EP2799584B1 - Production method for a high-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, - Google Patents

Production method for a high-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, Download PDF

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Publication number
EP2799584B1
EP2799584B1 EP12863408.6A EP12863408A EP2799584B1 EP 2799584 B1 EP2799584 B1 EP 2799584B1 EP 12863408 A EP12863408 A EP 12863408A EP 2799584 B1 EP2799584 B1 EP 2799584B1
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EP
European Patent Office
Prior art keywords
less
temperature
steel plate
rolling
central portion
Prior art date
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EP12863408.6A
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German (de)
English (en)
French (fr)
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EP2799584A4 (en
EP2799584A1 (en
Inventor
Yoshiko TAKEUCHI
Kazukuni Hase
Shinji Mitao
Yoshiaki Murakami
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JFE Steel Corp
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JFE Steel Corp
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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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/001—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
    • C22C38/02—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
    • 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • 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

Definitions

  • the present invention relates to a method for manufacturing a high-strength thick steel plate for structural use excellent in terms of brittle crack arrestability, and in particular to a method for manufacturing a steel plate having a thickness of 50 mm or more which can be preferably used for ships.
  • Ni content As a method for improving the brittle crack arrestability of a steel material, a method in which Ni content is increased has been known in the past. 9%-Ni steel is commercially used for the storage tanks of liquefied natural gases.
  • Patent Literature 1 proposes a steel material having an ultra fine crystallization microstructure in the surface portion in order to improve brittle crack arrestability without an increase in alloy cost.
  • the steel material having excellent brittle crack arrestability according to Patent Literature 1 is characterized in that, focusing on the fact that shear-lips (plastic deformation areas), which are formed in the surface portion of a steel material when a brittle crack propagates, are effective for improving brittle crack arrestability, the crystal grain size in the shear-lip portions is decreased in order to absorb the propagation energy of a propagating brittle crack.
  • an ultra fine ferrite structure or bainite structure is formed in the surface portion of the steel material by repeating once or more a process, in which the surface portion of a hot-rolled steel plate is cooled down to a temperature equal to or lower than the A r3 transformation point by performing controlled cooling and then the controlled cooling is stopped in order to allow the surface portion to recuperate to have a temperature equal to or higher than the transformation point, while the steel material is rolled in order for transformation or recrystallization due to deformation to repeatedly occur.
  • Patent Literature 2 it is disclosed that, in order to improve the brittle crack arrestability of a steel material having a microstructure mainly including a ferrite-pearlite phase, it is important to form a layer, in either of the surface portions of the steel material, including 50% or more of a ferrite structure having ferrite grains with a circle-equivalent average grain size of 5 ⁇ m or less and an aspect ratio of the grains of 2 or more, and to prevent the variation of a ferrite grain size, and that, as a method for preventing the variation, the maximum rolling reduction per pass of finishing rolling is controlled to be 12% or less in order to prevent local recrystallization.
  • Patent Literature 3 discloses a technique which is a modification of TMCP and in which, focusing not only on a decrease in ferrite crystal grain size but also on a subgrain formed in a ferrite grain, brittle crack arrestability is improved.
  • brittle crack arrestability is improved by controlling (a) rolling conditions such that fine ferrite crystal grains are achieved, (b) rolling conditions such that a fine ferrite structure is formed in a portion constituting 5% or more of the thickness of the steel material, (c) rolling conditions such that subgrains are formed by growing a texture in the fine ferrite structure and by rearranging dislocations introduced by applying deformation (rolling) using thermal energy and (d) cooling conditions such that an increase in the grain size of the formed fine ferrite crystal grains and an increase in the grain size of the formed fine subgrains are prevented.
  • a method in which brittle crack arrestability is improved by applying reduction forth of rolling to a transformed ferrite phase in order to grow a texture, is also known.
  • resistance to brittle fracture is increased by forming a separation parallel to the plate surface on the fracture surface of a steel material in order to reduce stress at the brittle crack tip.
  • Patent Literature 4 discloses that brittle fracture resistance is improved by performing controlled rolling in order to form a microstructure having an X-ray plane intensity ratio in the (110) plane showing a texture developing degree of 2 or more and including large-size grains having a diameter equivalent to a circle in the crystal grains of 20 ⁇ m or more in an amount of 10% or less.
  • Patent Literature 5 discloses, as a steel for welded structural use having excellent brittle crack arrestability in the joint part, a steel plate having an X-ray plane intensity ratio in the (100) plane showing a texture developing degree on a plane inside the plate parallel to the rolling surface of the plate of 1.5 or more. It is disclosed that the steel plate has excellent brittle crack arrestability owing to the difference in angle between the direction of applied stress and the direction of crack propagation as a result of the growth of the texture mentioned above.
  • JP 2007-254767 discloses a welded joint for a high-tensile strength thick steel plate with a thickness of 35 mm or more having both excellent fracture toughness (Kc) and brittle-fracture crack-propagation arrest toughness (Kca), wherein the steel plate has a composition consisting of, by mass%, C: 0.01-0.3%, Si: 0.01-2%, Mn: 0.1-3%, Al: 0.003-0.1%, N: 0.001-0.01%, P: 0.02% or less, S: 0.01% or less, and the balance Fe with unavoidable impurities.
  • Kc fracture toughness
  • Kca brittle-fracture crack-propagation arrest toughness
  • JP 2011-052243 discloses a method for producing a high-tensile strength thick steel plate for structural use having sufficient brittle crack arrestability, comprising heating a steel slab having an appropriate chemical composition to 950-1150°C, rough-rolling the steel slab with a cumulative rolling reduction of 30% or more at 900°C or higher, finish-rolling the rough-rolled material with a cumulative rolling reduction of 40% or more within a surface temperature range of Ar 3 to Ar 3 + 60°C, subsequently acceleration-cooling the surface to 200°C or lower from a temperature of Ar 3 or higher with a cooling rate of 8°C/s or more by average in a sheet thickness and then tempering the steel sheet.
  • Si is effective as a deoxidizing chemical element and as a chemical element for increasing the strength of steel, the effect cannot be realized in the case where the Si content is less than 0.03%.
  • the Si content is more than 0.5%, there is not only the deterioration of the surface quality of steel but also a significant decrease in toughness. Therefore, it is preferable that the Si content be 0.03% or more and 0.5% or less.
  • a small amount of B may be added as a chemical element which increases the hardenability of steel.
  • the B content is more than 0.0030%, since there is a decrease in the toughness of a weld zone, it is preferable that the B content be 0.0030% or less in the case where B is added.
  • the difference in rolling temperature between the first and the last passes in rolling performed while the central portion in the thickness direction has a temperature in the austenite non-recrystallization temperature range be 40°C or less.
  • rolling temperature means the temperature of the central portion in the thickness direction of a steel material immediately before the steel material is rolled.
  • the temperature of the central portion in the thickness direction can be derived from, for example, the thickness, the surface temperature and the cooling conditions by, for example, simulation calculation. For example, by calculating the temperature distribution in the thickness direction using a difference method, the temperature of the central portion in the thickness direction of the steel plate can be derived.
  • the rolling is performed so that the total cumulative rolling reduction in the austenite recrystallization temperature range and in the austenite non-recrystallization temperature range be 65% or more. This is because sufficient reduction cannot be applied to a microstructure in the case where the total reduction is small, which results in the target toughness and strength not being achieved, and because, by controlling the total cumulative rolling reduction to be 65% or more, it is possible to apply sufficient reduction to a microstructure, which results in the target toughness and strength being achieved.
  • a temper treatment may be performed on the cooled steel plate. By performing a temper treatment, it is possible to further increase the toughness of a steel plate. By controlling a tempering temperature to be equal to or lower than the A C1 point in terms of the average temperature of the steel plate, it is possible to prevent the desired microstructure obtained through rolling and cooling from being lost.
  • the A C1 point (°C) is derived using the equation below.
  • Kca value at a temperature of -10°C was determined by performing an ESSO test compliant with WES 3003.
  • the integration degree I of the RD//(110) plane in the central portion in the thickness direction was derived in the following way. Firstly, by performing mechanical polishing and electrolytic polishing on the surface parallel to the steel plate surface of a sample having a thickness of 1 mm cut out of the central portion in the thickness direction, a test piece for X-ray diffractometry was prepared. By performing X-ray diffraction measurement using a Mo X-ray source on this test piece, the pole figures of (200), (110) and (211) planes were obtained. Three dimensional orientation distribution function was calculated from the obtained pole figures by using a Bunge method.
  • Sample steel plates (serial Nos. 1 through 13 and 27 through 30) had a Kca(-10°C) of 6000 N/mm 3/2 or more, which means these sample steel plates had excellent brittle crack arrestability.
  • sample steel plates (serial Nos. 1 through 13), which had the Charpy fracture appearance transition temperature and the integration degrees I of the RD//(110) plane in the surface portion and the central portion in the thickness direction satisfying the relational expression (1), had higher Kca(-10°C) than sample steel plates (serial Nos. 27 through 30), which had the Charpy fracture appearance transition temperature and the integration degree I of the RD//(110) plane in the surface portion and the central portion in the thickness direction not satisfying the relational expression (1).
  • sample steel plates (serial Nos. 21 through 26), which had chemical compositions of the steel plate within the ranges as described above and were prepared under manufacturing conditions regarding heating and rolling conditions for the steel plate out of the range according to the present invention, had a Kca(-10°C) of less than 6000 N/mm 3/2 .
  • the textures of sample steel plates did not satisfy the specifications according to the present disclosure.
  • Sample steel plates (serial Nos. 14 through 20), which had chemical compositions of the steel plate out of the preferable ranges as described above, had toughness not satisfying the specifications according to the present disclosure and a Kca(-10°C) of less than 6000 N/mm 3/2 .

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP12863408.6A 2011-12-27 2012-05-18 Production method for a high-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, Active EP2799584B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2011285570 2011-12-27
JP2012111158A JP5304925B2 (ja) 2011-12-27 2012-05-15 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
PCT/JP2012/063409 WO2013099318A1 (ja) 2011-12-27 2012-05-18 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

Publications (3)

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EP2799584A1 EP2799584A1 (en) 2014-11-05
EP2799584A4 EP2799584A4 (en) 2015-01-07
EP2799584B1 true EP2799584B1 (en) 2019-01-02

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EP (1) EP2799584B1 (pt)
JP (1) JP5304925B2 (pt)
KR (1) KR101588258B1 (pt)
CN (1) CN104024462B (pt)
BR (1) BR112014015779B1 (pt)
WO (1) WO2013099318A1 (pt)

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CN105102650B (zh) * 2013-03-26 2017-10-24 杰富意钢铁株式会社 脆性裂纹传播停止特性优良的大线能量焊接用高强度厚钢板及其制造方法
KR101523229B1 (ko) * 2013-11-28 2015-05-28 한국생산기술연구원 저온 특성이 향상된 금속 재료 및 그 제조방법
KR101846759B1 (ko) * 2013-12-12 2018-04-06 제이에프이 스틸 가부시키가이샤 강판 및 그 제조 방법
KR20160127808A (ko) 2014-03-31 2016-11-04 제이에프이 스틸 가부시키가이샤 고장력 강판 및 그 제조 방법
US10883159B2 (en) 2014-12-24 2021-01-05 Posco High-strength steel having superior brittle crack arrestability, and production method therefor
EP3239331B1 (en) * 2014-12-24 2020-10-28 Posco High-strength steel having superior brittle crack arrestability, and production method therefor
KR101657827B1 (ko) * 2014-12-24 2016-09-20 주식회사 포스코 취성균열전파 저항성이 우수한 구조용 극후물 강재 및 그 제조방법
US10822671B2 (en) 2014-12-24 2020-11-03 Posco High-strength steel having superior brittle crack arrestability, and production method therefor
WO2017047088A1 (ja) * 2015-09-18 2017-03-23 Ｊｆｅスチール株式会社 構造用高強度厚鋼板およびその製造方法
JP6338022B2 (ja) * 2016-02-24 2018-06-06 Ｊｆｅスチール株式会社 脆性き裂伝播停止特性に優れた高強度極厚鋼板およびその製造方法
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WO2018030171A1 (ja) * 2016-08-09 2018-02-15 Ｊｆｅスチール株式会社 高強度厚鋼板およびその製造方法
JP6274375B1 (ja) * 2016-08-09 2018-02-07 Ｊｆｅスチール株式会社 高強度厚鋼板およびその製造方法
WO2018030186A1 (ja) * 2016-08-09 2018-02-15 Ｊｆｅスチール株式会社 高強度厚鋼板およびその製造方法

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SERAJZADEH S ET AL: "Prediction of temperature distribution in the hot rolling of slabs; Prediction of temperature distribution", MODELLING AND SIMULATION IN MATERIALS SCIENCE AND ENGINEERING, IOP PUBLISHING, BRISTOL, GB, vol. 10, no. 2, 1 March 2002 (2002-03-01), pages 185 - 203, XP020072682, ISSN: 0965-0393, DOI: 10.1088/0965-0393/10/2/306 *

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WO2013099318A1 (ja) 2013-07-04
KR20140097463A (ko) 2014-08-06
BR112014015779B1 (pt) 2019-04-09
KR101588258B1 (ko) 2016-01-25
EP2799584A4 (en) 2015-01-07
BR112014015779A2 (pt) 2017-06-13
JP5304925B2 (ja) 2013-10-02
BR112014015779A8 (pt) 2017-07-04
CN104024462B (zh) 2016-03-23
CN104024462A (zh) 2014-09-03
EP2799584A1 (en) 2014-11-05
JP2013151732A (ja) 2013-08-08

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