WO2014155440A1 - Plaque d'acier épaisse de haute résistance pour un soudage à apport de chaleur élevé dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes et procédé de fabrication associé - Google Patents

Plaque d'acier épaisse de haute résistance pour un soudage à apport de chaleur élevé dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes et procédé de fabrication associé Download PDF

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WO2014155440A1
WO2014155440A1 PCT/JP2013/006309 JP2013006309W WO2014155440A1 WO 2014155440 A1 WO2014155440 A1 WO 2014155440A1 JP 2013006309 W JP2013006309 W JP 2013006309W WO 2014155440 A1 WO2014155440 A1 WO 2014155440A1
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plate thickness
rolling
less
steel
brittle crack
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PCT/JP2013/006309
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Japanese (ja)
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長谷　和邦
佳子 竹内
三田尾　眞司
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Ｊｆｅスチール株式会社
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Priority to JP2013549634A priority Critical patent/JP5598618B1/ja
Priority to KR1020157028785A priority patent/KR101732997B1/ko
Priority to BR112015020815-0A priority patent/BR112015020815B1/pt
Priority to CN201380075070.7A priority patent/CN105102650B/zh
Publication of WO2014155440A1 publication Critical patent/WO2014155440A1/fr
Priority to PH12015501719A priority patent/PH12015501719A1/en

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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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C22C38/48—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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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 high-strength thick steel plate for high-heat input welding having excellent brittle cracking arrestability and a method for producing the same, and more particularly to a ship. It relates to a plate having a thickness of 50 mm or more suitable for use.
  • Ni steel As a means of improving the brittle crack propagation stopping characteristics of steel materials, a method of increasing the Ni content has been conventionally known. In a liquefied natural gas (LNG) storage tank, 9% Ni steel is commercially available. Used on a scale.
  • LNG liquefied natural gas
  • TMCP Thermo-Mechanical Control Process
  • Patent Document 1 a steel material in which the structure of the surface layer portion is ultrafine (ultra-fine-grained-steel) is proposed in Patent Document 1.
  • Patent Document 1 focuses on the fact that shear lips (plastic deformation regions shear-lips) that occur in the steel surface layer when brittle cracks propagate are effective in improving the brittle crack propagation stopping characteristics.
  • shear lips plastic deformation regions shear-lips
  • Patent Document 1 discloses that the surface layer portion is cooled below the Ar3 transformation point by controlled cooling after hot rolling, and then the controlled cooling is stopped to bring the surface layer portion above the transformation point.
  • the process of recuperate is repeated one or more times, and during this time, the steel material is subjected to reduction, and it is repeatedly transformed or processed and recrystallized, so that a superfine ferrite structure or bainite structure is formed on the surface layer portion. (bainite structure) is generated.
  • both surface portions of the steel material have a circle-equivalent average grain. size): 5 ⁇ m or less
  • aspect ratio of aspect ratio: a layer having 50% or more of a ferrite structure having two or more ferrite grains, and suppressing variation in ferrite grain size is important.
  • the maximum rolling reduction per pass during finish rolling is set to 12% or less to suppress the local recrystallization phenomenon.
  • Patent Document 3 attention is paid not only to the refinement of ferrite crystal grains but also to subgrains formed in ferrite crystal grains, and a technique on the extension of TMCP that improves brittle crack propagation stop characteristics. Is described.
  • a) rolling conditions for securing fine ferrite crystal grains without requiring complicated temperature control such as cooling and recuperation of the steel sheet surface layer (b) Rolling conditions for generating a fine ferrite structure in a portion of 5% or more of the steel sheet thickness, (c) Dislocation introduced by machining (rolling) and development of texture in the fine ferrite by thermal energy
  • the brittle crack propagation stop property is improved by rolling conditions for rearrangement to form subgrains and (d) cooling conditions for suppressing coarsening of the formed fine ferrite crystal grains and fine subgrain grains.
  • Patent Document 4 discloses that the (110) plane X intensity ratio (X-ray plane intensity ratio in the (110) plane showing a texture developing degree) is 2 or more by controlled rolling and the equivalent circle diameter (diameter equivalent). To a circle in the crystal grains) It is described that the brittle fracture resistance is improved by making coarse grains of 20 ⁇ m or more 10% or less.
  • Patent Document 5 is characterized in that, as a welded structural steel having excellent brittle crack propagation stopping performance in a joint part, the (100) plane X-ray plane strength ratio in the rolled surface inside the plate thickness is 1.5 or more. Steel sheet is disclosed, and it is described that excellent brittle crack propagation stopping characteristics can be obtained by the deviation of the angle between the stress load direction and the crack propagation direction due to the texture development.
  • Japanese Patent Publication No. 7-100814 JP 2002-256375 A Japanese Patent No. 3467767 Japanese Patent No. 3548349 Japanese Patent No. 2659661 Japanese Patent No. 3546308
  • Non-Patent Document 1 evaluates the brittle crack propagation stopping performance of a steel plate having a thickness of 65 mm, and reports a result that the brittle crack does not stop in a large-scale brittle crack propagation stopping test of the base material.
  • the Kca value at the use temperature of ⁇ 10 ° C. (hereinafter also referred to as Kca ( ⁇ 10 ° C.)) satisfies 3000 N / mm 3/2 .
  • Kca ( ⁇ 10 ° C.) satisfies 3000 N / mm 3/2 .
  • the steel sheet having a thickness of about 50 mm is the main target of the steel sheets having excellent brittle crack propagation stopping characteristics described in Patent Documents 1 to 5 described above.
  • Patent Documents 1 to 5 When the techniques described in Patent Documents 1 to 5 are applied to a thick material exceeding 50 mm, it is unclear whether the predetermined characteristics can be obtained, and the characteristics against crack propagation in the plate thickness direction necessary for the hull structure are completely different. Not verified.
  • the welding work requires high efficiency such as submerged arc welding, electrogas welding, electroslag welding, etc.
  • Heat input welding is applied.
  • the structure of the weld heat-affected zone (HeatffAffected; Zone; HAZ) becomes coarse, so that the toughness of the weld heat-affected zone decreases.
  • steel materials for high heat input welding have already been developed and put to practical use.
  • Patent Document 6 by controlling TiN precipitated in steel, it prevents coarsening of the weld heat affected zone structure and promotes intragranular ferrite transformation by dispersion of ferrite forming nuclei.
  • a technique for increasing the toughness of the weld heat affected zone is disclosed.
  • the toughness of the weld heat-affected zone of the high heat input weld zone is excellent, the brittle crack propagation stop property is not taken into consideration, and those satisfying both properties have not been obtained.
  • the present invention optimizes the steel composition and rolling conditions, controls the texture in the thickness direction, and has high brittle crack propagation stopping characteristics that can be stably manufactured by an extremely simple process industrially.
  • An object of the present invention is to provide a high-strength thick steel plate and a method for producing the same.
  • FIGS. 1A and 1B are diagrams schematically showing an example in which propagation of a crack 3 entering from a notch 2 of a standard ESSO test piece 1 stops at a tip shape 4 in a base material 5, and is schematically shown in FIG. It was confirmed that high arrestability was obtained when the short crack branch 3a as shown was confirmed. It is presumed that the stress is relieved by the crack branch 3a. 2.
  • the steel structure mainly composed of bainite in which a packet or the like is present is more advantageous than the steel structure mainly composed of ferrite, and the (100) surface which is a cleavage plane is propagated by cracks. It is effective to accumulate at an angle with respect to the rolling direction or the sheet width direction. 3.
  • the degree of integration on the (100) plane is too high, a large crack branch is generated from a very short crack branch.
  • Non-Patent Document 2 showing the design guideline for brittle crack arrest of ship structure, it is necessary to suppress the branching of brittle cracks in the standard ESSO test.
  • the texture at the center of the plate thickness is controlled by performing rolling in which the difference between the rolling temperature of the first pass and the rolling temperature of the last pass is 40 ° C. or less by controlling the texture at the center of the plate thickness to 40 to 70%. Can be realized. 6).
  • the composite sulfides of TiN, CaS and MnS are finely divided to suppress grain growth when exposed to high temperatures of welding, and in the subsequent cooling process It is effective to promote internal transformation and refine the heat affected zone structure at room temperature.
  • the present invention has been made by further study based on the obtained knowledge. That is, the present invention 1.
  • Steel composition is mass%, C: 0.03-0.15%, Si: 0.01-0.5%, Mn: 1.40-2.50%, Al: 0.005-0.08 %, P: 0.03% or less, S: 0.0005 to 0.0030%, N: 0.0036 to 0.0070%, Ti: 0.004 to 0.030%, Ca: 0.0005 to 0 .0030%, and each content of Ca, S, and O satisfies the following formula (1), the balance is Fe and inevitable impurities, the metal structure is mainly bainite, and the central portion of the plate thickness
  • the RD // (110) plane has a texture of 1.5 to 4.0, and the Charpy fracture surface transition temperature vTrs in the surface layer portion and the thickness center portion is ⁇ 40 ° C.
  • High strength thick steel plate for high heat input welding with excellent brittle crack propagation stopping characteristics. 0.30 ⁇ (Ca ⁇ (0.18 + 130 ⁇ Ca) ⁇ O) /1.25/S ⁇ 0.80 (1) However, in Formula (1), Ca, O, and S are made into content (mass%). 2.
  • the steel composition is further mass%, Nb: 0.05% or less, Cu: 1.0% or less, Ni: 1.0% or less, Cr: 0.5% or less, Mo: 0.5% or less, V: 0.2% or less, B: 0.003% or less, REM: 0.01% or less of one type or two or more types, which is excellent in brittle crack propagation stop property according to 1. High strength thick steel plate for high heat input welding. 3.
  • t is a plate thickness (mm).
  • the steel material having the composition described in 4.1 or 2 is heated to a temperature of 1000 to 1200 ° C., and rolling with a total cumulative rolling reduction of 65% or more in the austenite recrystallization temperature range and the austenite non-recrystallization temperature range is performed.
  • the rolling reduction is performed at a cumulative reduction ratio of 20% or more, and then in the state where the plate thickness central portion is in the austenite non-recrystallization temperature range.
  • the heat input is excellent in brittle crack propagation stopping characteristics, characterized in that the difference is within 40 ° C. and then cooled to 450 ° C. or lower at a cooling rate of 4.0 ° C./s or higher.
  • Method of producing a high strength steel plate for contact. 5 After accelerated cooling to 450 ° C. or lower, and further tempering to a temperature of A c1 point or lower, the high strength thickness for high heat input welding having excellent brittle crack propagation stopping characteristics according to 4 A method of manufacturing a steel sheet.
  • the present invention it is possible to obtain a high-strength thick steel plate and a method for producing the same, in which the texture is appropriately controlled in the plate thickness direction, and the brittle crack propagation stop property and the high heat input weld joint toughness are excellent.
  • Applying the present invention to a steel plate having a plate thickness of 50 mm or more, preferably more than 50 mm, more preferably 55 mm or more, and even more preferably 60 mm or more is more significant than the steel according to the prior art. It is effective because it demonstrates its properties. And, for example, in the shipbuilding field, it contributes to improving the safety of ships by applying the present invention to hatch side combing and deck members in the structure of large container ships and bulk carrier strong deck parts. .
  • FIG. 1 is a diagram schematically showing a fracture surface form of a standard ESSO test of a thick steel plate having a thickness of more than 50 mm, (a) is a view of the test piece observed from the plane side, and (b) is a fracture of the test piece. It is a figure which shows a surface.
  • C 0.03-0.15%
  • C is an element that improves the strength of steel, and in the present invention, it is necessary to contain 0.03% or more in order to ensure a desired strength. On the other hand, if it exceeds 0.15%, the weldability is deteriorated and the toughness is also adversely affected. Therefore, C is specified in the range of 0.03 to 0.15%. Preferably, it is 0.05 to 0.15%.
  • Si 0.01 to 0.5% Si is effective as a deoxidizing element and as a steel strengthening element. However, when the content is less than 0.01%, the effect is not obtained. On the other hand, if it exceeds 0.5%, not only the surface properties of the steel are impaired, but also the toughness is extremely deteriorated. Therefore, the addition amount is set to 0.01 to 0.5%. Preferably, it is 0.02 to 0.45% of range.
  • Mn 1.40-2.50% Mn is added as a strengthening element. If less than 1.40%, the effect is not sufficient. On the other hand, if it exceeds 2.50%, the weldability deteriorates and the steel material cost also increases. Therefore, Mn is set to 1.40 to 2.50%. Preferably, it is in the range of 1.42 to 2.40%.
  • P 0.03% or less
  • the toughness of the welded portion is significantly deteriorated.
  • the upper limit is made 0.03%.
  • it is 0.02% or less.
  • S 0.0005 to 0.0030%
  • S is required to be 0.0005% or more in order to generate necessary CaS and MnS.
  • S is set to 0.0005 to 0.0030%.
  • it is in the range of 0.0006 to 0.0025%.
  • Al acts as a deoxidizing agent, and for this purpose, a content of 0.005% or more is required. However, when it contains exceeding 0.08%, while reducing toughness, when welding, the toughness of a weld metal part will be reduced. For this reason, Al is specified in the range of 0.005 to 0.08%. Preferably, it is 0.02 to 0.06%.
  • Ti can form nitrides, carbides, or carbonitrides by adding a small amount, suppress austenite coarsening in the weld heat affected zone, and / or promote ferrite transformation as a ferrite transformation nucleus. This has the effect of refining the crystal grains and improving the base material toughness. The effect is obtained by adding 0.004% or more. However, the content exceeding 0.030% reduces the toughness of the base material and the weld heat affected zone due to the coarsening of the TiN particles. Therefore, Ti is set in the range of 0.004 to 0.030%. Preferably, it is 0.006 to 0.028% of range.
  • N 0.0036 to 0.0070%
  • N is an element necessary for securing the necessary amount of TiN. If it is less than 0.0036%, a sufficient amount of TiN cannot be obtained, and the weld toughness deteriorates. If it exceeds 0.0070%, TiN will re-dissolve when subjected to the welding heat cycle, and excessive N will be generated and the toughness will deteriorate significantly. For this reason, N is made 0.0036 to 0.0070%. Preferably, it is 0.0038 to 0.0065% of range.
  • Ca 0.0005 to 0.0030%
  • Ca is an element having an effect of improving toughness by fixing S. In order to exhibit such an effect, it is necessary to contain at least 0.0005% or more. However, the effect is saturated even if the content exceeds 0.0030%. Therefore, in the present invention, Ca is limited to the range of 0.0005 to 0.0030%. Preferably, it is in the range of 0.0007 to 0.0028%.
  • the above is the basic component composition of the present invention.
  • Nb 0.05% or less Nb precipitates as NbC during ferrite transformation or reheating, and contributes to increasing the strength. In addition, it has the effect of expanding the non-recrystallization temperature range in rolling in the austenite range, and contributes to the fine graining of bainite packets, so it is also effective in improving toughness. Since the effect is exhibited by containing 0.005% or more, when it contains, it is preferable to make it 0.005% or more. However, if added over 0.05%, coarse NbC precipitates and conversely causes a decrease in toughness. When it is contained, the upper limit is preferably made 0.05%. More preferably, it is in the range of 0.007 to 0.045%.
  • Cu, Ni, Cr, Mo Cu, Ni, Cr, and Mo are all elements that enhance the hardenability of steel. While contributing directly to strength enhancement after rolling, it can be added to improve functions such as toughness, high-temperature strength, or weather resistance, since these effects are exhibited by containing 0.01% or more, When contained, the content is preferably 0.01% or more. However, if it is excessively contained, toughness and weldability are deteriorated. Therefore, when it is included, the upper limit is 1.0% for Cu, 1.0% for Ni, 0.5% for Cr, and 0.5% for Mo. % Is preferable. More preferably, Cu: 0.02 to 0.95%, Ni: 0.02 to 0.95%, Cr: 0.02 to 0.46%, Mo: 0.02 to 0.46% is there.
  • V 0.2% or less
  • V is an element that improves the strength of steel by precipitation strengthening as V (C, N), and may be contained by 0.001% or more in order to exert this effect. However, when it contains exceeding 0.2%, toughness will be reduced. Therefore, when V is contained, the content is preferably 0.2% or less, and more preferably in the range of 0.001 to 0.10%.
  • B 0.003% or less
  • B is an element that enhances the hardenability of steel in a small amount, and may be contained by 0.0005% or more in order to exert this effect. However, if it exceeds 0.003%, the toughness of the welded portion is lowered. Therefore, when B is contained, the content is preferably 0.003% or less. More preferably, it is in the range of 0.0006 to 0.0025%.
  • REM 0.01% or less REM refines the structure of the weld heat-affected zone to improve toughness, and even if added, the effect of the present invention is not impaired, so it may be added as necessary. Since this effect is exhibited by containing 0.0010% or more, when it is contained, the content is preferably 0.0010% or more. However, if added excessively, coarse inclusions are formed and the toughness of the base material is deteriorated. Therefore, when added, the upper limit of the addition amount is preferably 0.01%.
  • O is contained in steel as an unavoidable impurity and reduces cleanliness. For this reason, in the present invention, it is desirable to reduce O as much as possible.
  • the O content exceeds 0.0050%, CaO inclusions are coarsened and the base material toughness is lowered. For this reason, Preferably it is 0.0050% or less.
  • the present invention in order to crystallize Ca as CaS, it is necessary to reduce the amount of O having strong binding force with Ca before adding Ca, and the residual oxygen amount before adding Ca is 0.0050%.
  • the following is preferable.
  • a method for reducing the amount of residual oxygen a method such as enhancing degassing or introducing a deoxidizer can be employed.
  • the balance other than the above components is Fe and inevitable impurities.
  • the brittle crack propagation stop property is exhibited for cracks that develop in the horizontal direction (in-plane direction of the steel sheet) such as the rolling direction or the direction perpendicular to the rolling direction.
  • the toughness at the surface thickness layer and the central portion and the degree of integration of the RD // (100) plane at the central portion of the thickness are appropriately defined according to the desired brittle crack propagation stop characteristics.
  • the Charpy fracture surface transition temperature at the plate thickness surface layer portion and the central portion is defined as ⁇ 40 ° C. or less as the toughness at the plate thickness surface layer portion and the center portion.
  • the Charpy fracture surface transition temperature at the center of the plate thickness is preferably ⁇ 50 ° C. or lower.
  • the cleavage plane is accumulated obliquely with respect to the main crack direction, and the effect of stress relaxation at the brittle crack tip by generating fine crack branching causes brittleness.
  • the crack propagation stop performance is improved.
  • the degree of integration of the RD // (110) plane in the central portion of the plate thickness needs to be 1.5 or more, preferably 1.7 or more. Therefore, in the present invention, the degree of integration of the RD // (110) plane at the center of the plate thickness is 1.5 or more, preferably 1.7 or more.
  • the integration degree of the RD // (110) plane is set to a range of 1.5 to 4.0.
  • the degree of integration of the RD // (110) plane in the central portion of the plate thickness refers to the following.
  • a sample with a plate thickness of 1 mm is taken from the center of the plate thickness, and a test piece for X-ray diffraction is prepared by mechanically polishing and electrolytic polishing a surface parallel to the plate surface.
  • an X-ray diffraction measurement was performed using an X-ray diffractometer using a Mo ray source, and (200), (110) and (211) positive electrode dot diagrams were obtained and obtained.
  • a three-dimensional crystal orientation density function is calculated from the positive electrode dot diagram by the Bunge method.
  • the integrated value is obtained by integrating the values of the three-dimensional crystal orientation density function of the orientation, and the value obtained by dividing the integrated value by the number of the integrated orientations is referred to as the degree of integration of the RD // (110) plane.
  • the Charpy fracture surface transition temperature at the center of the plate thickness and the degree of integration of the RD // (110) plane satisfy the following formula (2) in addition to the above-mentioned provisions of the base material toughness and texture.
  • formula (2) further excellent brittle crack propagation stopping performance can be obtained.
  • vTrs (1 / 2t) Charpy fracture surface transition temperature (° C.) at the center of the plate thickness I RD // (110) [1 / 2t] : RD // (110) integration degree at the center of the plate thickness.
  • t is a plate thickness (mm).
  • the degree of integration of the RD // (110) plane can be 1.5 or more, preferably 1.7 or more.
  • the metal structure obtained after rolling and cooling is mainly bainite.
  • that the metal structure is mainly bainite is that the area fraction of the bainite phase is 80% or more of the whole. The balance is acceptable if ferrite, martensite (including island martensite), pearlite, etc. are 20% or less in total area fraction.
  • the heating temperature, hot rolling conditions, cooling conditions, etc. of the steel material As manufacturing conditions, it is preferable to prescribe the heating temperature, hot rolling conditions, cooling conditions, etc. of the steel material.
  • hot rolling in addition to the cumulative reduction ratio in the sum of the austenite recrystallization temperature range and the austenite non-recrystallization temperature range, the case where the central portion of the plate thickness is in the austenite recrystallization temperature range, It is preferable to define the cumulative rolling reduction for each of the cases in the temperature range and the rolling temperature conditions in a state where the central portion of the plate thickness is in the austenite non-recrystallized region.
  • the Charpy fracture surface transition temperature vTrs in the surface layer portion and the plate thickness center portion of the thick steel plate, and the RD // (110) integration degree in the plate thickness center portion can be set to desired values.
  • molten steel having the above composition is melted in a converter or the like, and is made into a steel material (slab) by continuous casting or the like.
  • the heating temperature is preferably 1000 to 1200 ° C.
  • a more preferable heating temperature range is 1000 to 1150 ° C. from the viewpoint of toughness.
  • the degree of integration of the RD // (110) plane can be 1.5 or more, preferably 1.7 or more.
  • the hot rolling first, it is preferable to perform rolling with a cumulative reduction ratio of 20% or more in a state where the central portion of the plate thickness is in the austenite recrystallization temperature region.
  • a cumulative reduction ratio of 20% or more in a state where the central portion of the plate thickness is in the austenite recrystallization temperature region.
  • the cumulative reduction ratio of 40 to 70% or more in a state where the temperature at the center of the plate thickness is in the austenite non-recrystallization temperature range.
  • the cumulative reduction ratio in this temperature range is 40% or more, the texture at the center of the plate thickness is sufficiently developed, and the degree of integration of the RD // (110) plane at the center of the plate thickness is 1.5 or more. , And preferably 1.7 or more.
  • the range of the cumulative rolling reduction is set to 40 to 70%.
  • the rolling temperature refers to the temperature at the center of the plate thickness of the steel just before rolling.
  • the temperature at the center of the plate thickness is obtained by simulation calculation or the like from the plate thickness, surface temperature, thermal history, and the like. For example, the temperature at the center of the plate thickness of the steel sheet is obtained by calculating the temperature distribution in the plate thickness direction using the difference method.
  • the total cumulative rolling reduction of the austenite recrystallization temperature range and the austenite non-recrystallization temperature range be 65% or more.
  • the overall rolling reduction is small, the rolling of the structure is not sufficient, and the toughness and strength cannot achieve the target values.
  • the total cumulative reduction ratio By setting the total cumulative reduction ratio to 65% or more, a sufficient amount of reduction can be ensured for the structure, and the toughness and the degree of accumulation can achieve the target values.
  • the austenite recrystallization temperature range and the austenite non-recrystallization temperature range can be grasped by conducting a preliminary experiment in which the steel having the component composition is given a heat / working history with varying conditions.
  • end temperature of hot rolling is not particularly limited. From the viewpoint of rolling efficiency, it is preferable to terminate in the austenite non-recrystallization temperature range.
  • the rolled steel sheet is cooled to 450 ° C. or lower at a cooling rate of 4.0 ° C./s or higher.
  • the cooling rate is less than 4.0 ° C./s, the coarsening of the structure and ferrite transformation proceed at each plate thickness position, so that a desired structure cannot be obtained and the strength of the steel sheet also decreases.
  • the bainite transformation can be sufficiently advanced, and desired toughness and integration degree can be obtained. If the cooling stop temperature is higher than 450 ° C., the bainite transformation does not proceed sufficiently, and a structure such as ferrite or pearlite is also produced, and the bainite-based structure intended by the present invention cannot be obtained.
  • these cooling rate and cooling stop temperature be the temperature of the plate
  • Tempering temperature as follows C1 points A steel plate average temperature, by carrying out the tempering treatment, it is possible not impair the desired tissue obtained by rolling and cooling.
  • the AC1 point (° C.) is obtained by the following equation.
  • a C1 point 751-26.6C + 17.6Si-11.6Mn-169Al-23Cu-23Ni + 24.1Cr + 22.5Mo + 233Nb-39.7V-5.7Ti-895B
  • each element symbol is the content (% by mass) in steel, and 0 if not contained.
  • the average temperature of the steel sheet can also be obtained by simulation calculation or the like from the sheet thickness, surface temperature, cooling conditions, etc., similarly to the temperature at the center of the sheet thickness.
  • Molten steel (steel symbols A to Q) of each composition shown in Table 1 was melted in a converter and made into a steel material (slab 250 mm thickness or 300 mm thickness) by a continuous casting method. After hot rolling to a plate thickness of 55 to 100 mm, Cooling is performed, and no. Sample steels of 1 to 27 were obtained. Some were tempered after cooling. Table 2 shows hot rolling conditions and cooling conditions.
  • a JIS14A test piece having a diameter of 14 mm was collected from 1/4 part of the plate thickness so that the longitudinal direction of the test piece was perpendicular to the rolling direction, a tensile test was performed, and the yield strength (YS) and Tensile strength (TS) was measured.
  • the longitudinal direction of the test piece was measured in accordance with the JIS No. 4 impact test piece from the plate thickness surface layer portion and the plate thickness central portion (hereinafter, the plate thickness central portion may be referred to as a 1/2 t portion). Samples were taken so as to be parallel to the rolling direction, and Charpy impact tests were performed to determine fracture surface transition temperatures (vTrs).
  • the impact test piece of the surface layer part is assumed to have a surface closest to the surface at a depth of 1 mm from the steel sheet surface.
  • the degree of integration of the RD // (110) plane at the center of the plate thickness was determined as follows. First, a sample having a plate thickness of 1 mm was collected from the central portion of the plate thickness, and a test piece for X-ray diffraction was prepared by mechanically polishing and electrolytic polishing a surface parallel to the plate surface. Using this test piece, X-ray diffraction measurement was performed using an X-ray diffractometer using a Mo ray source, and (200), (110) and (211) positive electrode dot diagrams were obtained, and the obtained positive electrode A three-dimensional crystal orientation distribution density function is calculated from the dot diagram by the Bunge method.
  • test steel sheet was subjected to groove processing (groove angle 20 °), and heat input 300 was performed by electrogas welding using a commercially available wire for electrogas arc welding for low temperature steel.
  • a welded joint was prepared at ⁇ 750 kJ / cm, and the toughness of the bond portion was evaluated by a 2 mmV notch Charpy test as HAZ toughness.
  • the test was performed with vE -20 (average value of three) of Charpy absorbed energy at -20 ° C.
  • Table 3 shows the results of these tests.
  • the test steel plates (production Nos. 1 to 11) within the scope of the present invention exhibited excellent brittle crack propagation stopping performance with a Kca ( ⁇ 10 ° C.) of 6000 N / mm 3/2 or more. Further, the absorbed energy of the bond portion of the high heat input welded joint was vE-20 ⁇ 88 J, which was an excellent value. Further, in the test steel plates (manufacturing numbers 2 to 11) in which the Charpy toughness value (fracture surface transition temperature) of the surface layer portion and the center portion of the plate thickness and the RD // (110) accumulation degree satisfy the formula (2) Compared with the test steel plate (Production No. 1) not satisfying the formula (2), a higher Kca ( ⁇ 10 ° C.) value was obtained. Note that the metal structures of these test steel sheets (production Nos. 1 to 11) were mainly bainite.
  • the steel plate component is within the preferred range of the present invention
  • the steel plate (production Nos. 20 to 27) whose heating and rolling conditions are outside the preferred range of the present invention is Kca ( ⁇ 10 ° C.). The value did not reach 6000 N / mm 3/2 .
  • the absorbed energy of the large heat input welded joint: vE- 20 is 22 J or less, which is inferior to the present invention example. It was.

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Abstract

L'invention concerne une plaque d'acier épaisse de haute résistance pour un soudage à apport de chaleur élevé, la plaque d'une épaisseur de plaque préférée d'au moins 50 mm est mise en œuvre sur des navires et dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et un procédé de fabrication associé. Une plaque d'acier épaisse présentant une composition en constituants spécifique, le constituant principal de la structure métallique étant de la bainite, la plaque d'acier épaisse possédant une texture dans laquelle la densité d'une dans le plan RD//(110) au niveau de la partie centrale de l'épaisseur de plaque est de 1,5 à 4,0, et présente une température de transition de fracture de Charpy (vTrs) au niveau de la couche superficielle et de la partie centrale de l'épaisseur de plaque inférieure ou égale à -40 °C, et un procédé de fabrication associé.
PCT/JP2013/006309 2013-03-26 2013-10-24 Plaque d'acier épaisse de haute résistance pour un soudage à apport de chaleur élevé dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes et procédé de fabrication associé WO2014155440A1 (fr)

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JP2013549634A JP5598618B1 (ja) 2013-03-26 2013-10-24 脆性亀裂伝播停止特性に優れた大入熱溶接用高強度厚鋼板およびその製造方法
KR1020157028785A KR101732997B1 (ko) 2013-03-26 2013-10-24 취성 균열 전파 정지 특성이 우수한 대입열 용접용 고강도 후강판 및 그의 제조 방법
BR112015020815-0A BR112015020815B1 (pt) 2013-03-26 2013-10-24 Chapa de aço grossa de alta resistência para soldagem de elevado aporte de calor com excelente capacidade de interrupção de ruptura frágil e método para fabricação da mesma
CN201380075070.7A CN105102650B (zh) 2013-03-26 2013-10-24 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
PH12015501719A PH12015501719A1 (en) 2013-03-26 2015-08-04 High strength thick steel plate for high heat input welding with excellent brittle crack arrestability and manufacturing method therefor

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WO2017145651A1 (fr) * 2016-02-24 2017-08-31 Ｊｆｅスチール株式会社 Tôle d'acier ultra-épaisse de haute résistance, ayant d'excellentes caractéristiques d'arrêt de la propagation des fissures fragiles et son procédé de fabrication
JP2017160537A (ja) * 2016-03-07 2017-09-14 Ｊｆｅスチール株式会社 脆性き裂伝播停止特性および溶接熱影響部靭性に優れた高強度極厚鋼板およびその製造方法
WO2018030186A1 (fr) * 2016-08-09 2018-02-15 Ｊｆｅスチール株式会社 Plaque d'acier épaisse de haute résistance et son procédé de fabrication
WO2023219146A1 (fr) * 2022-05-12 2023-11-16 Ｊｆｅスチール株式会社 Tôle d'acier, et procédé de fabrication de celle-ci

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CN106702269A (zh) * 2015-11-17 2017-05-24 鞍钢股份有限公司 一种高强高韧性厚钢板及其生产方法
KR101819356B1 (ko) * 2016-08-08 2018-01-17 주식회사 포스코 취성균열전파 저항성이 우수한 극후물 강재 및 그 제조방법
KR102193527B1 (ko) * 2016-08-09 2020-12-21 제이에프이 스틸 가부시키가이샤 고강도 후강판 및 그의 제조 방법
JP6869151B2 (ja) * 2016-11-16 2021-05-12 株式会社神戸製鋼所 鋼板およびラインパイプ用鋼管並びにその製造方法
CN110076196B (zh) * 2019-05-15 2020-05-22 南京钢铁股份有限公司 一种集装箱船用止裂钢的生产方法

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WO2017145651A1 (fr) * 2016-02-24 2017-08-31 Ｊｆｅスチール株式会社 Tôle d'acier ultra-épaisse de haute résistance, ayant d'excellentes caractéristiques d'arrêt de la propagation des fissures fragiles et son procédé de fabrication
JPWO2017145651A1 (ja) * 2016-02-24 2018-03-08 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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JP7468800B2 (ja) 2022-05-12 2024-04-16 Ｊｆｅスチール株式会社 鋼板およびその製造方法

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BR112015020815A2 (pt) 2017-07-18
TWI523957B (zh) 2016-03-01
BR112015020815B1 (pt) 2021-06-29
KR20150126697A (ko) 2015-11-12
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