WO2017094593A1 - Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées - Google Patents

Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées Download PDF

Info

Publication number
WO2017094593A1
WO2017094593A1 PCT/JP2016/084857 JP2016084857W WO2017094593A1 WO 2017094593 A1 WO2017094593 A1 WO 2017094593A1 JP 2016084857 W JP2016084857 W JP 2016084857W WO 2017094593 A1 WO2017094593 A1 WO 2017094593A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
yield strength
bainite
amount
heat
Prior art date
Application number
PCT/JP2016/084857
Other languages
English (en)
Japanese (ja)
Inventor
皓至 倉田
晴弥 川野
喜一郎 田代
元樹 柿崎
Original Assignee
株式会社神戸製鋼所
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 株式会社神戸製鋼所 filed Critical 株式会社神戸製鋼所
Priority to CN201680064618.1A priority Critical patent/CN108350540A/zh
Priority to EP16870530.9A priority patent/EP3385399A4/fr
Priority to KR1020187018576A priority patent/KR20180085791A/ko
Publication of WO2017094593A1 publication Critical patent/WO2017094593A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B21C37/08—Making tubes with welded or soldered seams
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/08—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/38—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
    • C22C38/46—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a non-tempered steel sheet having high yield strength in which the low temperature toughness deterioration of the weld heat affected zone and the hardness of the weld heat affected zone are suppressed. More specifically, the present invention relates to a non-tempered steel sheet having high yield strength of API standard X80 class used for transportation line pipes such as oil and natural gas.
  • Controlling rolling is an example of a manufacturing method for satisfying these requirements.
  • Controlled rolling is a technique in which crystal grains are refined by appropriately controlling the temperature and rolling reduction during rolling, and accelerated cooling is performed after hot rolling. In controlled rolling, tempering such as heating after accelerated cooling is unnecessary.
  • a steel sheet obtained by such a method is generally called a non-tempered steel sheet.
  • Patent Documents 1 to 4 disclose a method for producing a steel sheet having a high yield strength of API standard X80 class with no tempering.
  • JP 2006-328523 A International Publication No. 2010/052927 Pamphlet JP 2006-169591 A JP 2008-261012 A
  • Patent Document 1 and Patent Document 2 do not control Ceq, which is an index for evaluating the toughness and hardness of the weld heat affected zone, toughness degradation in the weld heat affected zone and the weld heat impact. There is a risk of curing the part.
  • the present invention has been made in view of such circumstances, and its purpose is to provide a non-tempered steel sheet having a high yield strength that suppresses the low temperature toughness deterioration of the weld heat affected zone and the hardness of the weld heat affected zone. It is to provide.
  • the non-heat treated steel sheet having a high yield strength with suppressed low temperature toughness deterioration of the weld heat affected zone and hardness of the weld heat affected zone according to the present invention, which has solved the above problems, is C% by mass. % Over 0.10% or less, Si: 0.15 to 0.50%, Mn: 1.20 to 2.50%, P: over 0% to 0.020% or less, S: over 0% to 0.0050%
  • Nb 0.020 to 0.100%
  • Zr 0.0001 to 0.0100%
  • Ca 0.00.
  • the area ratio of the following metal structure satisfies bainite: 80 area% or more and island martensite: 0 area% or more and 0.26 area% or less, and the maximum hardness of the bainite is 270 HV. It has a gist where it meets the above.
  • Ceq C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 (1)
  • a value 1.15 ⁇ Mn + 2.20 ⁇ Mo + 6.50 ⁇ Nb (2)
  • B value 1.20 ⁇ Mn + 0.50 ⁇ Ni + 4.25 ⁇ Nb (3)
  • C, Mn, Cu, Ni, Cr, Mo, V, and Nb are mass%, respectively, and indicate the contents of C, Mn, Cu, Ni, Cr, Mo, V, and Nb.
  • the non-tempered steel sheet is for a line pipe.
  • a non-tempered steel sheet having a high yield strength with suppressed low temperature toughness deterioration of the weld heat affected zone and hardness of the weld heat affected zone can be obtained.
  • FIG. 1 is a graph showing the relationship between the bainite area ratio and the yield strength.
  • FIG. 2 is a graph showing the relationship between the maximum hardness of bainite and the yield strength.
  • FIG. 3 is a graph showing the relationship between the area ratio of the island martensite (hereinafter, the island martensite may be referred to as MA) and the yield strength.
  • the present inventors examined factors that govern the yield strength of non-tempered steel sheets.
  • the yield strength of the non-tempered steel sheet has a close correlation with the area ratio of bainite and island martensite in the metal structure, and the maximum hardness of bainite, and when these are controlled within a predetermined range It was found that high yield strength of API standard X80 grade can be obtained.
  • the present inventors have studied from various angles in order to realize a non-tempered steel sheet having high yield strength and low-temperature toughness deterioration of the weld heat affected zone and suppressing the hardness of the weld heat affected zone.
  • the chemical composition is controlled so as to satisfy the relationships of the above formulas (1) to (3), the low temperature toughness deterioration of the weld heat affected zone is suppressed, and the hardness of the weld heat affected zone is further reduced.
  • the present invention has been completed.
  • non-tempered steel sheet is preferably heated from a steel material satisfying a predetermined component composition by hot rolling, and then from a cooling start temperature of 730 ° C. or higher to a cooling stop temperature of 370 to 550 ° C., Average cooling rate: It can be produced by cooling at 10 to 50 ° C./second.
  • high yield strength of API standard X80 class means that the yield strength in the sheet width direction of the steel sheet is 555 MPa or more and 705 MPa or less.
  • each structure with respect to the entire metal structure is bainite: 80 area% or more, island-like martensite: 0 area% or more, 0.26 area at a quarter position of the sheet thickness t of the steel sheet. % Or less, and the maximum hardness of bainite: 270 HV or more is satisfied.
  • Bainite 80 area% or more Bainite is a structure that contributes to improving the yield strength, and is an important structure for securing high yield strength of API standard X80.
  • the lower limit of the area ratio of bainite when the area of the whole metal structure is 100% is 80 area% or more.
  • the lower limit of the area ratio of bainite is preferably 82 area% or more, more preferably 84 area% or more.
  • FIG. 1 shows No. 1 in Table 2 using steel types A to X in Table 1 of Examples described later.
  • 2 is a graph showing the relationship between the area ratio of bainite and the yield strength in a non-tempered steel sheet produced under the production conditions 1 to 24.
  • all examples satisfying the desired high yield strength of 555 MPa or more had a bainite area ratio of 80% or more in the metal structure, and in order to satisfy the high yield strength, the bainite area It can be seen that it is effective to increase the rate to 80% or more.
  • the yield strength does not satisfy 555 MPa or more even though the bainite area ratio is 80% or more.
  • these have a bainite hardness of less than 270 HV described later or an MA area ratio of 0. This is an example of over 26%.
  • Maximum hardness of bainite 270 HV or higher
  • the maximum hardness of bainite is important for obtaining high yield strength stably by suppressing variation in yield strength, and it is necessary to control it to 270 HV or higher. Thereby, high yield strength of API standard X80 class can be secured stably.
  • the lower limit of the maximum hardness of bainite is preferably 275 HV or higher.
  • the upper limit of the maximum hardness of the bainite is preferably 310 HV or less, more preferably 300 HV or less.
  • FIG. 2 shows No. 1 in Table 2 using steel types A to X in Table 1 of Examples described later.
  • 2 is a graph showing the relationship between the maximum hardness of bainite and the yield strength in a non-heat treated steel sheet produced under the production conditions 1 to 24.
  • all examples satisfying the desired 555 MPa or more have a maximum bainite hardness of 270 HV or more in the metal structure, and in order to satisfy high yield strength, the bainite maximum hardness is 270 HV or more. It can be seen that it is effective to increase it.
  • the bainite maximum hardness is 270 HV or more
  • the yield strength does not satisfy 555 MPa or more, but these have a bainite area ratio of less than 80% or an MA area ratio of 0.26%. It is an example of exceeding.
  • maximum hardness of bainite means the average value of the upper three points when the Vickers hardness of bainite is measured by the method described in the examples described later. The present inventors have found that high yield strength can be stably obtained by controlling the maximum hardness of bainite.
  • Island-like martensite 0 area% or more and 0.26 area% or less
  • Island-like martensite is a structure that lowers the yield strength, so it is necessary to reduce the MA area ratio in order to ensure the desired high yield strength. is there. Therefore, the upper limit of the MA area ratio when the area of the entire metal structure is 100% is set to 0.26 area% or less.
  • the upper limit of the MA area ratio is preferably 0.25 area% or less.
  • FIG. 3 shows No. in Table 2 using A to X in Table 1 of Examples described later.
  • 2 is a graph showing the relationship between the area ratio of island martensite and the yield strength in a non-tempered steel sheet produced under the production conditions of 1 to 24.
  • the MA area ratio in the metal structure is 0.26% or less, and in order to satisfy the high yield strength, the MA area ratio is 0.26%. It can be seen that the following control is effective.
  • the yield strength does not satisfy 555 MPa or more even though the MA area ratio is 0.26% or less, these may have a bainite area ratio of less than 80% or a bainite maximum hardness. This is an example of less than 270 HV.
  • the structure of the non-tempered steel sheet according to the present invention is as described above.
  • the remaining structure other than the above is ferrite, martensite, or pearlite.
  • C, Mn, Cu, Ni, Cr, Mo, and V are mass%, respectively, and show content of C, Mn, Cu, Ni, Cr, Mo, and V.
  • Ceq defined by the above formula (1) is an important index for determining the low temperature toughness of HAZ and the hardness of HAZ. When Ceq is 0.44 or more, the low temperature toughness of HAZ and the hardness properties of HAZ deteriorate rapidly, and if Ceq is less than 0.44, good low temperature toughness of HAZ and hardness of HAZ part can be ensured. it can.
  • the upper limit of Ceq is set to less than 0.44.
  • the upper limit of Ceq is preferably 0.43 or less, more preferably 0.42 or less.
  • the lower limit of Ceq is preferably 0.37 or more, more preferably 0.38 or more.
  • a value: 2.50 or more A value 1.15 ⁇ Mn + 2.20 ⁇ Mo + 6.50 ⁇ Nb (2)
  • Mn, Mo, and Nb are the mass%, respectively, and show content of Mn, Mo, and Nb.
  • the A value was found for the first time by the present inventors, and the contents of Mn and Mo effective for suppressing ferrite transformation among the elements constituting Ceq described above, and further the content of Nb Is a parameter controlled to satisfy the above equation (2).
  • By controlling the A value to 2.50 or more an increase in Ceq can be suppressed and a bainite area ratio important for realizing high yield strength can be secured. In order to increase the bainite area ratio, the higher the A value, the better.
  • the lower limit of the A value is 2.50 or more.
  • the lower limit of the A value is preferably 2.52 or more, more preferably 2.54 or more.
  • the upper limit of the A value is preferably 3.00 or less, more preferably 2.95 or less.
  • Mn, Ni, and Nb are mass%, respectively, and show the content of Mn, Ni, and Nb.
  • the B value was found for the first time by the present inventors, and by reducing the transformation temperature of bainite, each content of Mn, Ni, and Nb effective for introducing high-density dislocations is expressed by the above formula ( 3) Parameters controlled to satisfy.
  • the B value By setting the B value to 2.37 or more, the maximum hardness of bainite can be ensured while suppressing an increase in Ceq. In order to increase the maximum hardness of bainite, the higher the B value, the better.
  • the lower limit of the B value is 2.37 or more.
  • the lower limit of the B value is preferably 2.39 or more.
  • the upper limit of the B value is preferably 2.70 or less, more preferably 2.68 or less.
  • C more than 0.04% and 0.10% or less C is an element indispensable for securing the high yield strength of the base material (steel plate), and therefore the lower limit of the C content is more than 0.04%.
  • the lower limit of the C amount is preferably 0.05% or more, more preferably 0.06% or more.
  • the upper limit of the amount of C needs to be 0.10% or less. is there.
  • the upper limit of the C amount is preferably 0.09% or less, more preferably 0.08% or less.
  • Si 0.15-0.50% Si is an element that has a deoxidizing action and is effective for improving the yield strength of the base material. Therefore, the lower limit of the Si amount is set to 0.15% or more.
  • the lower limit of the Si amount is preferably 0.18% or more, more preferably 0.20% or more.
  • the upper limit of the Si amount needs to be 0.50% or less.
  • the upper limit of the Si amount is preferably 0.45% or less, more preferably 0.40% or less.
  • Mn 1.20-2.50%
  • Mn is an element effective for improving the yield strength of the base material.
  • the lower limit of the amount of Mn needs to be 1.20% or more.
  • the lower limit of the amount of Mn is preferably 1.50% or more, more preferably 1.70% or more.
  • the upper limit of the amount of Mn is made 2.50% or less.
  • the upper limit of the amount of Mn is preferably 2.20% or less, and more preferably 2.00% or less.
  • P more than 0% and 0.020% or less
  • P is an element inevitably contained in the steel material, and when the P content exceeds 0.020%, the low temperature toughness of the HAZ is remarkably deteriorated. Therefore, the upper limit of the P amount is 0.020% or less.
  • the upper limit of the amount of P is preferably 0.015% or less, more preferably 0.010% or less. Note that P is an impurity inevitably contained in the steel, and it is impossible to make the amount 0% in industrial production.
  • S more than 0% to 0.0050% or less S is an element that affects the low temperature toughness of HAZ as in the case of P.
  • the upper limit of the amount of S is made 0.0050% or less.
  • the upper limit of the amount of S is preferably 0.0030% or less, more preferably 0.0020% or less.
  • S is an impurity inevitably contained in the steel, and it is impossible for industrial production to make the amount 0%.
  • Nb 0.020 to 0.100%
  • Nb is an element effective for increasing the yield strength and the low temperature toughness of the base material without deteriorating the weldability, and therefore the lower limit of the Nb amount needs to be 0.020% or more.
  • the lower limit of the Nb amount is preferably 0.030% or more, more preferably 0.040% or more.
  • the upper limit of the Nb amount is made 0.100% or less.
  • the upper limit of the Nb amount is preferably 0.070% or less, more preferably 0.060% or less.
  • Ti is an element effective for improving the yield strength of the base metal, and further, it precipitates as TiN in the steel, and is necessary for improving the low temperature toughness of HAZ by suppressing coarsening of austenite grains in the HAZ during welding. It is an element.
  • the lower limit of the Ti amount needs to be 0.003% or more.
  • the lower limit of the Ti amount is preferably 0.005% or more, more preferably 0.007% or more.
  • the upper limit of the amount of Ti is made 0.020% or less.
  • the upper limit of the Ti amount is preferably 0.018% or less, more preferably 0.016% or less.
  • N 0.0010 to 0.0075%
  • N is an element necessary for improving the low temperature toughness of HAZ by suppressing the coarsening of austenite grains in the HAZ during welding by precipitating as TiN in the steel.
  • the lower limit of the N amount needs to be 0.0010% or more.
  • the lower limit of the N amount is preferably 0.0020% or more, and more preferably 0.0030% or more.
  • the upper limit of the amount of N is made 0.0075% or less.
  • the upper limit of the N amount is preferably 0.0070% or less, and more preferably 0.0065% or less.
  • Zr 0.0001 to 0.0100%
  • Zr is an element that contributes to the improvement of low temperature toughness in HAZ by forming and dispersing an oxide, and for that purpose, the lower limit of the amount of Zr needs to be 0.0001% or more.
  • the lower limit of the amount of Zr is preferably 0.0003% or more, more preferably 0.0005% or more.
  • the upper limit of the amount of Zr needs to be 0.0100% or less.
  • the upper limit of the amount of Zr is preferably 0.0050% or less, more preferably 0.0030% or less.
  • Ca 0.0005 to 0.0030%
  • Ca has an action of controlling the form of sulfide, and is an element that suppresses the formation of MnS by forming CaS and improves the low temperature toughness of HAZ.
  • the lower limit of the Ca amount is 0.0005% or more. It is necessary to.
  • the lower limit of the Ca content is preferably 0.0006% or more.
  • the upper limit of the Ca content is 0.0030% or less.
  • the upper limit of the Ca content is preferably 0.0028% or less, and more preferably 0.0026% or less.
  • REM 0.0001 to 0.0050% REM, which is a rare earth element, is an element effective for controlling the morphology of sulfides, and suppresses the generation of MnS that is harmful to the low temperature toughness of HAZ.
  • the lower limit of the REM amount is set to 0.0001% or more.
  • the amount of REM is preferably 0.0003% or more, more preferably 0.0005% or more.
  • the upper limit of the REM amount is 0.0050% or less.
  • the upper limit of the REM amount is preferably 0.0040% or less, more preferably 0.0030% or less.
  • REM means lanthanoid elements (15 elements from La to Lu), Sc (scandium), and Y (yttrium).
  • lanthanoid elements 15 elements from La to Lu
  • Sc scandium
  • Y yttrium
  • Al 0.010 to 0.050%
  • Al is a strong deoxidizing element, and in order to obtain a deoxidizing effect, the lower limit of the Al amount needs to be 0.010% or more.
  • the lower limit of the Al content is preferably 0.015% or more, more preferably 0.018% or more.
  • the upper limit of the amount of Al needs to be 0.050% or less.
  • the upper limit of the amount of Al is preferably 0.045% or less, and more preferably 0.042% or less.
  • B 0.0003% or less (including 0%)
  • the amount of B is an element that significantly deteriorates the low-temperature toughness of HAZ.
  • the upper limit of the amount of B is set to 0.0003% or less.
  • the upper limit of the amount of B is preferably 0.0002% or less, more preferably 0.0001% or less.
  • Mo more than 0% to 0.30% or less
  • Cu more than 0% to 0.30% or less
  • Ni more than 0% to 0.30% or less
  • Cr more than 0% to 0.30% or less
  • V more than 0%
  • One or more selected from the group consisting of 0.050% or less Mo, Cu, Ni, Cr, and V are effective elements for improving the yield strength. These elements may be added alone or in combination of two or more. The reasons for setting the ranges of the contents of these elements are as follows.
  • Mo more than 0% and 0.30% or less Mo is an element effective for improving the yield strength of the base material, and therefore the lower limit of the Mo amount is preferably 0.01% or more.
  • the lower limit of the amount of Mo is more preferably 0.05% or more, and more preferably 0.10% or more.
  • the upper limit of the Mo amount is set to 0.30% or less.
  • the upper limit of the Mo amount is preferably 0.25% or less, more preferably 0.20% or less.
  • Cu more than 0% and 0.30% or less Cu is an element effective for increasing the yield strength, and therefore the lower limit of the Cu content is preferably 0.01% or more.
  • the lower limit of the amount of Cu is more preferably 0.05% or more, and still more preferably 0.10% or more.
  • the upper limit of the amount of Cu is made 0.30% or less.
  • the upper limit of the amount of Cu is preferably 0.27% or less, more preferably 0.25% or less.
  • Ni more than 0% and 0.30% or less Ni is an element effective for improving the yield strength of the base metal, and therefore the lower limit of the Ni content is preferably 0.01% or more.
  • the lower limit of the Ni amount is more preferably 0.05% or more, and still more preferably 0.10% or more.
  • the upper limit of the Ni amount is set to 0.30% or less from an economical viewpoint.
  • the upper limit of the Ni content is preferably 0.27% or less, more preferably 0.25% or less.
  • Cr more than 0% and 0.30% or less Cr is an element effective for improving the yield strength, and therefore the lower limit of the Cr content is preferably 0.01% or more.
  • the lower limit of the Cr amount is more preferably 0.05% or more, and still more preferably 0.10% or more. However, if the Cr content exceeds 0.30%, it becomes easy to produce MA, so the upper limit of the Cr content is 0.30% or less.
  • the upper limit of the Cr amount is preferably 0.27% or less, more preferably 0.25% or less.
  • V more than 0% and 0.050% or less V is an element effective for improving the yield strength.
  • the lower limit of the V amount is preferably 0.001% or more.
  • the lower limit of the V amount is more preferably 0.002% or more, and still more preferably 0.003% or more.
  • the upper limit of the amount of V is made 0.050% or less.
  • the upper limit of the V amount is preferably 0.030% or less, more preferably 0.010% or less.
  • the elements in steel used in the present invention are as described above, and the balance is substantially iron. However, it is naturally allowed that steel contains inevitable impurities brought in depending on the situation of raw materials, materials, manufacturing equipment, and the like. Examples of the inevitable impurities include As, Sb, Sn, O, and H.
  • the steel sheet of the present invention can be produced, for example, by producing a slab such as a slab, heating the obtained slab, performing hot rolling, and then performing accelerated cooling.
  • the slab After casting as described above, the slab is heated and hot rolled.
  • the heating temperature for heating the slab is preferably 1000 to 1200 ° C. If the heating temperature is too low, Nb in the steel does not sufficiently dissolve, and high yield strength cannot be ensured. Therefore, the lower limit of the heating temperature is more preferably 1100 ° C. or more, and further preferably 1120 ° C. or more. However, if the heating temperature is too high, the austenite grains become coarse and the low temperature toughness of the base material deteriorates, so the upper limit of the heating temperature is more preferably 1180 ° C. or less.
  • the hot rolling start temperature is preferably 900 to 1100 ° C. If the hot rolling start temperature is too low, rolling in the austenite recrystallization region cannot be ensured, austenite grains become coarse, and the low temperature toughness of the base material may deteriorate. Therefore, the lower limit of the hot rolling start temperature is more preferably 930 ° C or higher, and still more preferably 950 ° C or higher. On the other hand, if the hot rolling start temperature is too high, the austenite grains after recrystallization become coarse and the low temperature toughness of the base material may be deteriorated. Therefore, the upper limit of the hot rolling start temperature is more preferably 1090 ° C. or less, and still more preferably 1080 ° C. or less.
  • the rolling reduction from 950 ° C. to the hot rolling end temperature is preferably 40 to 80%. If the rolling reduction from 950 ° C. to the hot rolling finish temperature is too low, the strain introduced into the austenite grains cannot be secured, and the grains after bainite transformation become coarse, which may deteriorate the low temperature toughness of the base material. Therefore, the lower limit of the rolling reduction is more preferably 50% or more, and still more preferably 60% or more. On the other hand, if the rolling reduction from 950 ° C. to the hot rolling end temperature is too high, strain is excessively introduced into the austenite grains, and the hardenability is lowered. Therefore, the upper limit of the rolling reduction is more preferably 77% or less, and further preferably 75% or less.
  • the hot rolling end temperature is preferably 770 to 880 ° C. If the hot rolling end temperature is too low, strain is excessively introduced into the austenite grains, and the hardenability is lowered. Therefore, the lower limit of the hot rolling end temperature is more preferably 790 ° C. or higher, further preferably 800 ° C. or higher. On the other hand, if the hot rolling finish temperature is too high, the strain introduced into the austenite grains cannot be ensured, and the grains after the bainite transformation become coarse, which may deteriorate the low temperature toughness of the base material. Therefore, the upper limit of the hot rolling end temperature is more preferably 860 ° C. or less, and further preferably 850 ° C. or less.
  • Accelerated cooling is preferably performed as follows after the hot rolling is completed. It is not necessarily limited to this condition.
  • the cooling start temperature after the hot rolling is preferably 730 ° C. or higher. If the temperature is lower than 730 ° C., ferrite transformation is promoted and ferrite precipitates, so that the metal structure does not become bainite, and it may be difficult to ensure high yield strength of the base material. Therefore, the lower limit of the cooling start temperature is more preferably 735 ° C. or higher, and further preferably 740 ° C. or higher. Although the upper limit of cooling start temperature is not specifically limited, More preferably, it is 860 degrees C or less, More preferably, it is 850 degrees C or less.
  • accelerated cooling is preferably performed at an average cooling rate of preferably 10 to 50 ° C./second.
  • the average cooling rate of accelerated cooling preferably 10 ° C./second or more, it is possible to prevent precipitation of ferrite by transforming untransformed austenite into a bainite structure, and further increase the maximum hardness of bainite. It is easy to improve the yield strength. Therefore, the lower limit of the average cooling rate is more preferably 13 ° C./second or more, and further preferably 15 ° C./second or more.
  • the upper limit of the average cooling rate is preferably 50 ° C./second or less.
  • the upper limit of the average cooling rate is more preferably 45 ° C./second or less in consideration of the formability to the steel pipe.
  • the cooling stop temperature is preferably 370 to 550 ° C.
  • the lower limit of the cooling stop temperature is more preferably 390 ° C. or higher, and further preferably 400 ° C. or higher.
  • the upper limit of the cooling stop temperature is more preferably 540 ° C. or less, and further preferably 530 ° C. or less.
  • the average cooling rate at this time is preferably about 0.1 to 5 ° C./second.
  • the plate thickness of the steel plate according to the present invention is not particularly limited, but in order to obtain a line pipe, the lower limit of the plate thickness is preferably 6 mm or more, more preferably 10 mm or more.
  • the upper limit of the plate thickness is preferably 32 mm or less, more preferably 30 mm or less, from the viewpoint of securing a necessary cooling rate and suppressing the precipitation of ferrite.
  • the non-tempered steel sheet obtained as described above is particularly useful for line pipes.
  • the line pipe obtained by using the non-heat treated steel sheet of the present invention reflects the characteristics of the non-heat treated steel sheet, and has excellent low temperature toughness and hardness characteristics and yield strength of HAZ.
  • REM 35Fe-30REM-35Si alloy containing 50% Ce and 20% La was used as the REM.
  • REM and Ca were added after deoxidation with Al and Zr.
  • REM and Ca were added in order of REM and Ca, and the time from REM addition to Ca addition was made into 4 minutes or more.
  • the slab was produced so that solidification might be completed within 200 minutes after Ca addition.
  • a test piece of 12 mm ⁇ 32 mm ⁇ 55 mm was cut out from the steel plates 1 to 24 so that the rolling direction and the vertical direction of the steel plate were the length of the test piece, and used as a reproducible thermal cycle test piece.
  • a thermal cycle with a maximum heating temperature of 1350 ° C. simulating a coarse-grained heat-affected zone in the vicinity of the melting line was applied to the reproduced thermal cycle test piece. Specifically, after heating to 1350 ° C. and holding for 5 seconds, the temperature range of 800 to 500 ° C. was cooled over 30 seconds.
  • the Charpy impact test was implemented by the method prescribed
  • a Charpy impact test was conducted at ⁇ 10 ° C., and the absorbed energy passed 27 J or more.
  • HAZ weld heat affected zone
  • No. in Table 2 Nos. 17 to 24 are Nos. 1 and 2 in Table 2 that satisfy the preferable requirements defined in the present invention by using the steel types Q to X in Table 1 that satisfy the component composition defined in the present invention. This is an example manufactured under the manufacturing conditions of 17-24. These show that the low temperature toughness and hardness characteristics of HAZ are good, and a steel sheet having a high yield strength of 555 MPa or more is obtained.
  • No. 1 to 16 do not satisfy any of the requirements defined in the present invention.
  • No. in Table 2. 1 is an example using the steel type A in Table 1 having a large Ceq, although the component composition of each element satisfies the requirements specified in the present invention, and the maximum hardness of the HAZ is high because of the large Ceq. As a result, the low temperature toughness of the HAZ was reduced.
  • No. in Table 2. 2 is an example using the steel type B of Table 1 with a large amount of B and a small A value and B value. Since the area ratio of bainite is low and the maximum hardness of bainite is low, the yield strength is low. Since the amount was large, the low temperature toughness of HAZ was lowered.
  • No. in Table 2 No. 3 is an example using the steel type C in Table 1 having a large B amount and Ti amount, and a small A value and B value, and the low temperature toughness of HAZ was lowered because the B amount and Ti amount were large.
  • a value and B value were small, since B exceeded 0.0003% and Mo was also compounded, the area ratio of bainite, the maximum hardness of bainite, and the yield strength increased.
  • No. 4 is an example using the steel type D of Table 1 having a small A value and B value, and the yield strength was low because the area ratio of bainite was low and the maximum hardness of bainite was low.
  • No. 5 is an example using the steel type E of Table 1 having a small A value. Since the area ratio of bainite was low, the yield strength was low.
  • No. in Table 2. 6 is an example using the steel type F of Table 1 with a small B value. Although the bainite has 80% by area or more, the yield strength is low because the maximum hardness of the bainite is low.
  • No. in Table 2. 7 is an example using the steel type G of Table 1 that does not include Mo, Cu, Ni, Cr, and V, and has a small A value and B value, and does not include Mo, Cu, Ni, Cr, and V.
  • the yield strength was low because the area ratio of bainite was low and the maximum hardness of bainite was low.
  • No. 8 is an example using the steel type H of Table 1 with a small amount of C and a small B value. Since the amount of C was small and the maximum hardness of bainite was low, the yield strength was low.
  • No. 9 is an example using the steel type I of Table 1 with a small amount of Si and a small A value. Since the amount of Si was small and the area ratio of bainite was low, the yield strength was low.
  • No. in Table 2. 11 is an example using the steel type K of Table 1 with a small amount of Mn and Nb, and a small A value and B value.
  • the amount of Mn and Nb is small, the area ratio of bainite is low, and the maximum hardness of bainite. , The yield strength was low.
  • No. in Table 2 is an example using the steel type L in Table 1 having a small Nb amount, containing no Mo, Cu, Ni, Cr, and V, and having a small A value and B value.
  • the Nb amount is small, and Mo, Cu, Since Ni, Cr, and V were not included, the area ratio of bainite was low, and the maximum hardness of bainite was low, so the yield strength was low.
  • No. in Table 2 No. 13 is an example using the steel type M of Table 1 with a large amount of Ni and a small A value and B value. MA was large, the area ratio of bainite was low, and the yield strength was low.
  • No. in Table 2. 14 is an example using the steel type N in Table 1 with a large amount of Cr and a small A value and B value. MA is large, the area ratio of bainite is low, the maximum hardness of bainite is low, and the yield strength is low. Became lower.
  • No. in Table 2. 15 is an example using the steel type O of Table 1 with a small amount of Mn, a large amount of Cr, and a small A value and B value.
  • the amount of Mn is small, the amount of MA is large, the area ratio of bainite is low, The maximum hardness decreased and the yield strength decreased.
  • No. in Table 2. 16 is an example using the steel type P of Table 1 with a large amount of V and a small A value and B value. MA is large, the area ratio of bainite is low, the maximum hardness of bainite is low, and the yield strength is low. Became lower.

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)
  • Treatment Of Steel In Its Molten State (AREA)

Abstract

L'invention concerne une tôle d'acier non traitée thermiquement ayant une limite élastique élevée, dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées. Une tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées est caractérisée en ce qu'elle comprend des composants prédéterminés dans l'acier, le Ceq spécifié par l'expression (1) est inférieur à 0,44, la valeur A spécifiée par l'expression (2) est supérieure ou égale à 2,5, la valeur spécifiée par l'expression (3) est supérieure ou égale à 2,37, les rapports de surface de la structure métallographique ci-dessous à 1/4 de l'épaisseur de la tôle d'acier satisfont les valeurs de 80 % ou plus de bainite et de 0 % à 0,26 % d'îlots de martensite, et la dureté maximale de la bainite est de 270 HV ou plus. (1) : Ceq = C + Mn/6 + (Cu + Ni)/15 + (Cr + Mo + V)/5. (2) : valeur A = 1,15 × Mn + 2,20 × Mo + 6,50 × Nb. (3) : valeur B = 1,20 × Mn + 0,50 × Ni + 4,25 × Nb.
PCT/JP2016/084857 2015-12-04 2016-11-24 Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées WO2017094593A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201680064618.1A CN108350540A (zh) 2015-12-04 2016-11-24 抑制了焊接热影响部的低温韧性劣化和焊接热影响部的硬度的具有高屈服强度的非调质钢板
EP16870530.9A EP3385399A4 (fr) 2015-12-04 2016-11-24 Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées
KR1020187018576A KR20180085791A (ko) 2015-12-04 2016-11-24 용접 열영향부의 저온 인성 열화 및 용접 열영향부의 경도를 억제한 고항복강도를 갖는 비조질 강판

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015-237839 2015-12-04
JP2015237839 2015-12-04

Publications (1)

Publication Number Publication Date
WO2017094593A1 true WO2017094593A1 (fr) 2017-06-08

Family

ID=58796697

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2016/084857 WO2017094593A1 (fr) 2015-12-04 2016-11-24 Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées

Country Status (5)

Country Link
EP (1) EP3385399A4 (fr)
JP (1) JP2017106107A (fr)
KR (1) KR20180085791A (fr)
CN (1) CN108350540A (fr)
WO (1) WO2017094593A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019050010A1 (fr) * 2017-09-08 2019-03-14 Ｊｆｅスチール株式会社 Tôle d'acier et son procédé de production
EP3733878A4 (fr) * 2018-01-30 2021-03-17 JFE Steel Corporation Matériau d'acier pour tube de conduite ainsi que procédé de fabrication de l'invention de celui-ci, et procédé de fabrication de tube de conduite
EP3733879A4 (fr) * 2018-01-30 2021-03-17 JFE Steel Corporation Matériau d'acier pour tube de conduite ainsi que procédé de fabrication de l'invention de celui-ci, et procédé de fabrication de tube de conduite

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113430460A (zh) * 2021-06-19 2021-09-24 宝钢湛江钢铁有限公司 一种屈服强度690MPa级低成本高强非调质钢板及其制造方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003160833A (ja) * 2001-11-22 2003-06-06 Kobe Steel Ltd 高靭性高張力非調質厚鋼板およびその製造方法
JP2006169591A (ja) * 2004-12-16 2006-06-29 Kobe Steel Ltd 高降伏強度を有する非調質鋼板
JP2009149917A (ja) * 2006-11-30 2009-07-09 Nippon Steel Corp 低温靱性に優れた高強度ラインパイプ用溶接鋼管及びその製造方法
JP2010209433A (ja) * 2009-03-11 2010-09-24 Kobe Steel Ltd 溶接熱影響部の靭性および母材疲労特性に優れた鋼材およびその製造方法
JP2011006772A (ja) * 2009-05-22 2011-01-13 Jfe Steel Corp 大入熱溶接用鋼材
JP2012193411A (ja) * 2011-03-16 2012-10-11 Kobe Steel Ltd Ｈａｚ靭性に優れた高強度厚鋼板
JP2013237101A (ja) * 2012-04-20 2013-11-28 Kobe Steel Ltd 耐水素誘起割れ性に優れた鋼材およびその製造方法

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005290554A (ja) * 2004-03-11 2005-10-20 Nippon Steel Corp 被削性と靭性および溶接性に優れた鋼板およびその製造方法
JP4772486B2 (ja) 2005-04-26 2011-09-14 新日本製鐵株式会社 低温用高強度鋼管
JP4768447B2 (ja) * 2006-01-11 2011-09-07 株式会社神戸製鋼所 溶接熱影響部の靭性に優れた耐候性鋼板
JP4950528B2 (ja) * 2006-03-16 2012-06-13 株式会社神戸製鋼所 溶接熱影響部の靭性に優れた低降伏比高張力鋼材およびその製法
JP4515427B2 (ja) * 2006-09-29 2010-07-28 株式会社神戸製鋼所 溶接熱影響部の靭性および疲労亀裂進展抵抗性に優れた鋼材およびその製法
JP4940886B2 (ja) * 2006-10-19 2012-05-30 Ｊｆｅスチール株式会社 耐ｈｉｃ特性に優れたラインパイプ用高強度鋼板およびその製造方法
JP5037204B2 (ja) 2007-04-12 2012-09-26 新日本製鐵株式会社 溶接熱影響部の靭性に優れる降伏応力５００ＭＰａ以上引張強さ５７０ＭＰａ以上の高強度鋼材の製造方法
RU2458996C1 (ru) 2008-11-06 2012-08-20 Ниппон Стил Корпорейшн Способ получения толстолистовой стали и стальных труб для ультравысокопрочного трубопровода
BRPI1012964A2 (pt) * 2009-06-11 2018-01-16 Nippon Steel Corp tubo de aço de alta resistência e método de produção do mesmo
CN102666898A (zh) * 2009-11-25 2012-09-12 杰富意钢铁株式会社 高压缩强度优异的管线管用焊接钢管及其制造方法
JP5561119B2 (ja) * 2009-11-25 2014-07-30 Ｊｆｅスチール株式会社 高圧縮強度耐サワーラインパイプ用溶接鋼管及びその製造方法
JP5910219B2 (ja) * 2012-03-23 2016-04-27 Ｊｆｅスチール株式会社 鋼板内の材質均一性に優れた大入熱溶接用高強度鋼板及びその製造方法
JP6226542B2 (ja) * 2013-03-22 2017-11-08 株式会社神戸製鋼所 溶接熱影響部の靭性に優れた鋼材
RU2653031C2 (ru) * 2014-03-31 2018-05-04 ДжФЕ СТИЛ КОРПОРЕЙШН Сталь для высокодеформируемых труб магистральных трубопроводов с высокой стойкостью к деформационному старению и водородному охрупчиванию, способ их изготовления и сварная стальная труба

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003160833A (ja) * 2001-11-22 2003-06-06 Kobe Steel Ltd 高靭性高張力非調質厚鋼板およびその製造方法
JP2006169591A (ja) * 2004-12-16 2006-06-29 Kobe Steel Ltd 高降伏強度を有する非調質鋼板
JP2009149917A (ja) * 2006-11-30 2009-07-09 Nippon Steel Corp 低温靱性に優れた高強度ラインパイプ用溶接鋼管及びその製造方法
JP2010209433A (ja) * 2009-03-11 2010-09-24 Kobe Steel Ltd 溶接熱影響部の靭性および母材疲労特性に優れた鋼材およびその製造方法
JP2011006772A (ja) * 2009-05-22 2011-01-13 Jfe Steel Corp 大入熱溶接用鋼材
JP2012193411A (ja) * 2011-03-16 2012-10-11 Kobe Steel Ltd Ｈａｚ靭性に優れた高強度厚鋼板
JP2013237101A (ja) * 2012-04-20 2013-11-28 Kobe Steel Ltd 耐水素誘起割れ性に優れた鋼材およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP3385399A4 *

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019050010A1 (fr) * 2017-09-08 2019-03-14 Ｊｆｅスチール株式会社 Tôle d'acier et son procédé de production
JPWO2019050010A1 (ja) * 2017-09-08 2019-11-07 Ｊｆｅスチール株式会社 鋼板およびその製造方法
EP3733878A4 (fr) * 2018-01-30 2021-03-17 JFE Steel Corporation Matériau d'acier pour tube de conduite ainsi que procédé de fabrication de l'invention de celui-ci, et procédé de fabrication de tube de conduite
EP3733879A4 (fr) * 2018-01-30 2021-03-17 JFE Steel Corporation Matériau d'acier pour tube de conduite ainsi que procédé de fabrication de l'invention de celui-ci, et procédé de fabrication de tube de conduite
US11401568B2 (en) 2018-01-30 2022-08-02 Jfe Steel Corporation Steel material for line pipes, method for producing the same, and method for producing line pipe

Also Published As

Publication number Publication date
CN108350540A (zh) 2018-07-31
EP3385399A4 (fr) 2019-05-22
EP3385399A1 (fr) 2018-10-10
JP2017106107A (ja) 2017-06-15
KR20180085791A (ko) 2018-07-27

Similar Documents

Publication Publication Date Title
JP5776398B2 (ja) 低温靭性に優れた低降伏比高強度熱延鋼板およびその製造方法
KR100799421B1 (ko) 용접성이 우수한 490ＭＰａ급 저항복비 냉간성형강관 및 그제조방법
JP5644982B1 (ja) 電縫溶接鋼管
JP5846311B2 (ja) 溶接熱影響部ｃｔｏｄ特性に優れた厚肉高張力鋼およびその製造方法
KR101709887B1 (ko) 라인 파이프용 강판 및 라인 파이프
JP6682785B2 (ja) 耐サワー性に優れた鋼板及びその製造方法
JP5910792B2 (ja) 厚鋼板及び厚鋼板の製造方法
JP6160574B2 (ja) 強度−均一伸びバランスに優れた高強度熱延鋼板およびその製造方法
JP7262288B2 (ja) 母材と溶接熱影響部の靭性に優れかつ音響異方性の小さい高強度低降伏比厚鋼板およびその製造方法
WO2017094593A1 (fr) Tôle d'acier non traitée thermiquement ayant une limite élastique élevée dans laquelle la dureté d'une zone affectée par la chaleur de soudage et la dégradation de la ténacité à basse température de la zone affectée par la chaleur de soudage sont supprimées
JP2016084524A (ja) 低温用ｈ形鋼及びその製造方法
JP6519024B2 (ja) 低温靭性に優れた低降伏比高強度熱延鋼板の製造方法
JP2017071827A (ja) Ｈ形鋼及びその製造方法
JP6288288B2 (ja) ラインパイプ用鋼板及びその製造方法とラインパイプ用鋼管
JP2019199649A (ja) 非調質低降伏比高張力厚鋼板およびその製造方法
JP5515954B2 (ja) 耐溶接割れ性と溶接熱影響部靭性に優れた低降伏比高張力厚鋼板
JP6521196B1 (ja) 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管
JP2016156032A (ja) 低温用ｈ形鋼及びその製造方法
JP2018115389A (ja) 厚鋼板および厚鋼板の製造方法
JP7163777B2 (ja) ラインパイプ用鋼板
WO2016068094A1 (fr) Tôle d'acier à haute résistance à la traction, présentant une excellente résilience aux basses températures de zones de soudage affectées thermiquement, et son procédé de production
JP2006241508A (ja) 溶接部の耐亜鉛めっき割れ性に優れたＨＴ４９０ＭＰａ級溶接構造用耐火鋼とその製造方法
JP6343472B2 (ja) 低温靭性に優れた高強度ラインパイプ用鋼板および高強度ラインパイプ用鋼管
WO2021200572A1 (fr) Tôle d'acier faiblement allié à haute résistance ayant une ténacité de matériau de base et une ténacité de joint soudé exceptionnelles, et procédé de fabrication de ladite tôle d'acier
JP2004076101A (ja) 溶接性に優れた高強度高靭性鋼管素材およびその製造方法

Legal Events

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

Ref document number: 16870530

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 20187018576

Country of ref document: KR

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 2016870530

Country of ref document: EP