WO2017047088A1 - Tôle d'acier épaisse à haute résistance pour une utilisation structurale et son procédé de fabrication - Google Patents

Tôle d'acier épaisse à haute résistance pour une utilisation structurale et son procédé de fabrication Download PDF

Info

Publication number
WO2017047088A1
WO2017047088A1 PCT/JP2016/004223 JP2016004223W WO2017047088A1 WO 2017047088 A1 WO2017047088 A1 WO 2017047088A1 JP 2016004223 W JP2016004223 W JP 2016004223W WO 2017047088 A1 WO2017047088 A1 WO 2017047088A1
Authority
WO
WIPO (PCT)
Prior art keywords
thick steel
less
brittle crack
thickness
vtrs
Prior art date
Application number
PCT/JP2016/004223
Other languages
English (en)
Japanese (ja)
Inventor
隆洋 ▲崎▼本
恒久 半田
聡 伊木
Original Assignee
Ｊｆｅスチール株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to CN201680052939.XA priority Critical patent/CN108026618B/zh
Priority to KR1020187006623A priority patent/KR102092000B1/ko
Priority to JP2016568462A priority patent/JP6245384B2/ja
Publication of WO2017047088A1 publication Critical patent/WO2017047088A1/fr

Links

Images

Classifications

    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • C22C38/02—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
    • C22C38/06—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
    • C22C38/12—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
    • C22C38/18—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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a structural steel plate suitable for large steel structures such as ships, marine structures, low-temperature storage tanks, and construction / civil engineering structures, and a method for producing the same. It relates to improvement of brittle crack propagation stopping performance.
  • TEU wenty feet Equivalent Unit
  • Steel materials such as thick steel plates used in large steel structures such as ships have excellent low temperature toughness and excellent brittle crack propagation stop toughness values at operating temperatures from the viewpoint of ensuring the safety of the structure. It is required to have. In particular, even if a brittle crack occurs, it is necessary to stop the propagation of the brittle crack before it reaches a large-scale fracture.
  • the toughness value (hereinafter also referred to as “arrest performance”) is an important characteristic.
  • Patent Document 1 describes a structural high-strength thick steel plate having excellent brittle crack propagation stopping characteristics.
  • the technology described in Patent Document 1 includes, in mass%, C: 0.03-0.20%, Si: 0.03-0.5%, Mn: 0.5-2.0%, Al: 0.005-0.08%, or Ti: 0.005- 0.03%, Nb: 0.005-0.05%, Cu: 0.01-0.5%, Ni: 0.01-1.0%, Cr: 0.01-0.5%, Mo: 0.01-0.5%, V: 0.001-0.1%, B: 0.003% or less , Ca: 0.005% or less, REM: 0.01% or less steel material containing one or more of them is heated to a temperature of 900-1200 ° C, and the temperature at the center of the plate thickness is Ar 3 or higher Cumulative rolling reduction: 30% or more, and rolling at a rolling temperature of 30% or more in the temperature range where the temperature at the center of the sheet thickness is Ar 3 points or less Ar 3 points -60 ° C or more, then
  • the (100) plane X-ray intensity ratio is 2.0 or more and the thickness is 1/4 portion.
  • Patent Document 2 describes a thick steel plate having a thickness of 50 mm or more, which is excellent in long brittle crack propagation stopping characteristics, and a manufacturing method thereof.
  • the technique described in Patent Document 2 includes, in mass%, C: 0.15% or less, Si: 0.60% or less, Mn: 0.80 to 1.80%, S: 0.001 to 0.05%, Ti: 0.005 to 0.050%, or Nb : Containing at least one selected from 0.001 to 0.1%, Cu: 2.0% or less, V: 0.2% or less, Ni: 2.0% or less, Cr: 0.6% or less, Mo: 0.6% or less, W : A steel material containing one or more selected from 0.5% or less, B: 0.0050% or less, Zr: 0.5% or less is heated to a temperature of 900-1300 ° C, and a surface temperature of 1000-850 After rolling at a cumulative reduction ratio of 10% or more in the temperature range of °C, the surface temperature is 900-600 °C and the internal temperature is 50-
  • the X-ray intensity ratio of the (211) surface or (100) surface at the rolled surface in the region of at least 20% of the plate thickness at the center of the plate thickness is 1.5 or more, and 1/4 to 1/1 of the plate thickness.
  • the tip shape of the brittle crack propagation stop in the cross section in the thickness direction of the fracture surface of the steel sheet is from 1/4 to 1/1 / of the plate thickness from the steel plate surface.
  • Thick steel plate that forms a concave recess with a maximum crack length of 10 or 3/4 to 9/10 of the plate thickness which is at least as long as the plate thickness and shorter than the direction of the brittle crack. It is said that long brittle cracks, which have been difficult in conventional thick steel plates, can be stopped even under conditions without stress reflection.
  • Patent Document 3 describes a method for producing a structural high-strength thick steel plate having a plate thickness of 50 mm or more and excellent brittle crack propagation stopping characteristics.
  • C 0.03-0.20%, Si: 0.03-0.5%, Mn: 0.5-2.2%, Al: 0.005-0.08%, P: 0.03% or less, S: 0.01% or less, N: 0.0050% or less, Ti: 0.005-0.03%, or Nb: 0.005-0.05%, Cu: 0.01-0.5%, Ni: 0.01-1.0%, Cr: 0.01-0.5%,
  • the total rolling reduction in the austenite recrystallization temperature range and the austenite non-recrystallization temperature range is 65% or more, and
  • the microstructure is mainly composed of ferrite, and the RD // (110) plane integration degree in the surface layer portion is 1.3 or more, and the RD // (110) plane integration degree in the central portion of the plate thickness is 1.8 or more.
  • Patent Document 4 describes a method for producing a structural high-strength thick steel plate having a thickness of 50 mm or more and excellent brittle crack propagation stopping characteristics.
  • C 0.03-0.20%, Si: 0.03-0.5%, Mn: 0.5-2.5%, Al: 0.005-0.08%, P: 0.03% or less, S: 0.01% or less, N: 0.0050% or less, Ti: 0.005-0.03%, or Nb: 0.005-0.05%, Cu: 0.01-0.5%, Ni: 0.01-1.0%, Cr: 0.01-0.5%,
  • the total rolling reduction in the austenite recrystallization temperature range and the austenite non-recrystallization temperature range is 65% or more, and the cumulative reduction rate
  • the cumulative rolling reduction in the state where the center of the plate thickness is in the austenite non-recrystallization temperature range is set to 40% or more and the center of the plate thickness is austenite.
  • rolling is performed so that the difference in rolling temperature between the first pass and the final pass is within 40 ° C, and then 450 ° C at a cooling rate of 4 ° C / s or more. It is supposed to cool to below °C.
  • the structure is mainly bainite
  • the RD // (110) surface has a texture of 1.5 or more in the surface layer
  • the Charpy fracture surface transition temperature in the surface layer and the center of the plate thickness is -40 ° C or less.
  • Patent Document 5 describes “a high-strength thick steel plate excellent in arrestability”.
  • the thick steel sheet described in Patent Document 5 is mass%, C: 0.04 to 0.16%, Si: 0.01 to 0.5%, Mn: 0.75 to 2.5%, Al: 0.001 to 0.1%, Nb: 0.003 to 0.05%, Ti: 0.005 ⁇ 0.05%, N: 0.001 ⁇ 0.008% included, P, S, Cu, Ni, Mo, V, B, Ca, Mg, REM are restricted to below specified values, and the remainder from Fe and inevitable impurities And having a composition with a carbon equivalent Ceq of 0.30 to 0.50%, a ferrite with an area ratio of 70% or less, and a microstructure containing 30% or more of bainite.
  • the grain boundary density which is the total length per unit area of grain boundaries with an orientation difference of 15 ° or more, is 400 to 1000 mm / mm 2 and has an angle within 15 ° with respect to the plane perpendicular to the main rolling direction (
  • the area ratio of the (100) plane is 10 to 40%, and at 1/2 part of the plate thickness, the grain boundary density is 300 to 900 mm / mm 2 and within 15 ° to the plane perpendicular to the main rolling direction.
  • the area ratio of (110) plane with angle is 40-7 It is a 0% high strength thick steel plate.
  • a steel slab having the composition described above is charged as a manufacturing method in a heating furnace having an atmospheric temperature of 1000 to 1250 ° C., and then exceeds a center thickness of 850 ° C. to 1150 ° C.
  • Finishing with ⁇ 15 passes shape ratio average of 0.5 ⁇ 1, cumulative reduction ratio of 40 ⁇ 80%, and then the sheet thickness center temperature is over 700 °C, and the thickness is 2 ⁇ 10 °C / s It is preferable to cool to 550 ° C. or lower at the center cooling rate.
  • the propagation of brittle cracks is suppressed by changing the texture to be developed between 1/2 part of the plate thickness and 1/4 part of the plate thickness.
  • the present invention has been made in view of the problems of the prior art, and an object thereof is to provide a high-strength thick steel plate having a plate thickness of 70 mm or more and excellent brittle crack propagation stopping performance and a method for producing the same.
  • “high strength” refers to the case where the yield strength is 400 N / mm 2 or more.
  • excellent in brittle crack propagation stopping performance here means that the brittle crack propagation stopping toughness value Kca -10 ° C at the hull design temperature of -10 ° C is 9500 N / mm 3/2 or more. It shall be said.
  • the present inventors paid attention to the difference in brittle crack propagation stopping performance at each position in the plate thickness direction in the thick steel plate, and distributed the brittle crack propagation stopping performance at each position in the plate thickness direction.
  • the relationship between the state and the brittle crack propagation stopping performance of the entire thick steel plate was studied. As a result, in a thick steel plate with a thickness of 70 mm or more, the brittle crack propagation stopping performance of the entire thick steel plate can be remarkably improved. Found it to exist.
  • an inner region (plate thickness central region) having a high brittle crack propagation stopping performance and the outer sides thereof are relatively compared with each other. It was found that a thick steel plate consisting of three layers having a region with low brittle crack propagation stopping performance is required. In such a thick steel plate, when a brittle crack propagates (propagates), a step occurs in the vicinity of the boundary between the central portion of the plate thickness and the outer portions thereof, and the brittle crack in which the crack tip branches into three layers. It has been found that the brittle crack propagation stopping performance of the entire thick steel plate changes greatly depending on the combination of the thickness of each layer and its characteristics, since it propagates as a crack.
  • Y vTrs-12 ⁇ I (100) ⁇ 22 ⁇ I (211) (A)
  • vTrs V notch Charpy impact test fracture surface transition temperature (° C)
  • I (100) X-ray diffraction intensity ratio of (100) plane parallel to the rolling surface (plate surface)
  • I (211) X-ray diffraction intensity ratio of (211) plane parallel to the rolling surface (plate surface)
  • I came up with the idea that it can be evaluated easily using the index Y (° C) defined in.
  • This index Y is based on the fracture surface transition temperature (vTrs) of the Charpy impact test and improves the brittle crack propagation stop toughness by taking into account the degree of texture development that affects the improvement of brittle crack propagation stop performance. This is a parameter introduced by some of the present inventors in order to define the fracture surface transition temperature (vTrs) necessary to achieve this. If a texture favorable for improving the brittle crack propagation stopping performance develops and I (100) and I (211) become large, the index Y becomes low temperature.
  • the present inventors use this index Y as an index of brittle crack propagation stopping performance at each position in the plate thickness direction, and in particular, brittle crack propagation stopping performance index Y 1 / 6t at 1/6 position of the plate thickness,
  • the brittle crack propagation stopping performance index Y 1 / 3t at the 1/3 position of the plate thickness and the brittle crack propagation stopping performance index Y 1 / 2t at the 1/2 position of the sheet thickness are expressed by the following equations (1) and (2 ) Formula Y 1 / 3t ⁇ 0.9Y 1 / 2t (1) Y 1 / 6t ⁇ 0.8 Y 1 / 2t (2) It was newly found out that by adjusting so as to satisfy the above, a steel plate having a significantly improved brittle crack propagation stop toughness value Kca in the entire thickness was obtained.
  • Formula (1) means that an internal region (plate thickness central region) having high brittle crack propagation stopping performance exists over a region between at least two plate thickness 1/3 positions.
  • Formula (2) means that the area
  • Y 1 / 2t , Y 1 / 3t and Y 1 / 6t are less than zero.
  • Various types of thick steel plates with a thickness of 70 mm or more were prepared by changing the composition, manufacturing conditions, and the like so that the characteristics at each position in the thickness direction changed. From each of the obtained thick steel plates, a full thickness ESSO test piece (size: t ⁇ 500 ⁇ 500 mm) and a reduced thickness ESSO test piece (size: 20 ⁇ centered on each position in the plate thickness direction) 500 ⁇ 500 mm) was collected.
  • Figure 1 shows a steel plate with brittle crack propagation stopping performance, which shows a high brittle crack propagation stopping toughness value Kca in the plate thickness internal region at 1/2 the plate thickness and 1/3 the plate thickness. Thickness indicating the distribution of brittle crack propagation stopping performance at each position in the plate thickness direction, consisting of three layers, showing a lower brittle crack propagation stopping toughness value Kca at 1/6 of the plate thickness on both outer sides. It is a steel plate.
  • the brittle crack propagation stop toughness value Kca at each position in the plate thickness direction is a result obtained using a test piece with a plate thickness of 20 mm.
  • the brittle crack propagation stopping toughness value Kca of the full thickness is the brittle crack at each position in the plate thickness direction. It is much higher than the crack propagation stop toughness value.
  • This thick steel plate was tested from each position in the plate thickness direction (1/6 position of plate thickness, 1/3 position of plate thickness, 1/2 position of plate thickness) in accordance with the provisions of JIS Z 2242.
  • V-notch Charpy impact test pieces were collected so that the longitudinal direction of the piece was the rolling direction, and the fracture surface transition temperature vTrs at each position in the plate thickness direction was determined.
  • a specimen was taken so that each position in the plate thickness direction (1/6 position of the plate thickness, 1/3 position of the plate thickness, 1/2 position of the plate thickness) of this thick steel plate becomes the measurement surface.
  • the X-ray diffraction intensity ratio between the (100) plane and the (211) plane parallel to the rolling surface (plate surface) was determined by the line diffraction method.
  • the index Y (Y 1 / 6t , Y 1 / 3t , Y 1 / 2t ) at each position in the plate thickness direction is calculated using the above-described equation (A).
  • Y 1 / 6t ⁇ 129 ° C.
  • Y 1 / 3t ⁇ 168 ° C.
  • Y 1 / 2t ⁇ 170 ° C., which satisfies both the above formulas (1) and (2).
  • a thick steel plate having a thickness of 70 mm or more has a high brittleness having a thickness of 1/3 of the total thickness centering on the central position of the plate thickness so as to satisfy the above formulas (1) and (2).
  • An internal region having a crack propagation stopping performance and a region having a thickness of 1/3 of the total plate thickness having a brittle crack propagation stopping performance relatively lower than the internal region are arranged on both outer sides thereof, It is possible to adjust the distribution of brittle crack propagation stop performance at each position in the plate thickness direction so that there are three layers with different brittle crack propagation stop performance in the plate thickness direction. It was found that Kca is important for making a thick steel plate.
  • the present invention has been completed based on such knowledge and further investigation. That is, the gist of the present invention is as follows.
  • Plate thickness t 70 mm or more, and a brittle crack propagation stopping performance index Y 1 / 2t (° C.) at the plate thickness 1 / 2t position defined by the following equation (a), and the following equation (b)
  • Sheet thickness The structural high-strength thick steel sheet according to [1], which is 100 mm or less.
  • composition is further in terms of mass%, Ni: 0.05 to 3%, Cu: 0.05 to 1.5%, Cr: 0.02 to 1.0%, Mo: 0.005 to 1.0%, V: 0.002 to 0.10%, B: 0.0002
  • a manufacturing method of a structural high-strength thick steel plate in which a steel material is subjected to a heating step and a hot rolling step to obtain a steel plate having a thickness t: 70 mm or more,
  • the steel material is, in mass%, C: 0.03-0.20%, Si: 0.03-0.5%, Mn: 0.5-2.5%, P: 0.03% or less, S: 0.01% or less, Al: 0.005-0.08%, Nb : 0.005 to 0.05%, Ti: 0.005 to 0.03%, N: 0.0050% or less, steel material having a composition consisting of the balance Fe and inevitable impurities
  • the heating step is a step of heating the steel material to a heating temperature: 900 to 1200 ° C.
  • In the hot rolling process primary rolling is performed at a surface temperature of 1000 to 850 ° C.
  • Y 1 / 3t ⁇ 0.9Y 1 / 2t (1) Y 1 / 6t ⁇ 0.8 Y 1 / 2t (2)
  • Y 1 / 2t (vTrs) 1 / 2t ⁇ 12 ⁇ ⁇ I (100) ⁇ 1 / 2t ⁇ 22 ⁇ ⁇ I (211) ⁇ 1 / 2t
  • Y 1 / 3t (vTrs) 1 / 3t ⁇ 12 ⁇ ⁇ I (100) ⁇ 1 / 3t ⁇ 22 ⁇ ⁇ I (211) ⁇ 1 / 3t
  • Y 1 / 6t (vTrs) 1 / 6t ⁇ 12 ⁇ ⁇ I (100) ⁇ 1 / 6t ⁇ 22 ⁇ ⁇ I (211) ⁇ 1 / 6t
  • composition is further mass%, Ni: 0.05-3%, Cu: 0.05-1.5%, Cr: 0.02-1.0%, Mo: 0.005-1.0%, V: 0.002-0.10%, B: 0.0002
  • composition according to [7] or [8], wherein the composition further contains, by mass%, one or two selected from Ca: 0.0005 to 0.003% and REM: 0.0005 to 0.010% A manufacturing method for structural high-strength thick steel plates.
  • the plate thickness 70 mm or more, yield strength: 400 N / mm 2 or more, and hull design temperature: ⁇ 10 ° C.
  • the brittle crack propagation stop toughness value Kca ⁇ 10 ° C. is 9500 N / mm 3 /
  • a high-strength thick steel plate excellent in brittle crack propagation stopping performance of 2 or more can be easily produced, and has a remarkable industrial effect.
  • the high-strength thick steel plate according to the present invention to hatch side combing and deck members in the strong deck structure of large container ships and bulk carriers, there is also a great effect of contributing to the improvement of ship safety. is there.
  • the high-strength thick steel plate of the present invention has a high brittle crack propagation stopping performance in the plate thickness central section including the plate thickness center position and 1/3 of the plate thickness in the plate thickness direction cross section.
  • This is a thick steel plate having a distribution of brittle crack propagation stopping performance in the three-layer thickness direction, having relatively low brittle crack propagation stopping performance in each outer region having a thickness of 1/3 of the plate thickness.
  • the brittle crack propagation stopping toughness value of the entire thick steel plate is high.
  • the distribution of brittle crack propagation stopping performance in the three-layer thickness direction that is, the brittle crack propagation stopping performance index Y at each position in each sheet thickness direction is ,
  • First (1) Formula Y 1 / 3t ⁇ 0.9Y 1 / 2t (1)
  • Second (2) Y 1 / 6t ⁇ 0.8Y 1 / 2t (2) Satisfied.
  • Y 1 / 2t is a brittle crack propagation stoppage performance index at the thickness 1 / 2t position
  • the following equation (a) Y 1 / 2t (vTrs) 1 / 2t ⁇ 12 ⁇ ⁇ I (100) ⁇ 1 / 2t ⁇ 22 ⁇ ⁇ I (211) ⁇ 1 / 2t
  • Y 1 / 2t (vTrs) 1 / 2t ⁇
  • vTrs Fracture transition temperature
  • the brittle crack arrest performance Y 1 / 3t in the sheet thickness 1 / 3t position is preferably -150 ° C. or less.
  • the brittle crack propagation stopping performance at the 1 / 6th plate thickness will be too high, and the progress of the brittle crack will be the same as in the central region of the plate thickness. Since the brittle crack fracture surface branched into three layers is not formed, the desired brittle crack propagation stop toughness value Kca cannot be secured.
  • the brittle crack propagation stopping performance Y 1 / 6t at the / 6t position is limited to a thick steel plate that satisfies the above-described formulas (1) and (2).
  • Such a thick steel plate is a thick steel plate having the desired high brittle crack propagation stop toughness value Kca.
  • the composition and structure are not particularly limited, but in mass%, C: 0.03-0.20%, Si: 0.03-0.5%, Mn: 0.5- Containing 2.5%, P: 0.03% or less, S: 0.01% or less, Al: 0.005 to 0.08%, Nb: 0.005 to 0.05%, Ti: 0.005 to 0.03%, N: 0.0050% or less, or optionally Ni: One or two selected from 0.05 to 3%, Cu: 0.05 to 1.5%, Cr: 0.02 to 1.0%, Mo: 0.005 to 1.0%, V: 0.002 to 0.10%, B: 0.0002 to 0.003%
  • C 0.03-0.20%
  • C is an element that contributes to an increase in strength. In order to ensure the desired strength of the thick steel plate of the present invention, it is necessary to contain 0.03% or more. On the other hand, if the content exceeds 0.20%, the toughness of the weld heat-affected zone decreases. Therefore, the C content is limited to the range of 0.03 to 0.20%. Preferably, it is 0.05 to 0.09% from the viewpoint of texture control. More preferably, it is 0.05 to 0.07%.
  • Si 0.03-0.5%
  • Si is an element that acts as a deoxidizer and contributes to an increase in strength by solid solution. In order to obtain such an effect, the content of 0.03% or more is required. On the other hand, if the content exceeds 0.5%, the toughness of the weld heat-affected zone decreases. Therefore, the Si content is limited to the range of 0.03 to 0.5%. Preferably, the content is 0.14 to 0.28%. More preferably, it is 0.14 to 0.17%.
  • Mn 0.5-2.5%
  • Mn is an element that contributes to an increase in strength through solid solution strengthening and hardenability, as well as an improvement in toughness and further a transformation texture. In order to acquire such an effect, 0.5% or more of content is required. On the other hand, if the content exceeds 2.5%, there is a concern that the toughness of the base material will decrease. Therefore, the Mn content is limited to the range of 0.5 to 2.5%. It is preferably 1.5 to 2.4%. More preferably, it is 1.8 to 2.0%.
  • P 0.03% or less
  • P is an element that exists in steel as an impurity and segregates at grain boundaries and adversely affects the toughness of the base metal, and is desirably reduced as much as possible. However, up to 0.03% is acceptable. For this reason, the P content is limited to 0.03% or less. In addition, Preferably it is 0.006% or less. On the other hand, from the viewpoint of dephosphorization cost, it is 0.0001% or more industrially.
  • S 0.01% or less S is an element that exists as sulfide inclusions in steel and reduces hot workability, base material toughness, base material ductility, and the like, and is preferably reduced as much as possible. However, up to 0.01% is acceptable. For this reason, S content was limited to 0.01% or less. In addition, Preferably it is 0.003% or less. On the other hand, from the viewpoint of desulfurization cost, it is 0.0001% or more industrially.
  • Al acts as a deoxidizer and also has a function of binding to nitrogen and precipitating as AlN to suppress coarsening of crystal grains. In order to acquire such an effect, 0.005% or more of content is required. On the other hand, if the content exceeds 0.08%, the amount of oxide inclusions increases and the cleanliness of the steel decreases. For this reason, the Al content is limited to a range of 0.005 to 0.08%. Note that the content is preferably 0.02 to 0.04%.
  • Nb 0.005-0.05%
  • Nb contributes to strength increase through precipitation strengthening and has the effect of suppressing recrystallization of austenite, facilitates processing (rolling) in the austenite non-recrystallization temperature range, and contributes to refinement of crystal grains Element.
  • 0.005% or more of content is required.
  • the content exceeds 0.05%, the amount of precipitates becomes excessive and the toughness tends to decrease. Therefore, the Nb content is limited to a range of 0.005 to 0.05%. Note that the content is preferably 0.02 to 0.04%.
  • Ti forms a nitride, suppresses coarsening of austenite grains, contributes to refinement of crystal grains of the base material, improves base material toughness, and contributes to refinement of the structure of the heat affected zone of the weld, Improve toughness of weld heat affected zone.
  • 0.005% or more of content is required.
  • the content exceeds 0.03%, toughness is reduced.
  • the Ti content is limited to the range of 0.005 to 0.03%.
  • the content is 0.008 to 0.015%.
  • N 0.0050% or less
  • N combines with Ti, Nb, and the like, contributes to refinement of crystal grains as a nitride, and contributes to improvement of base material toughness and toughness of weld heat affected zone.
  • the content 0.002% or more is required.
  • the toughness of the welded portion is lowered. For this reason, N content was limited to 0.0050% or less.
  • Ni 0.05 to 3%
  • Cu 0.05 to 1.5%
  • Cr 0.02 to 1.0%
  • Mo One or more selected from 0.005 to 1.0%
  • V 0.002 to 0.10%
  • B 0.0002 to 0.003%
  • Ca 0.0005 to 0.003%
  • REM 0.0005 to 0.010% 1 type or 2 types chosen from these can be contained.
  • Ni 0.05-3%
  • Cu 0.05-1.5%
  • Cr 0.02-1.0%
  • Mo 0.005-1.0%
  • V 0.002-0.10%
  • B 0.0002-0.003%
  • Two or more types Ni, Cu, Cr, Mo, V, and B are all elements that increase the strength, and can be selected as necessary and contained in one or more types.
  • Ni is an element that has a function of solid solution to improve toughness in addition to increasing strength, and also to prevent hot cracking when Cu is contained. In order to acquire such an effect, 0.05% or more of content is required. On the other hand, if the content exceeds 3%, the material cost will rise. Therefore, when Ni is contained, the Ni content is preferably limited to a range of 0.05 to 3%. More preferably, the content is 0.2 to 1%.
  • Cu is an element that contributes to an increase in strength by solid solution. To obtain such an effect, it needs to be contained in an amount of 0.05% or more. On the other hand, if the content exceeds 1.5%, the strength increases excessively and the toughness decreases. For this reason, when Cu is contained, the Cu content is preferably limited to a range of 0.05 to 1.5%. More preferably, it is 0.2 to 0.5%.
  • ⁇ Cr is an element that contributes to the increase in strength by solid solution, and in order to obtain such an effect, the content of 0.02% or more is required. On the other hand, if the content exceeds 1.0%, the toughness of the heat affected zone decreases. Therefore, when Cr is contained, the Cr content is preferably limited to a range of 0.02 to 1.0%. More preferably, the content is 0.1 to 0.6%.
  • Mo has the effect of suppressing the decrease in strength by forming a solid solution or further forming carbides. In order to acquire such an effect, 0.005% or more of content is required. On the other hand, a large content exceeding 1.0% reduces the toughness of the weld heat affected zone. For this reason, when Mo is contained, the Mo content is preferably limited to a range of 0.005 to 1.0%. More preferably, it is 0.005 to 0.01%.
  • V is an element that contributes to an increase in strength by forming a solid solution or further forming a precipitate (carbide). In order to acquire such an effect, 0.002% or more of content is required. On the other hand, if the content exceeds 0.10%, the effect is saturated and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, when V is contained, the V content is preferably limited to a range of 0.002 to 0.10%. More preferably, the content is 0.002 to 0.02%.
  • B is an element that segregates at the grain boundaries, improves the hardenability by containing a trace amount, and contributes to an increase in strength. In order to acquire such an effect, it is necessary to contain 0.0002% or more. On the other hand, if the content exceeds 0.003%, the toughness is decreased. For this reason, when B is contained, the B content is preferably limited to a range of 0.0002 to 0.003%. More preferably, the content is 0.0002 to 0.001%.
  • Ca 0.0005 to 0.003% and REM: 0.0005 to 0.010%.
  • Both Ca and REM can improve ductility and toughness through the form control action of sulfide inclusions. It is a contributing element. In order to obtain such an effect, it is necessary to contain Ca: 0.0005% or more and REM: 0.0005% or more. On the other hand, even if the content exceeds Ca: 0.003% and REM: 0.010%, the effect is saturated, and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, when one or both of Ca and REM are contained, it is preferable to limit the range to Ca: 0.0005 to 0.003% and REM: 0.0005 to 0.010%.
  • the balance other than the above components is composed of Fe and inevitable impurities.
  • Inevitable impurities include As: 0.03% or less, Sb: 0.01% or less, Sn: 0.02% or less, Pb: 0.01% or less, Bi: 0.01% or less.
  • the high-strength thick steel sheet of the present invention has the above composition and the whole thickness direction, excluding the steel sheet surface layer, with a bainite phase of 80% or more in volume ratio as the main phase and a total volume ratio of 20% or less as the second phase. (Including 0%) ferrite phase, pearlite, and martensite.
  • the high-strength thick steel plate of the present invention has a bainite phase as the main phase in order to maintain a high strength and a high toughness with a plate thickness of 70 mm or more and a yield strength of 400 N / mm 2 or more.
  • the main phase is a phase other than the bainite phase, it becomes difficult to combine the above-described high strength and high toughness in a thick steel plate having a thickness of 70 mm or more.
  • the “main phase” refers to a phase occupying 80% or more by volume.
  • the second phase other than the main phase is one or two selected from ferrite phase, pearlite, and martensite having a total volume ratio of 20% or less (including 0%). That's it. If the second phase exceeds 20% by volume, the desired high strength cannot be ensured. For this reason, the second phase is limited to one or more selected from ferrite phase, pearlite, and martensite having a total volume ratio of 20% or less (including 0%). The second phase contains 0% by volume. That is, the bainite phase may be 100%.
  • the steel material having the above composition is subjected to a heating step and a hot rolling step to obtain a thick steel plate having a thickness of 70 mm or more.
  • the manufacturing method of the steel material is not particularly limited, the molten steel having the above composition is melted in a conventional melting furnace such as a converter, and a slab is formed by a conventional casting method such as a continuous casting method. A method using a steel material is preferable from the viewpoint of productivity. Needless to say, a steel material may be used as a steel slab by the ingot-bundling rolling method.
  • the obtained steel material is then subjected to a heating process for hot rolling.
  • the steel material is heated to a temperature of 900 to 1200 ° C.
  • Heating temperature 900 ⁇ 1200 °C
  • the heating temperature is less than 900 ° C.
  • the hot deformation resistance becomes too high, the load on the rolling mill increases, and it becomes difficult to obtain a thick steel plate having a predetermined shape.
  • the heating temperature is higher than 1200 ° C.
  • the oxidation becomes remarkable and the yield is lowered, and the crystal grains become coarse, and the desired high toughness cannot be ensured.
  • the heating temperature was limited to a temperature in the range of 900 to 1200 ° C.
  • the temperature is preferably 1050 to 1150 ° C. from the viewpoint of forming a transformation texture having a desired degree of accumulation.
  • Hot rolling may be performed.
  • the heated steel material is subjected to a hot rolling process.
  • the hot rolling step is a step consisting of primary rolling, secondary rolling and cooling after rolling.
  • Primary rolling is rolling with a cumulative rolling reduction of 9% or less in the surface temperature range of 1000 to 850 ° C.
  • the austenite grains are uniformized without being coarsened, so that the variation of the transformation texture is reduced.
  • the rolling temperature exceeds 1000 ° C. as the surface temperature, the austenite grains become too coarse and the desired structure cannot be obtained even by subsequent hot rolling.
  • the rolling temperature is less than 850 ° C. at the surface temperature, it becomes an austenite non-recrystallization temperature range, which adversely affects the uniformity of crystal grains. For this reason, primary rolling was performed in the temperature range of 1000 to 850 ° C. as the surface temperature.
  • the primary rolling is limited to rolling with a cumulative rolling reduction of 9% or less in the temperature range of 1000 to 850 ° C. at the surface temperature.
  • the rolling reduction per pass is preferably about 3 to 5% from the viewpoint of regulating the austenite grain size.
  • the secondary rolling is a rolling with a one-pass reduction ratio of 7% or more, a cumulative reduction ratio of 55% or more, and a rolling end temperature of 800 to 550 ° C in a surface temperature range of 900 to 600 ° C. .
  • the vicinity of the steel sheet surface is a two-phase temperature range, and inside the steel sheet is an austenite region.
  • rolling strain is generated inside the steel sheet. Is intensively introduced, and the development of the texture is promoted.
  • the X-ray diffraction intensity ratio of the (100) plane and (211) plane parallel to the plate surface (rolled surface) which is effective for improving the brittle crack propagation stopping performance, is increased in the central region of the plate thickness.
  • the one-pass rolling reduction is less than 7%, the introduction of rolling strain into the steel sheet is weak and a desired texture cannot be formed.
  • the one-pass reduction ratio is preferably 9% or more from the viewpoint of securing the width of the texture development region in the desired center portion of the plate thickness.
  • the secondary rolling was limited to rolling with a one-pass reduction ratio of 7% or more and a cumulative reduction ratio of 55% or more in a temperature range of 900 to 600 ° C. at the surface temperature.
  • the one-pass rolling reduction is 9% or more, and the cumulative rolling reduction is 60% or more.
  • the one-pass rolling reduction is preferably 15% or less, and the cumulative rolling reduction is preferably 75% or less.
  • the rolling end temperature of secondary rolling is 800 to 550 ° C.
  • the texture development is insufficient.
  • the rolling end temperature is less than 550 ° C., the plastic strain accumulated in the grains becomes too much and the toughness is lowered, so that it becomes difficult to ensure the desired brittle crack propagation stopping performance.
  • the structure up to the plate thickness 1 / 2t position is the structure in which the bainite phase is the main phase. I can't.
  • the upper limit of the cooling rate is not particularly limited, but is preferably 30 ° C./s or less from the viewpoint of suppressing the formation of the martensite phase.
  • the average cooling rate is preferably 5 to 15 ° C./s.
  • cooling stop temperature exceeds 450 ° C.
  • the amount of the second phase other than the bainite phase exceeds 20% by volume, and a desired thick steel plate structure cannot be secured.
  • it is less than 400 ° C. a martensite phase appears and a desired thick steel plate structure cannot be secured. For this reason, cooling after hot rolling was performed at a cooling rate of 5 ° C / s or more at an average temperature range of 790 to 540 ° C at the surface temperature to a cooling stop temperature of 450 to 400 ° C. .
  • Molten steel having the composition shown in Table 1 was melted in a converter, and was cast into a slab (thickness: 300 mm) by a continuous casting method to obtain a steel material. These steel materials were subjected to a heating step under the conditions shown in Table 2 and a hot rolling step consisting of primary rolling, secondary rolling and cooling to obtain thick steel plates having the thicknesses shown in Table 2.
  • test method is as follows.
  • the tissue fraction (volume%) of each phase is obtained for each visual field, the tissue fraction in each visual field is arithmetically averaged, and the thickness It was set as the structure fraction of the position of the steel plate.
  • the ratio between the obtained X-ray diffraction intensity and the X-ray diffraction intensity of the random specimen is obtained, and the (100) plane X-ray diffraction intensity ratio parallel to the plate plane at each position in the plate thickness direction, (211) plane X-ray diffraction intensity ratio.
  • Table 3 shows the results at the plate thickness 1 / 6t position
  • Table 4 shows the results at the plate thickness 1 / 3t position
  • Table 5 shows the results at the plate thickness 1 / 2t position.
  • the obtained index Y at each position in the plate thickness direction is also shown in Tables 3-5.
  • the following formula (1) formula (2) Y 1 / 3t ⁇ 0.9Y 1 / 2t (1) Y 1 / 6t ⁇ 0.8 Y 1 / 2t (2)
  • ⁇ was evaluated, and “X” was evaluated otherwise.
  • Table 6 shows the obtained evaluation results.
  • ESSO test specimens full thickness
  • a temperature gradient type ESSO test is conducted in accordance with Annex A of the Brittle Crack Arrest Design Guidelines (Japan Maritime Association (2009)).
  • Ship hull design temperature The brittle crack propagation toughness value Kca -10 ° C at the full thickness at -10 ° C was determined.
  • the results of the obtained ESSO test are shown in Table 6 together with the results of the brittle crack propagation stopping performance index Y.
  • the brittle crack propagation stop performance index Y of the 1 / 3t thickness is high, and the brittle crack propagation stop performance index Y at each position in the thickness direction (1 / 6t, 1 / 3t, 1 / 2t) is (
  • the brittle crack propagation stopping performance is low at Kca- 10 ° C. of less than 9500 N / mm 3/2 .

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Cette invention concerne une tôle d'acier épaisse de haute résistance présentant une épaisseur supérieure ou égale à 70 mm et ayant une excellente capacité d'arrêt des fissurations de fragilité. Ladite tôle d'acier épaisse de haute résistance comprend trois couches constituées d'une région interne (une région centrale dans le sens de l'épaisseur) présentant une haute capacité d'arrêt des fissurations de fragilité et des régions présentant une basse capacité d'arrêt des fissurations de fragilité sur les deux côtés externes de la région interne. Spécifiquement, l'épaisseur (t) de la tôle est supérieure ou égale à 70 mm et l'indice de capacité d'arrêt des fissurations de fragilité Y (= vTrs-12 × I100 - 22 x I(211)) dans les positions à 1/6t, 1/3t et 1/2t dans la direction de l'épaisseur satisfait Y1/3t ≤ 0,9Y1/2t et Y1/6t ≥ 0,8Y1/2t. vTrs est la température de transition d'apparition de fracture (ºC) obtenue par l'essai de flexion par choc sur éprouvette Charpy à entaille en V. I (100) est un rapport d'intensité de diffraction des rayons X du plan (100) parallèle à la surface laminée (la surface de la tôle). I(211) est un rapport d'intensité de diffraction des rayons X du plan (211) parallèle à la surface laminée (la surface de la tôle).
PCT/JP2016/004223 2015-09-18 2016-09-15 Tôle d'acier épaisse à haute résistance pour une utilisation structurale et son procédé de fabrication WO2017047088A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201680052939.XA CN108026618B (zh) 2015-09-18 2016-09-15 结构用高强度厚钢板及其制造方法
KR1020187006623A KR102092000B1 (ko) 2015-09-18 2016-09-15 구조용 고강도 후강판 및 그 제조 방법
JP2016568462A JP6245384B2 (ja) 2015-09-18 2016-09-15 構造用高強度厚鋼板およびその製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015185050 2015-09-18
JP2015-185050 2015-09-18

Publications (1)

Publication Number Publication Date
WO2017047088A1 true WO2017047088A1 (fr) 2017-03-23

Family

ID=58288434

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2016/004223 WO2017047088A1 (fr) 2015-09-18 2016-09-15 Tôle d'acier épaisse à haute résistance pour une utilisation structurale et son procédé de fabrication

Country Status (4)

Country Link
JP (1) JP6245384B2 (fr)
KR (1) KR102092000B1 (fr)
CN (2) CN110878404B (fr)
WO (1) WO2017047088A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP7468814B1 (ja) 2022-11-14 2024-04-16 Ｊｆｅスチール株式会社 高強度極厚鋼板およびその製造方法

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101989251B1 (ko) * 2017-12-22 2019-09-30 현대제철 주식회사 구조용 강재 및 그 제조방법
CN108531810B (zh) * 2018-05-15 2019-11-12 马鞍山钢铁股份有限公司 一种超高强钢热轧基板及其制备方法
CN108546882B (zh) * 2018-06-01 2020-03-20 钢铁研究总院 一种Cu析出增强型高强耐火耐蚀钢及其制造方法
CN109023137A (zh) * 2018-09-04 2018-12-18 南京钢铁股份有限公司 一种脆性裂纹止裂性能优异的高强度钢板及其制造方法
CN111500931A (zh) * 2020-05-22 2020-08-07 包头钢铁（集团）有限责任公司 一种稀土耐低温汽车零部件用q460热轧圆钢的制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008169468A (ja) * 2006-12-14 2008-07-24 Nippon Steel Corp 脆性き裂伝播停止性能に優れた高強度厚鋼板
JP2012180590A (ja) * 2011-02-08 2012-09-20 Jfe Steel Corp 長大脆性き裂伝播停止特性に優れる板厚５０ｍｍ以上の厚鋼板およびその製造方法ならびに長大脆性き裂伝播停止性能を評価する方法および試験装置
WO2013099179A1 (fr) * 2011-12-27 2013-07-04 Ｊｆｅスチール株式会社 Plaque d'acier à haute résistance ayant une excellente capacité à arrêter les fissures fragiles et son procédé de fabrication

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3255790B2 (ja) * 1994-03-18 2002-02-12 新日本製鐵株式会社 脆性亀裂伝播停止特性と低温靭性の優れた厚鋼板の製造方法
CN100360698C (zh) * 2003-04-21 2008-01-09 杰富意钢铁株式会社 高强度热轧钢板及其制造方法
JP4449388B2 (ja) * 2003-09-25 2010-04-14 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性および超大入熱溶接熱影響部靱性に優れた高張力厚鋼板の製造方法
JP5151090B2 (ja) 2006-08-18 2013-02-27 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
KR101140097B1 (ko) * 2010-03-04 2012-06-14 신닛뽄세이테쯔 카부시키카이샤 고강도 후강판의 취성 균열 전파 정지 성능의 판정 방법
JP5304924B2 (ja) * 2011-12-27 2013-10-02 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
JP5304925B2 (ja) 2011-12-27 2013-10-02 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
TWI463018B (zh) 2012-04-06 2014-12-01 Nippon Steel & Sumitomo Metal Corp 具優異裂縫阻滯性之高強度厚鋼板
CN102888565A (zh) * 2012-09-22 2013-01-23 内蒙古包钢钢联股份有限公司 一种屈服强度690MPa级高强度钢板及其制造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008169468A (ja) * 2006-12-14 2008-07-24 Nippon Steel Corp 脆性き裂伝播停止性能に優れた高強度厚鋼板
JP2012180590A (ja) * 2011-02-08 2012-09-20 Jfe Steel Corp 長大脆性き裂伝播停止特性に優れる板厚５０ｍｍ以上の厚鋼板およびその製造方法ならびに長大脆性き裂伝播停止性能を評価する方法および試験装置
WO2013099179A1 (fr) * 2011-12-27 2013-07-04 Ｊｆｅスチール株式会社 Plaque d'acier à haute résistance ayant une excellente capacité à arrêter les fissures fragiles et son procédé de fabrication

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
KAZUKUNI HASE: "Development of YP460 N/mm2 Class Heavy Thick Plate with Excellent Brittle Crack Arrestability for Mega Container", JFE GIHO, February 2014 (2014-02-01), pages 13 - 18 *
SEISHI TSUYAMA: "Development of YP460 N/mm2 Class Heavy Thick Plate with Excellent Brittle Crack Arrestability for Mega Container", JOURNAL OF THE JAPAN WELDING SOCIETY, vol. 30, no. 2, 2012, pages 188 - 195 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP7468814B1 (ja) 2022-11-14 2024-04-16 Ｊｆｅスチール株式会社 高強度極厚鋼板およびその製造方法

Also Published As

Publication number Publication date
CN108026618B (zh) 2020-03-06
CN108026618A (zh) 2018-05-11
CN110878404A (zh) 2020-03-13
KR102092000B1 (ko) 2020-03-23
CN110878404B (zh) 2022-03-04
JP6245384B2 (ja) 2017-12-13
KR20180038029A (ko) 2018-04-13
JPWO2017047088A1 (ja) 2017-09-14

Similar Documents

Publication Publication Date Title
JP6245384B2 (ja) 構造用高強度厚鋼板およびその製造方法
EP3042976B1 (fr) Tôle d'acier pour tube de canalisation à paroi épaisse et à haute résistance mécanique ayant d'excellentes caracteristiques de résistance à la corrosion et à l'affaissement, et une ductilité aux basses températures, ainsi que tube de canalisation
EP2309014B1 (fr) Tôles d'acier épaisses laminées à chaud présentant une résistance élevée à la traction et une excellente résistance à basse température, et procédé de production de celles-ci
KR101686257B1 (ko) 내 ｈｉｃ 성이 우수한 후육 고장력 열연강판 및 그 제조 방법
KR101584235B1 (ko) 장대 취성 균열 전파 정지 특성이 우수한 판 두께 50㎜ 이상의 후강판 및 그의 제조 방법 그리고 장대 취성 균열 전파 정지 성능을 평가하는 방법 및 시험 장치
WO2013147197A1 (fr) Tuyau d'acier à haute résistance pour tuyau de canalisation ayant une excellente résistance à la fissuration induite par hydrogène, tuyau d'acier à haute résistance pour tuyau de canalisation l'utilisant et son procédé de fabrication
JP7147960B2 (ja) 鋼板およびその製造方法
JP6682967B2 (ja) 厚鋼板およびその製造方法
JP6856129B2 (ja) 高Ｍｎ鋼の製造方法
JP6620575B2 (ja) 厚鋼板およびその製造方法
KR20170118899A (ko) 저온 인성이 우수한 고강도 라인 파이프용 강판 및 고강도 라인 파이프용 강관
JP5515353B2 (ja) 熱間圧延ｔ形鋼およびその製造方法
JP7348948B2 (ja) 冷間曲げ性に優れた高強度構造用鋼材及びその製造方法
JP6112265B2 (ja) 高強度極厚鋼板およびその製造方法
WO2013175745A1 (fr) Plaque d'acier épaisse à résistance élevée pour une utilisation structurale qui a une excellente capacité d'arrêt de fissure fragile, et son procédé de fabrication
JP7099653B1 (ja) 鋼板およびその製造方法
JP2011068952A (ja) アレスト特性に優れた高強度厚肉鋼板
CN113840933B (zh) 厚钢板及其制造方法
CA3152893A1 (fr) Tole d'acier laminee a chaud pour tuyau en acier electrosoude et son procede de production, tuyau en acier electrosoude et son procede de production, canalisation et structure d'immeubl
JP7396322B2 (ja) 鋼板
JP7323091B1 (ja) 鋼板およびその製造方法
JP7396512B2 (ja) 厚鋼板および厚鋼板の製造方法
KR102506231B1 (ko) 용접 구조체
JP7388371B2 (ja) 電縫鋼管および電縫鋼管の製造方法
WO2017145651A1 (fr) 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

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2016568462

Country of ref document: JP

Kind code of ref document: A

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 16845962

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 20187006623

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 16845962

Country of ref document: EP

Kind code of ref document: A1