EP3561115A1 - Dickwandige stahlplatte mit hervorragender tieftemperatur-schlagzähigkeit und ctod-eigenschaft und herstellungsverfahren dafür - Google Patents

Dickwandige stahlplatte mit hervorragender tieftemperatur-schlagzähigkeit und ctod-eigenschaft und herstellungsverfahren dafür Download PDF

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EP3561115A1
EP3561115A1 EP17885144.0A EP17885144A EP3561115A1 EP 3561115 A1 EP3561115 A1 EP 3561115A1 EP 17885144 A EP17885144 A EP 17885144A EP 3561115 A1 EP3561115 A1 EP 3561115A1
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Prior art keywords
steel sheet
thick steel
impact toughness
equation
ctod
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French (fr)
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EP3561115A4 (de
EP3561115B1 (de
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Woo-Gyeom KIM
Kyung-Keun Um
Ki-Hyun Bang
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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
    • 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
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present disclosure relates to a thick steel sheet having excellent low temperature impact toughness and CTOD properties which may be preferably applied to an offshore structural steel material, and a method of manufacturing the same.
  • the North Pole has been considered as a land storing future energy sources, and the development of petroleum and gas sources have been conducted, centering on countries neighboring the Arctic Circle.
  • the development of energy sources in the Arctic will be accelerated due to the exhaustion of energy source of land, offshore regions, and deep sea regions.
  • a steel material applied to offshore structure facilities for mining, drilling, storing energy sources developed in the polar regions may need to have toughness at a low temperature of -60°C or lower, and may need to have a CTOD value representing fatigue fracture properties at -60°C. Also, strength and thickness of a steel material have been increased as the sizes of facilities have increased and facilities have been integrated.
  • brittleness cracks As for resistance against brittleness fracture, generally, there may be resistance against the formation of brittleness cracks and resistance against the propagation of brittleness cracks.
  • the formation of brittleness cracks may refer to, after fatigue cracks started in a defect portion in a structure is grown to a certain size, the generation of brittleness cracks from the grown fatigue cracks when high external stress is applied.
  • the resistance properties of the material which may prevent the formation of brittleness cracks may be referred to as resistance against the formation of brittleness cracks, and the resistance is tested using a CTOD (crack tip opening displacement) testing method prescribed in BS 7448 standard or ASTM 1290 standard.
  • CTOD crack tip opening displacement
  • reference 1 discloses a method of manufacturing a steel sheet to maintain excellent CTOD properties by maintaining a certain level of reduction ratios of final three passes during rolling the steel sheet including a rolling process in which a reduction ratio is low, such as a width widening rolling.
  • reference 1 has a problem in which it may be difficult to sufficient low temperature toughness and CTOD properties.
  • An aspect of the present disclosure is to provide a thick steel sheet having excellent low temperature impact toughness and CTOD properties which may be preferably applied to an offshore structural steel material, and a method of manufacturing the same.
  • An aspect of the present disclosure relates to a thick steel sheet having excellent low temperature impact toughness and CTOD properties comprising, by weight%, 0.02 to 0.06% of C, 0.005 to 0.08% of Si, 1.0 to 2.0% of Mn, 0.01% or less of P, 0.003% or less of S, 0.001 to 0.01% of Al, 0.5 to 2.0% of Ni, 0.001 to 0.02% of Ti, 0.005 to 0.03% of Nb, 0.05 to 0.4% of Cu, 0.002 to 0.006% of N, and a balance of Fe and inevitable impurities, the thick steel sheet satisfies Equation 1 and Equation 2 below, and a microstructure comprises ferrite of 95 area% or higher, and a sum of MA and cementite of 2 area% or lower.
  • An aspect of the present disclosure relates to a method of manufacturing a thick steel sheet having excellent low temperature impact toughness and CTOD properties, the method comprising heating a slab at 1020 to 1150°C, the slab comprising, by weight%, 0.02 to 0.06% of C, 0.005 to 0.08% of Si, 1.0 to 2.0% of Mn, 0.01% or less of P, 0.003% or less of S, 0.001 to 0.01% of Al, 0.5 to 2.0% of Ni, 0.001 to 0.02% of Ti, 0.005 to 0.03% of Nb, 0.05 to 0.4% of Cu, 0.002 to 0.006% of N, and a balance of Fe and inevitable impurities, and satisfying Equation 1 and Equation 2 below; recrystallization-region rolling the heated slab at 900°C or higher; obtaining a thick steel sheet by performing a non-recrystallization-region rolling process for a finish rolling temperature to be Ar3 to 850°C after the recrystallization-region rolling; cooling the thickness steel sheet to 250°
  • excellent yield strength may be secured with respect to a thick steel sheet having a thickness of 50mm or greater, excellent impact toughness may be secured even at an extremely low temperature of about -80°C, and a thick steel sheet having impact toughness and CTOD properties at -60°C and a method of manufacturing the same may be provided, which are effects of the present disclosure.
  • a thick steel sheet having excellent low temperature impact toughness and CTOD properties may include, by weight%, 0.02 to 0.06% of C, 0.005 to 0.08% of Si, 1.0 to 2.0% of Mn, 0.01% or less of P, 0.003% or less of S, 0.001 to 0.01% of Al, 0.5 to 2.0% of Ni, 0.001 to 0.02% of Ti, 0.005 to 0.03% of Nb, 0.05 to 0.4% of Cu, 0.002 to 0.006% of N, and a balance of Fe and inevitable impurities, and may satisfy Equation 1 and Equation 2 below, and a microstructure may include ferrite of 95 area% or higher, and a sum of MA and cementite of 2 area% or lower. 3.0 ⁇ Mn + 2 ⁇ Ni ⁇ 4.3 0.05 ⁇ C + Si + 10 ⁇ Al ⁇ 0.25 (in Equation 1 and Equation 2, each element symbol indicates a content of each element by weight%).
  • a unit of a content of each element may be wt% unless otherwise indicated.
  • C is an element which may be effective for strengthening solid solution, and may improve strength by forming Nb, and the like, and carbide.
  • a content of C When a content of C is lower than 0.02%, the above-described effect may be insufficient. When a content of C exceeds 0.06%, the formation of MA may be facilitated, and pearlite may be formed such that impact and fatigue properties at a low temperature may be deteriorated. Thus, a preferable content of C may be 0.02 to 0.06%.
  • a more preferable lower limit content of C may be 0.025%, and an even more preferable lower limit content of C may be 0.03%.
  • a more preferable upper limit content of C may be 0.055%, and an even more preferable upper limit content of C may be 0.05%.
  • Si is an element which may deoxidize molten steel auxiliary to Al, and may help improving yield strength and tensile strength, but may adversely affect impact and fatigue properties at a low temperature.
  • Si When a content of Si exceeds 0.08%, Si may interfere with dispersion of C such that the formation of MA may be facilitated, which may adversely affect impact and fatigue properties at a low temperature. Also, to control a content of Si to be 0.005% or less, a processing time of a steel making process may greatly increase, such that productivity may decrease. Thus, a preferable content of Si may be 0.005 to 0.08%.
  • a more preferable lower limit content of Si may be 0.01%, a more preferable upper limit content of Si may be 0.07%, and an even more preferable upper limit content of Si may be 0.055%.
  • Mn may have a great effect in increasing strength by strengthening solid solution, and thus, 1.0% or higher of Mn may be added.
  • a content of Mn is excessive, toughness may degrade due to the formation of an MnS inclusion, and the segregation of a central portion.
  • a preferable upper limit content of Mn may be 2.0%.
  • P is an element which may cause grain boundary segregation, and may thus be a cause of weakening steel.
  • a content of P may need to be controlled to be low as possible as P is one of impurities, and it may be preferable to control a content of P to be 0.01% or less. It may be substantially impossible to control a content of P to be 0%, and thus, 0% may not be included.
  • S may be a factor which may form an MnS inclusion by being combined with Mn, and the MnS inclusions may degrade low temperature toughness.
  • a content of S may need to be controlled to be low as possible as S is one of impurities. It may be preferable to control a content of S to be 0.003% or less to secure low temperature toughness and low temperature fatigue properties. It may be substantially impossible to control a content of S to be 0%, and thus, 0% may not be included.
  • Al is a main deoxidizer in the present disclosure, and it may be required to add 0.001% or higher of Al.
  • a content of Al exceeds 0.01%, Al may be a cause of gradation of low temperature toughness due to an increase of a fraction and a size of Al 2 O 3 inclusion.
  • Al similarly to Si, Al may facilitate the formation of an MA phase in a base material and a welding heat affected portion such that low temperature toughness and low temperature fatigue properties may degrade.
  • a preferable content of Al may be 0.001 to 0.01%.
  • Ni may not greatly improve strength, but Ni may improve strength and toughness at the same time.
  • Ni When a content of Ni is lower than 0.5%, the above-described effect may be insufficient. When a content of Ni exceeds 2.0%, Ni may facilitate the formation of MA due to an increase of hardenability such that impact and CTOD toughness may be deteriorated.
  • Ti is an element which may form a precipitation by being combined with oxygen or nitrogen, and may accordingly prevent a structure from being coarse, and may contribute to refinement and improvement of toughness.
  • Nb is an element which may prevent recrystallization during rolling or cooling by precipitating solute or carbonitride and may thus refine a structure and may increase strength.
  • Cu is an element which may not greatly degrade impact properties, and may improve strength by solid solution and precipitation.
  • N is an element which may refine an austenite structure during reheating by forming a precipitation along with Ti, Nb, Al, and the like, and may thus be helpful for improving strength and toughness. It may be preferable to add 0.002% or higher of N.
  • a content of N exceeds 0.006%, surface cracks may be created at a high temperature, and residual N which remains after a precipitation is formed may be present in an atomic state and may decrease toughness.
  • a preferable content of N may be 0.002 to 0.006%.
  • a remainder other than the above-described composition is Fe.
  • inevitable impurities may be inevitably added from raw materials or a surrounding environment, and thus, impurities may not be excluded.
  • a person skilled in the art may be aware of the impurities, and thus, the descriptions of the impurities may not be provided in the present disclosure.
  • An alloy composition of the present disclosure may need to satisfy the above-described element contents, and may also satisfy Equation 1 and Equation 2 below. 3.0 ⁇ Mn + 2 ⁇ Ni ⁇ 4.3 0.05 ⁇ C + Si + 10 ⁇ Al ⁇ 0.25 (in Equation 1 and Equation 2, each element symbol indicates a content of each element by weight%).
  • Equation 1 and Equation 2 may be to secure excellent low temperature impact toughness and CTOD properties without degradation of strength, and may be designed in consideration of correlation affecting an MA preventing effect and strength.
  • contents of C, Si, and Al may be controlled, and to compensate for degradation of strength caused by the control of contents of the elements, Mn and Ni may need to be added in accordance with Equation 1.
  • Equation 1 When a value of Equation 1 is lower than 3.0, an effect of improving strength may be insufficient. When the value exceeds 4.3, low temperature impact toughness and CTOD properties may degrade.
  • a preferable value of Equation 2 may be 0.05 or higher for steel making processes such as deoxidation, and the like.
  • a value of Equation 2 is lower than 0.05, it may be difficult to secure strength.
  • the value exceeds 0.25 a large amount of MA phase may be formed such that low temperature impact toughness and CTOD properties may degrade.
  • the alloy composition of the present disclosure may further include one or more of 0.001 to 0.05% of Mo and 0.0002 to 0.005% of Ca by weight%.
  • Mo is an element which may be effective for improving strength by increasing hardenability.
  • a preferable content of Mo may be 0.001% or higher.
  • toughness may degrade due to an increase of hardenability, and toughness may degrade by the formation of a precipitation of molybdenum carbide.
  • the Al-deoxidized Ca may be combined with S, mainly present as MnS, such that the formation of MnS may be prevented, and spheroidal CaS may be formed such that there may be an effect of preventing cracks in a central portion of a steel material.
  • S mainly present as MnS
  • spheroidal CaS may be formed such that there may be an effect of preventing cracks in a central portion of a steel material.
  • a content of Ca exceeds 0.005%, residual Ca may be combined with O and a coarse oxidated inclusion may be formed, which may work as a crack initiation point at a low temperature due to elongation and breakage of the inclusion during a rolling process.
  • a microstructure of a thick steel sheet of the present disclosure will be described in detail.
  • a microstructure of the thick steel sheet may include ferrite of 95 area% or higher, and a sum of MA and cementite of 2 area% or lower.
  • a structure of a base material and a fraction of MA may be important.
  • hardenability may increase, and C may be transformed to martensite having high hardenability or may remain as austenite, which may be referred to as martensite-austenite (MA).
  • MA may be vulnerable to fracture due to properties of high hardness, and may cause stress to be concentrated when soft ferrite around MA is transformed, and may accordingly work as initiation of fracture.
  • cementite may have a characteristic similar to that of MA, and may be a hard phase having hardenability higher than that of base material acicular ferrite, and cementite may deteriorate low temperature impact toughness and CTOD properties.
  • a sum of MA and cementite may be 2 area% or lower.
  • Ferrite has a grain size of 20 ⁇ m or less measured in equivalent circle diameter.
  • the grain size exceeds 20 ⁇ m, dislocation in ferrite may increase such that fracture propagation may easily occur such that low temperature impact toughness and CTOD properties may be deteriorated.
  • the smaller the grain size it may be more advantageous to securing low temperature impact toughness and CTOD properties, and thus, a lower limit content of ferrite may not be particularly limited.
  • Ferrite may also include polygonal ferrite and acicular ferrite, and specific fractions thereof may not be limited.
  • the thick steel sheet may have yield strength of 420MPa or higher, impact toughness of 200J or higher at -80°C, and a CTOD of 0.5mm or higher at -60°C. By securing such properties, the thick steel sheet may be appropriately applied to an offshore structural steel material used in an extremely low temperature environment. More preferably, a CTOD may be 1.0mm or higher at -60°C.
  • the thick steel sheet may have tensile strength of 500MPa or higher, an elongation rate of 25% or higher, and impact toughness of 400J or higher at -60°C.
  • the thickness steel sheet may have a thickness of 50 to 100mm.
  • the method of manufacturing a thick steel sheet having excellent low temperature impact toughness and CTOD properties may include heating a slab comprising the above-described alloy composition at 1020 to 1150°C; recrystallization-region rolling the heated slab at 900°C or higher; obtaining a thick steel sheet by performing a non-recrystallization-region rolling process for a finish rolling temperature to be Ar3 to 850°C after the recrystallization-region rolling; cooling the thickness steel sheet to 250°C or lower at a cooling speed of 2 to 15°C/sec; and tempering the cooled thick steel sheet at 500 to 650°C.
  • the slab satisfying the above-described alloy composition may be heated at 1020 to 1150°C.
  • the heated slab may be recrystallization-region rolled at 900°C or higher. When the temperature is lower than 900°C, it may be difficult to implement sufficient recrystallization of austenite.
  • the recrystallization-region rolling is performed at each of the reduction ratios of the final two passes to be within 15 to 20%, which may be to secure a uniform and fine final microstructure.
  • a thick steel sheet may be obtained by performing a non-recrystallization-region rolling for a finish rolling temperature to be Ar3 to 850°C after the recrystallization-region rolling.
  • a temperature of a surface of the thick steel sheet may be that of a two-phase region, and a two phase structure may be formed at a thickness of surface to 1/4t such that impact toughness may be deteriorated.
  • the finish rolling temperature exceeds 850°C, grain refinement may be insufficient such that strength and toughness may be deteriorated.
  • the non-recrystallization-region rolling may be performed for a thickness of the thick steel sheet to be 50 to 100mm.
  • the thick steel sheet may be cooled to 250°C or lower at a cooling speed of 2 to 15°C/sec.
  • cooling speed exceeds 15°C/sec, there may be a difference in properties due to a difference in cooling speed between a surface and a central portion of the thick steel sheet.
  • cooling speed is lower than 2°C/sec, distribution of acicular ferrite may decrease, and distribution of polygonal ferrite may increase.
  • the cooled thick steel sheet may be tempered at 500 to 650°C. Dislocation in an MA phase and ferrite may be factors which may greatly affect low temperature impact toughness and CTOD properties. Thus, the tempering may be performed to dissolve an MA phase and to decrease dislocation in ferrite.
  • the tempering temperature is lower than 500°C, the above-described effect may be insufficient.
  • carbide may be formed, which may degrade toughness.
  • Molten steel having a composition indicated in Table 1 below was prepared, and a slab was manufactured using a continuous casting process.
  • the slab was heated, recrystallization-region rolled, non-recrystallization-region roll, and cooled and tempered under manufacturing conditions as in Table 2 below, and a thick steel sheet having a thickness of 80mm was manufactured.
  • the recrystallization-region rolling was performed for each of reduction ratios of final two passes to be 18%.
  • a microstructure, mechanical properties, low temperature impact toughness and CTOD properties of the thick steel sheet were measured and listed in Table 3 below.
  • the microstructure was observed using a scanning electron microscope (SEM) and a transmission electron microscope (TEM), and a sum (a secondary phase) of MA and cementite was analyzed and listed in Table 3.
  • SEM scanning electron microscope
  • TEM transmission electron microscope
  • a portion other than the secondary phase was ferrite including polygonal ferrite and acicular ferrite.
  • Yield strength, tensile strength, and an elongation rate were measured through a tensile test.
  • Low temperature impact toughness was measured through a charpy impact test at -80°C and -60°C.
  • CTOD properties a sample was processed to have a size of 60mm ⁇ 120mm ⁇ 300mm in perpendicular to a rolling direction in accordance with BS 7448 standards, fatigue cracks were inserted such that a fatigue crack length became 50% of a sample width, and a CTOD test was carried out at -60°C.
  • the CTOD test was performed three times for each steel sheet, and a minimum value among the test values obtained from the three times of tests was listed in Table 3.
  • Equation 1 is a value of Mn+2Ni
  • Equation 2 is value of C+Si+10Al
  • each element symbol indicates a content of each element by weight %.
  • Equation 2 Classification Steel Type Slab Heating Temperature (°C) Recrystal lization-Region rolling Terminating Temperature (°C) Non-Recryst allization-Region Rolling Terminating Temperature (°C) Cooling Terminating Temperature (°C) Cooling Speed (°C/s) Tempering Temperature (°C)
  • Inventive example 1 A 1105 1021 775 224 3.4 552
  • Inventive example 4 D 1110 1023 781 213 2.6 550
  • Comparative example 1 A 1121 1022 875 229 3.1 551 Comparative example 2 B 1105 1032 780 195 3.0 Not Conducted Comparative example 3 C
  • Inventive examples which satisfied the overall alloy composition and the manufacturing conditions suggested in the present disclosure secured yield strength of 420MPa or higher, impact toughness of 200J or higher at -80°C, and a CTOD value of 0.5mm or higher at -60°C, which indicate that low temperature impact toughness and CTOD properties were excellent.
  • FIG. 1 is an image of a microstructure of inventive example 1. A small amount of MA and cementite were formed, and a grain size was also fine.
  • Comparative examples 1 to 3 satisfied the alloy composition suggested in the present disclosure, but did not satisfy the manufacturing conditions.
  • Comparative examples 4 to 7 satisfied the manufacturing conditions suggested in the present disclosure, but did not satisfy the alloy composition.
  • FIG. 2 is graphs illustrating yield strength in accordance with an Mn+2Ni value and a CTOD value at -60°C.
  • Mn+2Ni value is lower than 3.0, strength decreased.
  • CTOD value at -60°C greatly decreased.

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP17885144.0A 2016-12-23 2017-12-22 Dickwandige stahlplatte mit hervorragender tieftemperatur-schlagzähigkeit und ctod-eigenschaft und herstellungsverfahren dafür Active EP3561115B1 (de)

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PCT/KR2017/015320 WO2018117727A1 (ko) 2016-12-23 2017-12-22 저온 충격인성 및 ctod 특성이 우수한 후강판 및 그 제조방법

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JP4313730B2 (ja) * 2004-06-21 2009-08-12 株式会社神戸製鋼所 材質異方性が少なく低温靭性に優れた高張力鋼板
KR100851189B1 (ko) * 2006-11-02 2008-08-08 주식회사 포스코 저온인성이 우수한 초고강도 라인파이프용 강판 및 그제조방법
US8647564B2 (en) * 2007-12-04 2014-02-11 Posco High-strength steel sheet with excellent low temperature toughness and manufacturing thereof
KR100957968B1 (ko) * 2007-12-27 2010-05-17 주식회사 포스코 모재 ｃｔｏｄ특성이 우수한 고강도 고인성 후강판 및 그제조방법
KR20100066757A (ko) 2008-12-10 2010-06-18 주식회사 포스코 Ｃｔｏｄ 특성이 우수한 강판의 제조방법
TWI365915B (en) * 2009-05-21 2012-06-11 Nippon Steel Corp Steel for welded structure and producing method thereof
JP5459166B2 (ja) * 2010-09-28 2014-04-02 新日鐵住金株式会社 氷海構造物用鋼板
JP5177310B2 (ja) * 2011-02-15 2013-04-03 Ｊｆｅスチール株式会社 溶接熱影響部の低温靭性に優れた高張力鋼板およびその製造方法
KR20120097162A (ko) * 2011-02-24 2012-09-03 현대제철 주식회사 후강판 및 그 제조 방법
JP5304924B2 (ja) * 2011-12-27 2013-10-02 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
KR101403224B1 (ko) * 2011-12-28 2014-06-02 주식회사 포스코 저항복비 특성 및 저온인성이 우수한 후 강판 및 그 제조방법
JP5811032B2 (ja) * 2012-05-23 2015-11-11 新日鐵住金株式会社 Ｌｐｇタンク用鋼板
JP5618036B1 (ja) * 2013-03-12 2014-11-05 Ｊｆｅスチール株式会社 多層溶接継手ｃｔｏｄ特性に優れた厚鋼板およびその製造方法
CN103741027B (zh) * 2013-12-29 2015-10-28 首钢总公司 焊接接头ctod大于零点5毫米海洋工程钢及制备方法

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JP6824415B2 (ja) 2021-02-03
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JP2020509206A (ja) 2020-03-26
WO2018117727A1 (ko) 2018-06-28
CN110100026A (zh) 2019-08-06
CN110100026B (zh) 2021-10-08
EP3561115B1 (de) 2022-07-13

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