value of the P content, and 50% or more was accepted.
  • the thickness of the plating layer was measured on a cut surface obtained by plane cutting along the plate thickness direction so that the plate width direction perpendicular to the rolling direction of the galvannealed steel sheet was the observation surface.
  • Ten measurement points are provided by dividing a line segment section having a reference length of 50 mm in the plate width direction of the plated steel sheet into 10 equal parts, and the metal structure of the cut surface is observed at each measurement point, and a plating layer is formed.
  • the thickness of was measured.
  • the metal structure was observed at a magnification such that the observation field of view was approximately 1000 ⁇ m in the plate width direction.
  • the minimum value of the plating layer thickness of the galvannealed steel sheet at these 10 measurement points was compared with the maximum value of the thickness, and 50% or more was regarded as acceptable.
  • Table 4 shows the tensile strength, elongation, and r ave values that are mechanical properties.
  • Table 5 shows the segregation state of P, Ni, and Cu in the descaled rolled steel sheet, the variation in the P content in the galvannealed layer, the variation in the plating thickness, and the presence or absence of the surface pattern.
  • the alloyed hot-dip galvanized steel sheet as an example has excellent workability at the same time while satisfying mechanical properties, and variation in P content in the plating layer and There was little variation in plating thickness, and there was no surface pattern.
  • T is a comparative example in which the Ti content exceeds the upper limit.
  • This plated steel sheet had an r value of 0.9 and was inferior in workability.
  • Steel No. U is a comparative example in which the Ni content exceeds the upper limit.
  • Steel No. V is a comparative example in which the Cu content exceeds the upper limit. Furthermore, since the surface removal amount of these steels is below the lower limit, the surface plating properties of these plated steel sheets varied and patterns were observed.
  • Steel No. W is a comparative example in which the Nb content exceeds the upper limit. This plated steel sheet had an r value of 1.1 and was inferior in workability.
  • Steel No. KK is a comparative example in which the C content is lower than the lower limit.
  • this plated steel plate has a large load in steel making and causes an increase in cost.
  • Steel No. LL is a comparative example in which the C content exceeds the upper limit. This plated steel sheet was inferior in workability.
  • Steel No. MM is a comparative example in which the Si content is lower than the lower limit. This plated steel sheet was inferior in tensile strength.
  • Steel No. NN is a comparative example in which the Si content exceeds the upper limit. This plated steel sheet was inferior in workability.
  • Steel No. OO is a comparative example in which the Mn content is lower than the lower limit. This plated steel sheet was inferior in tensile strength.
  • Steel No. PP is a comparative example in which the P content is below the lower limit.
  • This plated steel sheet was inferior in tensile strength.
  • Steel No. QQ is a comparative example in which the Al content is lower than the lower limit. This plated steel sheet was inferior in workability because deoxidation was insufficient and oxide remained.
  • Steel No. RR is a comparative example in which the Al content exceeds the upper limit. This plated steel sheet was inferior in workability.
  • Steel No. SS is a comparative example in which the S content exceeds the upper limit. This plated steel sheet was inferior in workability.
  • Steel No. TT is a comparative example in which the B content exceeds the upper limit. This plated steel sheet was inferior in workability.
  • UU is a comparative example in which the heating temperature in the heating step is lower than the lower limit, and the finishing temperature in the hot rolling step is lower than the lower limit.
  • This plated steel sheet was inferior in workability.
  • Steel No. VV is a comparative example in which the finishing temperature in the hot rolling process is lower than the lower limit. This plated steel sheet was inferior in workability.
  • Steel No. WW is a comparative example in which the coiling temperature in the hot rolling process is below the lower limit. This plated steel sheet has a poor shape and cannot be used as a product.
  • Steel No. XX is a comparative example in which the coiling temperature in the hot rolling process exceeds the upper limit. This plated steel sheet has too many scales and cannot be used as a product.
  • Steel No. AB is a comparative example in which the Mo content exceeds the upper limit. This plated steel sheet was inferior in workability.
  • Steel No. AC is a comparative example in which the N content exceeds the upper limit. This plated steel
  • the present invention while satisfying mechanical properties such as tensile strength, at the same time, it has excellent workability and has a plating layer with few surface defects such as a linear pattern. Since it is possible to provide an alloyed hot-dip galvanized steel sheet for press working exhibiting a beautiful surface appearance and a method for producing the same, the industrial applicability is high.

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PCT/JP2012/075708 2012-10-03 2012-10-03 合金化溶融亜鉛めっき鋼板およびその製造方法 Ceased WO2014054141A1 (ja)

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CN201280076196.1A CN104685091B (zh) 2012-10-03 2012-10-03 合金化热浸镀锌钢板及其制造方法
PCT/JP2012/075708 WO2014054141A1 (ja) 2012-10-03 2012-10-03 合金化溶融亜鉛めっき鋼板およびその製造方法
KR1020157010234A KR101720891B1 (ko) 2012-10-03 2012-10-03 합금화 용융 아연 도금 강판 및 그 제조 방법
JP2013513873A JP5825343B2 (ja) 2012-10-03 2012-10-03 合金化溶融亜鉛めっき鋼板およびその製造方法
US14/429,520 US9850565B2 (en) 2012-10-03 2012-10-03 Method for producing a galvannealed steel sheet
BR112015007044-2A BR112015007044B1 (pt) 2012-10-03 2012-10-03 chapa de aço galvanizada com recozimento e método para produzir a mesma
IN2193DEN2015 IN2015DN02193A (enExample) 2012-10-03 2012-10-03
MX2015004208A MX380570B (es) 2012-10-03 2012-10-03 Lámina de acero revestida con zinc por inmersión en caliente aleada y método para producir la misma.

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KR20230165834A (ko) 2021-05-10 2023-12-05 닛폰세이테츠 가부시키가이샤 아연계 도금 강판

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CN112585287B (zh) * 2018-08-28 2022-03-01 杰富意钢铁株式会社 热轧钢板、冷轧钢板及它们的制造方法
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KR20230165834A (ko) 2021-05-10 2023-12-05 닛폰세이테츠 가부시키가이샤 아연계 도금 강판
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