EP3385402B1 - High-strength steel having excellent brittle crack arrestability and welding part brittle crack initiation resistance, and production method therefor - Google Patents

High-strength steel having excellent brittle crack arrestability and welding part brittle crack initiation resistance, and production method therefor Download PDF

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EP3385402B1
EP3385402B1 EP16871086.1A EP16871086A EP3385402B1 EP 3385402 B1 EP3385402 B1 EP 3385402B1 EP 16871086 A EP16871086 A EP 16871086A EP 3385402 B1 EP3385402 B1 EP 3385402B1
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Prior art keywords
brittle crack
less
welding
steel
temperature
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German (de)
English (en)
French (fr)
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EP3385402A1 (en
EP3385402A4 (en
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Hak-Cheol Lee
Sung-Ho Jang
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/16—Control of thickness, width, diameter or other transverse dimensions
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • the present disclosure relates to a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance, and to a method of manufacturing the same.
  • microstructures of thick steel plates may be coarse, so that low temperature properties on which grain sizes have the most significant effect may be degraded.
  • Such technologies may contribute to refining a structure of a surface portion, but may not solve a problem in which impact toughness is degraded due to coarsening of structures other than that of the surface portion. Thus, such technologies may not be fundamental countermeasures to brittle crack arrestability.
  • the microstructure in a HAZ includes low temperature transformation ferrite having high strength, such as bainite, there is a limitation in which HAZ properties, in detail, toughness, are significantly reduced.
  • brittle crack initiation resistance generally evaluated through a crack tip opening displacement (CTOD) test to evaluate the stability of the structure
  • COD crack tip opening displacement
  • martensite-austenite may be transformed to have a different phase through tempering, or the like, to secure physical properties.
  • HAZ in which an effect of tempering disappears due to thermal history, it is impossible to apply brittle crack initiation resistance.
  • KR2015-0112489 A discloses a steel material and a manufacturing method comprising by weight %, carbon (C): 0.05% to 0.09%, manganese (Mn): 1.5% to 2.0%, nickel (Ni): 0.3% to 0.8%, niobium (Nb): 0.005% to 0.04%, titanium (Ti): 0.005% to 0.04%, copper (Cu): 0.1% to 0.5%, silicon (Si): 0.05% to 0.3%, aluminum (Al) : 0.005% to 0.05%, phosphorus (P) : 100 ppm or less, sulfur (S): 40 ppm or less, iron (Fe) as a residual component thereof, and inevitable impurities and having a Cu/N ratio of 0.75, a yield strength of 517 MPa and a transition temperature of -65°C.
  • An aspect of the present disclosure may provide a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance.
  • Another aspect of the present disclosure may provide a method of manufacturing a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance.
  • a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance comprises, by wt%, carbon (C): 0.05% to 0.09%, manganese (Mn): 1.61% to 2.0%, nickel (Ni): 0.3% to 0.8%, niobium (Nb) : 0.005% to 0.04%, titanium (Ti) : 0.005% to 0.04%, copper (Cu): 0.1% to 0.5%, silicon (Si): 0.05% to 0.3%, aluminum (Al): 0.005% to 0.05%, phosphorus (P): 100 ppm or less, sulfur (S) : 40 ppm or less, iron (Fe) as a residual component thereof, and inevitable impurities, wherein a microstructure of a central portion includes, by area%, acicular ferrite in an amount of 70% or greater, pearlite in an amount of 10% or less, and one or more selected from a group consisting
  • a weight ratio of Cu and Ni may be set to be 0.8 or less, and in more detail, 0.6 or less.
  • the high-strength steel material may have yield strength of 390 MPa or greater.
  • the high-strength steel material may have a Charpy fracture transition temperature of -40°C or lower in a 1/2t position in a steel material thickness direction, where t is a steel sheet thickness.
  • a method of manufacturing a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance comprises rough rolling a slab at a temperature of 900°C to 1100°C after reheating the slab at 1000°C to 1100°C, including, by wt%, C: 0.05% to 0.09%, Mn: 1.61% to 2.0%, Ni: 0.3% to 0.8%, Nb: 0.005% to 0.04%, titanium (Ti): 0.005% to 0.04%, copper (Cu): 0.1% to 0.5%, silicon (Si): 0.1% to 0.3%, aluminum (Al): 0.005% to 0.05%, phosphorus (P): 100 ppm or less, sulfur (S): 40 ppm or less, iron (Fe) as a residual component thereof, and inevitable impurities; obtaining a steel sheet by finish rolling a bar obtained from the rough rolling a slab, at a temperature in a range of Ar 3 + 60°
  • a grain size of a central portion in a bar thickness direction before finish rolling after the rough rolling a slab may be 100 ⁇ m or less, and more specifically, 80 ⁇ m or less.
  • a reduction ratio during the finish rolling may be set such that a ratio of a slab thickness (mm) to a steel sheet thickness (mm) after the finish rolling may be 4 or greater.
  • the skin pass rolling is performed to secure a shape of a sheet (to secure a flat sheet) at a relatively low reduction rate, less than 5% in 1 to 2 passes of finish rolling.
  • a high-strength steel material having a relatively high level of yield strength, as well as excellent brittle crack arrestability and welding zone brittle crack initiation resistance may be provided.
  • FIG. 1 is an image captured using an optical microscope, illustrating a central portion of Inventive Steel 3 in a thickness direction.
  • the inventors of the present disclosure conducted research and experiments to improve yield strength, brittle crack arrestability, and welding zone brittle crack initiation resistance of a thick steel material and proposed the present disclosure based on results thereof.
  • a steel composition, a structure, and manufacturing conditions of a steel material may be controlled, thereby improving yield strength, brittle crack arrestability, and welding zone brittle crack initiation resistance of the thick steel material.
  • a main concept of an exemplary embodiment is as follows .
  • a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance comprises, by wt%, carbon (C): 0.05% to 0.09%, manganese (Mn): 1.61% to 2.0%, nickel (Ni): 0.3% to 0.8%, niobium (Nb) : 0.005% to 0.04%, titanium (Ti) : 0.005% to 0.04%, copper (Cu): 0.1% to 0.5%, silicon (Si): 0.05% to 0.3%, aluminum (Al): 0.005% to 0.05%, phosphorus (P): 100 ppm or less, sulfur (S) : 40 ppm or less, iron (Fe) as a residual component thereof, and inevitable impurities, wherein a microstructure of a central portion includes, by area%, acicular ferrite in an amount of 70% or greater, pearlite in an amount of 10% or less, and one or more selected from a group consisting
  • C Since C is the most significant element used in securing basic strength, C is required to be contained in steel within an appropriate range. In order to obtain an effect of addition, C may be added in an amount of 0.05% or greater.
  • the C content is limited to 0.05% to 0.09%.
  • the C content may be limited to 0.061% to 0.085%, and more specifically, to 0.065% to 0.075%.
  • Mn is a useful element improving strength through solid solution strengthening and increasing hardenability to generate low temperature transformation ferrite.
  • Mn since Mn may generate low temperature transformation ferrite even at a relatively low cooling rate due to improved hardenability, Mn is a main element used to secure strength of a central portion of a thick steel plate.
  • Mn may be added in an amount of 1,61% or greater.
  • the Mn content is limited to 1.61% to 2.0%. In detail, the Mn content may be limited to 1.7% to 1.9%.
  • Ni is a significant element used in improving impact toughness by facilitating a dislocation cross slip at a relatively low temperature and increasing strength by improving hardenability.
  • Ni may be added in an amount of 0.8% or greater.
  • hardenability may be excessively increased to generate low temperature transformation ferrite, thereby degrading toughness, and manufacturing costs may be increased due to a relatively high cost of Ni, as compared with other hardenability elements.
  • an upper limit value of the Ni content is limited to 0.8%.
  • the Ni content may be limited to 0.37% to 0.71%, and more specifically, to 0.4% to 0.6%.
  • Nb is educed to have a form of NbC or NbCN to improve strength of a base material.
  • Nb solidified when being reheated at a relatively high temperature is significantly finely educed to have the form of NbC during rolling to suppress recrystallization of austenite, thereby having an effect of refining a structure.
  • Nb is added in an amount of 0.005% or greater.
  • an upper limit value of an Nb content is limited to 0.04%.
  • the Nb content may be limited to 0.012% to 0.031%, and more specifically, to 0.017% to 0.03%.
  • Ti is a component educed to be TiN when being reheated and inhibiting growth of the base material and a grain in the HAZ to greatly improve low temperature toughness. In order to obtain an effect of addition, Ti is added in an amount of 0.005% or greater.
  • a Ti content is limited to 0.005% to 0.04%.
  • the Ti content may be limited to 0.012% to 0.023%, and more specifically, to 0.014% to 0.018%.
  • Si is a substitutional element improving strength of the steel material through solid solution strengthening and having a strong deoxidation effect, so that Si may be an element essential in manufacturing clean steel.
  • Si is added in an amount of 0.05% or greater.
  • a coarse martensite-austenite phase may be formed to degrade brittle crack arrestability and welding zone brittle crack initiation resistance.
  • an upper limit value of a Si content is limited to 0.3%.
  • the Si content may be limited to 0.1% to 0.27%, and more specifically, to 0.19% to 0.25%.
  • Cu is a main element used in improving hardenability and causing solid solution strengthening to enhance strength of the steel material.
  • Cu is a main element used in increasing yield strength through the generation of an epsilon Cu precipitate when tempering is applied.
  • Cu is added in an amount of 0.1% or greater.
  • an upper limit value of a Cu content is limited to 0.5%.
  • the Cu content may be limited to 0.15% to 0.31%, and more specifically, to 0.2% to 0.3%.
  • Contents of Cu and Ni may be set such that the weight ratio of Cu to Ni may be 0.8 or less, and in more detail, 0.6 or less. More specifically, the weight ratio of Cu to Ni may be limited to 0.5 or less.
  • Al is a component functioning as a deoxidizer.
  • an inclusion may be formed to degrade toughness.
  • an Al content is limited to 0.005% to 0.05%.
  • P and S are elements causing brittleness in a grain boundary or forming a coarse inclusion to cause brittleness.
  • a P content is limited to 100 ppm or less, while an S content is limited to 40 ppm or less.
  • a residual component of an exemplary embodiment is Fe.
  • a microstructure of a central portion includes, by area%, acicular ferrite in an amount of 70% or greater, pearlite in an amount of 10% or less, and one or more selected from a group consisting of ferrite, bainite, and martensite-austenite (MA), as residual components; a circle-equivalent diameter of pearlite being 15 ⁇ m or less; a surface portion microstructure in a region at a depth of 2 mm or less, directly below a surface, includes, by area%, ferrite in an amount of 30% or greater and one or more of bainite, martensite, and pearlite as residual components; and a heat affected zone (HAZ) formed during welding includes, by area%, martensite-austenite (MA) in an amount of 5% or less.
  • MA martensite-austenite
  • Ferrite refers to polygonal ferrite
  • bainite refers to granular bainite and upper bainite.
  • the fraction of acicular ferrite may be 75% or greater, and more specifically, may be limited to 80% or greater.
  • a microcrack may be generated in a front end of a crack during brittle crack propagation, thereby degrading brittle crack arrestability.
  • the fraction of pearlite in the central portion may be 10% or less.
  • the fraction of pearlite may be limited to 8% or less, and more specifically, to 5% or less.
  • the circle-equivalent diameter of pearlite in the central portion exceeds 15 ⁇ m, there is a problem in which a crack may be easily generated despite a relatively low fraction of pearlite being present in the central portion.
  • the circle-equivalent diameter of pearlite in the central portion is 15 ⁇ m or less.
  • the surface portion microstructure in the region at a depth of 2 mm or less, directly below the surface includes ferrite in an amount of 30% or greater, crack propagation may be effectively prevented on the surface at a time of brittle crack propagation, thereby improving brittle crack arrestability.
  • the fraction of ferrite may be limited to 40% or greater, and more specifically, to 50% or greater.
  • the fraction of martensite-austenite in the HAZ may be 5% or less.
  • Welding heat input during welding may be 0.5 kJ/mm to 10 kJ/mm.
  • a welding method during welding is not specifically limited and may include, for example, flux cored arc welding (FCAW), submerged arc welding (SAW), and the like.
  • FCAW flux cored arc welding
  • SAW submerged arc welding
  • the steel material may have yield strength of 390 MPa or greater.
  • the steel material may have a Charpy fracture transition temperature of -40°C or lower in a 1/2t position in a steel material thickness direction, where t is a steel sheet thickness.
  • the steel material have a thickness of 50 mm or greater, in detail, a thickness of 60 mm to 100 mm, and more specifically, 80 mm to 100 mm.
  • the method of manufacturing a high-strength steel material having excellent brittle crack arrestability and welding zone brittle crack initiation resistance comprises rough rolling a slab at a temperature of 900°C to 1100°C after reheating the slab at 1000°C to 1100°C, including, by wt%, C: 0.05% to 0.09%, Mn: 1.61% to 2.0%, Ni: 0.3% to 0.8%, Nb: 0.005% to 0.04%, Ti: 0.005% to 0.04%, Cu: 0.1% to 0.5%, Si: 0.1% to 0.3%, Al: 0.005% to 0.05%, P: 100 ppm or less, S: 40 ppm or less, Fe as a residual component thereof, and inevitable impurities; obtaining a steel sheet by finish rolling a bar obtained from the rough rolling a slab, at a temperature in a range of Ar 3 + 60°C to Ar 3 °C, based on a temperature of a central portion; and cooling the steel sheet to 700°
  • a slab is reheated before rough rolling.
  • a reheating temperature of the slab may be 1000°C or higher so that a carbonitride of Ti and/or Nb, formed during casting, may be solidified.
  • an upper limit value of the reheating temperature may be 1100°C.
  • a reheated slab is rough rolled.
  • a rough rolling temperature may be a temperature Tnr at which recrystallization of austenite is halted, or higher. Due to rolling, a cast structure, such as a dendrite formed during casting, may be destroyed, and an effect of reducing a size of austenite may also be obtained. In order to obtain the effect, the rough rolling temperature is limited to 900°C to 1100°C.
  • the rough rolling temperature may be 950°C to 1050°C.
  • a reduction ratio per pass of three final passes during rough rolling is 5% or greater, and a total cumulative reduction ratio is 40% or greater.
  • the reduction ratio per pass of the three final passes is limited to 5% or greater.
  • the reduction ratio per pass may be 7% to 20%.
  • the total cumulative reduction ratio during rough rolling is set to be 40% or greater.
  • the total cumulative reduction ratio may be 45% or greater.
  • a strain rate of the three final passes during rough rolling is 2/sec or lower.
  • the strain rate is limited to 2/sec or lower, thereby refining the grain size of the central portion.
  • generation of acicular ferrite may be facilitated.
  • a rough rolled bar may be finish rolled at a temperature of Ar 3 (a ferrite transformation initiation temperature) + 60°C to Ar 3 °C to obtain a steel sheet so that a further refined microstructure may be obtained.
  • Ar 3 a ferrite transformation initiation temperature
  • a relatively large amount of strain bands may be generated in austenite to secure a relatively large number of ferrite nucleation sites, thereby obtaining an effect of securing a fine structure in the central portion of a steel material.
  • a cumulative reduction ratio during finish rolling is maintained to be 40% or greater.
  • the reduction ratio per pass, not including skin pass rolling, is maintained to be 4% or greater.
  • the cumulative reduction ratio may be 40% to 80%.
  • the reduction ratio per pass may be 4.5% or greater.
  • finish rolling temperature is reduced to Ar 3 or lower
  • coarse ferrite is generated before rolling and is elongated during rolling, thereby reducing impact toughness.
  • finish rolling is performed at a temperature of Ar 3 + 60°C or higher
  • the grain size is not effectively refined, so that the finish rolling temperature during finish rolling is set to be a temperature of Ar 3 + 60 °C to Ar 3 °C.
  • a reduction ratio in an unrecrystallized region may be limited to 40% to 80% during finish rolling.
  • the grain size of the central portion of the bar in a thickness direction after rough rolling before finish rolling may be 150 ⁇ m or less, in detail, 100 ⁇ m or less, and more specifically, 80 ⁇ m or less.
  • the grain size of the central portion of the bar in a thickness direction after rough rolling before finish rolling may be controlled depending on a rough rolling condition, or the like.
  • the reduction ratio during finish rolling is set such that a ratio of a slab thickness (mm) to a steel sheet thickness (mm) after finish rolling may be 3.5 or greater, and in detail, 4 or greater.
  • an advantage of improving toughness of the central portion may be added by increasing yield strength/tensile strength, improving low temperature toughness, and decreasing the grain size of the central portion in the thickness direction through refinement of the final microstructure.
  • the steel sheet may have a thickness of 50 mm or greater, in detail, 60 mm to 100 mm, and more specifically, 80 mm to 100 mm.
  • the steel sheet is cooled to a temperature of 700°C, or lower, after finish rolling.
  • a microstructure may not be properly formed, so that sufficient yield strength may be difficult to secure. For example, yield strength of 390 MPa or greater may be difficult to secure.
  • the cooling end temperature may be 300°C to 600°C.
  • the steel sheet is cooled at a cooling rate of the central portion of 1.5°C/s or higher.
  • the cooling rate of the central portion of the steel sheet is lower than 1.5°C/s, the microstructure may not be properly formed, so that it may be difficult to secure sufficient yield strength. For example, yield strength of 390 MPa or greater may be difficult.
  • the steel sheet may be cooled at an average cooling rate of 2°C/s to 300°C/s.
  • a thickness of a bar having been rough rolled was 200 mm, while a grain size of a central portion after rough rolling before finish rolling, as illustrated in Table 2, was 75 ⁇ m to 89 ⁇ m.
  • a reduction ratio of three final passes during rough rolling was within a range of 7.2% to 14.3%.
  • a strain rate during rolling was within a range of 1.29/s to 1.66/s.
  • finish rolling was performed at a temperature equal to a difference between a finish rolling temperature and an Ar3 temperature, illustrated in Table 2 below to obtain a steel sheet having a thickness illustrated in Table 3 below, and then the steel sheet was cooled to a temperature of 412°C to 496°C at a cooling rate of 4.5°C/sec.
  • the Kca value in Table 4 is a value derived by performing an ESSO test on the steel sheet.
  • FCAW 0.7 kJ/mm
  • a C content had a value higher than an upper limit value of a C content of an exemplary embodiment. It can be confirmed that a relatively large amount of bainite was generated in the central portion during rough rolling, so an AF fraction of a final microstructure is less than 50%. Therefore, the Kca value measured at a temperature of -10° C was 6000 or less. It can be confirmed that a relatively large amount of a martensite-austenite (MA) structure was also generated in the HAZ, so the CTOD value was 0.25 mm or less.
  • MA martensite-austenite
  • a Si content had a value higher than an upper limit value of a Si content of an exemplary embodiment. It can be confirmed that a relatively large amount of Si was added to generate a relatively large amount of a coarse MA structure, so the microstructure in the central portion contains a relatively large amount of AF. However, the Kca value has a relatively low value similar to 6000 at a temperature of -10°C. It can be confirmed that a relatively large amount of MA is also generated in the HAZ, so the CTOD value is 0.25 mm or less.
  • a Mn content has a value higher than an upper limit value of a Mn content of an exemplary embodiment. It can be confirmed that due to having a relatively high level of hardenability, a microstructure in a base material is provided as upper bainite, thereby allowing the fraction of AF to be less than 50%. Thus, the Kca value is 6000 or less at a temperature of -10°C.
  • an Ni content had a value higher than an upper limit value of an Ni content of an exemplary embodiment. It can be confirmed that due to a relatively high level of hardenability, the microstructure of the base material is provided as granular bainite and upper bainite, and the fraction of acicular ferrite is less than 50%. Thus, the Kca value is 6000 or less at a temperature of -10°C.
  • an Nb and Ti content has a value higher than an upper limit value of an Nb and Ti content of an exemplary embodiment. It can be confirmed that an entirety of other conditions satisfies a condition suggested in an exemplary embodiment, but due to a relatively high Nb and Ti content, a relatively large amount of the MA structure is generated in the HAZ, thereby allowing the CTOD value to be 0.25 mm or less.
  • Inventive Example 7 includes a component exceeding a ratio of Cu to Ni suggested in an aspect of the present disclosure. It can be confirmed that despite having other, significantly excellent physical properties, a star crack was generated, thereby causing a defect in surface quality.
  • a C and Mn content has a value lower than a lower limit value of a C and Mn content of an exemplary embodiment. It can be confirmed that due to a relatively low level of hardenability, AF in the central portion is formed in an amount of less than 50%, and most structures have ferrite and a pearlite structure in an amount of 10% or greater. As pearlite has an average grain size of 15 ⁇ m or greater, the Kca value is 6000 or less at a temperature of -10°C.
  • the fraction of AF of the microstructure in the central portion is 70% or greater
  • the fraction of pearlite in the central portion is 10% or less
  • a circle-equivalent diameter of pearlite in the central portion is 15 ⁇ m or less
  • a fraction of MA phase in the HAZ is less than 5%.
  • FIG. 1 illustrates an image of a central portion of Inventive Steel 2 in a thickness direction, captured using an optical microscope. As illustrated in FIG. 1 , it can be confirmed that a microstructure in the central portion includes a relatively large amount of acicular ferrite (AF) structures, and pearlite is finely distributed.
  • AF acicular ferrite

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EP16871086.1A 2015-12-04 2016-12-02 High-strength steel having excellent brittle crack arrestability and welding part brittle crack initiation resistance, and production method therefor Active EP3385402B1 (en)

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KR1020150172687A KR101736611B1 (ko) 2015-12-04 2015-12-04 취성균열전파 저항성 및 용접부 취성균열개시 저항성이 우수한 고강도 강재 및 그 제조방법
PCT/KR2016/014124 WO2017095190A1 (ko) 2015-12-04 2016-12-02 취성균열전파 저항성 및 용접부 취성균열개시 저항성이 우수한 고강도 강재 및 그 제조방법

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JP6648271B2 (ja) 2020-02-14
CN108291287A (zh) 2018-07-17
KR101736611B1 (ko) 2017-05-17
EP3385402A1 (en) 2018-10-10
WO2017095190A1 (ko) 2017-06-08
US20180363107A1 (en) 2018-12-20
EP3385402A4 (en) 2018-10-10
CN108291287B (zh) 2020-03-03

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