WO2015030324A1 - 고강도 열연도금강판 및 그 제조 방법 - Google Patents

고강도 열연도금강판 및 그 제조 방법 Download PDF

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Publication number
WO2015030324A1
WO2015030324A1 PCT/KR2014/000854 KR2014000854W WO2015030324A1 WO 2015030324 A1 WO2015030324 A1 WO 2015030324A1 KR 2014000854 W KR2014000854 W KR 2014000854W WO 2015030324 A1 WO2015030324 A1 WO 2015030324A1
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Prior art keywords
steel sheet
rolled steel
hot
precipitate
weight
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PCT/KR2014/000854
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English (en)
French (fr)
Korean (ko)
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고강희
도형협
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현대제철 주식회사
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Priority to CN201480047150.6A priority Critical patent/CN105492635B/zh
Priority to US14/914,579 priority patent/US20160199892A1/en
Priority to EP14841141.6A priority patent/EP3040427B1/en
Publication of WO2015030324A1 publication Critical patent/WO2015030324A1/ko

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C22C38/04—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material

Definitions

  • the present invention relates to a hot-rolled steel sheet manufacturing technology in which a plated layer is formed on a hot-rolled steel sheet, and more particularly, to a high-strength hot-rolled steel sheet and a method of manufacturing the same, having a high strength of 780 MPa or more and suppressing material degradation during plating It is about.
  • Part of the automobile parts that require high-strength steel may be a typical car chassis parts.
  • Properties required for chassis parts materials require high tensile strength and high elongation and high burring properties for complex part shapes.
  • chassis parts are required to be corrosion resistant in order to prevent such corrosion.
  • chassis parts are mainly plated steel sheets, most of which are cold rolled steel sheets.
  • a cold-rolled steel sheet it is accompanied by a cold rolling process and an annealing heat treatment process, the manufacturing process is complicated, and thus there is a problem that the production cost of the plated steel sheet is high.
  • An object of the present invention is to provide a high-strength hot-rolled steel sheet and a method of manufacturing the same having a high strength and a small material change during plating through alloying components such as aluminum, silicon and process control.
  • High-strength hot-rolled steel sheet manufacturing method for achieving the above object is (a) wt%, carbon (C): 0.03 ⁇ 0.1%, silicon (Si): 0.06% or less, manganese (Mn) : 0.7 to 2.0%, phosphorus (P): 0.02% or less, sulfur (S): 0.01% or less, 0.1 to 0.5% of one or more precipitate-forming elements forming a precipitate at 500 to 900 ° C, aluminum (Al): 0.3 ⁇ 1.0%, molybdenum (Mo): reheating the slab plate consisting of 0.1 ⁇ 0.5% and the remaining iron (Fe) and inevitable impurities; (b) hot rolling the slab plate; (c) winding the hot rolled sheet and then winding it up; And (d) plating the wound sheet.
  • the method for manufacturing the hot-rolled steel sheet may further include (e) alloying the plate member on which the plating layer is formed.
  • step (b) may comprise the step of co-rolling the reheated slab plate at 950 ⁇ 1050 °C, and the step of finishing the cold-rolled plate at a finishing temperature condition of 800 ⁇ 900 °C; .
  • the hot rolled sheet is cooled at an average cooling rate of 100 ° C / sec or more, and then wound at 580 to 660 ° C.
  • step (d) after pickling by coiling the coiled sheet material, it is preferable to perform hot-dip plating without heat treatment at Ac1 or more.
  • the precipitate-forming element is a weight percent, niobium (Nb): 0.03 ⁇ 0.1%, titanium (Ti): 0.03 ⁇ 0.1% and vanadium (V): 0.08 ⁇ 0.3% may include at least one kind, niobium It is preferred to include both titanium, vanadium and the like.
  • High-strength hot-rolled steel sheet for achieving the above object by weight, carbon (C): 0.03 ⁇ 0.1%, silicon (Si): 0.06% or less, manganese (Mn): 0.7 ⁇ 2.0% , Phosphorus (P): 0.02% or less, sulfur (S): 0.01% or less, 0.1-0.5% of one or more precipitate-forming elements forming a precipitate at 500-900 ° C, aluminum (Al): 0.3-1.0%, molybdenum (Mo): hot-rolled steel sheet base material consisting of 0.1 ⁇ 0.5% and the remaining iron (Fe) and inevitable impurities; And a plating layer formed on the surface of the hot-rolled steel sheet base material, and characterized in that it exhibits tensile strength of 780 to 900 MPa, yield strength of 700 to 850 MPa, elongation of 14 to 22%, and hole expansion rate of 55% or more.
  • the hot-rolled steel sheet is a microstructure of the base material of the hot-rolled steel sheet is made of a ferrite single-phase structure, fine precipitates of less than 10nm may be formed.
  • the precipitate-forming element is a weight percent, niobium (Nb): 0.03 ⁇ 0.1%, titanium (Ti): 0.03 ⁇ 0.1% and vanadium (V): 0.08 ⁇ 0.3% may include at least one kind, niobium It is preferred to include both titanium, vanadium and the like.
  • a precipitate forming element such as niobium (Nb), titanium (Ti), vanadium (V), and silicon (Si) suppression, aluminum (Al).
  • Plating properties can be improved by addition.
  • a high strength hot-rolled steel sheet according to the present invention by containing 0.1 to 0.5% by weight of molybdenum (Mo), it is possible to reduce the carbon activity during plating, thereby suppressing coarsening of precipitates, accordingly It is possible to prevent the change of material during plating, it is possible to manufacture a high strength hot-rolled steel sheet excellent in physical properties such as high strength and elongation and burring properties.
  • Mo molybdenum
  • Figure 1 schematically shows a method of manufacturing a high strength hot rolled steel sheet according to an embodiment of the present invention.
  • Figure 2 shows the precipitate before and after plating of the specimen according to Example 1.
  • Figure 3 shows the microstructure before and after plating of the specimen according to Example 1.
  • Figure 4 shows the tensile strength and yield strength before and after plating of the specimen according to Example 1.
  • Figure 5 shows the surface after plating of the specimen according to Example 1, Comparative Examples 1 to 4.
  • the high strength hot rolled steel sheet according to the present invention includes a hot rolled steel sheet base material and a plating layer formed on the surface thereof.
  • the hot-rolled steel sheet base material of the high-strength hot-rolled steel sheet according to the present invention in weight%, carbon (C): 0.03 ⁇ 0.1%, silicon (Si): 0.06% or less, manganese (Mn): 0.7 ⁇ 2.0%, phosphorus ( P): 0.02% or less, sulfur (S): 0.01% or less, 0.1-0.5% of one or more precipitate-forming elements forming a precipitate at 500-900 ° C, aluminum (Al): 0.3-1.0%, molybdenum (Mo) : Contains 0.1 to 0.5%.
  • the rest of the alloy components are made of inevitable impurities generated during iron (Fe) and steelmaking.
  • Carbon (C) is an element that contributes to increasing the strength of steel.
  • the carbon is preferably added in an amount of 0.03 to 0.1% by weight of the total weight of the hot rolled steel base material according to the present invention.
  • the amount of carbon added is less than 0.03% by weight, it is difficult to secure a tensile strength of 780 MPa or more.
  • the amount of carbon added exceeds 0.1% by weight, there is a problem that the elongation and burring properties are lowered.
  • Silicon (Si) contributes to securing strength and also acts as a deoxidizer to remove oxygen in the steel.
  • the silicon is preferably added to less than 0.06% by weight of the total weight of the hot rolled steel base material according to the present invention.
  • the addition amount of silicon exceeds 0.06% by weight, there is a problem in that the plating property and alloying degree are lowered.
  • Manganese (Mn) is an element that increases the strength and toughness of steel and increases the hardenability of steel. The addition of manganese has less deterioration in ductility at the time of increasing strength than the addition of carbon.
  • the manganese is preferably added to 0.7 to 2.0% by weight of the total weight of the hot rolled steel base material according to the present invention.
  • amount of manganese added is less than 0.7% by weight, the effect of adding manganese is insufficient.
  • the added amount of manganese exceeds 2.0% by weight, excessively generating MnS-based non-metallic inclusions, there is a problem to reduce the weldability, such as crack generation during welding.
  • Phosphorus (P) contributes to strength improvement, but when included in a large amount, not only central segregation but also micro segregation may be formed, which may adversely affect the material, and may also deteriorate weldability.
  • the content of phosphorus is limited to 0.02% by weight or less of the total weight of the hot rolled steel base material.
  • S Sulfur
  • manganese combines with manganese to form nonmetallic inclusions, and such nonmetallic inclusions are a factor of lowering toughness, weldability, and the like.
  • the sulfur content is limited to 0.01% by weight or less of the total weight of the hot rolled steel base material.
  • the precipitate forming element is an element which forms a precipitate at 500 to 900 ° C., and typically, niobium (Nb), titanium (Mo), and vanadium (V) may correspond thereto.
  • Nb niobium
  • Mo titanium
  • V vanadium
  • One or two or more kinds of these precipitate forming elements may be included.
  • the precipitate forming element is preferably added in 0.1 to 0.5% by weight of the total weight of the hot rolled steel base material.
  • the content of precipitate forming element is less than 0.1% by weight, the effect of enhancing strength due to precipitation strengthening is insufficient.
  • the content of precipitate forming elements exceeds 0.5% by weight, workability, surface defects, etc. may be a problem due to excessive precipitate formation.
  • titanium (Ti) precipitates are precipitated at about 900 to 1000 ° C, and in the case of niobium, they are precipitated at around 600 to 800 ° C, and in the case of vanadium, they are precipitated at about 400 to 600 ° C. . In view of this point, it is preferable that all of niobium, titanium and vanadium are included so that precipitation occurs in the hot rolling and cooling processes.
  • the precipitate-forming element contains all of niobium, titanium and vanadium
  • each of these elements is added with niobium (Nb): 0.03 to 0.1%
  • Nb niobium
  • Ti titanium
  • Ti vanadium
  • V vanadium
  • vanadium when the addition of 0.03% by weight or more, respectively, the precipitation hardening effect is generated, but when 0.1% by weight or more is added, the workability and surface quality are deteriorated.
  • vanadium when 0.08% by weight or more is added, If the precipitation strengthening effect is generated, but exceeds 0.3% by weight, the workability is considered.
  • aluminum (Al) acts as a deoxidizer and also serves to improve plating properties.
  • the aluminum is preferably added in 0.3 ⁇ 1.0% by weight of the total weight of the hot rolled steel sheet base material according to the present invention.
  • the amount of aluminum added is less than 0.3% by weight, the deoxidation effect may be insufficient.
  • the aluminum content exceeds 1.0% by weight, the toughness of the steel sheet may be inhibited.
  • the surface of the hot-rolled steel sheet is subjected to plating, and in some cases alloying heat treatment, such a plating temperature, the alloying heat treatment temperature is approximately 450 ⁇ 550 °C overlapping the precipitation temperature range of vanadium. Accordingly, on the one hand, vanadium is the most advantageous for strengthening the precipitation among the precipitate forming elements, and on the other hand, when the vanadium precipitate is coarsened, the material change during plating or alloying heat treatment is the largest.
  • molybdenum when added, molybdenum lowers the activity of carbon (C) at a high temperature including the plating and alloying heat treatment temperature range, thereby inhibiting the growth of precipitates, and consequently deteriorating material during plating and alloying heat treatment. It can prevent.
  • the molybdenum is preferably included in 0.1 to 0.5% by weight of the total weight of the hot rolled steel base material.
  • the amount of molybdenum added is less than 0.1% by weight, the effect of addition is insufficient.
  • the addition amount of molybdenum exceeds 0.5% by weight, the moldability, burring property, and the like of the steel sheet may decrease.
  • the high-strength hot-rolled steel sheet according to the present invention may be various hot-dip galvanized steel sheet according to the hot-dip galvanizing process after manufacturing the hot-rolled steel sheet from the slab plate. More specifically, the high-strength hot-rolled steel sheet according to the present invention is a hot-rolled hot-dip galvanized steel sheet (HGI) having a hot-dip galvanized layer formed on its surface, or a hot-rolled alloy hot-dip galvanized steel sheet (HGA) having a hot-dip galvanized zinc alloy layer formed on its surface May be).
  • HGI hot-rolled hot-dip galvanized steel sheet
  • HGA hot-rolled alloy hot-dip galvanized steel sheet
  • High-strength hot-rolled steel sheet according to the present invention is made of a ferrite single-phase structure (ferrite containing 98% or more by area ratio) through the alloy composition of the above-described molybdenum, aluminum, precipitate forming elements, and the following hot rolling process and plating process , It may represent a final microstructure in which fine precipitates of less than 10 nm are formed.
  • the high-strength hot-rolled steel sheet according to the present invention may exhibit a tensile strength of 780 ⁇ 900MPa, yield strength 700 ⁇ 850MPa, elongation 14 ⁇ 22%, hole expansion rate 55% or more in terms of mechanical properties.
  • Figure 1 schematically shows a method of manufacturing a high strength hot rolled steel sheet according to an embodiment of the present invention.
  • the hot rolled steel sheet manufacturing method includes a slab reheating step (S110), hot rolling step (S120), cooling / winding step (S130) and plating step (S140).
  • the slab plate material of the semi-finished state having the above-described composition is reheated.
  • the slab reheating may be carried out, for example, by heating at least 1200 ° C. for at least 80 minutes.
  • precipitate-forming elements such as titanium, niobium, and vanadium may be re-used, and fine precipitation may occur during hot rolling.
  • the slab plate is hot rolled.
  • Hot rolling may be applied to a variety of known methods as long as the finish rolling temperature is higher than the Ar3 temperature. More preferably, after the rough rolling is performed at 950 to 1050 ° C., the hot rolling is performed at the finishing rolling temperature of 800 to 900 ° C. Can be presented. In the rough rolling condition, a high temperature precipitate may be generated in the finest and most, and the austenite grain size before ferrite transformation in the filamentous rolling condition is about 10 to 30 ⁇ m, which is preferable in terms of strength and elongation.
  • the hot rolled sheet is cooled and then wound.
  • the cooling is preferably performed at an average cooling rate of 100 ° C / sec or more to grow the grain size precipitate.
  • winding is performed at 580 ⁇ 660 °C is most advantageous to form a ferrite single-phase structure, fine and large amount of precipitates may be generated through the difference in the solid solution of titanium, niobium, vanadium and the like dissolved during ferrite transformation.
  • the grain size of the ferrite structure may be 2 ⁇ 7 ⁇ m.
  • the plating step (S140) to prepare a hot-rolled steel sheet by plating the prepared hot-rolled steel base material. Corrosion resistance of the steel sheet can be secured through plating.
  • a pickling process of pickling the surface of the steel sheet using hydrochloric acid or the like may be further included to remove scale from the surface of the hot rolled steel sheet.
  • Plating may be carried out by continuously immersing the steel plate in the plating bath, after the plating may further comprise a process of alloying heat treatment.
  • the heat treatment process may be accompanied by heating and maintaining the steel sheet to Ac1 or more before plating, but the steel sheet according to the present invention has a feature of less material deviation before plating and after plating, and performs hot dip plating without heat treatment after pickling. In this case, if the heat treatment process is omitted, the cost of manufacturing the hot-rolled steel sheet can be greatly reduced.
  • a hot rolled hot dip galvanized steel sheet (HGI) or a hot rolled alloy hot dip galvanized steel sheet (HGA) may be manufactured.
  • Plating temperature may be performed at approximately 450 ⁇ 500 °C.
  • the alloying heat treatment may be performed at about 460 ⁇ 500 °C for about 5 ⁇ 100 seconds.
  • Ingots with the compositions shown in Table 1 were prepared and then reheated at 1250 ° C. for 120 minutes. Thereafter, rough rolling was performed at about 1000 ° C., followed by finishing rolling at 850 ° C. finish rolling temperature. Thereafter, after cooling to 600 ° C. at an average cooling rate of 150 ° C./sec, after 30 seconds of holding at 600 ° C., natural cooling was performed to prepare a hot-rolled steel sheet material specimen.
  • the hot-rolled steel sheet specimens were pickled and hot-dipped galvanized at 460 ° C., followed by alloy heat treatment at 500 ° C.
  • Figure 2 shows the precipitate before and after plating of the specimen according to Example 1. 2, in the case of the specimen according to Example 1, it can be seen that there is little change in the precipitate size before and after plating.
  • Figure 3 shows the microstructure before and after plating of the specimen according to Example 1.
  • FIG. 3 in the case of the specimen according to Example 1, both the pre- and post-plating ferrite single phase structures were observed, and there was no change in structure.
  • the tensile test was based on JIS No. 5 test piece.
  • the hole expandability evaluation was performed by forming a boring hole with an initial diameter (d 0 : 10 mm) and then expanding it with a 60 ° conical punch so that the hole expansion rate (from the hole diameter d at the time when the crack penetrated the plate). (dd 0 ) / d 0 X 100) was evaluated.
  • tensile strength, yield strength, elongation and hole expansion rate are all target values, tensile strength 780-900 MPa, yield strength 700 It can be seen that it satisfies 850 MPa, elongation 14-22%, and hole expansion rate 55% or more.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
PCT/KR2014/000854 2013-08-30 2014-01-29 고강도 열연도금강판 및 그 제조 방법 WO2015030324A1 (ko)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201480047150.6A CN105492635B (zh) 2013-08-30 2014-01-29 高强度热轧电镀钢板及其制造方法
US14/914,579 US20160199892A1 (en) 2013-08-30 2014-01-29 High-strength hot-rolled plated steel sheet and method for manufacturing the same
EP14841141.6A EP3040427B1 (en) 2013-08-30 2014-01-29 High-strength hot-rolled plated steel sheet and method for manufacturing same

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KR10-2013-0104170 2013-08-30
KR20130104170A KR20150025952A (ko) 2013-08-30 2013-08-30 고강도 열연도금강판 및 그 제조 방법

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EP (1) EP3040427B1 (zh)
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WO (1) WO2015030324A1 (zh)

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WO2017051998A1 (ko) 2015-09-22 2017-03-30 현대제철 주식회사 도금 강판 및 이의 제조방법
JP7077309B2 (ja) * 2016-09-22 2022-05-30 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ 優れた伸びフランジ成形性及びエッジ疲労性能を有する熱間圧延高強度鋼の製造方法
JP6589903B2 (ja) * 2017-02-06 2019-10-16 Ｊｆｅスチール株式会社 溶融亜鉛めっき鋼板およびその製造方法
EP3408418B1 (en) * 2017-02-10 2023-05-10 Tata Steel Limited A hot rolled precipitation strengthened and grain refined high strength dual phase steel sheet possessing 600 mpa minimum tensile strength and a process thereof

Citations (6)

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EP3040427B1 (en) 2019-12-04
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EP3040427A1 (en) 2016-07-06
CN105492635A (zh) 2016-04-13
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