EP4261306A1 - Feuerverzinktes stahlblech und herstellungsverfahren dafür - Google Patents

Feuerverzinktes stahlblech und herstellungsverfahren dafür Download PDF

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Publication number
EP4261306A1
EP4261306A1 EP21910543.4A EP21910543A EP4261306A1 EP 4261306 A1 EP4261306 A1 EP 4261306A1 EP 21910543 A EP21910543 A EP 21910543A EP 4261306 A1 EP4261306 A1 EP 4261306A1
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EP
European Patent Office
Prior art keywords
steel sheet
less
hot
dip galvanized
temperature
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.)
Pending
Application number
EP21910543.4A
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English (en)
French (fr)
Inventor
Takuya Hirashima
Tatsuya Nakagaito
Masaki Koba
Yoichi Makimizu
Katsuya Hata
Shotaro TERASHIMA
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP4261306A1 publication Critical patent/EP4261306A1/de
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • 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
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • This disclosure relates to a hot-dip galvanized steel sheet that is suitably used for automobile members and the like, and a method of manufacturing the hot-dip galvanized steel sheet.
  • JP 2012-172159 A (PTL 1) describes "a high-strength cold-rolled steel sheet with excellent uniform deformability and local deformability, which contains, in mass%,
  • JP 2009-249733A (PTL 2) describes "a high-strength steel sheet having excellent hardenability with very little aging deterioration, which contains, in mass%,
  • steel sheets used as materials for automobile members are sometimes subjected to zinc or zinc alloy coating or plating, such as hot-dip galvanizing.
  • Si and Mn are oxidizable elements, which combine with oxygen to form oxides on the steel sheet surface.
  • the presence of such Si and Mn oxides on the surface of the base steel sheet during the coating or plating treatment reduces the wettability of the base steel sheet by a coating or plating bath (hot dip zinc), causing poor coating or plating appearance such as non-coating or non-plating and deterioration of coating or plating adhesion.
  • the coating or plating quality is improved by containing an appropriate amount of Fe in a hot-dip galvanized layer.
  • the dew point is set in a range of -20 °C or higher and 5 °C or lower and a certain amount of oxygen is ensured in the holding atmosphere of annealing, the internal oxidation in the surface layer of the base steel sheet is promoted.
  • the hydrogen concentration is set to 3 mass% or more and 20 mass% or less, oxides that have been formed on the surface of the base steel sheet (and oxides that have been formed during the holding of annealing) are reduced. Therefore, it is important to suppress the external oxidation while introducing sufficient oxygen from the atmosphere into the interior (surface layer) of the base steel sheet. It is also important to promote the diffusion of Fe from the base steel sheet to the coated or plated layer by setting the temperature of the cold-rolled steel sheet when it enters the coating or plating bath to at least 10 °C higher than the coating or plating bath temperature.
  • the performance of automobile bodies can be significantly improved.
  • C is an element that improves the hardenability. C also plays a role in increasing the strength of ferrite. Therefore, it is required to contain C to ensure a desired tensile strength (TS) of 750 MPa or more. When the C content is less than 0.09 %, the desired tensile strength cannot be obtained. Therefore, the C content is set to 0.09 % or more.
  • the C content is preferably 0.10 % or more and more preferably 0.11 % or more.
  • the C content exceeds 0.17 %, the stability of austenite increases, and it is difficult to form bainite. In addition, the strength of martensite increases excessively, and the yield ratio decreases. Therefore, the C content is set to 0.17 % or less.
  • the C content is preferably 0.16 % or less and more preferably 0.15 % or less.
  • Si 0.3 % or more and 1.1 % or less
  • Si is a solid-solution-strengthening element. Si also plays a role in increasing the yield ratio by increasing the strength of ferrite. To obtain this effect, the Si content is set to 0.3 % or more. The Si content is preferably 0.4 % or more and more preferably 0.5 % or more. On the other hand, if the Si content is too high, Si concentrates on the surface of the base steel sheet, causing external oxidation and deteriorating the coating quality such as coating appearance. Therefore, the Si content is set to 1.1 % or less. The Si content is preferably 1.0 % or less and more preferably 0.9 % or less.
  • Mn 1.9 % or more and 2.7 % or less
  • Mn is an element that improves the hardenability of steel. Therefore, it is required to contain Mn to ensure the desired tensile strength. When the Mn content is less than 1.9 %, the desired tensile strength cannot be obtained. Therefore, the Mn content is set to 1.9 % or more.
  • the Mn content is preferably 2.0 % or more and more preferably 2.1 % or more.
  • Mn tends to concentrate into austenite during, for example, the holding of annealing, and the strength of martensite that transforms from austenite excessively increases. Therefore, the Mn content is set to 2.7 % or less.
  • the Mn content is preferably 2.6 % or less and more preferably 2.5 % or less.
  • the P content is an element that strengthens steel. However, if the P content is too high, P segregates to grain boundaries and deteriorates the hole expansion formability. Therefore, the P content is set to 0.10 % or less.
  • the P content is preferably 0.05 % or less and more preferably 0.03% or less.
  • the lower limit of the P content is not particularly limited, it is preferably 0.001 % or more from the viewpoint of cost, for example.
  • the P content is more preferably 0.003 % or more and even more preferably 0.005 % or more.
  • the S content is set to 0.050 % or less.
  • the S content is preferably 0.030 % or less, more preferably 0.020 % or less, and even more preferably 0.015 % or less.
  • the lower limit of the S content is not particularly limited, it is preferably 0.0002 % or more from the viewpoint of cost, for example.
  • the S content is more preferably 0.0005 % or more.
  • Al 0.01 % or more and 0.20 % or less
  • Al is an element added as a deoxidizing material. Al also plays a role in reducing coarse inclusions in the steel and improving the hole expansion formability. When the Al content is less than 0.01 %, the above effect is insufficient. Therefore, the Al content is set to 0.01 % or more. The Al content is preferably 0.02 % or more. On the other hand, if the Al content exceeds 0.20 %, nitride-based precipitates such as AlN are coarsened, and the hole expansion formability is deteriorated. Therefore, the Al content is set to 0.20 % or less. The Al content is preferably 0.17 % or less and more preferably 0.15 % or less.
  • N is an element that contributes to the improvement of hole expansion formability by forming nitride-based precipitates such as AlN that pin crystal grain boundaries.
  • the N content is set to 0.10 % or less.
  • the N content is preferably 0.05 % or less and more preferably 0.010 % or less.
  • the lower limit of the N content is not particularly limited, it is preferably 0.0006 % or more from the viewpoint of cost, for example.
  • the N content is more preferably 0.0010 % or more.
  • the base steel sheet of the hot-dip galvanized steel sheet according to one embodiment of the present disclosure has a chemical composition containing the above elements and the balance of Fe (iron) and inevitable impurities. It is particularly preferable that the base steel sheet of the hot-dip galvanized steel sheet according to one embodiment of the present disclosure has a chemical composition containing the above elements, with the balance consisting of Fe and inevitable impurities.
  • the above describes the basic chemical composition of the base steel sheet of the hot-dip galvanized steel sheet according to one embodiment of the present disclosure.
  • the base steel sheet may contain, as optional elements, at least one selected from the group consisting of
  • it may contain, as optional elements, at least one selected from the group consisting of Ta, W, Ni, Cu, Sn, Sb, Ca, Mg, and Zr, where the selected elements are contained in a total amount of 0.1 % or less.
  • the Nb content is preferably 0.0010 % or more.
  • the Nb content is more preferably 0.0015 % or more and even more preferably 0.0020 % or more.
  • an excessively high Nb content results in an excessive amount of carbonitride-based precipitate, which deteriorates the hole expansion formability. Therefore, when Nb is contained, the Nb content is preferably 0.040 % or less.
  • the Nb content is more preferably 0.035 % or less and even more preferably 0.030 % or less.
  • the Ti like Nb, contributes to increasing the strength through the refinement of prior ⁇ grains and the formation of fine precipitates.
  • the fine precipitates increase the strength of ferrite and contribute to increasing the yield ratio.
  • the Ti content is preferably 0.0010 % or more.
  • the Ti content is more preferably 0.0015 % or more and even more preferably 0.0020 % or more.
  • an excessively high Ti content results in an excessive amount of carbonitride-based precipitate, which deteriorates the hole expansion formability. Therefore, when Ti is contained, the Ti content is preferably 0.030 % or less.
  • the Ti content is more preferably 0.025 % or less and even more preferably 0.020 % or less.
  • B is an element that improves the hardenability of steel.
  • the inclusion of B renders it possible to achieve the desired tensile strength even when the Mn content is low.
  • the B content is preferably 0.0001 % or more.
  • the B content is more preferably 0.0002 % or more.
  • a B content of 0.0030 % or more results in an excessive amount of nitride-based precipitate such as BN, which deteriorates the hole expansion formability. Therefore, when B is contained, the B content is preferably 0.0030 % or less.
  • the B content is more preferably 0.0025 % or less and even more preferably 0.0020 % or less.
  • the Cr content is an element that improves the hardenability of steel.
  • the Cr content is preferably 0.005 % or more.
  • an excessively high Cr content may cause oxide formation reaction accompanied by the formation of hydrogen ions, which may deteriorate the coating quality. Further, precipitates such as carbides are excessively precipitated, and the hole expansion formability is deteriorated. Therefore, when Cr is contained, the Cr content is preferably 0.3 % or less.
  • the Cr content is more preferably 0.2 % or less and even more preferably 0.1 % or less.
  • Mo is an element that improves the hardenability of steel.
  • the Mo content is preferably 0.005 % or more.
  • an excessively high Mo content may cause oxide formation reaction accompanied by the formation of hydrogen ions, which may deteriorate the coating quality. Further, precipitates such as carbides are excessively precipitated, and the hole expansion formability is deteriorated. Therefore, when Mo is contained, the Mo content is preferably 0.2 % or less.
  • the Mo content is more preferably 0.1 % or less and even more preferably 0.04 % or less.
  • V 0.065 % or less.
  • V is an element that improves the hardenability of steel.
  • the V content is preferably 0.005 % or more.
  • an excessively high V content may cause oxide formation reaction accompanied by the formation of hydrogen ions, which may deteriorate the coating quality. Further, precipitates such as carbides are excessively precipitated, and the hole expansion formability is deteriorated. Therefore, when V is contained, the V content is preferably 0.065 % or less.
  • the V content is more preferably 0.050 % or less and even more preferably 0.035 % or less.
  • Ta, W, Ni, Cu, Sn, Sb, Ca, Mg and Zr are elements that increase the strength without deteriorating the coating quality.
  • the content of these elements is preferably 0.0010 % or more, either singly or in total. However, when the total content of these elements exceeds 0.1 %, the above effect is saturated. Therefore, when at least one selected from the group consisting of Ta, W, Ni, Cu, Sn, Sb, Ca, Mg, and Zr are contained, the total content of these elements is preferably 0.1 % or less.
  • the balance other than the aforementioned elements is Fe and inevitable impurities.
  • the area ratio of ferrite is set to 30 % or more.
  • the area ratio of ferrite is preferably 35 % or more and more preferably 40 % or more.
  • an excess of ferrite reduces the area ratio of martensite required to ensure the strength, rendering it difficult to ensure the strength. It also suppresses the formation of bainite and reduces the hole expansion formability and the yield ratio. Therefore, the area ratio of ferrite is set to 85 % or less.
  • the area ratio of ferrite is preferably 80 % or less.
  • the ferrite is a microstructure containing crystal grains of BCC lattice, which is formed by transformation from austenite at relatively high temperatures.
  • Martensite contributes to the improvement of strength and is a phase necessary for ensuring the desired tensile strength. Therefore, the area ratio of martensite is set to 5 % or more.
  • the area ratio of martensite is preferably 8 % or more and more preferably 10 % or more.
  • an excess of martensite deteriorates the elongation. Therefore, the area ratio of martensite is set to 30 % or less.
  • the area ratio of martensite is preferably 28 % or less and more preferably 25 % or less.
  • the martensite refers to a hard microstructure formed from austenite at or below the martensite transformation temperature (also referred to simply as "Ms point"), which includes both so-called fresh martensite as quenched and so-called tempered martensite where fresh martensite is reheated and tempered.
  • Ms point martensite transformation temperature
  • Bainite is a phase necessary for improving the hole expansion formability and increasing the yield ratio. Therefore, the area ratio of bainite is set to 10 % or more.
  • the area ratio of bainite is preferably 15 % or more and more preferably 20 % or more.
  • an excess of bainite deteriorates the elongation. Therefore, the area ratio of bainite is set to 60 % or less.
  • the area ratio of bainite is preferably 55 % or less and more preferably 50 % or less.
  • the bainite is a hard microstructure in which fine carbides are dispersed in needle-like or plate-like ferrite, and it is formed from austenite at relatively low temperatures (at or above the martensitic transformation temperature).
  • the steel microstructure of the base steel sheet of the hot-dip galvanized steel sheet may contain metallic phases other than martensite, ferrite, and bainite. It is acceptable if the total area ratio of other metallic phases is 15 % or less. Therefore, the area ratio of other metallic phases is set to 15 % or less. The area ratio of other metallic phases is preferably 10 % or less and more preferably 5 % or less. The area ratio of other metallic phases may be 0 %.
  • Examples of the other metallic phases include pearlite, retained austenite, and non-recrystallized ferrite.
  • pearlite and non-recrystallized ferrite deteriorate the workability (El and ⁇ ), so that the total area ratio of pearlite and non-recrystallized ferrite is set to 5 % or less.
  • the area ratios of pearlite and non-recrystallized ferrite may each be 0 %.
  • retained austenite does not deteriorate the workability (El and ⁇ )
  • the area ratio of retained austenite is preferably 10 % or less and more preferably 5 % or less.
  • the area ratio of retained austenite may be 0 % or less.
  • the pearlite is a microstructure containing ferrite and needle-like cementite.
  • the retained austenite is austenite remaining without being transformed into martensite.
  • the non-recrystallized ferrite is ferrite that is not recrystallized, in which crystal grains include sub-boundaries.
  • the area ratio of each phase is measured as follows.
  • test piece is collected from the base steel sheet of the hot-dip galvanized steel sheet so that an L-section parallel to the rolling direction serves as a test surface.
  • the test surface of the test piece is subjected to mirror polishing, and the microstructure is revealed with a nital solution.
  • the test surface of the test piece with the revealed microstructure is observed with a SEM at a magnification of 1500x, and the area ratio of martensite, the area ratio of ferrite, and the area ratio of bainite at the 1/4 thickness position of the base steel sheet are measured with a point counting method.
  • martensite is a white microstructure. Further, fine carbides are precipitated inside tempered martensite among the martensite. Ferrite is a black microstructure. Bainite has white carbides precipitated in a black microstructure.
  • Each phase in the SEM image is identified based on the above description. However, depending on the plane orientation of block grains and the degree of etching, it may be difficult to reveal the internal carbides. In that case, etching is thoroughly performed for confirmation.
  • the total area ratio of the other metallic phases is calculated by subtracting the area ratio of martensite, the area ratio of ferrite, and the area ratio of bainite from 100 %.
  • pearlite is a microstructure containing ferrite and needle-like cementite as described above. Based on this, pearlite is identified in the SEM image, and the area ratio of pearlite is measured. Non-recrystallized ferrite has sub-boundaries inside crystal grains as described above. Based on this, non-recrystallized ferrite is identified in the SEM image, and the area ratio of non-recrystallized ferrite is measured.
  • the area ratio of retained austenite is measured as follows.
  • the base steel sheet of the hot-dip galvanized steel sheet is polished in the thickness direction (depth direction) to the 1/4 thickness position and then chemically polished by 0.1 mm to obtain an observation plane.
  • the observation plane is observed with the X-ray diffraction method.
  • ratios of the diffraction intensity of each of (200), (220) and (311) planes of fcc iron (austenite) to the diffraction intensity of each of (200), (211), and (220) planes of bcc iron are determined, and the volume fraction of retained austenite is calculated based on the ratio of diffraction intensity of each plane.
  • the volume fraction of retained austenite is taken as the area ratio of retained austenite.
  • Amount of oxygen present as oxide in the surface layer of the base steel sheet (hereinafter also referred to as “amount of oxygen in oxide form in the surface layer of the base steel sheet”): 0.05 g/m 2 or more and 0.50 g/m 2 or less per surface
  • Si and Mn are oxidizable elements, which combine with oxygen to form oxides on the steel sheet surface.
  • the presence of such Si and Mn oxides on the surface of the base steel sheet during coating treatment reduces the wettability of the base steel sheet by a coating bath (hot-dip zinc), causing poor coating appearance such as non-coating and deterioration of coating adhesion.
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet is set to 0.05 g/m 2 or more per surface (note that all the amount of oxygen described below is the amount for one surface).
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet is preferably 0.06 g/m 2 or more.
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet exceeds 0.50 g/m 2 , the oxides promote fracture and deteriorate the elongation and the hole expansion formability. Therefore, the amount of oxygen in oxide form in the surface layer of the base steel sheet is set to 0.50 g/m 2 or less.
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet is preferably 0.45 g/m 2 or less.
  • the surface layer is an area from the surface of the base steel sheet to a position at a depth of 100 ⁇ m.
  • Oxides are compounds of oxygen and elements such as Si, Mn, Fe, P, Al, Nb, Ti, B, Cr, Mo, and V contained in the base steel sheet, and the oxides are mainly Si oxides and Mn oxides.
  • the amount of internal oxidation is inversely related to the amount of external oxidation. Therefore, if external oxidation occurs in the base steel sheet, the amount of oxygen in oxide form in the surface layer of the base steel sheet is less than 0.05 g/m 2 .
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet is measured with an "impulse furnace-infrared absorption method".
  • the hot-dip galvanized layer is removed from the hot-dip galvanized steel sheet.
  • the method of removing the hot-dip galvanized layer is not limited if the hot-dip galvanized layer can be totally removed. Examples thereof include pickling, alkali dissolution, and mechanical polishing.
  • the measured value is taken as the total amount of oxygen OI (g) contained in the base steel sheet.
  • At least the surface layers an area from the surface of the base steel sheet to a position at a depth of 100 ⁇ m
  • the amount of oxygen in the steel of the base steel sheet is measured after the surface layers have been removed. The measured value is taken as OH (g).
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet is calculated based on the following formula.
  • Amount of oxygen in oxide form in the surface layer of the base steel sheet OI g ⁇ OH g ⁇ thickness of the base steel sheet before polishing mm / thickness of the base steel sheet after polishing mm ⁇ ( surface area of the base steel sheet per surface m 2 ⁇ 2
  • the amount of oxygen in oxide form in the surface layer of the base steel sheet is calculated by
  • the thickness of the base steel sheet of the hot-dip galvanized steel sheet according to one embodiment of the present disclosure is preferably 0.2 mm or more.
  • the thickness is preferably 3.2 mm or less.
  • Fe content in hot-dip galvanized layer 0.40 mass% or more
  • the Fe content in the hot-dip galvanized layer is set to 0.40 mass% or more.
  • the Fe content in the hot-dip galvanized layer is preferably 0.50 mass% or more.
  • an excess of Fe in the hot-dip galvanized layer results in the formation of a hard Fe-Zn alloy phase in the hot-dip galvanized layer.
  • the Fe content in the hot-dip galvanized layer is preferably 8.0 mass% or less.
  • the Fe content in the hot-dip galvanized layer is more preferably 7.5 mass% or less and even more preferably 7.0 mass% or less.
  • Coating weight in hot-dip galvanized layer 20 g/m 2 or more per surface
  • the coating weight is preferably 20 g/m 2 or more per surface (note that all the coating weight described below is the amount for one surface).
  • the coating weight is more preferably 25 g/m 2 or more and even more preferably 30 g/m 2 or more.
  • the upper limit of the coating weight is not particularly limited. However, if the coating weight exceeds 120 g/m 2 , the above effect is saturated. Therefore, the coating weight is preferably 120 g/m 2 or less.
  • the Fe content and the coating weight in the hot-dip galvanized layer are measured as follows.
  • the mass of the test piece is weighed for the first time.
  • two or three drops of inhibitor which is a corrosion inhibitor for Fe, are added to 30 cc of 1:3 HCl solution (HCl solution with a concentration of 25 vol.%), and then the test piece is immersed in the solution to dissolve the hot-dip galvanized layer of the test piece.
  • the solution is collected. After the test piece is collected and dried, the mass of the test piece is weighed for the second time.
  • dissolved amount of Fe, dissolved amount of Zn, and dissolved amount of Al The masses of Fe, Zn, and Al dissolved in the collected solution (hereinafter referred to as dissolved amount of Fe, dissolved amount of Zn, and dissolved amount of Al) are measured with the inductively coupled plasma (ICP) method, and the Fe content in the hot-dip galvanized layer is determined by the following formula.
  • ICP inductively coupled plasma
  • the hot-dip galvanized layer is mainly composed of Zn and is basically composed of Zn and the aforementioned Fe. Depending on the composition of the coating bath, the hot-dip galvanized layer may contain 0.30 mass% or less, specifically 0.15 mass% to 0.30 mass%, of Al. The balance other than Zn, Fe and Al is inevitable impurities.
  • the hot-dip galvanized layer may be provided on only one side or on both sides of the base steel sheet.
  • the hot-dip galvanized steel sheet according to one embodiment of the present disclosure has a tensile strength (TS) of 750 MPa or more.
  • the tensile strength (TS) is preferably 780 MPa or more.
  • the upper limit of the tensile strength is not particularly limited, a tensile strength of less than 980 MPa is preferred considering the balance with other properties.
  • TS tensile strength
  • YS yield stress
  • El elongation
  • a JIS No. 5 test piece with a gauge length of 50 mm and a gauge width of 25 mm is collected from the center of the width of the hot-dip galvanized steel sheet, with the rolling direction being the longitudinal direction.
  • the collected JIS No. 5 test piece is subjected to a tensile test in accordance with the provisions of JIS Z 2241 (2011) to measure the tensile strength (TS), the yield stress (YS), and the elongation (El).
  • the tensile speed is 10 mm/min.
  • ⁇ is the maximum hole expansion ratio (%), which is measured as follows.
  • a 100 mm square test piece is collected from the center of the width of the hot-dip galvanized steel sheet.
  • the collected test piece is subjected to a hole expanding test according to the Japan Iron and Steel Federation standard JFST1001 to measure ⁇ . Specifically, after punching a hole with a diameter of 10 mm in the test piece, a 60-degree conical punch is pressed into the hole while the surrounding area is being restrained, and the diameter of the hole at the crack initiation limit is measured.
  • the maximum hole expansion ratio ⁇ (%) is determined by the following formula.
  • Excellent coating quality means that there is no peeling of the hot-dip galvanized layer in a ball impact test under the following conditions, and that there is no non-coating defect in the hot-dip galvanized layer (preferably, there is no uneven coating appearance) found by appearance observation.
  • the non-coating defect refers to an area of several micrometers to several millimeters in size where the base steel sheet is exposed without the hot-dip galvanized layer.
  • temperature is the surface temperature of the steel sheet or slab unless otherwise specified.
  • the surface temperature of the steel sheet or slab is measured, for example, using a radiation thermometer.
  • a steel material (steel slab) having the chemical composition described above is subjected to hot rolling to obtain a hot-rolled steel sheet.
  • the steel material used is preferably obtained by continuous casting to prevent macro-segregation of components.
  • the steel material can also be obtained by ingot casting or thin slab casting.
  • the heating temperature of the slab is preferably 1200 °C or higher.
  • the heating temperature of the slab is more preferably 1230 °C or higher and even more preferably 1250 °C or higher.
  • the upper limit of the heating temperature of the slab is not particularly limited, but 1400 °C or lower is preferred.
  • the heating temperature of the slab is more preferably 1350 °C or lower.
  • Rolling finish temperature 840 °C or higher and 900 °C or lower
  • the rolling finish temperature is preferably 840 °C or higher.
  • the rolling finish temperature is more preferably 860 °C or higher.
  • the rolling finish temperature is preferably 900 °C or lower.
  • the rolling finish temperature is more preferably 880 °C or lower.
  • Coiling temperature 450 °C or higher and 650 °C or lower
  • the steel material is subjected to hot rolling as described above to obtain a hot-rolled steel sheet, and then the hot-rolled steel sheet is coiled.
  • the coiling temperature is higher than 650 °C, the surface of the steel substrate may be decarburized. This may cause a difference in microstructure between the interior and the surface of the base steel sheet, resulting in uneven alloy concentration. Further, coarse carbides and nitrides may be formed, which deteriorates the hole expansion formability. Therefore, the coiling temperature is preferably 650 °C or lower.
  • the coiling temperature is more preferably 630 °C or lower.
  • the coiling temperature is preferably 450 °C or higher to prevent deterioration of cold rolling manufacturability.
  • the coiling temperature is more preferably 470 °C or higher.
  • the hot-rolled steel sheet may be subjected to pickling after coiling.
  • the conditions of the pickling are not particularly limited, and conventional methods may be followed. Further, the hot-rolled steel sheet may be subjected to heat treatment after coiling to soften the microstructure.
  • the hot-rolled steel sheet obtained in the hot rolling process is subjected to cold rolling to obtain a cold-rolled steel sheet.
  • the cold rolling ratio is preferably 20 % or more.
  • the cold rolling ratio is more preferably 30 % or more.
  • the cold rolling ratio is preferably 90 % or less.
  • the cold rolling ratio is more preferably 80 % or less.
  • the cold-rolled steel sheet obtained in the cold rolling process is heated to an annealing temperature, held at the annealing temperature, and then cooled.
  • Average heating rate 1 °C/s or higher and 7 °C/s or lower
  • the average heating rate is preferably a low rate so that ferrite is recrystallized and the desired area ratio of ferrite is ensured. Therefore, the average heating rate is set to 7 °C/s or lower.
  • the average heating rate is preferably 6 °C/s or lower and more preferably 5 °C/s or lower.
  • Mn which diffuses at a low rate, also concentrates into austenite and stabilizes the austenite. As a result, it is difficult to cause bainite transformation, and the desired complex structure cannot be obtained. Therefore, the average heating rate is set to 1 °C/s or higher.
  • the average heating rate is preferably 2 °C/s or higher and more preferably 3 °C/s or higher.
  • Annealing temperature (A C1 point + 50 °C) or higher and (A C3 point + 20 °C) or lower
  • the annealing temperature is set to (A C1 point + 50 °C) or higher.
  • the annealing temperature is preferably (A C1 point + 60 °C) or higher.
  • the annealing temperature is set to (A C3 point + 20 °C) or lower.
  • the annealing temperature is preferably (A C3 point + 10 °C) or lower.
  • the A C1 point and the A C3 point are calculated by the following formulas, respectively.
  • (% element symbol) refers to the content (mass %) of each element in the chemical composition of the base steel sheet. If the element is not contained (including cases where it is inevitably contained), it is calculated as 0.
  • a C1 723 + 22 % Si ⁇ 18 % Mn + 17 % Cr + 4.5 % Mo + 16 % V
  • a C3 910 ⁇ 203 ⁇ % C + 45 % Si ⁇ 30 % Mn ⁇ 20 % Cu ⁇ 15 % Ni + 11 % Cr + 32 % Mo + 104 % V + 400 % Ti + 460 % Al
  • the annealing temperature may be constant during the holding.
  • the annealing temperature may not be constant during the holding, if it is within the above temperature range and the temperature fluctuation range is within ⁇ 10 °C of the set temperature.
  • Annealing time 1 second or longer and 40 seconds or shorter
  • the annealing time is an important condition to transform austenite to bainite. From the viewpoint of avoiding concentration of Mn in austenite, i.e., avoiding excessive stabilization of austenite and obtaining an appropriate amount of bainite, the annealing time is preferably short. Therefore, the annealing time is set to 40 seconds or shorter. The annealing time is preferably 30 seconds or shorter and more preferably 25 seconds or shorter. On the other hand, if the annealing time is shorter than 1 second, recrystallization of ferrite is not promoted, resulting in deteriorated hole expansion formability. Therefore, the annealing time is set to 1 second or longer. The annealing time is preferably 5 seconds or longer. The annealing time is the holding time at the annealing temperature.
  • the dew point of the holding atmosphere is set to -20 °C or higher.
  • the dew point of the holding atmosphere is preferably -18 °C or higher and more preferably -15 °C or higher.
  • the dew point of the holding atmosphere is set to 5 °C or lower.
  • the dew point of the holding atmosphere is preferably 0 °C or lower.
  • Hydrogen concentration in holding atmosphere 3 mass% or more and 20 mass% or less.
  • the hydrogen concentration in the holding atmosphere is set to 3 mass% or more.
  • the hydrogen concentration in the holding atmosphere is preferably 5 mass% or more.
  • the hydrogen concentration in the holding atmosphere is set to 20 mass% or less.
  • the hydrogen concentration in the holding atmosphere is preferably 17 mass% or less.
  • the primary cooling rate is set to 10 °C/s or higher.
  • the primary cooling rate is preferably 12 °C/s or higher and more preferably 15 °C/s or higher.
  • the upper limit of the primary cooling rate is not limited, because a high primary cooling rate is preferred to suppress pearlite transformation. For example, there is no problem if the primary cooling rate reaches 2000 °C/s or higher by water cooling or like.
  • Primary cooling stop temperature 450 °C or higher and 600 °C or lower
  • the primary cooling stop temperature is set to 450 °C or higher and 600 °C or lower to suppress pearlite transformation during the primary cooling and to ensure the specified amount of bainite during the secondary cooling. That is, if the primary cooling stop temperature exceeds 600 °C, pearlite transformation is accelerated during the secondary cooling. Therefore, the primary cooling stop temperature is set to 600 °C or lower.
  • the primary cooling stop temperature is preferably 580 °C or lower and more preferably 560 °C or lower.
  • bainite transformation is suppressed during the secondary cooling, rendering it difficult to ensure the specified fraction of bainite. Therefore, the primary cooling stop temperature is set to 450 °C or higher.
  • the primary cooling stop temperature is preferably 460 °C or higher and more preferably 470 °C or higher.
  • Secondary cooling time 20 seconds or longer and 100 seconds or shorter
  • the secondary cooling time is set to 20 seconds or longer.
  • the secondary cooling time is preferably 25 seconds or longer and more preferably 30 seconds or longer.
  • the secondary cooling time is set to 100 seconds or shorter.
  • the secondary cooling time is preferably 90 seconds or shorter and more preferably 80 seconds or shorter.
  • Secondary cooling stop temperature 400 °C or higher and 500 °C or lower
  • the secondary cooling stop temperature is set to 400 °C or higher and 500 °C or lower from the viewpoint of ensuring the specified fraction of bainite and controlling the temperature of the cold-rolled steel sheet when it enters the coating bath in the coating treatment process, which will be described later, within the specified range. That is, if the secondary cooling stop temperature exceeds 500 °C, bainite transformation is accelerated during the secondary cooling, and the fraction of bainite becomes too high. Therefore, the secondary cooling stop temperature is set to 500 °C or lower.
  • the secondary cooling stop temperature is preferably 495 °C or lower and more preferably 490 °C or lower.
  • the secondary cooling stop temperature is set to 400 °C or higher.
  • the secondary cooling stop temperature is preferably 420 °C or higher and more preferably 440 °C or higher.
  • the cold-rolled steel sheet is subjected to hot-dip galvanizing treatment after the annealing treatment.
  • the temperature of the cold-rolled steel sheet when it enters the coating bath be at least 10 °C higher than the coating bath temperature.
  • the temperature of the cold-rolled steel sheet when it enters the coating bath higher than the coating bath temperature, especially to a temperature at least 10 °C higher than the coating bath temperature.
  • the temperature of the cold-rolled steel sheet when it enters the coating bath is preferably at least 15 °C higher than the coating bath temperature and more preferably at least 20 °C higher than the coating bath temperature.
  • the upper limit of the temperature of the cold-rolled steel sheet when it enters the coating bath is not particularly limited, but it is preferably 500 °C or lower.
  • the coating bath is basically composed of Zn, and it may contain 0.15 mass% to 0.30 mass% of Al. The balance other than Zn and Al is inevitable impurities.
  • the coating bath temperature is preferably 440 °C to 500 °C.
  • the annealing process and the coating treatment process may be performed on a continuous annealing line (CAL) or on a continuous annealing hot-dip galvanizing line (CGL). Each process may be performed by batch processing.
  • CAL continuous annealing line
  • CGL continuous annealing hot-dip galvanizing line
  • temper rolling may be performed for shape adjustment.
  • each obtained hot-dip galvanized steel sheet was used to identify the microstructure in the base steel sheet, measure the amount of oxygen in oxide form in the surface layer of the base steel sheet, and measure the coating weight and the Fe content per surface in the hot-dip galvanized layer, according to the procedure described above.
  • the desired tensile strength (TS) is 750 MPa or more.
EP21910543.4A 2020-12-24 2021-12-15 Feuerverzinktes stahlblech und herstellungsverfahren dafür Pending EP4261306A1 (de)

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