WO2018117228A1 - Ｈ形鋼及びその製造方法 - Google Patents

Ｈ形鋼及びその製造方法 Download PDF

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WO2018117228A1
WO2018117228A1 PCT/JP2017/045965 JP2017045965W WO2018117228A1 WO 2018117228 A1 WO2018117228 A1 WO 2018117228A1 JP 2017045965 W JP2017045965 W JP 2017045965W WO 2018117228 A1 WO2018117228 A1 WO 2018117228A1
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steel
rolling
flange
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PCT/JP2017/045965
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English (en)
French (fr)
Japanese (ja)
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昌毅 溝口
市川　和利
杉山　博一
徹哉 清家
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新日鐵住金株式会社
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Priority to KR1020197007720A priority Critical patent/KR102021726B1/ko
Priority to JP2018558074A priority patent/JP6468408B2/ja
Priority to CN201780057895.4A priority patent/CN109715842B/zh
Priority to EP17885325.5A priority patent/EP3533893A4/en
Priority to US16/329,163 priority patent/US20190203309A1/en
Publication of WO2018117228A1 publication Critical patent/WO2018117228A1/ja
Priority to PH12019500350A priority patent/PH12019500350A1/en

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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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 by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • B21B1/08—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 structural sections, i.e. work of special cross-section, e.g. angle steel
    • B21B1/088—H- or I-sections
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    • 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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • 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
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    • 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
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C21D2211/001—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 invention relates to a thick H-section steel excellent in strength and low-temperature toughness and a method for producing the same.
  • Patent Document 1 obtains a steel material that secures high strength by applying accelerated cooling while securing toughness by utilizing the refinement effect of prior austenite grains by Ca—Al-based oxides. Technology has been proposed.
  • Patent Document 2 proposes a technique for obtaining a steel material that secures high strength by applying accelerated cooling while securing toughness using the refinement effect of prior austenite grains due to Mg-S inclusions. Yes.
  • the use of thick H-section steel is desired for large buildings, but this H-section has a unique shape.
  • Universal rolling or the like is applied to form a steel slab into an H shape, but the rolling conditions (temperature, rolling reduction) are limited in universal rolling. Therefore, when manufacturing an H-section steel, especially when manufacturing a thick H-section steel having a flange thickness of 20 mm or more, the mechanical characteristics are controlled as compared with a general thick steel sheet (thick steel sheet). It is not easy.
  • Patent Documents 3 and 4 propose a method of reducing the amount of C and hot-rolling a steel piece to which B is added and then allowing it to cool to ensure uniform mechanical properties.
  • Patent Documents 5 to 8 disclose thick H-shaped steels or methods for producing H-shaped steels for the purpose of high strength, high toughness and the like.
  • the present invention has been made in view of such a situation, and an object thereof is to provide a thick H-section steel excellent in strength and low-temperature toughness and a method for producing the same.
  • the gist of the present invention is as follows. (1) In the H-section steel according to one aspect of the present invention, the steel is, as a chemical component, in mass%, C: 0.05 to 0.160%, Si: 0.01 to 0.60%, Mn: 0.80 to 1.70%, Nb: 0.005 to 0.050%, V: 0.05 to 0.120%, Ti: 0.001 to 0.025%, N: 0.0001 to 0.
  • the structure other than the ferrite and the MA is limited to 37% or less, the average grain size of the ferrite is 1 to 30 ⁇ m, and the shape is H when the steel is viewed in a cross section perpendicular to the rolling direction.
  • the thickness of the flange is 20 to 140 mm, and when the length in the width direction of the flange is F, the tensile yield stress is 385 at a position of (1/6) F from the end surface in the width direction of the flange.
  • the steel may contain Nb: more than 0.02 to 0.050% by mass as the chemical component.
  • the steel may contain N: more than 0.005 to 0.0120% by mass as the chemical component.
  • the steel may be limited to less than 0.03% by mass as the chemical component in terms of mass%. . (5) In the H-section steel according to any one of the above (1) to (4), the steel may be limited to less than 0.003% Al by mass% as the chemical component. . (6) In the H-section steel according to any one of (1) to (5) above, the thickness of the flange may be 25 to 140 mm.
  • a method for producing an H-section steel according to an aspect of the present invention is the method for producing an H-section steel according to any one of (1) to (6) above, wherein the (1) to ( 5) A steel making process for obtaining molten steel having the chemical component according to any one of 5), a casting process for obtaining a steel slab by casting the molten steel after the steel making process, and 1100 for the steel slab after the casting process. From the end face in the width direction of the flange so that the shape when viewed in a cut surface perpendicular to the rolling direction is H-shaped with respect to the heating step of heating to ⁇ 1350 ° C.
  • Cumulative rolling reduction at the position of F is more than 20% at over 900 ° C. to 1100 ° C., cumulative rolling reduction at the above position is at least 15% at 730 to 900 ° C., rolling at 730 ° C. or more
  • a hot rolling process in which rolling is performed under conditions to end the cooling, and cooling to cool the hot-rolled material after the hot rolling process Includes a degree, the.
  • a thick H-section steel having a flange thickness of 20 mm or more has been required to have toughness at room temperature or at most 0 ° C.
  • thick H-section steel is required to have excellent toughness at a lower temperature of about ⁇ 20 ° C.
  • the yield stress specifically, yield strength or 0.2% proof stress
  • the present inventors have investigated the steel composition that affects the strength and low temperature toughness with respect to thick H-section steel (hereinafter sometimes referred to as “steel material”), particularly with respect to the flange, which is an important part in the structure of H-section steel.
  • steel material thick H-section steel
  • the strength means the tensile yield stress and the maximum tensile strength
  • the low temperature toughness means the absorbed energy of the Charpy test at ⁇ 20 ° C.
  • an excessive increase in hardenability due to the addition of alloying elements promotes the formation of a martensite-austenite mixed structure (hereinafter referred to as MA) in the steel material, leading to a decrease in low-temperature toughness.
  • MA martensite-austenite mixed structure
  • B tends to promote the formation of MA among the alloy elements. Therefore, it is effective to limit B to an impurity level or less without positively adding B.
  • Nb is effective to achieve high yield stress (yield strength or 0.2% yield strength) and at the same time improve the toughness at ⁇ 20 ° C. Since Nb increases the strength of the steel material through precipitation strengthening, it is not necessary to excessively increase the hardenability, and the strength of the steel material can be increased without promoting the formation of MA. Nb also has the effect of suppressing recrystallization of austenite during hot rolling, accumulating strain in the steel material due to rolling, and reducing the ferrite grain size after transformation.
  • V precipitates as carbonitride (VC, VN, or a composite thereof) and functions as a nucleation site of ferrite, and has the effect of causing finer ferrite.
  • Mn further improves strength and low temperature toughness.
  • controlling the steel composition and controlling the ferrite area fraction, the MA area fraction, the average crystal grain size of ferrite, etc. as the steel structure can achieve both high strength and low temperature toughness. Is important.
  • the cooling rate difference between the surface and the inside of the steel material is small when cooling after hot rolling.
  • the cooling rate is reduced on the surface and inside of the steel material, and the difference is also reduced.
  • the average cooling rate on the surface and inside of the steel material from 800 ° C. to 500 ° C. is 1 ° C./second or less.
  • the C content is 0.05% to 0.160%
  • B is not added, it is limited to the impurity level or less
  • Nb and V are actively added
  • the alloy element content is appropriately controlled, and the carbon equivalent Ceq is controlled within the range of 0.30 to 0.48.
  • the manufacturing conditions are optimally controlled to create the ferrite area fraction, the MA area fraction, the average grain size of ferrite, and the like as the steel structure. As a result, it is possible to obtain a thick H-section steel having excellent strength and low temperature toughness.
  • the H-section steel according to the present embodiment includes a basic element as a chemical component, includes a selection element as necessary, and the balance is composed of Fe and impurities.
  • C, Si, Mn, Nb, V, Ti, and N are basic elements (main alloying elements).
  • C (C: 0.05-0.160%) C (carbon) is an element effective for strengthening steel. Therefore, the lower limit for the C content is 0.05%. Preferably, the lower limit of the C content is 0.060%, 0.070%, or 0.080%. On the other hand, when the C content exceeds 0.160%, the low temperature toughness is reduced. Therefore, the upper limit of C content is 0.160%. In order to further improve the low temperature toughness, the upper limit of the C content is preferably set to 0.140%, 0.130%, or 0.120%.
  • Si silicon
  • Si silicon
  • the lower limit for the Si content is 0.01%.
  • the lower limit of the Si content is 0.05%, 0.10%, or 0.15%.
  • the upper limit of Si content is 0.60%.
  • the upper limit of the Si content is preferably set to 0.40% or 0.30%.
  • Mn manganese
  • the lower limit of the Mn content is 0.80%.
  • the lower limit of the Mn content is preferably set to 1.0%, 1.1%, or 1.2%.
  • the upper limit of the Mn content is 1.70%.
  • the upper limit of the Mn content is 1.60% or 1.50%.
  • Nb 0.005 to 0.050%
  • Nb niobium
  • the lower limit of the Nb content is set to 0.005%.
  • the lower limit of the Nb content is 0.010%, more than 0.020%, 0.025%, or 0.030%.
  • the upper limit of Nb content is 0.050%.
  • the upper limit of the Nb content is 0.045%, 0.043%, or 0.040%.
  • V vanadium
  • V vanadium
  • the lower limit of V content is 0.05%.
  • the lower limit of the V content is more than 0.05%, 0.06%, or 0.07%.
  • the upper limit of V content is 0.120%.
  • the upper limit of the V content is 0.110% or 0.100%.
  • Ti titanium
  • Ti titanium
  • the lower limit of the Ti content is set to 0.001%.
  • the lower limit of the Ti content is preferably set to 0.005%, 0.007%, or 0.010%.
  • the upper limit of the Ti content is 0.025%.
  • the upper limit of the Ti content is 0.020%, 0.015%, or 0.012%.
  • N nitrogen
  • the lower limit of the N content is set to 0.0001%.
  • the lower limit of the N content is 0.0020%, 0.0035%, more than 0.0050%, or 0.0060%.
  • the upper limit of N content is 0.0120%.
  • the upper limit of the N content is 0.0110%, 0.0100%, or 0.0090%.
  • the H-section steel according to the present embodiment contains impurities as chemical components.
  • the “impurities” refer to those mixed from ore or scrap as a raw material or from a production environment when steel is industrially produced. For example, it means elements such as Al, B, P, S and O.
  • Al and B are preferably limited as follows in order to sufficiently exhibit the effects of the present embodiment.
  • limit a lower limit and the lower limit of an impurity may be 0%.
  • Al 0.10% or less
  • Al aluminum
  • Al is an element used as a deoxidizing element.
  • the Al content exceeds 0.10%, the oxide becomes coarse and becomes a starting point for brittle fracture, and low-temperature toughness decreases. Therefore, the upper limit of the Al content is limited to 0.10%.
  • Ti works as a deoxidizing element, and Ti oxide is precipitated in the steel. This Ti oxide functions as a nucleation site for V carbonitrides, refines the ferrite grain size, and contributes to the improvement of low temperature toughness.
  • the upper limit of the Al content may be limited to less than 0.003%, 0.002%, or 0.001% using Al as an impurity.
  • Al is intentionally contained in the steel.
  • B (boron) improves hardenability, promotes the formation of MA, and lowers low temperature toughness. For this reason, in the present embodiment, B is not actively added and is limited to the impurity level or less.
  • the upper limit of B content is limited to 0.0003%.
  • the upper limit of the B content is limited to less than 0.0003%, 0.0002%, or 0.0001%. In general, in order to make the B content more than 0.0003%, B is intentionally contained in the steel.
  • P 0.03% or less, S: 0.02% or less, O: 0.005% or less
  • P (phosphorus), S (sulfur), and O (oxygen) are impurities.
  • P and S are segregated by solidification, promote weld cracking, and reduce low temperature toughness.
  • the upper limit of the P content is limited to 0.03%, 0.02%, or 0.01%.
  • the upper limit of the S content is limited to 0.02% or 0.01%.
  • O dissolves in steel and lowers the low temperature toughness, and lowers the low temperature toughness by coarsening of oxide particles.
  • the upper limit of the O content is limited to 0.005%, 0.004%, or 0.003%.
  • the H-section steel according to the present embodiment may contain a selective element in addition to the basic elements and impurities described above.
  • a selective element instead of a part of Fe which is the above-described remaining part, Cr, Mo, Ni, Cu, W, Ca, Zr, Mg, and / or REM may be included as a selective element.
  • These selective elements may be contained depending on the purpose. Therefore, it is not necessary to limit the lower limit values of these selected elements, and the lower limit value may be 0%. Moreover, even if these selective elements are contained as impurities, the above effects are not impaired.
  • Cr Cr (chromium) is an element that contributes to improving the strength. If necessary, the Cr content may be 0 to 0.30%. In order to further improve the strength, the lower limit of the Cr content is preferably set to 0.01%, 0.05%, or 0.10%. On the other hand, if the Cr content exceeds 0.30%, the formation of MA may be promoted and the low temperature toughness may be reduced. Therefore, preferably, the upper limit of the Cr content is set to 0.30%, 0.25%, or 0.20%.
  • Mo mobdenum
  • Mo mobdenum
  • the Mo content may be 0 to 0.20%.
  • the lower limit of the Mo content is preferably set to 0.01%, 0.05%, or 0.10%.
  • the upper limit of the Mo content is 0.20%, 0.17%, or 0.15%.
  • Ni (Ni: 0 to 0.50%) Ni (nickel) is an element that contributes to improvement in strength by solid solution in steel. If necessary, the Ni content may be 0 to 0.50%. In order to further improve the strength, the lower limit of the Ni content is preferably set to 0.01%, 0.05%, or 0.10%. However, if the Ni content exceeds 0.50%, the hardenability is increased, the formation of MA is promoted, and the low temperature toughness may be lowered. Therefore, preferably, the upper limit of the Ni content is 0.50%, 0.30%, or 0.20%.
  • Cu (copper) is an element contributing to the improvement of strength. If necessary, the Cu content may be 0 to 0.35%. However, the addition of Cu facilitates the formation of MA and may reduce the low temperature toughness. Therefore, preferably, even if the Cu content is limited to 0.30% or less, 0.20% or less, 0.10% or less, or less than 0.03% or less than 0.01%, which is an impurity level. Good.
  • W tungsten
  • the W content may be 0 to 0.50%.
  • the lower limit of the W content is 0.001%, 0.01%, or 0.10%.
  • the upper limit of the W content is 0.50%, 0.40%, or 0.30%.
  • W content contained as an impurity is less than 0.001%. In order to make the W content 0.001% or more, W is intentionally contained in the steel.
  • Ca (Ca: 0 to 0.0050%)
  • Ca (calcium) is an element that is effective in controlling the form of sulfide, suppresses the formation of coarse MnS, and contributes to the improvement of low-temperature toughness.
  • the Ca content may be 0 to 0.0050%.
  • the lower limit of the Ca content is 0.0001%, 0.0005%, or 0.0010%.
  • the upper limit of the Ca content is set to 0.0050%, 0.0040%, or 0.0030%.
  • Zr zirconium
  • Zr zirconium
  • the Zr content may be 0 to 0.0050%.
  • the lower limit of the Zr content is 0.0001%, 0.0005%, or 0.0010%.
  • the upper limit of the Zr content is 0.0050%, 0.0040%, or 0.0030%.
  • the Zr content contained as an impurity is less than 0.0001%. In order to make the Zr content 0.0001% or more, Zr is intentionally contained in the steel.
  • Mg manganesium
  • REM rare earth elements
  • HAZ heat affected zone
  • the Mg content may be 0 to 0.0050% and the REM content may be 0 to 0.0050%.
  • the lower limit of the Mg content is 0.0005%, 0.0010%, or 0.0020%
  • the lower limit of the REM content is 0.0005%, 0.0010%, or 0.0020%.
  • the upper limit of Mg content is 0.0040%, 0.0030%, or 0.0025%
  • the upper limit of REM content is 0.0040%, 0.0030%, or 0.0025. %.
  • the carbon equivalent Ceq is controlled from the viewpoint of securing strength. Specifically, when Ceq is represented by the following formula 1, C, Mn, Cr, Mo, V, Ni, and Cu in the chemical components of the H-shaped steel are in mass%, and 0.30 ⁇ Ceq ⁇ 0. 48 is satisfied. If Ceq is less than 0.30, the strength is insufficient. Therefore, the lower limit of Ceq is set to 0.30. Preferably, the lower limit of Ceq is set to 0.32%, 0.34%, or 0.35%. On the other hand, when Ceq exceeds 0.48, low temperature toughness decreases. Therefore, the upper limit of Ceq is set to 0.48.
  • the upper limit of Ceq is 0.45%, 0.43%, or 0.40%.
  • an element whose content in steel is equal to or lower than the detection limit may be calculated by substituting 0 into formula 1 as a value.
  • the above steel components may be measured by a general steel analysis method.
  • the steel component may be measured using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry).
  • C and S may be measured using a combustion-infrared absorption method
  • N may be measured using an inert gas melting-thermal conductivity method
  • O may be measured using an inert gas melting-non-dispersive infrared absorption method.
  • the steel structure includes an area fraction of ferrite of less than 60 to 100%, the mixed structure MA of martensite and austenite is limited to 3.0% or less, and the ferrite and MA The organization other than is limited to 37% or less. Moreover, the average particle diameter of ferrite is 1 ⁇ m or more and 30 ⁇ m or less.
  • Ferrite is a main constituent phase in the steel structure of the H-section steel according to the present embodiment.
  • the area fraction of ferrite is less than 60%, the low temperature toughness decreases. Therefore, the lower limit of the ferrite fraction is set to 60%.
  • the lower limit of the ferrite fraction is 65%, 70%, or 75%.
  • the upper limit of the ferrite fraction is set to less than 100%.
  • the upper limit of the ferrite fraction is preferably 90%, 85%, or 80%.
  • the MA fraction is limited to 3.0% or less.
  • the upper limit of the MA fraction is 2.5%, 2.0%, or 1.5%. Since the MA fraction is preferably as small as possible, the lower limit of the MA fraction may be 0%.
  • the steel structure of the H-section steel according to the present embodiment includes bainite, pearlite, and the like as structures other than the above-described ferrite and MA. If the structure other than ferrite and MA is excessively contained, the low temperature toughness is lowered. Therefore, the area fraction of the structure other than ferrite and MA (the above-mentioned ferrite and the remainder of MA) is limited to 37% or less. Preferably, the fraction of the structure other than ferrite and MA is 35% or less, 30% or less, or 25% or less. Since the fraction of the structure other than ferrite and MA is preferably as small as possible, this lower limit may be 0%.
  • the average particle diameter of the ferrite is preferably fine.
  • the upper limit of the ferrite grain size is set to 30 ⁇ m.
  • the upper limit of the ferrite grain size is 25 ⁇ m, 22 ⁇ m, or 18 ⁇ m.
  • the lower limit of the ferrite particle size is 1 ⁇ m.
  • the lower limit of the ferrite grain size is 3 ⁇ m, 5 ⁇ m, or 10 ⁇ m.
  • FIG. 1 is a schematic cross-sectional view orthogonal to the rolling direction of H-section steel, but the steel structure is observed using the vicinity of the evaluation site 7 shown in FIG. 1 as an observation surface.
  • the evaluation part is located at a position (1/6) F from the flange width direction end surface 5 a and a position (1/4) t 2 from the outer surface 5 b in the thickness direction of the flange.
  • the steel structure is observed using the vicinity of 7 as the observation surface.
  • This observation surface is a surface parallel to the flange end surface 5a in the width direction.
  • the fraction of ferrite and MA is obtained from the observation surface that has undergone nital corrosion, the remainder is the fraction of the structure of pearlite and bainite, and the MA fraction is obtained from the observation surface that has undergone repeller corrosion.
  • measurement points are arranged in a lattice shape with a side of 25 ⁇ m on a 200 ⁇ optical micrograph (if necessary, multiple fields of view) taken on the observation surface that has been corroded at night, and at least 1000 measurement points Whether it is ferrite or MA is determined, and the value obtained by dividing the number of measurement points determined to be ferrite or MA by the number of all measurement points is defined as the ferrite or MA fraction.
  • measuring points are arranged in a lattice shape with a side of 25 ⁇ m on a 200 ⁇ optical micrograph (if necessary, multiple fields of view) taken on an observation surface that has undergone repeller corrosion.
  • a value obtained by dividing the number of measurement points determined to be MA by the number of all measurement points is defined as an MA fraction.
  • the ferrite fraction is obtained by subtracting the total fraction of pearlite, bainite, and MA fraction obtained above from 100%.
  • the average particle diameter of the ferrite is calculated from the cutting method in accordance with JIS G0551 (2013) using a 200-fold optical micrograph taken on the above-mentioned observation surface subjected to the nital corrosion. Ask.
  • a test piece is taken from a region including the evaluation portion 7 shown in FIG. 1 as a position where average mechanical properties (strength and low temperature toughness) are obtained, and mechanical properties are evaluated.
  • FIG. 1 is a schematic cross-sectional view orthogonal to the rolling direction of H-section steel.
  • the X-axis direction is defined as the flange width direction
  • the Y-axis is defined as the flange thickness direction
  • the Z-axis direction is defined as the rolling direction.
  • the center of the evaluation part 7 is (1/6) F from the width direction end face of the flange, where F is the length in the width direction of the flange and t 2 is the thickness of the flange.
  • the position is (1/4) t 2 from the outer surface in the thickness direction of the flange.
  • the surface on the outer side in the thickness direction of the flange is one surface in the thickness direction of the flange and is the surface not in contact with the web 6, and is the surface 5b shown in FIG.
  • the end face in the width direction of the flange is the end face 5a shown in FIG.
  • test piece for evaluating low temperature toughness by the Charpy test is collected from the position of the evaluation site 7 so that the longitudinal direction of the test piece is parallel to the rolling direction.
  • the surface on which the notch is formed in the test piece is any surface parallel to the end surface 5a in the width direction of the flange.
  • the test piece is taken from any position as long as it is a position (1/6) F from the flange width direction end surface 5a and a position (1/4) t 2 from the outer surface 5b in the thickness direction of the flange. May be.
  • a test piece for evaluating the yield stress (yield strength or 0.2% proof stress) and the tensile strength (maximum tensile strength) by a tensile test is (1/6) F from the width direction end face 5a of the flange in FIG. Samples are taken so that the position is the center of the specimen in the thickness direction.
  • the test piece may be formed such that the longitudinal direction of the test piece is parallel to the rolling direction and the entire thickness direction of the flange is cut out.
  • the test piece may be collected from any position as long as the position is (1/6) F from the end face 5a in the width direction of the flange.
  • the yield stress at room temperature is 385 MPa or more
  • the tensile strength is 490 MPa or more
  • the Charpy absorbed energy at ⁇ 20 ° C. is 100 J or more.
  • the upper limit of the yield stress is preferably 530 MPa and the upper limit of the tensile strength is preferably 690 MPa.
  • the upper limit of the Charpy absorbed energy at ⁇ 20 ° C. may be set to 500 J.
  • normal temperature refers to 20 degreeC.
  • the tensile test is performed according to JIS Z2241 (2011), and the Charpy test is performed according to JIS Z2242 (2005).
  • the yield strength is obtained as the yield stress
  • the 0.2% yield strength is obtained as the yield stress.
  • the flange thickness t 2 and 20 ⁇ 140 mm For example, in a high-rise building structure, thick H-section steel is required as a strength member. Therefore, the lower limit of the flange thickness is 20 mm. Preferably, the lower limit of the flange thickness is 25 mm, 40 mm, or 56 mm. On the other hand, if the thickness t 2 of the flange is greater than 140 mm, it is difficult achieve both the hot working volume during processing is insufficient strength and low temperature toughness. Therefore, the upper limit of the flange thickness is 140 mm. Preferably, the upper limit of the flange thickness is set to 125 mm, 89 mm, or 77 mm. For example, the flange thickness t 2 is preferably 25 to 140 mm.
  • the thickness t 1 of the H-shaped steel web is not particularly specified, but is preferably 20 to 140 mm, and more preferably 25 to 140 mm.
  • the flange thickness / web thickness ratio (t 2 / t 1 ) is preferably 0.5 to 2.0.
  • the flange thickness / web thickness ratio (t 2 / t 1 ) exceeds 2.0, the web may be deformed into a wavy shape.
  • the flange thickness / web thickness ratio (t 2 / t 1 ) is less than 0.5, the flange may be deformed into a wavy shape.
  • the manufacturing method of the H-section steel according to the present embodiment includes a steel making process, a casting process, a heating process, a hot rolling process, and a cooling process.
  • the chemical composition of the molten steel is adjusted so that the above steel composition is obtained.
  • molten steel produced by converter refining or secondary refining may be used, or molten steel melted in an electric furnace may be used as a raw material.
  • deoxidation treatment or vacuum degassing treatment may be performed as necessary.
  • the molten steel after the steel making process is cast to obtain a steel piece. Casting is performed by a continuous casting method, an ingot method, or the like. From the viewpoint of productivity, continuous casting is preferable.
  • the shape of the billet is preferably a beam blank having a shape close to the H-shaped steel to be manufactured, but is not particularly limited.
  • the thickness of the steel slab is preferably 200 mm or more from the viewpoint of productivity, and is preferably 350 mm or less in consideration of reduction of segregation, homogeneity of the heating temperature before hot rolling, and the like.
  • the steel slab after the casting process is heated to 1100 to 1350 ° C.
  • the lower limit of the heating temperature is 1100 ° C.
  • the lower limit of the heating temperature is set to 1150 ° C. in order to sufficiently dissolve elements that form carbides or nitrides such as Nb.
  • the upper limit of the heating temperature is 1350 ° C.
  • a steel piece that has not been cooled to room temperature after the casting process may be used.
  • rough rolling, intermediate rolling, and finish rolling are performed on the steel pieces after the heating process.
  • rough rolling forming is performed such that the shape when viewed on a cut surface perpendicular to the rolling direction is substantially H-shaped.
  • This nearly H-shaped steel slab is hot-rolled with a cumulative rolling reduction of 20% or more in a temperature range where the steel surface temperature is over 900 ° C to 1100 ° C, and the steel surface temperature is 730 ° C to Hot rolling is performed in a temperature range of 900 ° C. with a cumulative rolling reduction of 15% or more.
  • forming is performed so that the shape when viewed on the cut surface is finally H-shaped.
  • the cumulative reduction ratio is set to 20% or more in order to reduce the amount of bainite and MA produced by refining austenite grains.
  • the lower limit of the cumulative rolling reduction in the temperature range of more than 900 ° C. to 1100 ° C. is 25%, 30%, or 35%.
  • the upper limit of the cumulative rolling reduction in the temperature range from over 900 ° C. to 1100 ° C. may be set to 60%.
  • the cumulative rolling reduction is set to 15% or more due to finer ferrite.
  • the lower limit of the cumulative rolling reduction in the temperature range of 730 ° C. to 900 ° C. is 20%, 25%, or 30%.
  • the upper limit of the cumulative rolling reduction in the temperature range of 730 ° C. to 900 ° C. may be set to 50%.
  • the rolling end temperature is 730 ° C. or higher at the surface temperature of the steel.
  • the upper limit of the rolling finishing temperature is 750 ° C.
  • rough rolling, intermediate rolling, and finish rolling are performed.
  • rolling in a temperature range of over 900 ° C. to 1100 ° C. may be performed by rough rolling, intermediate rolling, or finish rolling.
  • rolling in the temperature range of 730 ° C. to 900 ° C. may be performed by any of rough rolling, intermediate rolling, or finish rolling.
  • the cumulative rolling reduction in the above temperature range may be controlled.
  • the cumulative reduction ratio in the above temperature range is obtained based on the flange thickness at the position corresponding to (1/6) F from the width direction end face 5a of the flange shown in FIG.
  • the cumulative rolling reduction in the temperature range above 900 ° C. to 1100 ° C. is the rolling reduction calculated from the difference between the flange thickness when the surface temperature of the steel is 1100 ° C. and the flange thickness just before reaching 900 ° C. To do.
  • the cumulative rolling reduction in the temperature range of 730 ° C. to 900 ° C. is a rolling reduction calculated from the difference between the flange thickness at the time when the surface temperature of the steel is 900 ° C. and the flange thickness at the time of 730 ° C.
  • the method of rough rolling, intermediate rolling, and finish rolling in the hot rolling process is not particularly limited.
  • breakdown rolling is performed as rough rolling
  • universal rolling or edging rolling is performed as intermediate rolling
  • universal rolling is performed as finishing rolling, so that the shape when viewed in a cross section perpendicular to the rolling direction becomes H-shaped. What is necessary is just to shape
  • water cooling may be performed between rolling passes.
  • Water cooling between rolling passes is cooling performed for the purpose of temperature control in a temperature range higher than the temperature at which austenite undergoes phase transformation. Bainite and MA are not generated in the steel by water cooling between rolling passes.
  • the two-heat rolling is a rolling method in which the steel slab is cooled to 500 ° C. or lower after the primary rolling, and then the steel slab is heated again to 1100 to 1350 ° C. to perform secondary rolling.
  • the amount of plastic deformation in the hot rolling is small and the decrease in temperature in the rolling process is small, so that the second heating temperature can be lowered.
  • the hot rolled material after the hot rolling process is cooled.
  • the hot-rolled material is allowed to cool in the air as it is after the hot rolling is finished.
  • the average cooling rate on the surface and inside of the steel material from 800 ° C to 500 ° C is 1 ° C / second or less.
  • the cooling rate on the surface and inside of the steel material becomes uniform, so that variations in mechanical properties due to the portion of the steel material are suppressed.
  • the cooling is performed in the atmosphere without performing forced cooling from immediately after hot rolling until the steel material temperature becomes 400 ° C. or lower. means.
  • the manufacturing method of the H-section steel according to the present embodiment does not require advanced steelmaking technology or accelerated cooling, it is possible to reduce the manufacturing load and the work period. Therefore, the H-section steel according to the present embodiment can improve the reliability of a large building without impairing the economy.
  • the conditions in the examples are one example of conditions adopted to confirm the feasibility and effects of the present invention.
  • the present invention is not limited to this one condition example.
  • the present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.
  • Steels having chemical components shown in Tables 1 to 3 were melted, and steel pieces having a thickness of 240 to 300 mm were manufactured by continuous casting.
  • the steel was melted in a converter, subjected to primary deoxidation, alloy elements were added to adjust the components, and vacuum degassing was performed as necessary.
  • the obtained steel slab was heated and subjected to hot rolling to produce an H-shaped steel.
  • Ingredient No. The steel components shown as 1 to 48 were obtained by chemical analysis of samples collected from each H-shaped steel after production. Although not shown in the table, in all Examples, P was 0.03% or less, S was 0.02% or less, and O was 0.005% or less.
  • surface represents that it was not actively added to steel or content was below the detection limit.
  • the manufacturing process of H-section steel is shown in FIG.
  • the steel slab heated in the heating furnace 1 was subjected to a universal rolling apparatus row including a rough rolling mill 2a, an intermediate rolling mill 2b, and a finishing rolling mill 2c.
  • the hot-rolled material was allowed to cool to 400 ° C. or less as it was after the hot rolling.
  • the average cooling rate on the surface and inside of the hot rolled material from the hot rolling end temperature to 500 ° C. was 1 ° C./second or less.
  • water cooling devices 3 provided before and after the intermediate universal rolling mill (intermediate rolling mill) 2b. At this time, reverse rolling was performed.
  • Tables 4 to 6 show manufacturing conditions and manufacturing results.
  • the rolling reduction during hot rolling shown in Tables 4 to 6 is the cumulative rolling reduction in each temperature region at a position corresponding to (1/6) F from the widthwise end face 5a of the flange shown in FIG.
  • the manufactured H-shaped steel was subjected to a Charpy test at ⁇ 20 ° C. using a test piece taken from the evaluation site 7 shown in FIG.
  • a tensile test was performed at normal temperature (20 ° C.) using a test piece having a position (1/6) F from the flange width direction end surface 5a at the center in the thickness direction, and tensile properties were evaluated.
  • the structure was observed using a sample having an observation surface in the vicinity of the evaluation site 7 shown in FIG. 1 to evaluate the steel structure.
  • the tensile test was performed according to JIS Z2241 (2005).
  • the yield stress was taken as the yield point when the stress-strain curve of the tensile test showed yield behavior, and the yield stress was taken as 0.2% proof stress when no yield behavior was shown.
  • the Charpy impact test was performed according to JIS Z2242 (2005). The Charpy impact test was conducted at -20 ° C.
  • the ferrite fraction, the MA fraction, and the fraction of the structure other than ferrite and MA were measured by the above-described method using an optical micrograph.
  • the structure other than ferrite and MA is bainite or pearlite.
  • the average particle diameter of the ferrite was calculated
  • a steel material having a yield stress (YS) at room temperature of 385 MPa or more and a tensile strength (TS) of 490 MPa or more was judged to be acceptable.
  • a steel material having Charpy absorbed energy (vE-20) at ⁇ 20 ° C. of 100 J or more was judged to be acceptable.
  • Manufacturing No. No. 9 had a rolling reduction ratio of over 900 ° C. to 1100 ° C., the ferrite fraction in the steel structure was insufficient, and the fraction of the structure other than ferrite and MA became excessive, and at ⁇ 20 ° C. This is an example where Charpy absorbed energy is insufficient.
  • Manufacturing No. No. 10 is an example in which since the rolling reduction at 730 ° C. to 900 ° C. was insufficient, the ferrite grain size became coarse and the Charpy absorbed energy at ⁇ 20 ° C. was insufficient.
  • Manufacturing No. No. 19 had an insufficient rolling reduction at temperatures exceeding 900 ° C. to 1100 ° C., so that the ferrite fraction became insufficient, the MA fraction became excessive, the fraction of the structure other than ferrite and MA became excessive, and ⁇ 20 This is an example in which Charpy absorbed energy at °C is insufficient.
  • Manufacturing No. No. 20 has a high C content.
  • No. 25 has a high Nb content.
  • No. 26 has a high V content, and production no. No. 28 has a high Al content.
  • No. 29 has a high Ti content, and production No. No. 30 has a high N content.
  • No. 31 is an example in which the Charpy absorption energy at ⁇ 20 ° C. is insufficient because Ceq is excessive.
  • Manufacturing No. No. 21 has a low C content.
  • No. 24 has a low Mn content, and production no. No. 32 has insufficient Ceq.
  • No. 46 is an example in which YS and TS are insufficient because the Si content is low.
  • Manufacturing No. No. 22 has a high Si content
  • production No. 22 No. 23 is an example in which the Charpy absorbed energy at ⁇ 20 ° C. is insufficient because the Mn content is large and the MA fraction is excessive.
  • Manufacturing No. No. 27 is an example in which since the V content was small, the ferrite grain size became coarse and the Charpy absorbed energy at ⁇ 20 ° C. was insufficient.
  • Manufacturing No. No. 33 has an excess of B content and Ceq. No. 49 is an example in which since the B content was large, the MA fraction was excessive and the Charpy absorbed energy at ⁇ 20 ° C. was insufficient.
  • Manufacturing No. 44 and production no. No. 45 is an example in which since the V content was small, the ferrite grain size became coarse and the Charpy absorbed energy at ⁇ 20 ° C. was insufficient.
  • Manufacturing No. No. 47 is an example where the Nb content was small, the ferrite grain size was coarse, YS and TS were insufficient, and Charpy absorbed energy at ⁇ 20 ° C. was insufficient.
  • Manufacturing No. No. 48 is an example in which since the Ti content was small, the ferrite grain size became coarse and Charpy absorbed energy at ⁇ 20 ° C. was insufficient.
  • Manufacturing No. No. 50 is an example in which the Charpy absorbed energy at ⁇ 20 ° C. was insufficient because the rolling finishing temperature was low.

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