WO2016105003A1 - Acier de structure ultra épais présentant une excellente résistance à la propagation de fissures fragiles et son procédé de production - Google Patents

Acier de structure ultra épais présentant une excellente résistance à la propagation de fissures fragiles et son procédé de production Download PDF

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Publication number
WO2016105003A1
WO2016105003A1 PCT/KR2015/013557 KR2015013557W WO2016105003A1 WO 2016105003 A1 WO2016105003 A1 WO 2016105003A1 KR 2015013557 W KR2015013557 W KR 2015013557W WO 2016105003 A1 WO2016105003 A1 WO 2016105003A1
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Prior art keywords
crack propagation
slab
bar
brittle crack
temperature
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Ceased
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PCT/KR2015/013557
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English (en)
Korean (ko)
Inventor
이학철
장성호
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Posco Holdings Inc
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Posco Co Ltd
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Priority to US15/535,570 priority Critical patent/US20170342518A1/en
Priority to EP15873530.8A priority patent/EP3239329B8/fr
Priority to CN201580070961.2A priority patent/CN107109591A/zh
Priority to JP2017532807A priority patent/JP6475839B2/ja
Publication of WO2016105003A1 publication Critical patent/WO2016105003A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving particular fabrication steps or treatments of ingots or slabs
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • 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
    • C22C38/08—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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a structural ultra-thick steel and excellent manufacturing method having excellent brittle crack propagation resistance.
  • the structure of the structure can be reduced in weight and economical benefits can be obtained, and the thickness of the steel sheet can be reduced, thereby ensuring ease of machining and welding operations.
  • the core structure becomes coarse because sufficient deformation is not made in the center due to a decrease in the total reduction ratio during the manufacture of the ultra-thick material, and thus the hardenability is increased to generate a low temperature transformation phase such as bainite.
  • Patent Document 1 Korean Unexamined Patent Publication No. 2009-0069818
  • Patent Document 2 Korean Unexamined Patent Publication No. 2002-0091844
  • C 0.02 to 0.10%
  • Mn 0.8 to 2.5%
  • Ni 0.05 to 1.5%
  • Nb 0.005 to 0.1%
  • Ti 0.005 to 0.1%
  • balance Fe and One containing other unavoidable impurities and one selected from the group consisting of ferrite single phase, bainite single phase, complex of ferrite and bainite, complex of ferrite and perlite, and complex of ferrite, bainite and perlite
  • a structural ultra thick steel having excellent brittle crack propagation resistance having a microstructure including a structure of is provided.
  • the steel may preferably have a particle size of 15 ⁇ m (micrometer) or less, having a high-angle boundary of 15 degrees or more, as measured by the EBSD method at the center of the plate thickness.
  • the steel may preferably have a yield strength of 350 MPa or more and a central impact transition temperature of ⁇ 60 ° C. or less.
  • C 0.02 to 0.1%, Mn: 0.8 to 2.5%, Ni: 0.05 to 1.5%, Nb: 0.005 to 0.10%, Ti: 0.005 to 0.1%, remaining Fe and other unavoidable impurities
  • a method for producing this excellent structural ultra thick steel is provided.
  • the total cumulative reduction rate is preferably 40% or more.
  • the steel sheet may be cooled at a central cooling rate of 2 ° C./s or more.
  • Cooling of the steel sheet can be carried out at an average cooling rate of 3 ⁇ 300 °C / s.
  • the inventors of the present invention solve the conventional problems and at the same time, as a result of research to secure the ultra-structure structural steel having a superior yield strength and impact transition temperature of the center compared to the conventional, as a result of the alloy design and microstructure of the ultra-structure structural steel By controlling appropriately, it is recognized that the brittle crack propagation resistance of the ultra-thick structural steel can be improved, and the present invention has been completed based on this.
  • the ultra-thick steel having excellent brittle crack propagation resistance is in weight%, C: 0.02 to 0.10%, Mn: 0.8 to 2.5%, Ni: 0.05 to 1.5%, Nb: 0.005 to 0.1%, and Ti: 0.005 to 0.1%, containing residual Fe and other unavoidable impurities, and ferrite single phase structure, bainite single phase structure, ferrite and bainite complex, ferrite and perlite complex, and ferrite, bainite and perlite It has a microstructure including one tissue selected from the group consisting of complex tissues.
  • Such ultra-thick steels may have a thickness of 10 to 100 mm, more preferably 50 to 100 mm.
  • C is the most important element for securing basic strength, it needs to be contained in steel within an appropriate range, and in order to obtain such an addition effect, it is preferable to add C 0.02% or more.
  • the content of C exceeds 0.10%, low-temperature toughness is lowered due to the generation of large amount of phase martensite and the high strength of the ferrite itself, so the content of C is preferably limited to 0.02 to 0.10%.
  • Mn is a useful element that enhances the strength by solid solution strengthening and improves the hardenability so that low-temperature transformation phases are produced.
  • Mn content exceeds 2.5%
  • the excessive increase in hardenability promotes the formation of upper bainite and martensite, thereby degrading impact toughness and brittle crack propagation resistance, so that the Mn content is 0.8. It is preferable to limit to 2.5%.
  • Ni is an important element that facilitates cross slip of dislocations at low temperature, and improves impact toughness and hardenability, thereby improving strength.
  • Ni is added at 0.05% or more to improve impact toughness and brittle crack propagation resistance. It is preferable. However, when the Ni is added at least 1.5%, the hardenability is excessively increased to form low-temperature transformation phase, which may lower toughness and increase manufacturing cost, so the upper limit of the Ni content is preferably limited to 1.5%.
  • Nb precipitates in the form of NbC or NbCN to improve the base material strength.
  • Nb dissolved in reheating at a high temperature precipitates very finely in the form of NbC during rolling, thereby suppressing recrystallization of austenite, thereby miniaturizing the structure.
  • Nb is preferably added at least 0.005%, but if excessively added, there is a possibility of causing brittle cracks at the corners of the steel, so the lower limit of the Nb content is preferably limited to 0.1%.
  • Ti is a component that precipitates with TiN upon reheating and inhibits the growth of crystal grains of the base metal and the weld heat affected zone to greatly improve low-temperature toughness. To obtain such an additive effect, Ti is preferably added at least 0.005%.
  • the Ti content is preferably limited to 0.005 to 0.1%.
  • the remaining component of the present invention is iron (Fe).
  • Steel of the present invention is a single structure selected from the group consisting of ferrite single phase structure, bainite single phase structure, ferrite and bainite complex structure, ferrite and perlite complex structure, and ferrite, bainite and perlite complex structure. It has a microstructure that contains.
  • the proportion of perlite is preferably limited to 30% by volume or less.
  • the ferrite is preferably acicular ferrite, and the bainite is preferably granular bainite.
  • the ferrite may use a polygonal ferrite if necessary.
  • the fraction of acicular ferrite or polygonal ferrite and granular bainite increases, thereby increasing the strength.
  • the steel may preferably have a particle size of 15 ⁇ m or less having a high-angle boundary of 15 degrees or more, measured by an EBSD method at the center of the plate thickness.
  • the steel may preferably have a yield strength of 350 MPa or more and a central impact transition temperature of ⁇ 60 ° C. or less.
  • a method for producing an extremely thick steel having excellent brittle crack propagation resistance is C: 0.02 to 0.1%, Mn: 0.8 to 2.5%, Ni: 0.05 to 1.5%, Nb: 0.005 to 0.10%, and Ti: 0.005 to Reheating the slab containing 0.1%, remaining Fe and other unavoidable impurities to 950-1100 ° C. and then roughly rolling at a temperature of 1100-900 ° C .; Finishing rolling the rough rolled bar at a temperature of Ar 3 or higher to obtain a steel sheet; And cooling the steel sheet to a temperature of 700 ° C. or less, such that the temperature difference between the central portion on the thickness of the slab or bar before rolling and the outer surface of the slab or bar is 100 ° C. or more during the rough rolling.
  • the slab reheating temperature is preferably at least 950 ° C, in order to solidify the carbonitrides of Ti and / or Nb formed during casting. Moreover, in order to fully solidify the carbonitride of Ti and / or Nb, it is more preferable to heat to 1000 degreeC or more. However, when reheating excessively high temperature, austenite may coarsen, so the upper limit of the reheating temperature is preferably 1100 ° C.
  • Rough rolling temperature 1100 to 900 ° C. and temperature difference between the center of the slab or bar thickness before rough rolling and the outer surface of the slab or bar: 100 ° C. or more
  • Crimp the reheated slab It is preferable to make rough rolling temperature more than the temperature (Tnr) at which recrystallization of austenite stops.
  • the casting structure such as the dendrite formed during casting, is destroyed by rolling, and the effect of reducing the size of austenite can also be obtained.
  • the rough rolling temperature is preferably limited to 1100 ⁇ 900 °C.
  • the temperature difference between the central portion on the thickness of the slab or bar immediately before rolling and the outer surface of the slab or bar is roughly 100 ° C or more during rough rolling.
  • This center-to-surface temperature difference can be obtained, for example, by cooling the heated slab or bar using a chiller.
  • the cooling device is not particularly limited, and for example, at least one of water, air, liquid coolant, and gaseous coolant may be used as the cooling medium.
  • the surface portion of the slab or bar maintains a lower temperature than the center, and rolling is performed in the state where such temperature difference exists.
  • the central mean particle size may be maintained at 15 ⁇ m or less.
  • This technology utilizes the phenomenon that more deformation occurs in the center of relatively low strength because the surface of the lower temperature has higher strength than the center of relatively high temperature, and in order to effectively give more deformation to the center, It is preferable that the temperature difference between surfaces is 100 degreeC or more, and more preferable temperature difference is 100-300 degreeC.
  • the temperature difference between the center on the thickness of the slab or the bar and the outer surface of the slab or bar is taken into consideration the surface temperature of the slab or bar measured immediately before rough rolling, the cooling conditions and the thickness of the slab or bar immediately before rough rolling. The difference in calculated core temperature.
  • the measurement of the surface temperature and the thickness of the slab is carried out before the first rough rolling, and the measurement of the surface temperature and the thickness of the bar is carried out from the two rough rolling before the rough rolling.
  • the temperature difference between the center of the thickness of the slab or the bar and the outer surface of the slab or the bar is measured by measuring the pass temperature difference between the rough rolling and calculating the average value of the whole. It means more than.
  • the total cumulative reduction rate during the rough rolling is preferably 40% or more.
  • the rough rolled bar is finish rolled over Ar3 to obtain a steel sheet.
  • the austenite structure becomes a deformed austenite structure.
  • Cooling after rolling Cooling below 700 °C
  • the steel sheet After finish rolling, the steel sheet is cooled to 700 ° C or lower.
  • the cooling end temperature exceeds 700 °C, the microstructure is not formed properly, there is a possibility that the yield strength is 350Mpa or less.
  • the cooling of the steel sheet can be performed at a central cooling rate of 2 ° C / s or more. If the central cooling rate of the steel sheet is less than 2 ° C / s, the microstructure is not formed properly, and the yield strength may be 350 Mpa or less. .
  • the steel sheet may be cooled at an average cooling rate of 3 to 300 ° C / s.
  • the difference between the center-surface average temperature at rough rolling in Table 2 represents the difference between the temperature of the slab or bar surface measured immediately before rough rolling, the number of sprayed bars and the thickness of the slab just before rough rolling, and the calculated central temperature. It is the result of calculating the average value of the whole by measuring the pass temperature difference of each rough rolling.
  • a finish rolling was performed at a finish rolling temperature of 780 ° C. to obtain a steel sheet having the thickness shown in Table 2, and then cooled to a temperature of 700 ° C. or less at a cooling rate of 5 ° C./sec.
  • microstructure, yield strength, central mean particle size, central impact transition temperature, and Kca value (brittle crack propagation resistance coefficient) of the steel sheets manufactured as described above were examined, and the results are shown in Table 2 below.
  • Kca value of Table 2 is the value evaluated by performing ESSO test on the steel sheet.
  • Comparative steels 3 and 5 have higher values than the upper limits of C and Mn proposed in the present invention, and upper bainite is produced despite the refinement of the core austenite grain size through cooling during rough rolling. Due to this, the final microstructures have a particle size of 32 and 38 ⁇ m or more, and the central impact transition temperature is -60 ° C. or more due to having the upper bainite easily formed as a known structure.
  • Kca value also has a value of 6000 or less at -10 °C.
  • Comparative steel 4 has a higher value than the upper limit of the Ni content presented in the present invention, and it can be seen that the microstructure of the base material is granular bainite and upper bainite due to the high hardenability.
  • the particle size of the central austenite was refined through cooling during rough rolling, the final microstructure had a particle size of 26 ⁇ m, and the upper bainite where brittleness was easily formed was known, resulting in a central impact transition temperature. It can be seen that more than -60 °C.
  • the Kca value also has a value of 6000 at -10 ° C.
  • the microstructure has a light structure or acicular ferrite single phase tissue, or a complex structure of acicular ferrite or polygonal ferrite and granular bainite, and a complex structure of acicular ferrite, pearlite and granular bainite.
  • the impact transition temperature of the center is -60 °C or less, and the Kca value satisfies the value of 6000 or more at -10 °C.
  • FIG. 1 shows a photograph of an observation of the center of thickness of the inventive steel 1 with an optical microscope, it can be seen that the invention has a fine central structure.

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  • Physics & Mathematics (AREA)
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  • Heat Treatment Of Steel (AREA)

Abstract

La présente invention porte sur un acier de structure ultra épais présentant une excellente résistance à la propagation de fissures fragiles et sur son procédé de production. La présente invention concerne : un acier de structure ultra épais, qui présente une excellente résistance à la propagation de fissures fragiles, comprend entre 0,02 et 0,10 % en poids de carbone (C), entre 0,8 et 2,5 % en poids de manganèse (Mn), entre 0,05 et 1,5 % en poids de nickel (Ni), entre 0,005 et 0,1 % en poids de niobium (Nb) et entre 0,005 et 0,1 % en poids de titane (Ti), le reste étant du fer (Fe) et d'autres impuretés inévitables, et comporte des microstructures comprenant une structure choisie dans le groupe constitué par une structure à phase unique de ferrite, une structure à phase unique de bainite, une structure à phase complexe de ferrite et de bainite, une structure à phase complexe de ferrite et de perlite, et une structure à phase complexe de ferrite, de bainite et de perlite ; et son procédé de production. Selon un aspect de la présente invention, un acier de structure ultra épais, qui présente une excellente résistance à la propagation de fissures fragiles et présente une excellente limite d'élasticité et une excellente température de transition d'impact au centre, peut être obtenu.
PCT/KR2015/013557 2014-12-24 2015-12-11 Acier de structure ultra épais présentant une excellente résistance à la propagation de fissures fragiles et son procédé de production Ceased WO2016105003A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US15/535,570 US20170342518A1 (en) 2014-12-24 2015-12-11 Structural ultra-thick steel having excellent resistance to brittle crack propagation, and production method therefor
EP15873530.8A EP3239329B8 (fr) 2014-12-24 2015-12-11 Acier de structure ultra épais présentant une excellente résistance à la propagation de fissures fragiles et son procédé de production
CN201580070961.2A CN107109591A (zh) 2014-12-24 2015-12-11 耐脆性裂纹扩展性优异的构造用超厚钢材及其制造方法
JP2017532807A JP6475839B2 (ja) 2014-12-24 2015-12-11 脆性亀裂伝播抵抗性に優れた構造用極厚鋼材及びその製造方法

Applications Claiming Priority (2)

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KR10-2014-0188465 2014-12-24
KR1020140188465A KR101657827B1 (ko) 2014-12-24 2014-12-24 취성균열전파 저항성이 우수한 구조용 극후물 강재 및 그 제조방법

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WO2016105003A1 true WO2016105003A1 (fr) 2016-06-30

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EP (1) EP3239329B8 (fr)
JP (1) JP6475839B2 (fr)
KR (1) KR101657827B1 (fr)
CN (1) CN107109591A (fr)
WO (1) WO2016105003A1 (fr)

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CN115354219A (zh) * 2022-07-06 2022-11-18 江阴兴澄特种钢铁有限公司 一种200～400℃高温强度优异的SA516Gr70钢板及其制造方法

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KR101940880B1 (ko) * 2016-12-22 2019-01-21 주식회사 포스코 저온인성 및 후열처리 특성이 우수한 내sour 후판 강재 및 그 제조방법
KR102209561B1 (ko) 2018-11-30 2021-01-28 주식회사 포스코 취성균열전파 저항성이 우수한 극후물 강재 및 그 제조방법
KR102209547B1 (ko) * 2018-12-19 2021-01-28 주식회사 포스코 취성균열개시 저항성이 우수한 구조용 극후물 강재 및 그 제조방법

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