WO2017131055A1 - Tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé et son procédé de production - Google Patents

Tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé et son procédé de production Download PDF

Info

Publication number
WO2017131055A1
WO2017131055A1 PCT/JP2017/002616 JP2017002616W WO2017131055A1 WO 2017131055 A1 WO2017131055 A1 WO 2017131055A1 JP 2017002616 W JP2017002616 W JP 2017002616W WO 2017131055 A1 WO2017131055 A1 WO 2017131055A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
steel sheet
plating
temperature
strength
Prior art date
Application number
PCT/JP2017/002616
Other languages
English (en)
Japanese (ja)
Inventor
裕美 吉冨
拓弥 平島
弘之 増岡
斉祐 津田
正貴 木庭
康弘 西村
達也 中垣内
Original Assignee
Ｊｆｅスチール株式会社
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
Priority claimed from JP2017009277A external-priority patent/JP6249113B2/ja
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to US16/072,606 priority Critical patent/US20190032185A1/en
Priority to EP17744285.2A priority patent/EP3409807B1/fr
Priority to KR1020187021589A priority patent/KR102171029B1/ko
Priority to CN201780008448.XA priority patent/CN108603263B/zh
Priority to MX2018009164A priority patent/MX2018009164A/es
Publication of WO2017131055A1 publication Critical patent/WO2017131055A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/60—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
    • 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

Definitions

  • the present invention uses a high-strength steel sheet containing Mn as a base material, a high yield strength type high-strength galvanized steel sheet that is excellent in high yield strength, plating appearance, post-processing corrosion resistance, and anti-plating resistance during high processing, and its manufacture.
  • the present invention relates to a method for manufacturing the method.
  • a hot dip galvanized steel sheet uses a thin steel sheet obtained by hot rolling or cold rolling a slab as a base material, and the base steel sheet is used in an annealing furnace of a continuous hot dip galvanizing line (hereinafter referred to as CGL). Manufactured by annealing and hot dip galvanizing. In the case of an alloyed hot-dip galvanized steel sheet, it is manufactured after further hot-dip galvanizing treatment.
  • a heating furnace type of the CGL annealing furnace there are a DFF type (direct flame type), a NOF type (non-oxidation type), an all radiant tube type (ART type), and the like.
  • DFF type direct flame type
  • NOF type non-oxidation type
  • ART type all radiant tube type
  • all radiant tube type heating furnaces do not have an oxidation step immediately before annealing, so for steel plates containing oxidizable elements such as Mn. It is disadvantageous in terms of securing plating properties.
  • Patent Document 1 and Patent Document 2 specify a heating temperature in a reduction furnace by an expression expressed by a water vapor partial pressure, and a dew point.
  • a technique for internal oxidation of the surface layer of the railway is disclosed.
  • Patent Document 3 not only the oxidizing gases H 2 O and O 2 but also the CO 2 concentration are simultaneously defined, so that the surface layer immediately before plating is internally oxidized to suppress external oxidation. A technique for improving the appearance is disclosed.
  • Patent Document 4 also discloses that the dew point of the atmosphere in the annealing furnace is ⁇ 45 ° C. or lower in the temperature range of 820 ° C. or higher and 1000 ° C. or lower in the annealing process and 750 ° C. or higher in the cooling process.
  • a technique for reducing the oxygen potential, reducing surface enrichment without forming internal oxidation, and improving the plating appearance is disclosed.
  • the anti-plating peeling property at the time of high processing is regarded as important. Specifically, it is required to suppress plating peeling at the processed part when the plated steel sheet is bent at an angle of more than 90 ° and bent at an acute angle or when the steel sheet is processed by impact.
  • the present invention has been made in view of such circumstances, and uses a steel plate containing Mn as a base material, and has high yield ratio, high yield strength, plating appearance, corrosion resistance, and high plating ratio peeling resistance during high processing.
  • An object is to provide a high-strength galvanized steel sheet and a method for producing the same.
  • the present inventors have deliberately examined a heating temperature region of Ac3 point or higher. As a result, the present invention has been achieved.
  • the present inventors examined a method for solving the problem by a new method that is not bound by the conventional idea.
  • the atmospheric dew point and heating temperature in the annealing process to have a specific metal structure and a Mn content in the plating layer within a specific range, high yield strength, plating appearance, corrosion resistance and resistance
  • a high yield ratio type high-strength galvanized steel sheet with good plating peelability was obtained. This is presumed to be because the formation of internal oxidation and surface enrichment can be suppressed in the surface layer portion of the steel plate immediately below the plating layer.
  • the temperature range of the heating temperature T: Ac3 point to 950 ° C is set to a hydrogen concentration of 5 vol.
  • Mn surface concentration hardly occurs because Mn approaches the reduction region from the oxidation region in the high temperature region above the Ac3 point.
  • the surface concentration of Mn can be suppressed without forming internal oxidation on the steel sheet surface, It is expected that a high yield ratio type high strength galvanized steel sheet having high yield strength and excellent corrosion resistance after processing will be obtained.
  • the Mn surface enrichment formed during annealing in the furnace is taken into the plating layer when the plating bath reacts with the steel plate in the plating process, so the Mn surface enrichment is estimated from the Mn content during plating. it can.
  • the present invention is based on the above, and the features thereof are as follows.
  • Component composition having a composition of 0.1 to 0.1%, the balance being Fe and inevitable impurities, an area ratio of ferrite of 20% or less, bainite and tempered martensite in total of 40% or more, as-quenched martens
  • a metal structure having a site of 60% or less and an average crystal grain size of bainite of 6.0 ⁇ m or less, a steel sheet having the metal structure, and a plating adhesion amount per side of 20 to 120 g / m 2 ; because the Mn content is 0.05 g / m 2 or less
  • Comprising a can layer a high yield ratio high-strength galvanized steel sheet yield ratio is more than 950MPa There tensile strength at least 65%.
  • the component composition further includes, in mass%, at least one of Mo, Cr, Cu, and Ni in a total of 0.1 to 0.5% and / or B: 0.0003 to 0.005%
  • a steel material having the composition according to any one of [1] to [3] is heated to 1100 ° C. or higher and 1350 ° C. or lower, and then hot rolled at a finish rolling temperature of 800 ° C. or higher and 950 ° C. or lower. Next, a hot rolling step of winding at a temperature of 450 ° C. or higher and 700 ° C.
  • the heating temperature T Ac 3 point to 950 ° C.
  • the obtained annealed plate is plated, and the average cooling rate is 5 ° C.
  • a high-yield ratio type high-strength galvanized steel sheet excellent in high yield strength, plating appearance, corrosion resistance, and plating peeling resistance during high processing can be obtained.
  • the high yield ratio type high strength galvanized steel sheet of the present invention When the high yield ratio type high strength galvanized steel sheet of the present invention is applied to a skeleton member of an automobile body, it can greatly contribute to improvement of collision safety and weight reduction.
  • the component composition of the high yield ratio type high strength galvanized steel sheet is mass%, C: 0.12% or more and 0.25% or less, Si: less than 1.0%, Mn: 2.0% or more and 3%.
  • P 0.05% or less
  • S 0.005% or less
  • Al 0.1% or less
  • N 0.008% or less
  • Ca 0.0003% or less
  • Ti, Nb, V One or more of Zr is contained in an amount of 0.01 to 0.1%, with the balance being Fe and inevitable impurities.
  • the above component composition further includes, in mass%, at least one of Mo, Cr, Cu, and Ni in a total of 0.1 to 0.5% and / or B: 0.0003 to 0.005%. You may contain.
  • the component composition may further contain Sb: 0.001 to 0.05% by mass.
  • % representing the content of a component means “% by mass”.
  • C 0.12% or more and 0.25% or less
  • C is an element effective for increasing the strength of the steel sheet, and contributes to increasing the strength by forming martensite containing supersaturated C.
  • C also contributes to high strength by forming carbide forming elements such as Nb, Ti, V, and Zr and fine alloy compounds or alloy carbonitrides.
  • the C content needs to be 0.12% or more.
  • the C content exceeds 0.25%, the spot weldability of the steel sheet is remarkably deteriorated, and at the same time, the steel sheet is hardened due to an increase in martensite and YR and bending workability tend to be lowered. Therefore, the C content is 0.12% or more and 0.25% or less. From the viewpoint of characteristics, it is preferably 0.23% or less. Moreover, a preferable range for the lower limit is 0.13% or more.
  • Si Less than 1.0% Si is an element that contributes to high strength mainly by solid solution strengthening. The decrease in ductility is relatively small as the strength increases, and it improves the balance between strength and ductility as well as strength. Contribute.
  • Si tends to form a Si-based oxide on the surface of the steel sheet and may cause non-plating. Therefore, it is sufficient to add only the amount necessary for securing the strength, but the upper limit of the Si content is set to less than 1.0% from the viewpoint of plating properties. Preferably it is 0.8% or less.
  • the Si content is preferably 0.01% or more. More preferably, it is 0.05% or more.
  • Mn 2.0% or more and 3% or less
  • Mn is an element that contributes to high strength by solid solution strengthening and martensite formation. In order to acquire this effect, it is necessary to make Mn content 2.0% or more. Preferably it is 2.1% or more, More preferably, it is 2.2% or more.
  • Mn content exceeds 3%, spot welded portion cracking is caused, and the metal structure is likely to be uneven due to segregation of Mn and the like, and various workability is lowered. Further, Mn tends to concentrate as an oxide or composite oxide on the steel sheet surface, which may cause non-plating. Therefore, the Mn content is 3% or less. Preferably it is 2.8% or less, more preferably 2.7% or less.
  • P 0.05% or less
  • P is an element that contributes to increasing the strength of a steel sheet by solid solution strengthening.
  • the P content exceeds 0.05%, workability such as weldability and stretch flangeability is deteriorated. For this reason, it is desirably 0.03% or less.
  • the lower limit of the P content is not particularly specified, but if it is less than 0.001%, the production efficiency is lowered and the dephosphorization cost is increased in the production process. In addition, if P content is 0.001% or more, the said effect of high intensity
  • S 0.005% or less
  • S is a harmful element that causes hot brittleness, and is present in the steel as sulfide inclusions and reduces workability of the steel sheet such as bendability. For this reason, it is preferable to reduce S content as much as possible.
  • an S content of up to 0.005% is acceptable. Preferably it is 0.002% or less.
  • the lower limit is not particularly defined, if the S content is less than 0.0001%, the production efficiency is lowered and the cost is increased in the production process. Therefore, the S content is preferably 0.0001% or more.
  • Al 0.1% or less Al is added as a deoxidizer.
  • the Al content is preferably 0.01% or more. More preferably, it is 0.02% or more.
  • the Al content is 0.1% or less. Preferably it is 0.08% or less.
  • the N content is set to 0.008% or less, preferably 0.006% or less. From the viewpoint of improving ductility by ferrite cleaning, it is preferable that the N content is as small as possible. On the other hand, if the N content is excessively reduced, the production efficiency is lowered and the cost is increased in the production process, so the N content is preferably 0.0001% or more.
  • Ca 0.0003% or less Ca forms sulfides and oxides in steel and lowers the workability of the steel sheet. Therefore, the Ca content is set to 0.0003% or less. Preferably it is 0.0001% or less. A lower Ca content is preferred, and it may be 0%.
  • Ti, Nb, V and Zr 0.01 to 0.1%
  • Ti, Nb, V, and Zr form carbides and nitrides (sometimes carbonitrides) with C and N to become precipitates. Fine precipitates contribute to increasing the strength of the steel sheet.
  • these elements have the effect of refining the structure of the hot-rolled coil, and by refining the microstructure after the subsequent cold rolling / annealing, it contributes to improving workability such as strength increase and bendability. For this reason, the total content of these elements is set to 0.01% or more. Preferably it is 0.02% or more.
  • the total content of these components is 0.1% or less. Preferably it is 0.08% or less.
  • the component composition of a steel plate may include the following components.
  • One or more of Mo, Cr, Cu and Ni in total 0.1 to 0.5% and / or B: 0.0003 to 0.005% These elements contribute to high strength because they enhance the hardenability and facilitate the formation of martensite.
  • the total content of one or more of Mo, Cr, Cu, and Ni is preferably 0.1% or more.
  • Mo, Cr, Cu, Ni the excessive addition leads to saturation of an effect and a cost increase.
  • Cu induces cracks during hot rolling and causes surface defects. Therefore, the total content is 0.5% or less. Since Ni has an effect of suppressing the generation of surface flaws due to the addition of Cu, it is desirable to add it simultaneously with the addition of Cu. It is preferable to make Ni more than 1/2 of the Cu content.
  • B also enhances hardenability and contributes to high strength.
  • a lower limit is set for the B content from the viewpoint of obtaining the effect of suppressing the formation of ferrite that occurs in the annealing cooling process and from the viewpoint of improving hardenability.
  • 0.0003% or more is preferable. More preferably, it is 0.0005% or more.
  • the excessive addition will set an upper limit because of saturation of the effect. Specifically, 0.005% or less is preferable. More preferably, it is 0.002% or less.
  • Excessive hardenability also has disadvantages such as weld cracking during welding.
  • Sb 0.001 to 0.05%
  • Sb is an element effective in suppressing strength reduction of a steel sheet by suppressing decarburization, denitrification, deboronation, and the like.
  • the Sb content is preferably 0.001% or more because it is also effective for suppressing spot weld cracking. More preferably, it is 0.002% or more.
  • the Sb content is preferably 0.05% or less. More preferably, it is 0.02% or less.
  • the metal structure of the high yield ratio type high strength galvanized steel sheet is 20% or less in ferrite, 40% or more in total for bainite and tempered martensite, and 60% or less in the as-quenched martensite.
  • the crystal grain size is 6.0 ⁇ m or less.
  • Ferrite is not more than 20%
  • the presence of ferrite is not preferable from the viewpoint of steel sheet strength, but up to 20% is allowed in the present invention. Preferably it is 15% or less. Further, the ferrite may be 0%.
  • As the area ratio a value measured by the method described in Examples is adopted.
  • bainite containing no carbides generated at a relatively high temperature is not distinguished from ferrite by observation with a scanning electron microscope described in Examples described later, and is regarded as ferrite.
  • Bainite and tempered martensite total 40% or more
  • bainite because bainite containing no carbide is considered to be ferrite, as described above, this bainite contains carbite containing carbide.
  • tempered martensite are 40% or more in total area ratio.
  • this bainite and tempered martensite are important in the present invention, and in order to obtain high YS, it is necessary to be 40% or more.
  • it is 45% or more, More preferably, it is 50% or more, More preferably, it is 55% or more.
  • the upper limit is not particularly limited, but is preferably 90% or less, more preferably 80% or less, and still more preferably 70% or less, from the viewpoint of balance with strength and ductility.
  • As the area ratio a value measured by the method described in Examples is adopted.
  • Quenched martensite is 60% or less Quenched martensite is hard and effective for increasing the strength of the steel sheet, and in order to obtain the effect of increasing TS, the area ratio is preferably 20% or more. More preferably, it is 25% or more, and more preferably 30% or more.
  • hard martensite as hardened lowers YR, so the upper limit is made 60% or less. Preferably it is 50% or less, More preferably, it is 40% or less, More preferably, it is 30% or less.
  • As the area ratio a value measured by the method described in Examples is adopted.
  • the average crystal grain size of bainite is 6.0 ⁇ m or less.
  • bainite and tempered martensite are important for obtaining high YS in the present invention.
  • it is important that the average crystal grain size of bainite is 6.0 ⁇ m or less.
  • it is 5 ⁇ m or less.
  • 1.0 micrometer or more is preferable substantially, More preferably, it is 2.0 micrometers or more.
  • the average crystal grain size is a value measured by the method described in the examples.
  • each structure of the metal structure is as described above, but the high yield ratio type high-strength galvanization with high yield strength, plating appearance, corrosion resistance and anti-plating resistance is good by the manufacturing method described later.
  • a steel plate is obtained. This is a manufacturing method to be described later.
  • the metal structure may contain ferrite, bainite, tempered martensite, or other than quenched martensite.
  • examples of other structures include pearlite and retained austenite.
  • the area ratio of other tissues is preferably 10% or less.
  • the plating layer has a plating adhesion amount of 20 to 120 g / m 2 per side.
  • An adhesion amount of 20 g / m 2 or more is necessary to ensure corrosion resistance.
  • it is 30 g / m 2 or more.
  • It must be 120 g / m 2 or less in order to improve the plating peel resistance.
  • it is 90 g / m 2 or less.
  • the Mn content in the plating layer is 0.05 g / m 2 or less.
  • the Mn oxide formed in the heat treatment step before plating reacts with the plating bath and the raw steel plate to form the FeAl or FeZn alloy phase. Although it is taken in, if the amount of oxide is excessive, it remains at the plating / base metal interface and deteriorates the plating adhesion. Therefore, there is no lower limit to the amount of Mn oxide formed in the heat treatment step, and the lower the better.
  • the amount of Mn oxide formed in the heat treatment step can be quantified from the Mn content in the plating layer after the plating step, and the measurement is performed by the method described in the examples. Therefore, by measuring the “Mn content in the plating layer”, it is possible to evaluate the presence or absence and degree of the problem caused by the Mn oxide.
  • the plating layer is preferably a galvanizing layer.
  • the galvanized layer may be an alloyed galvanized layer subjected to an alloying treatment.
  • the manufacturing method of the present invention includes a hot rolling process, a cold rolling process, an annealing process, a galvanizing process, and a temper rolling process.
  • the hot rolling step is to heat a steel material having the above composition to 1100 ° C. or higher and 1350 ° C. or lower, then perform hot rolling at a finish rolling temperature of 800 ° C. or higher and 950 ° C. or lower, and then 450 ° C. or higher.
  • This is a step of winding at a temperature of 700 ° C. or lower.
  • the temperature means the steel sheet surface temperature.
  • the steel material used in the production method of the present invention is produced by a continuous casting method generally called a slab.
  • the continuous casting method is used for the purpose of preventing macro segregation of alloy components.
  • the steel material may be manufactured by an ingot-making method or a thin slab casting method.
  • the steel slab is charged with a hot furnace without being cooled to near room temperature and hot-rolled. Any of the method of hot rolling immediately after performing the supplementary heat treatment or the method of hot rolling while maintaining a high temperature state after casting may be used.
  • the hot rolling conditions are as follows: a steel material having the above component composition is heated at a temperature of 1100 ° C. or higher and 1350 ° C. or lower, hot rolled at a finish rolling temperature of 800 ° C. or higher and 950 ° C. or lower, and 450 ° C. or higher and 700 ° C.
  • the winding condition is as follows.
  • the heating temperature of the steel slab is in the range of 1100 ° C to 1350 ° C. If the temperature is outside the above upper limit temperature range, the precipitates present in the steel slab are likely to be coarsened, which may be disadvantageous when securing strength by precipitation strengthening, for example. Further, if the temperature is outside the upper limit temperature range, there is a possibility that the structure formation may be adversely affected in the subsequent annealing process using coarse precipitates as nuclei. On the other hand, it is beneficial to achieve a smooth steel plate surface by reducing cracks and irregularities on the steel plate surface by scaling off bubbles and defects on the slab surface by appropriate heating. In order to acquire such an effect, it is necessary to set it as 1100 degreeC or more.
  • the austenite grains become coarse, and the metal structure of the final product also becomes coarse, which may cause deterioration in workability such as strength, bendability and stretch flangeability of the steel sheet.
  • Hot rolling Hot rolling including rough rolling and finish rolling is performed on the steel slab obtained as described above.
  • a steel slab becomes a sheet bar by rough rolling, and becomes a hot-rolled coil (hot-rolled steel plate) by finish rolling and winding.
  • the hot rolling conditions need to be the following conditions.
  • Finishing rolling temperature 800 ° C. or more and 950 ° C. or less
  • the finishing rolling temperature 800 ° C. or more and 950 ° C. or less
  • the structure obtained by the hot rolled coil can be made uniform.
  • the ability to make the tissue uniform at this stage contributes to a uniform structure of the final product. If the structure is not uniform, workability such as ductility, bendability, stretch flangeability, and the like is deteriorated.
  • the temperature exceeds 950 ° C. the amount of oxide (scale) generated increases, the interface between the base iron and the oxide becomes rough, and the surface quality after pickling and cold rolling deteriorates. Further, when the temperature exceeds 950 ° C., the crystal grain size becomes coarse in the structure, which may cause a decrease in workability such as strength, bendability and stretch flangeability of the steel plate as in the case of the steel slab.
  • cooling is started within 3 seconds after finishing rolling, and the temperature range from [Finishing rolling temperature] to [Finishing rolling temperature-100] ° C is set. It is preferable to cool at an average cooling rate of 10 to 250 ° C./s.
  • Winding temperature 450-700 ° C It is necessary from the viewpoint of fine precipitation of NbC or the like that the winding temperature is 450 ° C. or higher as the temperature immediately before winding the hot rolled coil.
  • the coiling temperature of 700 ° C. or lower is necessary from the viewpoint of preventing the precipitates from becoming too coarse.
  • the lower limit is preferably 500 ° C. or higher.
  • the upper limit is preferably 680 ° C. or lower.
  • the cold rolling process is a process in which cold rolling is performed on the hot rolled sheet (hot rolled steel sheet) obtained in the hot rolling process. Normally, after the scale is dropped by pickling, cold rolling is performed to form a cold rolled coil. This pickling is performed as necessary.
  • Cold rolling is preferably performed at a reduction rate of 20% or more. This is to obtain a uniform fine microstructure (metal structure) in the subsequent annealing. If it is less than 20%, if it tends to become coarse grains during annealing, it may tend to become a non-uniform structure, and as described above, there is a concern that the strength and workability of the final product plate will be reduced.
  • the upper limit of the rolling reduction is not particularly specified, since it is a high-strength steel sheet, a high rolling reduction may cause a shape defect in addition to a decrease in productivity due to a rolling load.
  • the rolling reduction is preferably 90% or less.
  • the heating temperature T Ac 3 point to 950 ° C.
  • the furnace dew point D in the temperature range: (1) The expression is satisfied, and annealing is performed under the conditions of a heating time in a temperature range of Ac3 to 950 ° C .: 60 s or less and a residence time in a temperature range of 450 to 550 ° C .: 5 s or more (annealing step).
  • Heating temperature T Ac3 point to 950 ° C
  • the heating temperature annealing temperature
  • Ac3 937-477C + 56Si-20Mn-16Cu-27Ni-5Cr + 38Mo + 125V + 136Ti + 35Zr-19Nb + 198Al + 3315B.
  • the element symbol in said formula means content of each element, and the component which does not contain is set to 0.
  • Hydrogen concentration H in the temperature range of Ac 3 to 950 ° C .: 5 vol% or more If the volume fraction of hydrogen gas in the atmosphere is less than 5 vol%, the activation effect by reduction cannot be obtained and the plating appearance deteriorates.
  • the upper limit is not particularly specified, but if it exceeds 20 vol%, the effect of improving the plating appearance is saturated and the cost is increased. Therefore, the volume fraction of hydrogen gas is preferably 5 vol% or more and 20 vol% or less.
  • the gas component in the furnace is composed of nitrogen gas and unavoidable impurity gas other than hydrogen gas. Other gas components may be included as long as the effects of the present invention are not impaired.
  • the hot dip galvanizing treatment can be performed by a conventional method. Further, except for the above temperature range, the hydrogen concentration may not be in the range of 5 vol% or more.
  • D means furnace dew point (° C.)
  • T means heating temperature (° C.).
  • Heating time in the temperature range from Ac3 point to 950 ° C .: 60 s or less The heating time in the temperature range from Ac3 point to 950 ° C. is controlled to 60 s or less. When it exceeds 60 s, the amount of Si, Mn, or a complex oxide thereof formed on the steel sheet surface is concentrated, which causes poor appearance.
  • the heating time is preferably 20 s or less.
  • the heating time in this temperature range is preferably 3 seconds or more from the viewpoint of material stabilization (homogenization of the microstructure (metal structure)).
  • Residence time in the temperature range of 450 to 550 ° C: 5 s or longer By retaining for 5 s or more in the temperature range of 450 to 550 ° C before the plating process, the microstructure, especially bainite, can be obtained stably, and the plate before entering the plating bath Stabilize the temperature. That is, in order to obtain a desired microstructure and good plating quality, the high YS and the plate temperature before entering the plating bath can be stabilized by retaining for 5 s or more in a predetermined temperature range.
  • the temperature at which the liquid is normally retained is the cooling stop temperature, so that plating is performed at a temperature lower than 450 ° C., and the quality of the plating bath is deteriorated in the galvanizing process. Therefore, the lower limit of the temperature range is set to 450 ° C.
  • the plate temperature before entering the bath exceeds 550 ° C.
  • the temperature of the plating bath is increased, and dross is likely to occur, and the generated dross adheres to the surface, which causes poor appearance. Therefore, the upper limit of the temperature range is set to 550 ° C.
  • the cooling stop temperature may be 450 to 550 ° C., but may be once cooled to a temperature lower than this and retained in a temperature range of 450 to 550 ° C. by reheating.
  • a galvanizing process is a process of giving the plating process to the annealing plate obtained by annealing, and cooling to 50 degrees C or less on conditions with an average cooling rate of 5 degrees C / s or more.
  • the plating treatment may be performed so that the amount of plating attached on one side is 20 to 120 g / m 2 .
  • An adhesion amount of 20 g / m 2 or more is necessary to ensure corrosion resistance, and 120 g / m 2 or less is necessary to improve plating resistance.
  • Other conditions for plating treatment are not particularly limited.
  • Fe in mass%, Fe: 0.1-18.0%, Al: 0.001% -1.0%, Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co
  • a plating layer containing 0 to 30% in total of one or more selected from Ca, Cu, Li, Ti, Be, Bi and REM, with the balance being Zn and inevitable impurities is obtained by the above method. It is the process of forming on the surface of the obtained annealing board.
  • the plating method is hot dip galvanizing. Conditions may be set as appropriate. Moreover, you may perform the alloying process heated after hot dip galvanization.
  • the alloying process is, for example, a process of holding in a temperature range of 450 to 600 ° C. for about 1 to 60 seconds.
  • the Fe content of the plating layer is preferably 7.0 to 15.0% by mass. If it is less than 7% by mass, unevenness in alloying and flaking properties may be deteriorated. On the other hand, if it exceeds 15% by mass, the plating peel resistance may deteriorate.
  • the average cooling rate is preferably 30 ° C./s or less in order to obtain a suitably tempered martensite for obtaining a high YR.
  • the temper rolling step is a step of subjecting the plated plate after the galvanizing step to temper rolling at an elongation rate of 0.1% or more.
  • the plated plate is subjected to temper rolling at an elongation rate of 0.1% or more for the purpose of stably obtaining high YS.
  • leveling may be performed instead of temper rolling. Excessive temper rolling introduces excessive strain on the steel sheet surface and lowers the evaluation value of bendability and stretch flangeability. Moreover, excessive temper rolling reduces ductility and increases the equipment load due to the high strength steel sheet. Therefore, the rolling reduction of temper rolling is preferably 3% or less.
  • GA 0.14 mass% Al containing Zn bath
  • GI 0.18 mass% Al containing Zn bath.
  • the adhesion amount was adjusted by gas wiping, and GA was alloyed.
  • cooling cooling after plating treatment
  • the evaluation method is as follows.
  • Tensile test A JIS No. 5 tensile test piece (JISZ2201) was sampled from a galvanized steel sheet in a direction perpendicular to the rolling direction, and a tensile test was performed at a constant tensile speed (crosshead speed) of 10 mm / min.
  • Yield strength (YS) is the value obtained by reading the 0.2% proof stress from the slope of the stress 100-200 MPa stress range
  • the tensile strength is the value obtained by dividing the maximum load in the tensile test by the initial cross-sectional area of the parallel part of the specimen. It was.
  • the plate thickness in calculating the cross-sectional area of the parallel portion the plate thickness value including the plating thickness was used.
  • the ripple pattern is of a level that is acceptable for automobile interior panel parts.
  • the non-plating defect means a region having a size of several ⁇ m to several mm, where no plating is present and the steel plate is exposed.
  • the cellophane tape was pressed against the processed portion bent by 120 ° to transfer the peeled material to the cellophane tape, and the amount of the peeled material on the cellophane tape was determined by the fluorescent X-ray method as the Zn count number.
  • the mask diameter is 30 mm
  • the fluorescent X-ray acceleration voltage is 50 kV
  • the acceleration current is 50 mA
  • the measurement time is 20 seconds.
  • Ball impact conditions are a ball weight of 1000 g and a drop height of 100 cm.
  • ⁇ (NG): peeling of plating layer Corrosion resistance after processing Prepare the test piece that does not peel off the tape by performing the same processing as the plating peeling resistance test.
  • FC-E2011 FC-E2011
  • a surface conditioner PL-X
  • a chemical conversion treatment agent Palbond PB-L3065
  • the chemical conversion treatment film adhesion amount is 1.7 to 3.0 g / m 2 under the following standard conditions. Chemical conversion treatment was performed.
  • Metallographic observation A specimen for microstructure observation was taken from a hot dip galvanized steel sheet, and after polishing the L cross section (thickness cross section parallel to the rolling direction), it was corroded with a nital liquid and 1 / from the surface with a scanning electron microscope (SEM). An image obtained by observing a position near 4t (t is a plate thickness) at three times or more at a magnification of 3000 was analyzed (an area ratio was measured for each observation field to calculate an average value). Further, the bainite average crystal grain size was calculated by a method of taking an arithmetic average of diameter lengths in two perpendicular directions (horizontal direction and vertical direction on the paper surface) using the above image. An example of the image is shown in FIG.
  • Mn content in galvanized layer The Mn content in the galvanized layer was measured by dissolving the plated layer in dilute hydrochloric acid to which an inhibitor was added and using ICP emission spectroscopy.
  • the steel sheet of the example of the present invention obtained with the components and production conditions within the scope of the present invention is a steel sheet having TS ⁇ 950 MPa and YR ⁇ 65% and having a predetermined plating quality.
  • the hot-dip galvanized steel sheet of the present invention not only has high tensile strength, but also has high yield strength and good surface properties, so that it is mainly used for skeletal parts of automobile bodies, especially around cabins that affect crash safety. When applied, it can contribute to environmental aspects such as CO 2 emission by improving the safety performance and contributing to weight reduction of the vehicle body due to the effect of thinning high strength. In addition, since it has good surface properties and plating quality, it can be actively applied to places where there is concern about corrosion due to rain and snow, such as undercarriage, and the performance of rust prevention and corrosion resistance of the car body is also improved. Can be expected. Such characteristics are not limited to automobile parts, but are also effective materials in the fields of civil engineering / architecture and home appliances.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne une tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé qui comporte une tôle d'acier contenant du Mn en tant que substrat, qui présente une limite d'élasticité élevée, un aspect galvanisé exceptionnel, une résistance à la corrosion, de manière complémentaire à la résistance au pelage du placage lorsqu'elle est fortement usinée ; et son procédé de production. La tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé comprend une tôle d'acier présentant une composition constitutive spécifique et une structure métallique dans laquelle, en termes de rapport de surface, la ferrite ne dépasse pas 20 %, le total de bainite et de martensite revenue est d'au moins 40 %, la martensite trempée ne dépasse pas 60 %, et la taille moyenne de grain cristallin de bainite ne dépasse pas 6,0 µm, et une couche de placage formée sur ladite tôle métallique, et ayant un poids de placage revêtu par face allant de 20 à 120 g/m2 et la teneur en Mn ne dépassant pas 0,05 g/m2. La tôle d'acier galvanisée haute résistance à rapport d'élasticité élevé présente un rapport d'élasticité d'au moins 65 % et une résistance à la traction d'au moins 950 MPa.
PCT/JP2017/002616 2016-01-27 2017-01-26 Tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé et son procédé de production WO2017131055A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
US16/072,606 US20190032185A1 (en) 2016-01-27 2017-01-26 High-yield-ratio high-strength galvanized steel sheet and method for producing the same
EP17744285.2A EP3409807B1 (fr) 2016-01-27 2017-01-26 Tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé et son procédé de production
KR1020187021589A KR102171029B1 (ko) 2016-01-27 2017-01-26 고항복비형 고강도 아연 도금 강판 및 그의 제조 방법
CN201780008448.XA CN108603263B (zh) 2016-01-27 2017-01-26 高屈服比型高强度镀锌钢板及其制造方法
MX2018009164A MX2018009164A (es) 2016-01-27 2017-01-26 Lamina de acero galvanizado de alta resistencia y alta relacion de rendimiento y metodo para producir la misma.

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2016-013205 2016-01-27
JP2016013205 2016-01-27
JP2017009277A JP6249113B2 (ja) 2016-01-27 2017-01-23 高降伏比型高強度亜鉛めっき鋼板及びその製造方法
JP2017-009277 2017-01-23

Publications (1)

Publication Number Publication Date
WO2017131055A1 true WO2017131055A1 (fr) 2017-08-03

Family

ID=59398058

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2017/002616 WO2017131055A1 (fr) 2016-01-27 2017-01-26 Tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé et son procédé de production

Country Status (1)

Country Link
WO (1) WO2017131055A1 (fr)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6525114B1 (ja) * 2017-11-29 2019-06-05 Ｊｆｅスチール株式会社 高強度亜鉛めっき鋼板およびその製造方法
WO2019106894A1 (fr) * 2017-11-29 2019-06-06 Ｊｆｅスチール株式会社 Tôle d'acier galvanisée à résistance élevée et son procédé de fabrication
WO2021033407A1 (fr) * 2019-08-20 2021-02-25 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance laminée à froid et son procédé de fabrication
CN115003840A (zh) * 2020-01-24 2022-09-02 日本制铁株式会社 板件
CN115612930A (zh) * 2022-10-08 2023-01-17 包头钢铁（集团）有限责任公司 一种低粗糙度汽车座椅滑轨用钢及其生产方法
US11795531B2 (en) 2018-03-30 2023-10-24 Jfe Steel Corporation High-strength galvanized steel sheet, high strength member, and method for manufacturing the same

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007211279A (ja) * 2006-02-08 2007-08-23 Nippon Steel Corp 耐水素脆性に優れた超高強度鋼板とその製造方法及び超高強度溶融亜鉛めっき鋼板の製造方法並びに超高強度合金化溶融亜鉛めっき鋼板の製造方法
JP2010065314A (ja) * 2008-08-12 2010-03-25 Jfe Steel Corp 高強度溶融亜鉛系めっき鋼板およびその製造方法
JP2011117041A (ja) * 2009-12-03 2011-06-16 Sumitomo Metal Ind Ltd 溶接性に優れた高Ｓｉ含有合金化溶融めっき鋼板およびその製造方法
JP2013147736A (ja) * 2011-12-19 2013-08-01 Kobe Steel Ltd 加工性に優れた高降伏比高強度鋼板
WO2013146606A1 (fr) * 2012-03-27 2013-10-03 株式会社神戸製鋼所 Feuille d'acier galvanisé par immersion à chaud à résistance élevée et feuille d'acier galvanisé par immersion à chaud d'un allié à résistance élevée présentant une excellente malléabilité en flexion et une différence de résistance minimale entre la partie centrale et les pièces d'extrémité en direction de largeur de feuille et son procédé de fabrication
WO2016002141A1 (fr) * 2014-07-02 2016-01-07 Ｊｆｅスチール株式会社 Procédé de fabrication de tôle d'acier galvanisée par immersion à chaud de résistance élevée

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007211279A (ja) * 2006-02-08 2007-08-23 Nippon Steel Corp 耐水素脆性に優れた超高強度鋼板とその製造方法及び超高強度溶融亜鉛めっき鋼板の製造方法並びに超高強度合金化溶融亜鉛めっき鋼板の製造方法
JP2010065314A (ja) * 2008-08-12 2010-03-25 Jfe Steel Corp 高強度溶融亜鉛系めっき鋼板およびその製造方法
JP2011117041A (ja) * 2009-12-03 2011-06-16 Sumitomo Metal Ind Ltd 溶接性に優れた高Ｓｉ含有合金化溶融めっき鋼板およびその製造方法
JP2013147736A (ja) * 2011-12-19 2013-08-01 Kobe Steel Ltd 加工性に優れた高降伏比高強度鋼板
WO2013146606A1 (fr) * 2012-03-27 2013-10-03 株式会社神戸製鋼所 Feuille d'acier galvanisé par immersion à chaud à résistance élevée et feuille d'acier galvanisé par immersion à chaud d'un allié à résistance élevée présentant une excellente malléabilité en flexion et une différence de résistance minimale entre la partie centrale et les pièces d'extrémité en direction de largeur de feuille et son procédé de fabrication
WO2016002141A1 (fr) * 2014-07-02 2016-01-07 Ｊｆｅスチール株式会社 Procédé de fabrication de tôle d'acier galvanisée par immersion à chaud de résistance élevée

Cited By (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111433380A (zh) * 2017-11-29 2020-07-17 杰富意钢铁株式会社 高强度镀锌钢板及其制造方法
US11427880B2 (en) 2017-11-29 2022-08-30 Jfe Steel Corporation High-strength galvanized steel sheet and method for manufacturing same
WO2019106894A1 (fr) * 2017-11-29 2019-06-06 Ｊｆｅスチール株式会社 Tôle d'acier galvanisée à résistance élevée et son procédé de fabrication
JP2019099922A (ja) * 2017-11-29 2019-06-24 Ｊｆｅスチール株式会社 高強度亜鉛めっき鋼板
JP6544494B1 (ja) * 2017-11-29 2019-07-17 Ｊｆｅスチール株式会社 高強度亜鉛めっき鋼板およびその製造方法
CN111386358A (zh) * 2017-11-29 2020-07-07 杰富意钢铁株式会社 高强度镀锌钢板及其制造方法
WO2019106895A1 (fr) * 2017-11-29 2019-06-06 Ｊｆｅスチール株式会社 Tôle d'acier galvanisée à résistance élevée et son procédé de fabrication
EP3719156A4 (fr) * 2017-11-29 2020-12-02 JFE Steel Corporation Tôle d'acier galvanisée à résistance élevée et son procédé de fabrication
JP6525114B1 (ja) * 2017-11-29 2019-06-05 Ｊｆｅスチール株式会社 高強度亜鉛めっき鋼板およびその製造方法
CN114645219B (zh) * 2017-11-29 2023-12-12 杰富意钢铁株式会社 高强度镀锌钢板及其制造方法
EP3719157A4 (fr) * 2017-11-29 2020-12-02 JFE Steel Corporation Tôle d'acier galvanisée à résistance élevée et son procédé de fabrication
US11408059B2 (en) 2017-11-29 2022-08-09 Jfe Steel Corporation High-strength galvanized steel sheet and method for manufacturing same
CN114645219A (zh) * 2017-11-29 2022-06-21 杰富意钢铁株式会社 高强度镀锌钢板及其制造方法
US11795531B2 (en) 2018-03-30 2023-10-24 Jfe Steel Corporation High-strength galvanized steel sheet, high strength member, and method for manufacturing the same
JP6879441B1 (ja) * 2019-08-20 2021-06-02 Ｊｆｅスチール株式会社 高強度冷延鋼板およびその製造方法
CN114269961A (zh) * 2019-08-20 2022-04-01 杰富意钢铁株式会社 高强度冷轧钢板及其制造方法
WO2021033407A1 (fr) * 2019-08-20 2021-02-25 Ｊｆｅスチール株式会社 Tôle d'acier haute résistance laminée à froid et son procédé de fabrication
US11926881B2 (en) 2019-08-20 2024-03-12 Jfe Steel Corporation High-strength cold-rolled steel sheet and method for manufacturing the same
CN115003840A (zh) * 2020-01-24 2022-09-02 日本制铁株式会社 板件
CN115003840B (zh) * 2020-01-24 2023-04-21 日本制铁株式会社 板件
CN115612930A (zh) * 2022-10-08 2023-01-17 包头钢铁（集团）有限责任公司 一种低粗糙度汽车座椅滑轨用钢及其生产方法
CN115612930B (zh) * 2022-10-08 2024-01-19 包头钢铁（集团）有限责任公司 一种低粗糙度汽车座椅滑轨用钢及其生产方法

Similar Documents

Publication Publication Date Title
JP6249113B2 (ja) 高降伏比型高強度亜鉛めっき鋼板及びその製造方法
US11427880B2 (en) High-strength galvanized steel sheet and method for manufacturing same
WO2019106895A1 (fr) Tôle d'acier galvanisée à résistance élevée et son procédé de fabrication
WO2017131055A1 (fr) Tôle d'acier galvanisé haute résistance à rapport d'élasticité élevé et son procédé de production
JP5982906B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法
JP5982905B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法
WO2010114142A1 (fr) Plaque en acier galvanisée à chaud de grande résistance et son procédé de fabrication
JP5888267B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法および高強度溶融亜鉛めっき鋼板
JP6249140B1 (ja) 高降伏比型高強度亜鉛めっき鋼板及びその製造方法
JP5552863B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
JP5552859B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
JP5593771B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法
JP5552864B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
JP5552862B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
WO2013031105A1 (fr) Tôle d'acier laminée à chaud pour tôle d'acier laminée à froid, tôle d'acier laminée à chaud pour tôle d'acier galvanisée par immersion à chaud, procédé pour la production de tôle d'acier laminée à chaud pour tôle d'acier laminée à froid et procédé pour la production de tôle d'acier laminée à chaud pour tôle d'acier galvanisée par immersion à chaud
WO2015125435A1 (fr) Tôle d' acier galvanisée par immersion à chaud à haute résistance et procédé de production de cette dernière
JP5593770B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法
JP5971155B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法および高強度溶融亜鉛めっき鋼板
JP5962544B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法および高強度溶融亜鉛めっき鋼板
JP5552861B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
JP5552860B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法

Legal Events

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

Ref document number: 17744285

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 20187021589

Country of ref document: KR

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: MX/A/2018/009164

Country of ref document: MX

Ref document number: 1020187021589

Country of ref document: KR

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: 2017744285

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 2017744285

Country of ref document: EP

Effective date: 20180827