EP3666919A1 - Tôle d'acier plaquée ayant une excellente qualité de surface, une excellente résistance et une excellente ductilité - Google Patents

Tôle d'acier plaquée ayant une excellente qualité de surface, une excellente résistance et une excellente ductilité Download PDF

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EP3666919A1
EP3666919A1 EP18845253.6A EP18845253A EP3666919A1 EP 3666919 A1 EP3666919 A1 EP 3666919A1 EP 18845253 A EP18845253 A EP 18845253A EP 3666919 A1 EP3666919 A1 EP 3666919A1
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steel sheet
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hot
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content
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EP3666919A4 (fr
EP3666919B1 (fr
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Yong-Woo Kim
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Posco Holdings Inc
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Posco Co Ltd
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    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • 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
    • C22C38/12—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
    • 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
    • C23C2/04—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
    • 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
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present disclosure relates to a plated steel sheet having excellent surface quality, strength, and ductility, and more particularly, to a plated steel sheet having excellent surface quality, strength, and ductility, which may be preferably used as a pre-engineered building (PEB) structure.
  • PEB pre-engineered building
  • the PEB method may be a method that minimizes the use of materials through optimal design, considering the supporting load, and may be a construction method capable of reducing construction costs and shortening a construction period.
  • the PEB structure used in the PEB method may be required to have excellent strength in order to prevent buckling by load, and the like. Therefore, a steel sheet conventionally used as the PEB structure may be generally manufactured by adding C, Si, Mn, Ti, Nb, Mo, V, and the like to a high purity steel having minimized impurities therein.
  • Patent Document 1 a method of utilizing precipitation strengthening of the following elements by adding Ti, Nb, V, Mo, and the like
  • Patent Document 3 Patent Document 4
  • Patent Document 5 a method of increasing impact strength and tensile characteristics by temper annealing Mn and Cr-added steel
  • the PEB structure is required to have excellent corrosion resistance, a plating film may be generally formed on the surface of the steel sheet used as the PEB structure. Therefore, in the case of the steel sheet used as the PEB structure, the surface quality of the hot-rolled steel sheet before performing a plating process becomes a very important factor.
  • the alloy material may be relatively excessive, and the hot-rolling resistance may be relatively high. Therefore, in producing thin sheets having less than 2.0t thickness, there may be a problem that the plating quality is deteriorated due to occurrence of sand-type scales by a hot-rolling process.
  • An aspect of the present disclosure is to provide a plated steel sheet having excellent surface quality, strength, and ductility, and a method of manufacturing the same.
  • a plated steel sheet having a plating film on a surface of a hot-rolled steel sheet wherein the hot-rolled steel sheet comprises, by weight, 0.15 to 0.25% of C, 0.5% or less of Si, 0.5 to 2.0% of Mn, 0.03% or less of P, 0.015% or less of S, 0.05% or less of Al, 0.01% or less of N, 0.05% or less of Ti (excluding 0%), 0.01% or less of B (excluding 0%), a balance of Fe, and inevitable impurities, satisfies the following relationship 1, and comprises, by area, 10 to 30% of ferrite, 20 to 40% of pearlite, and 35 to 55% of bainite, as a microstructure: 0.235 C + 0.0158 Mn + 0.0625 Si + 0.0423 Mo + 0.317 Ti + 1.36 Nb ⁇ 0.075
  • a method for manufacturing a plated steel sheet comprising: reheating a slab to 1100 to 1300°C; finish-rolling the reheated slab to a temperature of Ar3°C or higher to obtain a hot-rolled steel sheet; coiling the hot-rolled steel after cooling the hot-rolled steel sheet at a rate of Vc to (Vc+30)°C/s defined by the following equation 1; and hot-dip plating by dipping the coiled hot-rolled steel sheet in a hot-dip bath, wherein the slab comprises, by weight, 0.15 to 0.25% of C, 0.5% or less of Si, 0.5 to 2.0% of Mn, 0.03% or less of P, 0.015% or less of S, 0.05% or less of Al, 0.01% or less of N, 0.05% or less of Ti (excluding 0%), 0.01% or less of B (excluding 0%), a balance of Fe, and inevitable impurities, satisfies the following relationship 1: 0.235 C + 0.0158
  • the plated steel sheet according to the present disclosure may have the advantages not only of excellent surface quality, such as no surface defects, but also excellent balance of yield strength and elongation.
  • a plated steel sheet having excellent surface quality, strength, and ductility may include a hot-rolled steel sheet, and a plating film formed on a surface of the hot-rolled steel sheet.
  • the plating film may include, but is not necessarily limited to, Mg: 10% or less (excluding 0%), Al: 5% or less (excluding 0%), a balance of Zn, and inevitable impurities.
  • alloying element and preferred content ranges of the hot-rolled steel sheet will be described in detail. It is to be noted that the content of each element described below may be based on weight unless otherwise specified.
  • the C may be the most economical and effective element for securing strength.
  • the C content is 0.15% or more, and it is more preferable that the C content is 0.16% or more.
  • the C content is preferably 0.25% or less, and more preferably 0.22% or less.
  • Si may contribute to an increase in strength due to solid solution strengthening and deoxidation of molten steel, but may be not intentionally added in the present disclosure. Even when Si is not added, there may be no major problem in terms of securing physical properties. When the content is overly excessive, red scale due to Si may be formed on the surface of the hot-rolled steel sheet. Therefore, surface quality and plating quality may be deteriorated. In some cases, the Si content may exclude 0%.
  • Manganese (Mn) 0.5 - 2.0%
  • Mn may be an effective element for solute strengthening of steel, and may need to be added 0.5% or more, preferably 0.6% or more to secure appropriate strength.
  • the Mn content may be 2.0% or less, and it is more preferable that the Mn content may be 1.8% or less.
  • Phosphor (P) 0.03% or less
  • the P may be an inevitable impurity contained in steel, and it is preferable to control its content as low as possible. In particular, when the content is excessive, the risk of weldability deterioration and brittleness of the steel may increase. Therefore, in the present disclosure, the P content may be managed to be 0.03% or less. In some cases, the P content may exclude 0%.
  • S may be an impurity that may be inevitably included in steel, and it is preferable to control its content as low as possible.
  • the content when the content is excessive, it may be combined with Mn to form a non-metallic inclusion, and the risk of brittleness of the steel may increase. Therefore, in the present disclosure, the content may be managed to be 0.015% or less. In some cases, the S content may exclude 0%.
  • Al may contribute to deoxidation of molten steel, but may be not intentionally added in the present disclosure. Even when Al is not added, there may be no major problem in terms of securing physical properties. When the content is excessive, nozzle clogging, and the like may occur in the continuous casting process. In the present disclosure, the content may be managed to be 0.05% or less. In some cases, the Al content may exclude 0%.
  • N may contribute to improvements in strength of steel, but in the present disclosure may be not added intentionally. Even when N is not added, there may be no major problem in terms of securing physical properties. When the content is excessive, the risk of brittleness of the steel may increase. Therefore, in the present disclosure, the content may be managed to be 0.01% or less. In some cases, the N content may exclude 0%.
  • Ti may be present in steel as TiN, to suppress growth of crystal grains during a heating operation for hot-rolling. In addition, it may serve to remove N, such that B does not react with N. When the content is excessive, there may be a risk of clogging the nozzle during the continuous casting process due to excessive TiN precipitation. Therefore, the Ti content is preferably 0.05% or less, more preferably 0.04% or less, and even more preferably 0.03% or less. Further, since Ti needs to be added to steel to obtain the above-mentioned effect, the content of Ti content may exclude 0%. In addition, in the present disclosure, the lower limit of the Ti content is not particularly limited, but the lower limit thereof may be limited to 0.01% in terms of securing a sufficient crystal grain growth inhibiting effect.
  • the B may be contained as an alternative element of Si, improve quenchability in very small amounts, and strengthen grain boundaries to improve strength.
  • the content is excessive, there may be a risk of surface quality deterioration due to excessive BN precipitation. Therefore, the B content is preferably 0.01% or less, more preferably 0.008% or less, and even more preferably 0.005% or less. Further, since B needs to be added to steel to obtain the above-mentioned effect, the B content may exclude 0%.
  • the lower limit of the B content is not particularly limited, but the lower limit thereof may be limited to 0.0005%, more preferably 0.001% in terms of securing sufficient quenchability.
  • the rest may be Fe.
  • inevitable impurities that may be not intended from the raw materials or the surrounding environment may be inevitably mixed, these cannot be excluded. Since these impurities are known to those skilled in the art, not all of them may be specifically mentioned in the present specification. Addition of an effective element other than the above composition may be not excluded.
  • the relationship 1 may be a factor of surface quality of the steel sheet.
  • the finish temperature of hot-rolling may be secured to less than 900°C thanks to the reduction of the hot-rolling resistance. Therefore, since sand-type scale, which is generated by a high temperature during hot-rolling, is not generated, it is possible to secure a plated steel sheet having excellent surface quality after a final plating operation.
  • sand-type scale may be generated due to the high temperature during the hot-rolling operation, and plating quality may be degraded. 0.235 C + 0.0158 Mn + 0.625 Si + 0.0423 Mo + 0.317 Ti + 1.36 Nb ⁇ 0.075
  • the hot-rolled steel sheet which may be the base of the plated steel sheet of the present disclosure, may comprise, by area, 10 to 30% of ferrite, 20 to 40% of pearlite, and 35 to 55% of bainite, and more preferably 15 to 25% of ferrite, 25 to 35% of pearlite, and 40 to 50% of bainite, as a microstructure.
  • phase fractions as described above are not secured, it may be difficult to secure a balance of target strength and ductility due to a decrease in strength or ductility.
  • the sum of the fractions of ferrite, pearlite, and bainite may be 90 area% or more.
  • an average grain size of the ferrite may be 20 ⁇ m or less (excluding 0 ⁇ m), and more preferably 15 ⁇ m or less (excluding 0 ⁇ m).
  • the average grain size of the ferrite exceeds 20 ⁇ m, it may be difficult to secure the desired strength.
  • the grain size refers to an equivalent circular diameter of particles detected by observing one cross section of the steel.
  • an average colony size of pearlite may be 30 ⁇ m or less (excluding 0 ⁇ m), and more preferably 20 ⁇ m or less (excluding 0 ⁇ m).
  • the colony size of pearlite exceeds 30 ⁇ m, it may be difficult to secure a desired combination of strength x ductility due to inferior ductility, and in particular, cracking may occur due to deterioration of bendability during the manufacture of final product.
  • the colony size refers to an equivalent circular diameter of particles, divided by tilt boundaries having misorientation angle of 15 degrees or more detected by observing the inside of pearlite.
  • residual structure other than the ferrite, pearlite, and bainite, is not particularly limited, and in some cases, may be further include at least one second phase of martensite, cementite, and residual austenite. All of these second phases may be hard phases. When the area ratio of these second phases is too high, the combination of strength x ductility may be deteriorated, because the strength is relatively high and the ductility is relatively low. The sum of these area ratios may be controlled to be preferably 10% or less, more preferably 5% or less.
  • Plated steel sheet of the present disclosure may have a relatively high yield strength, and, according to an example, may have a yield strength of 450 - 600MPa.
  • the plated steel sheet of the present disclosure may have the advantage of excellent balance of strength and ductility, and, according to an example, the product of yield strength and elongation may be 8,500MPa ⁇ % or more.
  • a plated steel sheet of the present disclosure described above may be manufactured by various methods, and a method for manufacturing the same is not particularly limited. As a preferred example, it may be prepared by the following method.
  • a slab having the above-described composition system may be reheated at 1100 to 1300°C.
  • the reheating temperature is less than 1100°C, the rolling load may be too large in a subsequent hot-rolling process.
  • the reheating temperature is higher than 1300°C, austenite grains may be partially coarsened due to abnormal growth of some austenite grains, such that the grain size of the final microstructure may be not homogeneous.
  • slab reheating time is not specifically limited, and is acceptable under normal conditions. In a non-limiting example, the slab reheating time may be 100 to 400 minutes.
  • the rough-rolled slab may be finish-rolled at the austenite single phase temperature (temperature of Ar3°C or higher), to obtain a hot-rolled steel steel.
  • rough-rolling refers to a series of intermediate rolling processes performed before finish-rolling.
  • the rough-rolling is not specifically limited, and is acceptable under normal conditions.
  • a thickness of the rough-rolled slab relative to a thickness of the reheated slab may be 10 to 25%, and the rough-rolling temperature may be set to a sufficiently high temperature at which the finish-rolling temperature is ensured.
  • the finish-rolling may be carried out in the range of (FDT-20)°C to (FDT+20)°C defined by the following equation 2.
  • FDT-20°C austenitic grains of the slab may be coarsened such that sizes of the final ferrite grains and pearlite colonies may be coarse, leading to a decrease in strength. Therefore, it may be difficult to secure desired excellent strength x ductility.
  • the finish-rolling temperature is less than FDT-20°C, mixed-grain structure may be generated due to two phase temperature rolling, to reduce the ductility, and rolling load may greatly increase during hot-rolling, to decrease productivity.
  • the mixed-grain structure refers that crystal grains having different particle sizes are mixed.
  • the austenitic structure of the hot finish-rolled steel sheet has an average grain size of 10 - 40 ⁇ m.
  • FDT ° C 1002.1 ⁇ 353 C + 43.9 Si ⁇ 74.1 Mn ⁇ 20.4 Cu ⁇ 19.9 Cr ⁇ 45.6 Ni ⁇ 80 Mo
  • the hot-rolled steel sheet may be cooled at a cooling rate of Vc°C/s or more and (Vc+30) °C/s or less, defined by the following equation 1, and may be then coiled.
  • Vc°C/s the cooling rate is less than Vc°C/s, it may be difficult to secure the desired strength, because the fraction of ferrite and pearlite exceeds the range limited by the present disclosure.
  • the cooling rate exceeds (Vc+30)°C/s, the fraction of bainite or second phase may exceed the limit of the present disclosure, to deteriorate the ductility. Therefore, a combination of excellent (yield strength x ductility) may be not be obtained.
  • Vc 158.0 ⁇ 156.6 C + 246.6 Si ⁇ 40.32 Mn ⁇ 25.74 Cr ⁇ 73.26 Ni ⁇ 8820 B ⁇ 1483.2 Ti + 1108.8 Nb ⁇ 291.6 Mo ⁇ 1092.6
  • Vc 158.0 ⁇ 156.6 C + 246.6 Si ⁇
  • the coiling may be carried out in a range of (CT-20) °C to (CT+20) °C defined by the following equation 3.
  • CT+20 coarse ferrite and pearlite may be formed to lower yield strength. Therefore, the desired (yield strength x elongation) value may be not be obtained.
  • the coiling temperature is less than CT-20°C, ductility may be deteriorated. More specifically, when the coiling temperature is less than CT-20°C, bainite may be excessively formed beyond the fraction of the present disclosure to cause the ductility deteriorated while making the yield strength increase. Therefore, the desired (yield strength x elongation) value may be not be obtained.
  • CT 751.7 ⁇ 357.3 C ⁇ 85.3 Mn ⁇ 35 Si ⁇ 73 Cr ⁇ 36 Ni ⁇ 84.4 Mo
  • hot-dip plating process of the coiled hot-rolled steel sheet may be followed.
  • the hot-dip plating process according to an embodiment of the present disclosure may be carried out by hot-dip plating a solution comprising, by weight, Mg: 10% or less (excluding 0), Al: 5% or less (excluding 0), a balance of Zn, and inevitable impurities.
  • a steel slab having a component system described in the following Table 1 (the contents of P and S as impurities in each steel were controlled at 0.03% by weight or less and 0.015% by weight or less, respectively, the Cu content was 0% by weight, and the N content was 0.005% by weight) was heated to 1200°C, and finish-rolling was performed at the hot finish-rolling temperature shown in the following Table 2, to obtain a hot-rolled steel sheet. Thereafter, the hot-rolled steel sheet was cooled to the coiling temperature described in the following Table 2 at a cooling rate (CR, °C/s), and then coiled up. Thereafter, the coiled hot-rolled steel sheet was subjected to hot-dip plating.
  • Table 1 the contents of P and S as impurities in each steel were controlled at 0.03% by weight or less and 0.015% by weight or less, respectively, the Cu content was 0% by weight, and the N content was 0.005% by weight
  • Comparative Examples 7 and 8 may be cases in which the cooling rate did not satisfy the ranges defined by the present disclosure. As a result, the fractions of ferrite and pearlite were higher than the value to be controlled by the present disclosure, and the yield of bainite was low. Therefore, sufficient yield strength could not be obtained.
  • FIG. 1 Portion (a) in FIG. 1 is a photograph of a surface of a plated steel sheet of Comparative Example 2, and portion (b) in FIG. 1 is a photograph of a surface of a plated steel sheet of Inventive Example 1.
  • FIG. 2 is a graph illustrating elongation to yield strength of the Inventive and Comparative Examples.

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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EP18845253.6A 2017-08-09 2018-08-03 Tôle d'acier plaquée ayant une excellente qualité de surface, une excellente résistance et une excellente ductilité Active EP3666919B1 (fr)

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PCT/KR2018/008848 WO2019031773A1 (fr) 2017-08-09 2018-08-03 Tôle d'acier plaquée ayant une excellente qualité de surface, une excellente résistance et une excellente ductilité

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KR102492030B1 (ko) * 2020-12-21 2023-01-26 주식회사 포스코 저항복비를 갖는 고강도 열연강판 및 그 제조방법

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WO2019031773A1 (fr) 2019-02-14
EP3666919A4 (fr) 2020-06-17
PT3666919T (pt) 2024-02-08
KR20190016826A (ko) 2019-02-19
JP6952869B2 (ja) 2021-10-27
CN110997963A (zh) 2020-04-10
JP2020530068A (ja) 2020-10-15
KR101977474B1 (ko) 2019-05-10
US20200377963A1 (en) 2020-12-03
ES2970206T3 (es) 2024-05-27
EP3666919B1 (fr) 2023-11-08

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