US20160199892A1 - High-strength hot-rolled plated steel sheet and method for manufacturing the same - Google Patents

High-strength hot-rolled plated steel sheet and method for manufacturing the same Download PDF

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US20160199892A1
US20160199892A1 US14/914,579 US201414914579A US2016199892A1 US 20160199892 A1 US20160199892 A1 US 20160199892A1 US 201414914579 A US201414914579 A US 201414914579A US 2016199892 A1 US2016199892 A1 US 2016199892A1
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hot
steel sheet
rolled
slab
strength
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Kang-Hee Ko
Hyeong-Hyeop Do
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Hyundai Steel Co
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Hyundai Steel Co
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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 technology for manufacturing a hot-rolled steel sheet having a plated layer formed thereon, and more particularly, to a high-strength hot-rolled plated steel sheet capable of suppressing material deterioration at the time of plating, while having a high tensile strength of 780 Ma or more, and a method for manufacturing the same.
  • Representative examples of automobile parts requiring high-strength steel may include a chassis.
  • the material for a chassis requires high tensile strength for durability and high elongation and burring property for implementing the shape of a complex part.
  • a snow-removing work using calcium chloride is frequently conducted.
  • the chassis may be corroded by the calcium chloride. Therefore, the material for a chassis requires a corrosion-resistant property in order to prevent such corrosion.
  • a plated steel sheet As the material for a chassis, a plated steel sheet is usually used. Most plated steel sheets are cold-rolled plated steel sheets. The cold-rolled plated steel sheets require a cold rolling process and an anneal heat treatment. Thus, the manufacturing process is complex, and the manufacturing cost for the cold-rolled plated steel sheets is high.
  • a hot-rolled plated steel sheet obtained by plating a hot-rolled steel sheet has been developed.
  • material deterioration may occur at the time of plating.
  • the plating is applied only to hot-rolled steel sheets having a tensile strength of 440 MPa or less.
  • Embodiments of the present invention are directed to a high-strength hot-rolled plated steel sheet of which the material quality is not almost changed at the time of plating, while having high strength, through process control and alloy elements such as aluminum and silicon, and a method for manufacturing the same.
  • a method for manufacturing a high-strength hot-rolled plated steel sheet may include: (a) reheating a slab composed of 0.03-0.1 wt % of carbon (C), below 0.06 wt % of silicon (Si), 0.7-2.0 wt % of manganese (Mn), below 0.02 wt % of phosphorous (P), below 0.01 wt % of sulfur (S), 0.1-0.5 wt % of one or more precipitate forming elements, 0.3-1.0 wt % of aluminum (Al), 0.1-0.5 wt % of molybdenum (Mo), steel (Fe), and unavoidable impurities, the precipitate forming elements forming a precipitate at 500 to 900° C.; (b) hot-rolling the slab; (c) cooling the hot-rolled slab, and then winding the cooled slab; and (d) plating the wound slab.
  • C 0.03-0.1 wt % of carbon
  • Si silicon
  • the method may further include (e) alloying the slab having the plated layer formed thereon.
  • the step (b) may include: roughing rolling the reheated slab at 950 to 1,050° C.; and finishing rolling the roughing-rolled slab at a finishing temperature condition of 800 to 900° C.
  • the step (c) may include cooling the hot-rolled slab at an average cooling speed of 100° C./sec or more, and then winding the cooled slab at 580 to 660° C.
  • the step (d) may include uncoiling and pickling the wound slab, and hot-dip plating the slab without a heat treatment at a temperature of Ac1 or more.
  • the precipitate forming element may include one or more of 0.03-0.1 wt % of niobium (Nb), 0.03-0.1 wt % of titanium (Ti), and 0.08-0.3 wt % of vanadium (V), or include all of Nb, Ti, and V.
  • a high-strength hot-rolled plated steel sheet may include: a hot-rolled steel sheet base material composed of 0.03-0.1 wt % of C, below 0.06 wt % of Si, 0.7-2.0 wt % of Mn, below 0.02 wt % of P, below 0.01 wt % of S, 0.1-0.5 wt % of one or more precipitate forming elements, 0.3-1.0 wt % of Al, 0.1-0.5 wt % of Mo, Fe, and unavoidable impurities, the precipitate forming elements forming a precipitate at 500 to 900° C.; and a plated layer formed on the surface of the hot-rolled steel sheet base material, wherein the high-strength hot-rolled plated steel sheet exhibits a tensile strength of 780 to 900 MPa, a yield strength of 700 to 850 MPa, an elongation of 14 to 22%, and a hole expansion of 55% or more.
  • the hot-rolled steel sheet base material of the hot-rolled plated steel sheet may have a microstructure which is composed of a ferrite single-phase structure and in which fine precipitates having a size of less than 10 nm are formed.
  • the precipitate forming element may include or e or more of 0.03-0.1 wt % of Nb, 0.03-0.1 wt % of Ti, and 0.08-0.3 wt % of V, or include all of Nb, Ti, and V.
  • the strength can be secured through the precipitate forming elements such as Nb, Ti, and V, and the plateability can be improved through the suppression for Si and the addition of Al.
  • the activity of C can be reduced at the time of plating, and the coarsening of the precipitate can be suppressed.
  • material deterioration can be prevented at the time of plating, it is possible to manufacture a high-strength hot-rolled plated steel sheet which has an excellent elongation and burring property, while having high strength.
  • FIG. 1 schematically shows a method for manufacturing a high-strength hot-rolled plated steel sheet in accordance with an embodiment of the present invention
  • FIG. 2 shows precipitates of a specimen in accordance with Embodiment 1 before and after plating
  • FIG. 3 shows the microstructure of the specimen in accordance with Embodiment 1 before and after plating
  • FIG. 4 shows the tensile strength and yield strength of the specimen in accordance with Embodiment 1 before and after plating.
  • FIG. 5 shows the surfaces of specimens in accordance with Embodiment 1 and Comparative Examples 1 to 4.
  • the high-strength hot-rolled plated steel sheet in accordance with the embodiment of the present invention may include a hot-rolled steel sheet base material and a plated layer formed on the surface thereof.
  • the hot-rolled steel sheet base material of the high-strength hot-rolled plated steel sheet in accordance with the embodiment of the present invention may include 0.03-0.1 wt % of carbon (C), below 0.06 wt % of silicon (Si), 0.7-2.0 wt % of manganese (Mn), below 0.02 wt % of phosphorous (P), below 0.01 wt % of sulfur (S), 0.1-0.5 wt % of one or more precipitate forming elements, 0.3-1.0 wt % of aluminum (Al), and 0.1-0.5 wt % of molybdenum (Mo).
  • the precipitate forming element may form a precipitate at a temperature of 500 to 900° C.
  • the other elements excluding the above-described alloy elements may include steel (Fe) and unavoidable impurities which occur during a steelmaking process.
  • C is an element which contributes to increasing the strength of steel.
  • C may be added at 0.03-0.1 wt % with respect to the entire weight of the hot-rolled steel sheet base material in accordance with the embodiment of the present invention.
  • C is less than 0.03 wt %, it is difficult to secure a target tensile strength of 780 MPa or more.
  • the addition of C exceeds 0.1 wt %, the elongation and burring property may be degraded.
  • Si is an element which contributes to securing strength, and serves as a deoxidizer for removing oxygen in steel.
  • Si may be added at below 0.06 wt % with respect to the entire weight of the hot-rolled steel sheet base material in accordance with the embodiment of the present invention.
  • Si exceeds 0.06 wt %, the plateability and alloying degree may be degraded.
  • Mn is an element which increases the strength and toughness of steel and improves the hardenability of steel.
  • the addition of Mn may suppress the reduction of ductility with the increase of strength, compared to the addition of C.
  • Mn may be added at 0.7-2.0 wt % with respect to the entire weight of the hot-rolled steel sheet base material in accordance with the embodiment of the present invention.
  • the addition of Mn is less than 0.7 wt %, the addition may have no effect.
  • MnS-based non-metallic inclusions may be excessively formed. During a welding operation, a crack or the like may occur to reduce the weldability.
  • P is an element which contributes to improving strength.
  • fine segregations as well as center segregations may be formed to have a bad effect on the material quality, and degrade the weldability.
  • the content of P is limited to below 0.02 wt % with respect to the entire weight of the hot-rolled steel sheet base material.
  • S is an element which is coupled to Mn and forms non-metallic inclusions, and the non-metallic inclusions may degrade the toughness and weldability.
  • the content of S is limited to below 0.01 wt % with respect to the entire weight of the hot-rolled steel sheet base material.
  • the precipitate forming element serves to form a precipitate at a temperature of 500 to 900° C.
  • Representative examples of the precipitate forming element may include niobium (Nb), titanium (Ti), and vanadium (V).
  • the hot-rolled steel sheet base material may include one or two or more kinds of precipitate forming elements.
  • the precipitate forming element may be added at 0.1-0.5 wt % with respect to the entire weight of the hot-rolled steel sheet base material in accordance with the embodiment of the present invention.
  • the content of the precipitate forming element is less than 0.1 wt %, the effect of strength improvement by precipitation hardening is insufficient.
  • the content of the precipitate forming element exceeds 0.5 wt %, an excessive amount of precipitate may be formed to degrade the processability and the surface quality.
  • Ti precipitate may be formed at a temperature of 900 to 1,000° C.
  • Ni precipitate may be formed at a temperature of 600 to 800° C.
  • V precipitate may be formed at a temperature of 400 to 600° C.
  • all of Ni, Ti, and V may be included in the precipitate forming element such that the precipitation is performed during a hot rolling and cooling process.
  • Nb, Ti, and V When all of Nb, Ti, and V are included in the precipitate forming element, Nb, Ti, and V may be added at 0.03 to 0.1 wt %, 0.03-0.1%, and 0.08-0.3%, respectively, which considers the following aspects.
  • Nb and Ti When Nb and Ti are added at over 0.03 wt %, the precipitation hardening effect may be obtained, but when Nb and Ti are added at over 0.1 wt %, the processability and surface quality may be degraded.
  • V when V is added at over 0.08 wt %, the precipitation hardening effect may be obtained, but when V is added at over 0.3 wt %, the processability may be degraded.
  • Al may serve as a deoxidizer, and serve to improve the plateability.
  • Al may be added at 0.3-1.0 wt % with respect to the entire weight of the hot-rolled steel sheet base material in accordance with the embodiment of the present invention.
  • the addition of Al is less than 0.3 wt %, the deoxidation effect may be insufficient.
  • the content of Al exceeds 1.0 wt %, the toughness of the steel sheet may be reduced.
  • plating may be performed on the surface of the hot-rolled steel sheet, and an alloying heat treatment may be performed, if necessary.
  • the plating and the alloying heat treatment may be performed at a temperature of 450 to 550° C. which overlaps the precipitation temperature range of V.
  • V is the most suitable for precipitation hardening.
  • the material quality may be significantly changed during the plating process or alloying heat treatment.
  • Mo when Mo is added, Mo may reduce the activity of C at a high temperature including the temperature range of the plating and alloying heat treatment, and disturb the growth of the precipitate. As a result, the material deterioration at the time of the plating process or alloying heat treatment can be prevented.
  • Mo may be added at 0.1-0.5 wt % with respect to the entire weight of the hot-rolled steel sheet base material.
  • the addition of Mo is less than 0.1 wt %, the addition may have no effect.
  • the addition of Mo exceeds 0.5 wt %, the formability and burring property of the steel sheet may be degraded.
  • the high-strength hot-rolled plated steel sheet in accordance with the embodiment of the present invention may be manufactured as a variety of hot-dip plated steel sheets, through a hot-dip plating process after a hot-rolled steel sheet is manufactured from a slab. More specifically, the high-strength hot-rolled plated steel sheet may include an HGI (Hot-dip Galvanized) steel sheet having a hot-rolled galvanized layer formed thereon or an HGA (Hot-rolled Galvanized) steel sheet having an alloyed hot-rolled galvanized layer formed on a hot-rolled steel sheet base material.
  • HGI Hot-dip Galvanized
  • HGA Hot-rolled Galvanized
  • the high-strength hot-rolled plated steel sheet in accordance with the embodiment of the present invention may have a final microstructure which is composed of a ferrite single-phase structure and in which fine precipitates having a size of 10 nm or less are formed, through the alloy composition of Mo, Al, and the precipitate forming elements and the hot-rolling and plating process.
  • the ferrite In the ferrite single-phase structure, the ferrite may have an area rate of 98% or more.
  • the high-strength hot-rolled plated steel sheet in accordance with the embodiment of the present invention may exhibit a tensile strength of 780 to 900 Mpa, a yield strength of 700 to 850 MPa, an elongation of 14 to 22%, and a hole expansion rate of 55% or more.
  • FIG. 1 schematically shows a method for manufacturing a high-strength hot-rolled plated steel sheet in accordance with an embodiment of the present invention.
  • the method for manufacturing a high-strength hot-rolled plated steel sheet in accordance with the embodiment of the present invention may include slab reheating (S 110 ), hot rolling (S 120 ), cooling/winding (S 130 ), and plating (S 140 ).
  • a half-finished slab having the above-described composition may be reheated.
  • the slab reheating may be performed at a temperature of 1,200° C. or more for 80 minutes or more, for example.
  • the precipitate forming elements such as Ti, Nb, and V may be reemployed.
  • fine precipitates may be formed during the hot rolling process.
  • the slab may be hot-rolled.
  • the hot rolling may include a variety of publicly-known methods which are performed under the condition that the finishing rolling temperature is equal to or more than Ar3. More desirably, roughing rolling may be performed at a temperature of 950 to 1,050° C., and finishing rolling may be then performed at a temperature of 800 to 900° C. Under the above-described roughing rolling condition, a large quantity of fine high-temperature precipitates may be formed. Under the finishing rolling condition, austenite grains before ferrite transformation may have a size of 10 to 30 ⁇ m, which is preferable in terms of strength and elongation.
  • the hot-rolled slab may be cooled and wound, in order to secure sufficient strength and toughness.
  • the cooling may be performed at an average cooling speed of 100° C./sec or more such that grain precipitates are grown.
  • the winding may be performed at a temperature of 580 to 660° C. which is the most suitable for forming the ferrite single-phase structure, and a large quality of fine precipitates may be formed due to a difference in employment rate among Ti, Nb, and V during ferrite transformation.
  • the grain size of the ferrite structure may be set in the range of 2 to 7 ⁇ m through the cooling/winding process.
  • the slab may be naturally cooled to the room temperature.
  • the manufactured hot-rolled steel sheet base material may be plated to manufacture a hot-rolled plated steel sheet.
  • the steel sheet can have corrosion resistance.
  • a pickling process may be further performed to pickle the surface of the steel sheet using hydrochloric acid, in order to remove scales on the hot-rolled steel sheet base material.
  • the plating process may include successively dipping the steel sheet in a plating bath. After the plating process, an alloying heat treatment may be further performed.
  • a heat treatment may be performed to heat the steel sheet at a temperature of Ac1 or more.
  • hot-dip plating may be performed without a heat treatment after the pickling process. When a heat treatment is skipped, the manufacturing cost for the hot-rolled plated steel sheet can be significantly reduced.
  • an HGI or HGA steel sheet may be manufactured.
  • the plating process may be performed at a temperature of 450 to 500° C. Furthermore, the alloying heat treatment may be performed at a temperature of 460 to 500° C. for about 5 to 100 seconds.
  • Ingots having compositions of Table 1 below were manufactured, and then reheated at a temperature of 1,250° C. for 120 minutes. Then, roughing rolling was performed at a temperature of about 1,000° C., and finishing rolling was performed at a temperature of 850° C. Then, the ingots were cooled to 600° C. at an average cooling speed of 150° C./sec, and maintained at 600° C. for 30 seconds. Then, the ingots were naturally cooled to manufacture specimens of the hot-rolled steel sheet base material.
  • the specimens of the hot-rolled steel sheet base material were pickled, hot-dip galvanized at a temperature of 460° C., and alloying-heat-treated at a temperature of 500° C.
  • FIG. 2 shows precipitates of the specimen in accordance with Embodiment 1 before and after plating. Referring to FIG. 2 , the size of precipitates in the specimen in accordance with Embodiment 1 is not changed before and after plating.
  • FIG. 3 shows the microstructure of the specimen in accordance with Embodiment 1 before and after plating.
  • the specimen in accordance with Embodiment 1 has a ferrite single-phase structure before and after plating, and the structure thereof is not changed.
  • FIGS. 2 and 3 are because, as the activity of C was reduced due to the addition of Mo, material deterioration did not occur at the time of plating.
  • the tensile test was performed by a JIS-5 specimen.
  • the hole expansion test was performed as follows: a hole having the initial diameter d 0 of 10 mm was formed and then expanded by a 60-degree cone punch, and the diameter d of the hole at the point of time that a crack passed through the sheet was measured to evaluate the hole expansion ((d-d 0 )/d 0 ⁇ 100).
  • the specimens in accordance with Embodiments 1 to 3 which satisfy the conditions suggested in the present invention, satisfy a tensile strength of 780 to 900 MPa, a yield strength of 700 to 850 MPa, an elongation of 14 to 22%, and a hole expansion of 55% or more, which correspond to the target values of the tensile strength, the yield strength, the elongation, and the hole expansion.
  • Comparative Example 1 which does not include a sufficient amount of precipitate forming element, exhibits low strength
  • Comparative Example 2 which does not include Mo, also exhibits low strength.
  • the results of Comparative Examples 1 and 2 are because no precipitates were formed due to an insufficient amount of precipitate forming element, or precipitates were coarsened during a plating process or a maintenance process after a cooling process, which corresponds to a winding process.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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US14/914,579 2013-08-30 2014-01-29 High-strength hot-rolled plated steel sheet and method for manufacturing the same Abandoned US20160199892A1 (en)

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KR20130104170A KR20150025952A (ko) 2013-08-30 2013-08-30 고강도 열연도금강판 및 그 제조 방법
KR10-2013-0104170 2013-08-30
PCT/KR2014/000854 WO2015030324A1 (ko) 2013-08-30 2014-01-29 고강도 열연도금강판 및 그 제조 방법

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JP2019533082A (ja) * 2016-09-22 2019-11-14 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Ｔａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ 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

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