WO2005052205A1 - Acier a haute resistance mecanique presentant une zone soudee d'une durete excellente et une structure offshore associee - Google Patents

Acier a haute resistance mecanique presentant une zone soudee d'une durete excellente et une structure offshore associee Download PDF

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Publication number
WO2005052205A1
WO2005052205A1 PCT/JP2004/017575 JP2004017575W WO2005052205A1 WO 2005052205 A1 WO2005052205 A1 WO 2005052205A1 JP 2004017575 W JP2004017575 W JP 2004017575W WO 2005052205 A1 WO2005052205 A1 WO 2005052205A1
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Prior art keywords
steel
toughness
strength
temperature
less
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PCT/JP2004/017575
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English (en)
Japanese (ja)
Inventor
Takahiro Kamo
Takeshi Urabe
Hirofumi Nakamura
Kazushi Ohnishi
Masahiko Hamada
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Sumitomo Metal Industries, Ltd.
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Application filed by Sumitomo Metal Industries, Ltd. filed Critical Sumitomo Metal Industries, Ltd.
Priority to JP2005515812A priority Critical patent/JP4432905B2/ja
Publication of WO2005052205A1 publication Critical patent/WO2005052205A1/fr
Priority to US11/443,849 priority patent/US20070051433A1/en
Priority to US12/557,892 priority patent/US20100226813A1/en

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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
    • C22C38/001—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
    • C22C38/18—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
    • C22C38/48—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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a high-strength steel and an offshore structure, particularly to a high-strength steel for welding and an offshore structure having excellent weld toughness.
  • the present invention is applied to high-strength steel for welding used as a welding structure in buildings, civil engineering structures, construction machines, ships, pipes, tanks, marine structures, etc., and particularly to marine structures.
  • high-strength steel for welding and offshore structures for example
  • the present invention relates to a high-strength steel plate having a yield strength of 420 N / mm 2 or more and a plate thickness of 50 mm or more, and an offshore structure using the same.
  • high-strength steel with a high strength of 460-70 OMPa class and a plate thickness exceeding 100 mm may be used.
  • the steel materials used in these offshore structures are required to have toughness in a very severe low-temperature range of, for example, 40 ° C or less, and also to have weldability.
  • the CTOD value at the lowest operating temperature is also specified to evaluate toughness. It is becoming. In other words, even if a micro test piece cut and sampled to a size of 10 mm X 10 mm obtains stable characteristics in the Charpy test, which is an evaluation test for all, In many cases, the required characteristics cannot be satisfied with the CTOD characteristics evaluated using a test piece with the actual thickness of the structure, and even more severe CTOD characteristics are required today.
  • Japanese Patent Publication No. Hei 7-81164 Japanese Patent Laid-Open No. 5-186820, Japanese Patent Laid-Open No. 5-17934
  • No. 4 proposes a Cu-precipitated steel having excellent toughness of a weld.
  • Japanese Patent Publication No. 7-81164 only evaluated the Charpy characteristics of a welded joint obtained with a plate thickness of 30 mm and a welding heat input of 40 kjZcm, and is unlikely to be a material compatible with large heat input welding.
  • Japanese Patent Application Laid-Open No. 5-186820 proposes a high-strength steel having a tensile strength of 686 MPa or more obtained by adding 0.5 to 4.0% Cu and adding copper. Since the transition temperature of the Charpy test is even 30 ° C, it is thought that low-temperature CTOD characteristics of extra-thick steel plates can be secured. hard.
  • Japanese Patent Application Laid-Open No. 5-179344 proposes a Cu-precipitated steel excellent in the Charpy toughness of a weld, but only evaluates the Charpy characteristics of a welded joint obtained at a welding heat input of 5 kJ, mm. Therefore, it is difficult to imagine that it is a technology that can sufficiently satisfy the safety of structures during adult thermal welding.
  • an object of the present invention is to provide a high-strength steel for welding which generally improves the low-temperature toughness of a weld, especially the HAZ low-temperature toughness.
  • the present inventors have conducted various experiments on steel components and a method for producing the same in order to develop a thick high-strength steel sheet having excellent weld toughness, and have obtained the following findings.
  • the strength and toughness balance can be controlled by arranging the distribution state of the Cu particles by the average value of the equivalent circle diameter obtained from the TEM photograph and the area equivalent area ratio.
  • Cu particles are easily generated on crystal defects (mainly dislocations) in steel. If the dislocation density is high, the precipitation of Cu particles is promoted. Also, Cu particles on dislocations hinder dislocation movement and increase the yield strength.
  • the dislocation density in the steel must be controllable under rolling and water cooling conditions.
  • reduction of rolling temperature increase of total reduction, increase of water cooling start temperature, increase of cooling rate, decrease of water cooling stop temperature, all of which must increase dislocation density.
  • the HAZ toughness can be improved by lowering the weld crack susceptibility index Pcm value with high Cu component materials, and it was a component that low C and low Mn-Dani were effective for that purpose.
  • Pcm weld crack susceptibility index
  • it was necessary to supplement with other elements, and by controlling the amount of added Mo, it was also a component that the strength can be stabilized.
  • the present invention has been constituted based on such knowledge, and the gist thereof is as follows.
  • Pcm C + (Si / 30) + (Mn / 20) + (Cu / 20) + (Ni / 60) + (Cr / 20) + (Mo / 15) + ( ⁇ / 10) + 5 ⁇ ⁇ ⁇ ( ⁇ )
  • a yield stress excellent in weldability which enables welding with a welding heat input of 300 KJ / cm or more by a welding method such as, but not limited to, gas arc welding at an electoral port, is excellent in weldability.
  • a welding method such as, but not limited to, gas arc welding at an electoral port.
  • Production of two or more high-strength steels became possible. As a result, the efficiency and safety of on-site welding were significantly improved.
  • C is added to secure the strength of the steel and to produce the effect of refining the structure when adding Nb, V, and the like. Below 0.01%, these effects are not sufficient. If too much force is applied, a hardened structure called martensite-austenite constituent (M-A) will be formed in the welded area, deteriorating the HAZ toughness and reducing the toughness and weldability of the base metal. Also have an adverse effect. Therefore, C should be 0.10% or less. Preferably 0.02-0.08. More preferably ⁇ or 0. 02-0. 05 0/0.
  • Si does not form a solid solution in force cementite, which is an effective element for pre-deoxidation of molten steel, so if added in a large amount, untransformed austenite grain force inhibits decomposition into S ferrite grains and cementite, Promotes the formation of island martensite.
  • the content of Si in the steel is 0.5% or less.
  • Mn is an element necessary for ensuring strength, and is also an effective element as a deoxidizing agent. Therefore, the content of Mn must be 0.8% or more. Excessive addition of Mn excessively increases the hardenability and degrades the weldability and HAZ toughness.
  • Mn is considered as an element that promotes central segregation, its content in terms of suppressing central segregation should not exceed 1.8%. Therefore, the content of Mn should be 0.8-1.8% or less. Preferably it is 0.9-1.5%.
  • P is an impurity element inevitably contained in steel, and is a grain boundary segregation element, which causes grain boundary cracking in HAZ.
  • the P content is set to 0.0020% or less. Preferably it is 0.015% or less, more preferably 0.01% or less.
  • the content of S should be 0.01% or less. It is preferably 0.008% or less, more preferably 0.005%.
  • Cu has the effect of increasing the strength and toughness of the steel material, but has little adverse effect on the HAZ toughness. In particular, 0.8% or more is required in order to expect the effect of increasing strength by ⁇ -Cu precipitation during aging treatment.
  • the Cu content was set to 1.5% or less. Preferably, it is 0.9-1.1%.
  • Ni is an effective element for increasing the strength and toughness of the steel material and for further increasing the HAZ toughness. However, if the content is less than 0.2%, these effects will be lost.If the content exceeds 1.5%, it is not possible to obtain an effect worth the cost increase. It was decided. Preferably it is 0.4-1.2%.
  • A1 is an essential element for deoxidation. However, as the content increases, the toughness tends to deteriorate, especially in HAZ. This is presumably because coarse cluster-like alumina-based inclusion particles are easily formed. Therefore, the content of A1 is set to 0.001-0.05%. Preferably ⁇ or 0. 001 0.03 0/0. In addition there is preferably ⁇ or 0. 001 0.015 0/0
  • ⁇ contributes to fine graining of the structure by forming a nitride, but when excessively added, In addition, the toughness is deteriorated through the aggregation of nitride. Therefore, the content of N is set to 0.003-0.008%. Preferably it is 0.0035-0.0065%.
  • CTOD characteristics can be improved.
  • O oxygen
  • the content of O is set to 0.0005 to 0.0035%.
  • ⁇ is 0.0008-0.0018%.
  • Ti has an action of generating nitrides to suppress the coarsening of crystal grains and to refine the transformed structure.
  • the addition of less than the specified amount does not exert the above-mentioned effects, and the addition of a large amount adversely affects the toughness of the base metal and the toughness of the welded portion. Therefore, the content of Ti is set to 0.005 to 0.03%. Preferably, it is 0.007-0.015%.
  • Nb improves the strength and toughness of the base material by grain refinement and carbide precipitation. On the other hand, if it is added excessively, the effect of improving the performance of the base material saturates and the toughness of HAZ is significantly impaired.
  • the Nb content is set to 0.003—0.03%. Preferably, it is 0.003% to 0.015%.
  • Mo has the effect of securing quenchability and improving HAZ toughness. Mo, when added excessively, causes significant hardening in HAZ and deteriorates toughness. Therefore, the content of Mo is set to 0.1 to 0.8%. Preferably it is 0.1-0.5%.
  • Cr enhances the hardenability of steel materials and is effective in ensuring strength. However, when added in a small amount, Cr does not show an improvement effect. When added excessively, it prevents the hardening of the weld metal and HAZ and prevents low-temperature cracking of the weld. Tends to increase sensitivity. Therefore, when Cr is added, the Cr content is set to 0.03-0.80%. Preferably it is 0.05-0.60%.
  • B has the effect of improving hardenability and increasing strength. On the other hand, if it is added excessively, the effect of increasing the strength is saturated, and the tendency of toughness deterioration of both the base material and HAZ becomes remarkable. Therefore, when adding B, the content of B shall be 0.0002-0.002%. Preferably it is 0.003-0.0015%.
  • V has a function of generating carbonitrides to suppress the coarsening of the crystal grains and to refine the transformed structure.
  • the addition of less than the specified amount does not exert the above-mentioned effects, and the addition of a large amount adversely affects the toughness of the base metal and the toughness of the welded portion. Therefore, when adding V, the content of V should be 0.001-0.05%. Preferably it is 0.005-0.04%.
  • Ca, Mg, and REM are elements that generate oxides and sulfides that serve as precipitation nuclei for intragranular ferrite. In addition, it controls the form of the sulphide and improves the low-temperature toughness.
  • the content of Ca must be 0.0005% or more, and in the case of Mg or REM, the content must be 0.001% or more.
  • the steel of the present invention has a Pcm represented by the following formula (I) of 0.25 or less, and the average force of the circle-equivalent diameter of Cu particles dispersed in the steel and having a major axis of 1 nm or more is not less than 1 nm. It is preferable that the thickness is 25 nm and the distribution amount in terms of plane ratio is 3 to 20%.
  • Pcm C + (Si / 30) + (Mn / 20) + (Cu / 20) + (Ni / 60) + (Cr / 20) + (Mo / 15) + ( ⁇ / 10) + 5 ⁇ ⁇ ⁇ ( ⁇ )
  • Pcm is an index that indicates the susceptibility to weld cracking. If its value is 0.25 or less, weld cracks will not occur under normal welding conditions. Therefore, Pcm should be 0.25 or less. Preheating during welding can be omitted by reducing Pcm. Preferably it is 0.22 or less, more preferably 0.20 or less.
  • the reason for targeting Cu particles with a diameter of 1 mm or more is that particles smaller than 1 mm contribute to increasing strength. This is because the force S is small.
  • the upper limit of the major axis of the Cu particles is not particularly defined, but no particles exceeding 100 nm will appear if the average value is in the range of 425 nm.
  • the precipitation form of the Cu particles is approximately spherical, it is not easy to measure the three-dimensional shape, so the projected shape is measured.
  • the equivalent circle diameter is the diameter of a circle having the same area as the projected area of the particle, and specifically,
  • d ⁇ (4a / pai) a: Projected area (nm 2 ), d: Circle equivalent diameter (nm pai: 3.14
  • a steel material is processed into a thin film, and a portion having a thickness of about 0.2 micrometer is observed with a TEM, and is distributed three-dimensionally in the thin film test piece. It is calculated by measuring the area ratio when the Cu particles are planarly projected on a TEM photograph with a magnification of 100,000.
  • the average diameter / distribution amount of the Cu precipitated particles is specified as described above in order to balance the increase in strength due to Cu precipitation and the decrease in CTOD value.
  • the reason why the equivalent circle diameter is set to 425 is to balance strength and toughness, and the reason why the flatness equivalent distribution is set to 3 to 20% is to balance strength and toughness.
  • the following factors can be considered as factors for controlling the Cu particle diameter and the distribution amount.
  • the distribution amount increases as the Cu addition amount increases.
  • the average particle size is determined mainly by the structure before the aging treatment, the temperature and the time of the aging treatment. If the amount is less than the proper amount, the precipitation of Cu particles is insufficient and the particle size is small. If the amount is large, the particle size tends to be large.
  • the structure before aging is preferably a fine structure mainly composed of ferrite and bainite.
  • the aging temperature and time are important factors.
  • the target particle dispersion state is controlled by strictly adjusting the Cu diffusion rate and the particle growth rate according to the aging treatment conditions.
  • the present invention is not particularly limited as long as it is performed by a conventional method up to the steel making process.
  • slabs are obtained following the steelmaking process, slabs (slabs) are preferably manufactured by a continuous sintering method from the viewpoint of cost reduction.
  • the caloric heat temperature of Maokagata was set to 900-1120 ° C.
  • the total reduction at 900 ° C or less is desirably 50% or more.
  • start water cooling at a temperature above the Ar point and stop at a temperature of 600 ° C or less.
  • the rolling finish temperature is 700 ° C or more
  • the cooling start temperature is 680 ° C to 750 ° C
  • the cooling rate to the cooling stop temperature is 1 to 50 ° C / s. If the water cooling stop temperature exceeds 600 ° C, the precipitation strengthening effect in the tempering treatment will be insufficient.
  • the Ar point is determined by a method of measuring a change in volume of the minute test piece.
  • the water-cooled steel is heated, if necessary, subjected to an aging treatment at a temperature of 540 or more and an Ac point or less, and then cooled.
  • the average heating rate up to the aging temperature of 100 ° C. and the average cooling rate up to 500 ° C. are controlled.
  • This aging treatment is to sufficiently precipitate and harden the precipitates of Cu, and the control of the heating Z cooling rate is performed to make the dispersion of the Cu particles uniform. Therefore, the heating rate is 5-50 ° CZ for the average heating rate up to the target temperature of 100 ° C, the holding time is 1 hour or more, and the cooling rate is 5-60 ° CZ for the cooling rate up to 500 ° C. It is preferable to do so.
  • the heating temperature in the present specification is the furnace atmosphere temperature
  • the holding time after heating is the holding temperature at the furnace atmosphere temperature
  • the rolling end temperature and the water cooling start / stop temperature are the surface layer temperature of the steel material
  • the average heating / cooling rate during reheating shall be calculated from the temperature calculation at the steel material thickness l / 2t position.
  • the offshore structure includes a platform laid on the sea floor, a semi-sub rig (a semi-submersible oil digging ij rig) that is not only a jack-up rig, etc. There are no particular restrictions on the offshore structure required.
  • “large” means that the thickness of the steel used for it is 50 mm or more.
  • a 300 mm-thick steel slab having the chemical components shown in Tables 1 and 2 was produced by a continuous casting method.
  • the temperature of the molten steel is not excessively increased, and the difference between the solidification temperature determined by the composition force of the molten steel and the solidification temperature is set within 50 ° C. Under the control, electromagnetic stirring immediately before coagulation and reduction during coagulation were performed.
  • Tables 3 and 4 show the processing conditions for the billets having the chemical components shown in Tables 1 and 2.
  • the processing conditions shown in Tables 3 and 4 are the processing conditions for steel slabs having the chemical components shown in Tables 1 and 2, respectively.
  • the slab having a thickness of 300 mm was heated at each heating temperature and each heating time, and then subjected to hot rolling, and then cooled to a water cooling start temperature at an average cooling rate of 5 ° C / s to a water cooling stop temperature.
  • the steel plate was 77 mm thick. (These conditions are shown in Tables 3 and 4 as initial heating and rolling conditions.)
  • the heating rate is controlled so that the average heating rate up to the aging temperature-100 ° C is 10 ° C / min, and the cooling rate is 10 ° C / min up to 500 ° C.
  • the heating rate is controlled so that the average heating rate up to the aging temperature-100 ° C is 10 ° C / min, and the cooling rate is 10 ° C / min up to 500 ° C.
  • the tensile test of the steel obtained in this manner was performed by taking a tensile test specimen having a diameter of 12.5 mm in the parallel part from the center of the thickness in the direction perpendicular to the rolling direction in accordance with the ASTM standard.
  • the welded joints were obtained by performing FCAW welding (Flux Cored Arc Welding) of 10. Okj / cm on the butt joints of the K-grooves in accordance with BS7448 standard.
  • FCAW welding Fluor Cored Arc Welding
  • the joint obtained in this way was processed at 40 ° C on a specimen obtained by processing the CTOD specimen so that the fatigue notch of the specimen became the weld line on the straight part side of the V-shaped groove.
  • a CTOD test was performed.
  • the same steel was subjected to 20 ° V groove processing, then butt-joined, and welded joints were produced by electorifice gas arc welding (EGW) with a heat input of 350kjZcm. did.
  • EGW electorifice gas arc welding
  • the welded joints produced at this time were subjected to a CTOD test according to ASTM E1290.
  • the CTOD test piece was applied so that the fatigue notch became the weld line, and the critical CTOD value was measured at a test temperature of -10 ° C.
  • the average value of the circle equivalent diameter of the Cu particles was determined using a transmission electron microscope with a magnification of 100,000.
  • TEM TEM
  • 10 fields of view one field of view is a rectangle of 900 X 700 nm
  • the average value was used.
  • Table 1 shows test materials satisfying the chemical components specified in the present invention. As shown in Table 5, when the test steels were manufactured and processed under the processing conditions shown in Table 3, the deviations also satisfied the dispersion state of the Cu particles within the specified range. Therefore, the base metal strength, base metal CTOD characteristics, and joint CTOD characteristics (-40 ° C and -10 ° C) of all test steels were high.o

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un acier à haute résistance mécanique, caractérisée en ce qu'il présente une composition chimique comprenant, en pourcentage en masse : C: 0,01 à 0,10 %, Si: inférieur ou égal à 0,5 %, Mn: 0,8 à 1,8 %, P: inférieur ou égal 0,020 %, S: inférieur ou égal 0,01 %, Cu: 0,8 à 1,5 %, Ni: 0,2 à 1,5 %, Al: 0,001 à 0,05 %, N: 0,0030 à 0,0080 %, O: 0,0005 à 0,0035 %, éventuellement un élément ou deux parmi Ti: 0,005 à 0,03 %, Nb: 0,003 à 0,03 % et Mo: 0,1 à 0,8 %, et le reste: Fe ou des impuretés, à la condition que N/Al soit compris entre 0,3 et 3,0. L'acier à haute résistance mécanique de l'invention peut être soudé à très haute température, et présente une dureté excellente à faible température.
PCT/JP2004/017575 2003-11-27 2004-11-26 Acier a haute resistance mecanique presentant une zone soudee d'une durete excellente et une structure offshore associee WO2005052205A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
JP2005515812A JP4432905B2 (ja) 2003-11-27 2004-11-26 溶接部靱性に優れた高張力鋼および海洋構造物
US11/443,849 US20070051433A1 (en) 2003-11-27 2006-05-26 High tensile strength steel and marine structure having excellent weld toughness
US12/557,892 US20100226813A1 (en) 2003-11-27 2009-09-11 High tensile strength steel and marine structure having excellent weld toughness

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JP2003-397531 2003-11-27
JP2003397531 2003-11-27

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JP2008163446A (ja) * 2006-12-06 2008-07-17 Jfe Steel Kk 大入熱溶接用鋼材
JP2009209401A (ja) * 2008-03-03 2009-09-17 Kobe Steel Ltd 溶接熱影響部の靭性と均一伸びに優れた鋼板
WO2011081349A3 (fr) * 2009-12-28 2011-11-10 주식회사 포스코 Tôle d'acier à haute résistance présentant une excellente résistance aux fissures fragiles et procédé de fabrication de celle-ci
CN103741079A (zh) * 2014-01-09 2014-04-23 鞍钢股份有限公司 一种超高强度海洋工程用钢板及其生产方法
CN105296845A (zh) * 2015-10-21 2016-02-03 苏州雷格姆海洋石油设备科技有限公司 一种超低温耐腐蚀的高强度锻件毛坯的制造方法
WO2017183719A1 (fr) * 2016-04-21 2017-10-26 新日鐵住金株式会社 Acier à haute résistance à la traction et structure marine

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EP2045348B1 (fr) * 2006-07-13 2013-03-13 Nippon Steel & Sumitomo Metal Corporation Tuyau coudé et son procédé de fabrication
BRPI0808457B1 (pt) 2007-12-07 2018-09-11 Nippon Steel & Sumitomo Metal Corp aços superiores em propriedades ctod da zona afetada pelo calor
KR101318227B1 (ko) 2008-05-23 2013-10-15 한국기계연구원 구리를 함유한 복합 베이나이트계 강재 및 그 제조방법
BRPI1007386A2 (pt) 2009-05-19 2016-02-16 Nippon Steel Corp aço para estrutura soldada e método de produção do mesmo
DE102010019563A1 (de) * 2010-05-05 2011-11-10 Kme Germany Ag & Co. Kg Korrosionsschutzanordnung für Offshore Stahlstrukturen sowie ein Verfahren zu seiner Aufbringung
CN104603313A (zh) 2012-09-06 2015-05-06 杰富意钢铁株式会社 焊接热影响部ctod特性优异的高张力厚钢及其制造方法
CN103014498A (zh) * 2012-12-21 2013-04-03 首钢总公司 一种355MPa级低焊接裂纹敏感性钢板及生产方法
CN103225044B (zh) * 2013-04-24 2015-06-17 马钢(集团)控股有限公司 一种钒微合金化低温钢筋用钢及其轧制工艺
CN104520463B (zh) 2013-08-13 2016-03-30 新日铁住金株式会社 钢板
CN103451536B (zh) * 2013-09-30 2015-06-24 济钢集团有限公司 一种低成本厚规格海底管线钢板及其制造方法
CN105980588B (zh) 2013-12-12 2018-04-27 杰富意钢铁株式会社 钢板及其制造方法
CN103882312B (zh) * 2014-03-04 2016-04-27 南京钢铁股份有限公司 低成本高韧性-140℃低温用钢板的制造方法
DE102014205392A1 (de) * 2014-03-24 2015-09-24 Comtes Fht A. S. Bauteile aus einer Stahllegierung und Verfahren zur Herstellung hochfester Bauteile
JP6245352B2 (ja) 2014-03-31 2017-12-13 Ｊｆｅスチール株式会社 高張力鋼板およびその製造方法
EP3722448B1 (fr) * 2017-12-07 2024-03-06 JFE Steel Corporation Acier riche en mn, et procédé de fabrication de celui-ci

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CN1886530A (zh) 2006-12-27
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