WO2007015311A1 - ACIER À FORTE RÉSISTANCE À LA TRACTION DE GRADE 409 MPa DESTINÉ À DES STRUCTURE SOUDÉES PRÉSENTANT UNE EXCELLENTE RÉSISTANCE À HAUTE TEMPÉRATURE ET PROCÉDÉ DE PRODUCTION DE CELUI-CI - Google Patents

ACIER À FORTE RÉSISTANCE À LA TRACTION DE GRADE 409 MPa DESTINÉ À DES STRUCTURE SOUDÉES PRÉSENTANT UNE EXCELLENTE RÉSISTANCE À HAUTE TEMPÉRATURE ET PROCÉDÉ DE PRODUCTION DE CELUI-CI Download PDF

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Publication number
WO2007015311A1
WO2007015311A1 PCT/JP2005/014461 JP2005014461W WO2007015311A1 WO 2007015311 A1 WO2007015311 A1 WO 2007015311A1 JP 2005014461 W JP2005014461 W JP 2005014461W WO 2007015311 A1 WO2007015311 A1 WO 2007015311A1
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WO
WIPO (PCT)
Prior art keywords
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steel
strength
temperature
temperature strength
Prior art date
Application number
PCT/JP2005/014461
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English (en)
Japanese (ja)
Inventor
Yasushi Mizutani
Yoshiyuki Watanabe
Ryuuji Uemori
Tatsuya Kumagai
Original Assignee
Nippon Steel Corporation
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 Nippon Steel Corporation filed Critical Nippon Steel Corporation
Priority to PCT/JP2005/014461 priority Critical patent/WO2007015311A1/fr
Priority to CNA2005800465281A priority patent/CN101098978A/zh
Priority to TW094126181A priority patent/TW200706659A/zh
Publication of WO2007015311A1 publication Critical patent/WO2007015311A1/fr

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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
    • 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
    • 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 architecture, civil engineering, offshore structures, shipbuilding, various storage tanks.
  • This invention is mainly intended for thick plates (thick steel plates), but also includes steel pipes and shaped steel.
  • the strength of general welded structural steel has been reduced from about 350 ° C, and its allowable temperature is about 500 ° C. For this reason, when these steel materials are used in buildings, offices, residences, multi-storey parking lots, and other buildings, it is mandatory to provide fireproof coatings to ensure safety in fires.
  • the building-related laws and regulations stipulate that the temperature of a steel material does not exceed 350 " € in the event of a fire. This is because the steel material has a proof stress (yield strength) strength of about s' 350 ° C and 2/3 of room temperature. This is because the fireproof coating has a great influence on the construction cost.
  • B is in the midst of merits and demerits, such as increasing hardenability. For example, during low heat input welding, the weld heat affected zone hardens significantly, resulting in poor toughness. Conversely, if the heat input becomes too high, it precipitates at the austenite grain boundaries and the hardenability of B cannot be used effectively. The problem was that the weld heat input range was limited due to the coarse structure and poor toughness.
  • An object of the present invention is to provide a high-strength steel for welded structure having excellent high-temperature strength in a temperature range of 600 to 800 ° C, and a production method capable of industrially supplying the steel. .
  • the present invention achieves the object by limiting the steel components, microstructures, etc. to appropriate ranges, and the gist thereof is as follows.
  • P CM C + Si / 30 + Mn / 20 + CU / 20 + N1 / 60 + Cr / 20 + Mo / 15+ V / 10 + 5 B
  • Weld crack susceptibility composition P CM define the 15% or less 0.1 and contains substantially no B, with a remainder being iron and unavoidable impurities, microstructure was a mixed structure mainly of ferrite preparative base Inai Bok 490MPa class high-strength steel for welded structures with excellent high-temperature strength, characterized by a 20-90% portion of the vane.
  • the average equivalent circle diameter of the old austenite grains having a cross section parallel to the rolling direction at a thickness of 1/4 thickness is 120 m or less. 490MPa class high strength steel for welded structures with excellent high temperature strength as described.
  • High-temperature strength is enhanced by the addition of Mo and Nb, which promotes the precipitation of stable carbonitrides at high temperatures and increases the dislocation density due to the formation of chromite structure, and further dislocations by solid solution Mo and Nb. It is effective to delay recovery.
  • Mo and Nb which promotes the precipitation of stable carbonitrides at high temperatures and increases the dislocation density due to the formation of chromite structure, and further dislocations by solid solution Mo and Nb. It is effective to delay recovery.
  • a large amount of Mo is indispensable in the extension of conventional knowledge, but excellent welding as a steel for welded structures. Contrary to the viewpoint of securing the weldability and weld toughness, it is extremely difficult to achieve high temperature strength.
  • the alloy element is optimized and the structure is controlled, particularly by the thermal stability of the matrix structure at a high temperature, the appropriate coherent precipitation strengthening effect, and the dislocation recovery delay effect.
  • the thermal stability of the matrix structure at a high temperature we have found that it is possible to achieve both high weldability, weld toughness and high-temperature strength.
  • C has the most prominent effect on the properties of steel, and must be controlled within a narrow range, with a limited range of 0.005% or more and less than 0.040%.
  • the amount of C is less than 0.005%, the strength is insufficient, and when it exceeds 0.040%, the amount of Mo. added is large.
  • the weldability and weld toughness are deteriorated, and the cooling rate after the rolling is finished. If it is too large, the yield of the bainty increases and the risk of excess strength increases.
  • the mixed matrix structure of Paynite and Ferai ⁇ is kept thermodynamically stable and consistent with Mo, Nb, V, and Ti composite carbonitride precipitates. Maintenance Therefore, C is required to be less than 0.040% in order to secure the strengthening effect.
  • Si is an element contained in deoxidized upper steel and has a substitutional solid solution strengthening action, so it is effective in improving the strength of the base metal at room temperature, but is particularly effective in improving the high temperature strength above 600 ° C. There is no.
  • the upper limit is limited to 0.5%. Deoxidation of steel is possible with Ti and A1 alone, and is preferably as low as possible from the viewpoint of weld toughness and hardenability, and is not necessarily added.
  • Mn is an indispensable element for securing strength and toughness, but Mn, a substitutional solid solution strengthening element, is effective in increasing the strength at room temperature, but it is particularly suitable for high-temperature strength at 600. There is not much improvement effect. Therefore, it is necessary to relatively viewpoint from less than 0.5% of the weldability improving i.e. P CM reduced in steel containing a large amount of Mo such as in the present invention.
  • the upper limit of M n low, it is advantageous from the viewpoint of center segregation of the continuous forged slab.
  • addition of 0.1% or more is necessary to adjust the strength and toughness of the base metal.
  • P and S are impurities in the steel of the present invention, and the lower the better. P segregates at the grain boundaries and promotes grain boundary fracture, and S forms sulfides typified by MnS and degrades the toughness of the base metal and welds, so the upper limit is 0.02% and 0.01% respectively. %.
  • Mo is an indispensable element along with Nb from the viewpoint of high temperature strength development and maintenance in the steel of the present invention. It is more advantageous to add more from the standpoint of high-temperature strength, but it should be constrained in consideration of the base metal strength, weldability, and weld toughness.
  • Mo is allowed up to 1.5%.
  • the lower limit is the combined addition with Nb, or the addition of V and Ti, which are effective for improving the high temperature strength described later, ensuring stable high temperature strength. In order to achieve this, it is necessary to add 0.3% or more.
  • Nb is an element that must be added in combination with Mo.
  • Nb is an element useful for raising the recrystallization temperature of austenite and maximizing the effect of controlled rolling during hot rolling. It also contributes to the refinement of the heated austenite cake during reheating prior to rolling. In addition, it has the effect of improving high temperature strength by strengthening precipitation and suppressing dislocation recovery, and by adding it together with Mo, it contributes to further improvement of high strength. If less than 0.03%, the effect of suppressing precipitation hardening and dislocation recovery at 700 ° C and 800 ° C is small ⁇ , and if exceeding 0.15%, the degree of hardening decreases with respect to the amount added, which is also economically favorable. Not only does it deteriorate, but the toughness of the welds also deteriorates. For these reasons, Nb is limited to the range of 0.03 to 0.15%.
  • a 1 is an element generally contained on deoxidation, but deoxidation is performed by Si or
  • N is contained in steel as an unavoidable impurity.
  • Nb and T i described later are added, Nb combines with Nb to form carbonitride to increase the strength. To enhance the properties of steel. For this reason, at least 0.001% is necessary as the N amount.
  • an increase in the amount of N is detrimental to weld zone toughness and weldability, and in the present invention the upper limit is 0.006%.
  • This upper limit is not necessarily limited in terms of characteristics, and is limited within the range confirmed by the present inventors.
  • Cu, Ni which can be contained if necessary
  • the reasons for the addition of Cr, V, Ti, Ca, REM, and Mg and the range of the amount added are explained.
  • the main purpose of adding these elements to the basic components is This is because the characteristics such as strength and toughness are improved without impairing the excellent characteristics of the steel of the present invention. Therefore, the amount of addition is of a nature that should be restricted naturally.
  • the upper limit was limited to 1.0%. It is known that the Cu crack itself can be avoided by adding appropriate Ni depending on the amount of Cu. Since the weldability is also related to the amount of other alloy elements including the C amount, the upper limit is not necessarily limited. It does not have a limit taste.
  • Ni exhibits almost the same effect as Cu, and has a particularly large effect on improving the toughness of the base metal. In order to enjoy these effects reliably, at least
  • the upper limit is 1.0%.
  • Cr can be added as necessary to improve the strength of the base material. It can be clearly distinguished from the small amount of playing cards / elements from scrap, etc.
  • V has almost the same effect and action as Nb, including improved high-temperature strength. The effect is small compared to that of Nb.
  • V is as can be seen from the fact that also contains the expression of P CM, hardenability, ⁇ boss the impact on the weldability. Therefore, the lower limit is set to 0.01% to ensure the effect of V addition, and the upper limit is set to 0.1% to eliminate adverse effects.
  • Ti like Nb and V, is effective in improving high temperature strength. In addition to this, it is preferable to add them particularly when the requirements for the base metal and the weld zone toughness are severe. Because, Ti, when the amount of A1 is small (e.g., 0.003%), combined with O form precipitates composed mainly of Ti 2 0 3, becomes intragranular ferrite formation of nuclei, weld zone toughness Improve. In addition, Ti combines with N and precipitates finely in the slab as TiN, which suppresses the coarsening of austenite grains during heating and is effective in refining the rolling structure. The fine TiN present in the steel sheet ⁇ Refine the grain structure of the heat affected zone during welding. To obtain these effects, Ti must be at least 0.005%. However, if the amount is too large, TiC is formed and low temperature toughness deteriorates weldability, so the upper limit is 0.025%.
  • Ca and REM combine with the impurity S to improve toughness and suppress cracking due to diffusible hydrogen in the weld, but if too much, coarse inclusions are formed, which adversely affects toughness. Therefore, both are limited to the range of 0.0005 to 0.004%. Since both elements have almost the same effect, at least one of them should be added in order to enjoy the above-described effect.
  • Mg has the effect of suppressing the growth of austenite grains in the weld heat-affected zone and making it finer, making it possible to strengthen the weld zone. In order to enjoy such effects, Mg needs to be 0.0001% ⁇ . On the other hand, as the additive amount increases, the effect on the additive amount decreases and the economic efficiency is lost, so the upper limit was set to 0.006%.
  • B is not made intentionally, and steelmaking The point is that it does not contain substantially beyond the level included as a contamination in the process.
  • B is extremely advantageous in terms of microstructure control and strength improvement when used in high-strength steel because B significantly increases hardenability, but it also has the risk of degrading weldability and weld toughness. Have both.
  • the graphical addition of B is avoided and the material is substantially B-free.
  • P CM C + Si / 30 + Mn / 20 + Cu / 20 + Ni / 60 + Cr / 20 + Mo / 15+ V / 10+ ⁇ B
  • P CM has excellent low as weldability, not more than 0.22%, preheating (for welding cold cracking prevention) during welding are said unnecessary.
  • preheating for welding cold cracking prevention
  • Pe M is 0 15% or less is a very low value
  • ⁇ ⁇ ⁇ organization is also limited.
  • the microstructure is mainly composed of a mixture of ferrite and Payne cake, and the fraction of the Payne cake is limited to 20 to 90%. This is because 490MPa class room temperature is a little higher than the pay rate fraction.
  • the present invention is limited to clarify the characteristics of the present invention, and is not necessarily limited.
  • microstructures are representative of 14 thickness positions in the thickness direction.
  • name of “Bainite” as an organization name is unclear at certain points in the area when measuring fractions due to the variety of force variations that are widely used by those skilled in the art. May occur. In that case, there is also a method of judging with “Ferrai ⁇ ”, which is another organization in the organizational structure.
  • the X-ray distribution ratio of this place a is 10% to 80%. It is a polygonal or pseudopolygonal ferrule that does not contain any light (not including needle-shaped ferrules).
  • the austenite grain size before transformation after rolling needs to be appropriately limited in order to control (toughen) the toughness of a relatively high Mo-added steel such as the present invention.
  • the finer the austenite the finer the final transformation structure and the better the toughness.
  • the austenite grain size at the position of 1 to 4 'thickness in the sheet thickness cross-section direction in the final rolling direction of the steel sheet is limited to an average equivalent circle diameter of 120 m or less.
  • the austenity particle size In many cases, it is not always easy to determine the austenity particle size. In such a case, use an impact test piece with a notch sampled in the direction perpendicular to the final rolling direction of the steel sheet, centering on the position where the thickness is 1/4 thickness, for example, JISZ 2202 2mmV notch test piece, Brittle fracture at sufficiently low temperature In this case, the average equivalent circle diameter should be 120 m or less as well. is there.
  • the excellent properties aimed at by the present invention including the structure (structure, tissue fraction, former austenite particle size, etc.) and the high temperature characteristics as limited to the above, are as follows. It can be easily obtained.
  • the reheating of billets or slabs with a given steel composition is limited to a temperature range of 1 100-1250 ° C.
  • the lower limit of 1100 is to make Mo, Nb, and V and Ti added as needed, in a solid solution state with the primary purpose of ensuring high-temperature properties.
  • the higher the reheating temperature the better, but the heating austenite grains are coarsened and are not preferred from the standpoint of base material toughness, so the upper limit is limited to 1250.
  • the limitation of the rolling conditions is directly to control the austenite grain size before the transformation after rolling to a relatively fine grain as described above, mainly for ensuring toughness. For this reason, rolling requires that the cumulative reduction at 1 100 ° C or less be 30% or more.
  • the rolling end temperature is limited to 850: or more as the lower limit temperature for precipitation of Mo, Nb, or V, Ti added as needed as carbides under low temperature pressure.
  • Cooling after rolling should also be limited from the viewpoint of structure control. Although it depends on the steel composition, a relatively thin material can obtain a specified structure even at a cooling rate that is about the same as that of cooling. However, if it is thicker, the cooling rate becomes slower when cooling is needed, and accelerated cooling is required. There is. In this case, accelerated cooling is most commonly water cooling in the production of thick steel sheets, but it is not always necessary to use water cooling. In addition, accelerated cooling is aimed at increasing the cooling speed in the transformation region for controlling the structure, so it is necessary to perform from 800 to above 650 ° C.
  • P high temperature yield stress
  • Force Steel temperature T (° C) Force Within the range of 600 ° C to 800 ° C, p ⁇ —0.0033 XT + 2.80.
  • Steel sheets of various steel components are manufactured in a continuous forging process of a converter-thick plate process.
  • the mechanical properties, weldability, and weld toughness are evaluated according to JIS.
  • the presence or absence of root cracks in the shape weld cracking test and the HAZ toughness of reproduction equivalent to small heat input and super large heat input welding by the welding reproducible heat cycle were investigated.
  • Table 1 shows the steel components of the present invention together with the comparative example
  • Table 2 shows the manufacturing conditions
  • Table 3 shows the results of the investigation of the structure and various properties.
  • the comparative example is inferior in characteristics to the inventive example because at least one of the steel components, production conditions, and structure deviates from the limited range of the present invention. I understand. That is, in Comparative Example 19, the amount of C is low, and thus the fraction of the vein is low, and both the room temperature strength and the high temperature strength (ratio) are low. In Comparative Example 20, the amount of C is high, so the bainitic fraction is high, and the room temperature strength is high. In addition, the base metal toughness, reproducible HAZ toughness is also inferior.
  • Comparative Example 21 Since Comparative Example 21 has a low Mo content and a low acceleration cooling start temperature, the high-temperature strength (ratio) is low due to the low payin fraction. Comparative Example IV has a low Nb content, a low heating temperature and a rolling end temperature, and a high accelerated cooling stop temperature, resulting in low normal temperature strength and high temperature strength (ratio). In Comparative Example 23, since B is added, when accelerated cooling is applied, the bainite fraction is high and the base metal toughness is poor. In addition, the reproducible HAZ toughness is inferior.
  • Comparative Example 24 has a high amount of Mn, P CM In addition, the cumulative reduction amount below 1 100 is also low, and therefore the base material strength becomes excessive as 490MPa grade steel with a high percentage of baseite, resulting in poor base metal toughness and reproducible HAZ toughness.
  • the root crack in the oblique y-type weld crack test was about 0.185% in Comparative Example 24 although Pc M was higher than the limited range of the present invention, and it did not occur in any case.
  • Charpy impact test piece JIS I 2202 2mniV notch, rolling direction
  • High-temperature tensile specimen Round bar (8 ⁇ or 10mm ⁇ , 1/4 thickness position, perpendicular to the rolling direction
  • Thermal history 1 1400 at X 1 sec, '800 ⁇ 500 cooling time 8 sec
  • the steel materials produced by the steel components and production methods based on the present invention have been demonstrated in the examples that the microstructure also satisfies the limited range of the present invention and is excellent not only in high temperature strength but also in weldability and weld toughness. It was. In other words, it is possible to industrially stably mass-produce welded structural steels with high-temperature properties far exceeding the conventional refractory steels that guarantee high-temperature properties up to about 600. For architectural use, for example, it is expected that applied buildings and completely fire-resistant coatings will be greatly expanded.

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  • 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

L’invention concerne un acier à forte résistance à la traction de grade 490 MPa destiné à des structures soudées qui présente une excellente résistance à haute température dans une gamme de 600 °C à 800 °C. Ledit acier à forte résistance à la traction de grade 490 MPa destiné à des structures soudées est caractérisé en ce qu’il a une composition chimique consistant en pas moins de 0,005 % et moins de 0,040 % de C, 0,5 % ou moins de Si, pas moins de 0,1 % et moins de 0,5 % de Mn, 0,02 % ou moins de P, 0,01 % ou moins de S, de 0,3 % à 1,5 % de Mo, de 0,03 % à 0,15 % de Nb, 0,06 % ou moins de Al, 0,006 % ou moins de N et le reste en fer et en impuretés inévitables, tout en contenant facultativement, si nécessaire, un ou plusieurs parmi Cu, Ni, Cr, V, Ti, Ca, REM et Mg. Ledit acier à forte résistance à la traction est de plus caractérisé en ce qu’il a une composition de sensibilité au craquage par soudure (PCM), qui est définie par la formule PCM = C + Si/30 + Mn/20 + Cu/20 + Ni/60 + Cr/20 + Mo/15 + V/10 + 5B, de pas plus de 0,15 %, et ne contenant substantiellement aucun B. Ledit acier à forte résistance à la traction est de plus caractérisé en ce qu’il a une micro-structure principalement composée d’une structure mixte de ferrite et de bainite, et que la bainite représente de 20 % à 90 % de la structure mixte. L’invention concerne également un procédé de fabrication dudit acier à forte résistance à la tension.
PCT/JP2005/014461 2005-08-01 2005-08-01 ACIER À FORTE RÉSISTANCE À LA TRACTION DE GRADE 409 MPa DESTINÉ À DES STRUCTURE SOUDÉES PRÉSENTANT UNE EXCELLENTE RÉSISTANCE À HAUTE TEMPÉRATURE ET PROCÉDÉ DE PRODUCTION DE CELUI-CI WO2007015311A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
PCT/JP2005/014461 WO2007015311A1 (fr) 2005-08-01 2005-08-01 ACIER À FORTE RÉSISTANCE À LA TRACTION DE GRADE 409 MPa DESTINÉ À DES STRUCTURE SOUDÉES PRÉSENTANT UNE EXCELLENTE RÉSISTANCE À HAUTE TEMPÉRATURE ET PROCÉDÉ DE PRODUCTION DE CELUI-CI
CNA2005800465281A CN101098978A (zh) 2005-08-01 2005-08-01 高温强度优异的焊接结构用490MPa级高强度钢及其制造方法
TW094126181A TW200706659A (en) 2005-08-01 2005-08-02 490 MPa grade high strength weldable structural steel having excellent in high temperature strength

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2005/014461 WO2007015311A1 (fr) 2005-08-01 2005-08-01 ACIER À FORTE RÉSISTANCE À LA TRACTION DE GRADE 409 MPa DESTINÉ À DES STRUCTURE SOUDÉES PRÉSENTANT UNE EXCELLENTE RÉSISTANCE À HAUTE TEMPÉRATURE ET PROCÉDÉ DE PRODUCTION DE CELUI-CI

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WO2007015311A1 true WO2007015311A1 (fr) 2007-02-08

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CN102666884B (zh) * 2010-02-08 2013-07-31 新日铁住金株式会社 厚钢板的制造方法
CN104419871B (zh) * 2013-09-05 2017-02-01 鞍钢股份有限公司 耐海洋环境腐蚀性能优良的焊接结构用钢及其制造方法
CN107475630B (zh) * 2017-09-01 2019-09-27 新冶高科技集团有限公司 一种热镀锌用纳米强化高强度低碳含Nb钢及其制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0941035A (ja) * 1995-08-04 1997-02-10 Kawasaki Steel Corp 靱性に優れる低降伏比熱延鋼板の製造方法
JP2002294393A (ja) * 2001-04-02 2002-10-09 Nippon Steel Corp 溶接性に優れた高張力鋼およびその製造方法
JP2004339549A (ja) * 2003-05-14 2004-12-02 Nippon Steel Corp 溶接性、ガス切断性に優れた構造用４９０ＭＰａ級高張力耐火鋼ならびにその製造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0941035A (ja) * 1995-08-04 1997-02-10 Kawasaki Steel Corp 靱性に優れる低降伏比熱延鋼板の製造方法
JP2002294393A (ja) * 2001-04-02 2002-10-09 Nippon Steel Corp 溶接性に優れた高張力鋼およびその製造方法
JP2004339549A (ja) * 2003-05-14 2004-12-02 Nippon Steel Corp 溶接性、ガス切断性に優れた構造用４９０ＭＰａ級高張力耐火鋼ならびにその製造方法

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