WO2010082361A1 - Acier pour construction soudée ayant une excellente résistance à température élevée et une excellente résilience aux basses températures et procédés de production de l'acier - Google Patents

Acier pour construction soudée ayant une excellente résistance à température élevée et une excellente résilience aux basses températures et procédés de production de l'acier Download PDF

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WO2010082361A1
WO2010082361A1 PCT/JP2009/050906 JP2009050906W WO2010082361A1 WO 2010082361 A1 WO2010082361 A1 WO 2010082361A1 JP 2009050906 W JP2009050906 W JP 2009050906W WO 2010082361 A1 WO2010082361 A1 WO 2010082361A1
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steel
temperature
less
strength
low
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PCT/JP2009/050906
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English (en)
Japanese (ja)
Inventor
渡部義之
植森龍治
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新日本製鐵株式会社
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Priority to PCT/JP2009/050906 priority Critical patent/WO2010082361A1/fr
Priority to KR1020097012504A priority patent/KR101189263B1/ko
Priority to BRPI0901011A priority patent/BRPI0901011B1/pt
Priority to US12/449,512 priority patent/US20110262298A1/en
Priority to EP09707108.8A priority patent/EP2380997B1/fr
Priority to CN2009800000583A priority patent/CN101849026B/zh
Priority to JP2009509204A priority patent/JP4834149B2/ja
Publication of WO2010082361A1 publication Critical patent/WO2010082361A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/18—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
    • C22C38/38—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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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 is mainly intended for building construction refractory steel for the purpose of maintaining proof stress at high temperatures such as fires, but is not limited to architectural use, and is widely used for marine structures, ships, bridges, various storage tanks, etc. Applicable to welded structural steel.
  • the strength level of the steel plate as a target is a class generally called as 40 kg or 50 kg steel, which has a yield strength of 235 to 475 MPa and a tensile strength of 400 to 640 MPa.
  • Refractory steel with increased resistance is being used.
  • Mo is added to refractory steel for the purpose of maintaining high-temperature strength.
  • Mo has a large change in market conditions, and depending on the amount added, it is often more expensive than the fireproof coating cost. For this reason, development and practical use of an inexpensive refractory steel not containing Mo have been awaited.
  • An object of this invention is to obtain the steel for welded structures which is excellent also in the low temperature toughness which is one of the basic performances of steel materials with the outstanding high temperature strength, without adding expensive Mo.
  • refractory steel that has excellent high-temperature strength, suppressed weld cracking susceptibility, and secured low-temperature toughness is industrially stable and low-cost. It provides a method that can be supplied by According to the present invention, a large amount of welded structural steel having sufficient proof strength can be supplied even in an environment exposed to a high temperature such as a fire, and this contributes to improving the safety of a wide range of welded steel structures for various applications. Is possible.
  • the point of the present invention is to secure a high-temperature strength at 600 ° C.
  • the inventors have found that it is very finely precipitated in the matrix, and that high-temperature strength can be secured and maintained at a high level, resulting in the present invention.
  • the refractory steel not containing Mo is very innovative in itself, and at the same time, the basic performance (strength and toughness) as a welded structural steel is low by not containing Mo with high hardenability. Of course, it also leads to improved weldability and gas cutting performance.
  • the present invention Cr, not Nb only defines C, Si, individual element content and weld crack susceptibility composition P CM, including Mn, by further limiting the manufacturing conditions, the use of costly Mo Not only has excellent high-temperature strength and low-temperature toughness compatible, but also ensures various use performances as welded structural steel.
  • the summary is as follows.
  • a method for producing a welded structural steel having excellent high temperature strength and low temperature toughness (2) After finishing the hot rolling, accelerated cooling is started from a temperature of 750 ° C. or higher, and accelerated cooling is stopped at a temperature of 550 ° C. or lower. A method for producing welded structural steel with excellent low temperature toughness. (3) Furthermore, in mass%, V: 0.01 to 0.10% Ti: 0.005 to 0.025% (1) or (2), the method for producing a welded structural steel having excellent high-temperature strength and low-temperature toughness.
  • C 0.003 to 0.05%
  • C is limited to a very low level as a high strength steel. This is closely related to the production method along with other components. Among steel components, C has the greatest influence on the properties of steel materials.
  • the lower limit of 0.003% is a minimum value for preventing the heat-affected zone such as securing strength and welding from being softened more than necessary. If the amount of C is too large, the hardenability is increased more than necessary, which adversely affects the balance between strength and toughness of the steel material and weldability.
  • the upper limit was made 0.05%.
  • the lower limit is preferably 0.005%, more preferably 0.01%, in order to avoid strength reduction from the balance with operational fluctuations and other components.
  • the upper limit is preferably 0.04%, and more preferably 0.03%.
  • Si 0.60% or less Si is an element contained in steel for deoxidation, but if added in large amounts, weldability and HAZ toughness deteriorate, so the upper limit was made 0.60%.
  • the content may be determined by balance with these elements. However, it is preferably as low as possible from the viewpoints of HAZ toughness, hardenability, etc., and may be free of additives. For this reason, the upper limit may be limited to 0.40%, 0.20%, and 0.10%.
  • Mn 0.6 to 2.0% Mn is an indispensable element for securing the strength and toughness at room temperature, and its lower limit is 0.6%. Preferably it is 0.8% or more or 1.0% or more.
  • the upper limit was made 2.0%. Preferably it is 1.8% or less, More preferably, it is 1.6% or less or 1.4% or less. P: 0.020% or less Since the amount of P tends to decrease the grain boundary fracture in HAZ when the amount is small, the smaller the amount, the better. If the content is large, the low temperature toughness of the base metal and the weld zone is deteriorated, so the upper limit is made 0.020%. More preferably, the content is 0.015% or less, 0.010% or less, or 0.008% or less.
  • S 0.010% or less S is more preferable from the viewpoint of low temperature toughness of the base material. If the content is large, the low temperature toughness of the base metal and the welded portion is deteriorated, so the upper limit is made 0.010%. 0.008% or less, 0.006%, and 0.004% are more preferable. Of course, no additives may be added.
  • Cr 0.20 to 1.5% Cr is one of the most important elements in the present invention. It is essential to add Cr together with Nb to ensure high temperature strength.
  • the Cr content should be at least 0.20%. Preferably it is 0.35% or more, more preferably 0.50% or more, 0.8% or 1.0% or more. However, if the addition amount is too large, the base material, the toughness of the welded portion and the weldability are deteriorated and the economical efficiency is also lost, so the upper limit was made 1.5%. Preferably it is 1.3% or less.
  • Nb 0.005 to 0.05%
  • Nb is the most important element in the present invention together with Cr. This is because, like Cr, precipitation strengthening by Nb precipitates (carbonitrides) is used to ensure high temperature strength. For this reason, at least 0.005% or more is necessary. Preferably it is 0.010% or more. However, if the addition amount is too large, the toughness of the weld zone is deteriorated, so the upper limit was made 0.05%. Preferably it is 0.045% or less, Furthermore, it is good in it being 0.030% or less.
  • Nb addition raises the non-recrystallization temperature of austenite and contributes also to exhibiting the effect of the controlled rolling at the time of hot rolling to the maximum.
  • Al 0.060% or less
  • Al is an element generally contained in steel for deoxidation. Since deoxidation is also performed with Si or Ti, the amount may be determined in balance with these elements. However, when the amount of Al increases, not only the cleanliness of steel deteriorates but also the toughness of the weld metal deteriorates, so the upper limit is made 0.060%. Preferably it is 0.040% or less. The smaller the amount, the better.
  • N 0.001 to 0.006% N is contained in the steel as an unavoidable impurity, but combines with Nb to form carbonitride to increase the strength, and TiN to increase the properties of the steel as described above. .
  • the N amount is required to be at least 0.001%. Preferably it is 0.0015% or more.
  • an increase in the amount of N is detrimental to the weld heat affected zone toughness and weldability, and the upper limit of the steel of the present invention is 0.006%. More preferably, it is 0.0045% or less.
  • V 0.01 to 0.10%
  • the lower limit was set to 0.01% as the minimum amount that can surely enjoy the effect of V addition. Preferably, it is 0.025% or more.
  • the upper limit is set to 0.10% in consideration the influence on the weld crack susceptibility composition P CM which will be described later. Preferably, it is 0.08% or less, further 0.05% or less.
  • Ti 0.005 to 0.025%
  • Ti is preferably added to improve the toughness of the base material and the weld heat affected zone. This is because when Ti has a small amount of Al (for example, 0.003% or less), it combines with O to form precipitates mainly composed of Ti2O3, which becomes the nucleus of intragranular transformation ferrite formation and has a weld heat affected zone toughness. Improve. Further, Ti is combined with N and finely precipitated in the steel as TiN, which suppresses the coarsening of ⁇ grains during heating and is effective for making the rolled structure finer. Further, the fine TiN present in the steel material refines the weld heat affected zone structure during welding and improves toughness. In order to obtain these effects, Ti needs to be at least 0.005%.
  • the upper limit was made 0.025%.
  • it is 0.020% or less.
  • the main purpose of adding these elements to the basic components is to improve properties such as strength and toughness without impairing the excellent characteristics of the steel of the present invention. Therefore, the amount added is of a nature that should naturally be limited.
  • Ni 0.05 to 0.50% If Ni is not added excessively, it improves the strength and toughness of the base material without adversely affecting the weldability and weld heat affected zone toughness. In order to exert these effects, addition of at least 0.05% is essential.
  • the lower limit should be the minimum amount for obtaining a substantial effect, and is 0.05%.
  • the upper limit may be limited to 0.30%.
  • Mg 0.0002 to 0.005% Mg suppresses the growth of austenite grains in the weld heat-affected zone and has the effect of making the grains finer, so that the weld zone can be strengthened. In order to enjoy such an effect, Mg needs to be 0.0002% or more.
  • the upper limit is set to 0.005% because this is not a cost effective measure. Preferably it is 0.0035% or less.
  • Ca and REM control the morphology of MnS, improve the low temperature toughness of the base material, and reduce the susceptibility to hydrogen induced cracking (HIC, SSC, SOHIC) in a wet hydrogen sulfide environment. In order to exert these effects, 0.0005% is necessary at least. However, too much addition adversely deteriorates the cleanliness of the steel, and increases the base metal toughness and susceptibility to hydrogen-induced cracking (HIC, SSC, SOHIC) in a wet hydrogen sulfide environment. REM was limited to 0.004% and 0.008%, respectively. Preferably, they are 0.003% and 0.006% or less, respectively.
  • the value of the weld crack susceptibility composition P CM which is defined by the following expression below 0.22%.
  • P CM C + Si / 30 + Mn / 20 + Cu / 20 + Ni / 60 + Cr / 20 + Mo / 15 + V / 10 + 5B PCM is an index representing weldability. The lower the CM, the better the weldability.
  • JIS G 3106 Rolled steel for welded structure
  • JIS G 3106 Rolled steel for welded structure
  • the most severe one is specified to be 0.24% or less.
  • those with limited P CM below 0.22% as a condition can prevent more severe constraints, reliably welded cold cracking even at ambient conditions is there.
  • the lower limit is not particularly limited, the lower limit is naturally limited by the limited range of each component. Subsequently, manufacturing conditions will be described.
  • the reason why the heating temperature prior to hot rolling is limited to 1000 to 1300 ° C. is to keep the austenite grains during heating small and to refine the rolled structure. 1300 ° C.
  • the austenite during heating is not extremely coarsened.
  • the heating temperature is exceeded, the austenite grains are coarsely mixed and the structure after transformation is also coarsened, so that the toughness of the steel is remarkably deteriorated.
  • the heating temperature is too low, depending on the plate thickness, it is difficult not only to secure the rolling end temperature, which will be described later, but also to increase the non-recrystallization temperature of austenite and to cause the solution of Nb to develop precipitation strengthening.
  • the lower limit was set to 1000 ° C.
  • the most preferable heating temperature range is 1050 to 1250 ° C.
  • the steel material heated on the above conditions is cooled after 800 degreeC or more complete
  • the cooling means is not particularly limited. Although it may be cooled by leaving it in the atmosphere, the properties of the steel material can be further improved by performing accelerated cooling from a temperature of 750 ° C. or higher to a temperature of 550 ° C. or lower.
  • the rolling end temperature is lower than 800 ° C., in the steel of the present invention having a relatively small amount of C, ferrite is likely to undergo transformation transformation and the ferrite may be processed (rolled), which is not preferable in terms of ensuring low temperature toughness.
  • the rolling end temperature is limited to 800 ° C. or higher. Preferably it is 820 degreeC or more. After hot rolling at 800 ° C.
  • 40 kg class steel for example, JIS standard SM400, SN400 steel
  • 50kg steel for example, JIS standard SM490, SN490 steel
  • 40kg steel if the plate thickness is too thick, it will be difficult to ensure stable strength when left in the atmosphere.
  • the accelerated cooling after rolling is intended to enhance the properties of the steel material, and does not impair the excellent features of the present invention. In the first place, accelerated cooling is intended to refine the structure by increasing the cooling speed in the transformation region and simultaneously improve strength and toughness.
  • the accelerated cooling start temperature is limited to 750 ° C. or higher.
  • This accelerated cooling requires cooling to a temperature of 550 ° C. or lower in order to enjoy the effect. This is because when the temperature exceeds 550 ° C., the transformation during accelerated cooling does not proceed sufficiently, and the structure is not sufficiently refined.
  • the preferred accelerated cooling start temperature is 760 ° C. or higher, and the preferred accelerated cooling stop temperature range is 520 or lower and 300 ° C. or higher.
  • the cooling rate during accelerated cooling depends on the steel composition, the intended strength, and the low temperature toughness level, but from the accelerated cooling start temperature to 550 ° C.
  • the average cooling rate is desirably 3 ° C./second or more. Moreover, even if the tempering process below Ac1 temperature is added with respect to the rolled material after cooling, the outstanding characteristic of this invention is not impaired. It is rather preferable in order to cancel the non-uniformity of cooling and increase the in-plate uniformity of the material.
  • the comparative steel 12 is not added with Nb, and the comparative steel 13 has a low Cr content, the high temperature strength is low. Since the comparative steel 14 has a low C content, the high temperature strength is low. Since the comparative steel 15 has a high Cr content, both the base material and the reproduced HAZ are inferior in toughness. Since comparative steel 16 has high Nb, it is inferior in HAZ toughness.
  • the components of the comparative steels 17-1 to 17-3 are the same as those of the present invention steel 5. However, the comparative steel 17-1 has a low rolling end temperature, and as a result, the accelerated cooling start temperature cannot be ensured and has become low, so both the room temperature and the high temperature strength are low.
  • comparative cooling steel 17-2 has a low accelerated cooling start temperature, both the room temperature and the high temperature strength are low. Since comparative steel 17-3 has a high accelerated cooling stop temperature, both normal temperature and high temperature strength are low. Comparative Steel 18, the individual elements and production methods are within the present invention range, normal temperature, although such temperature strength and toughness satisfies the required properties as 490MPa class, because of the high P CM, weldability (oblique Cracks occurred in the y-type weld crack test).
  • the present invention has made it possible to provide a large amount and a low cost of welded structural steel having excellent high temperature strength and low temperature toughness. As a result, it has become possible to reduce or omit the fireproof coating for building structures. In addition to the basic properties such as strength and toughness in applications other than construction, it also has high-temperature strength. Can be further improved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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 pour construction soudée qui a une excellente résistance à température élevée et une excellente résilience aux basses températures et qui peut être produit à faible coût. L'acier pour construction soudée est produit par l'étape consistant à chauffer un produit d'acier comportant C : 0,003 à 0,05 %, Si : pas plus de 0,60 %, Mn : 0,6 à 2,0 %, P : pas plus de 0,020 %, S : pas plus de 0,010 %, Cr : 0,20 à 1,5 %, Nb : 0,005 à 0,05 %, Al : pas plus de 0,060 %, N : 0,001 à 0,006 %, et Mo comme impureté limitée à pas plus de 0,03 %, le reste comprenant du fer et des impuretés inévitables, le produit d'acier ayant une valeur de composition de sensibilisation au criquage de la soudure (PCM), que définit PCM = C + Si/30 + Mn/20 + Cu/20 + Ni/60 + Cr/20 + Mo/15 + V/10 + 5B, de pas plus de 0,22 %, à une température de 1000 à 1300°C, l'étape consistant à terminer le laminage à chaud à une température de 800°C ou plus, et puis l'étape consistant à refroidir le produit d'acier.
PCT/JP2009/050906 2009-01-15 2009-01-15 Acier pour construction soudée ayant une excellente résistance à température élevée et une excellente résilience aux basses températures et procédés de production de l'acier WO2010082361A1 (fr)

Priority Applications (7)

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PCT/JP2009/050906 WO2010082361A1 (fr) 2009-01-15 2009-01-15 Acier pour construction soudée ayant une excellente résistance à température élevée et une excellente résilience aux basses températures et procédés de production de l'acier
KR1020097012504A KR101189263B1 (ko) 2009-01-15 2009-01-15 고온 강도와 저온 인성이 우수한 용접 구조용 강 및 그 제조 방법
BRPI0901011A BRPI0901011B1 (pt) 2009-01-15 2009-01-15 aço para estruturas soldadas e método de produção do mesmo
US12/449,512 US20110262298A1 (en) 2009-01-15 2009-01-15 Steel for welded structures excellent in high temperature strength and low temperature toughness and method of production of same
EP09707108.8A EP2380997B1 (fr) 2009-01-15 2009-01-15 Acier pour construction soudée ayant une excellente résistance à température élevée et une excellente résilience aux basses températures et procédés de production de l'acier
CN2009800000583A CN101849026B (zh) 2009-01-15 2009-01-15 高温强度和低温韧性优异的焊接结构用钢及其制造方法
JP2009509204A JP4834149B2 (ja) 2009-01-15 2009-01-15 高温強度と低温靭性に優れる溶接構造用鋼とその製造方法

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PCT/JP2009/050906 WO2010082361A1 (fr) 2009-01-15 2009-01-15 Acier pour construction soudée ayant une excellente résistance à température élevée et une excellente résilience aux basses températures et procédés de production de l'acier

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CN (1) CN101849026B (fr)
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WO2016068094A1 (fr) * 2014-10-28 2016-05-06 Ｊｆｅスチール株式会社 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
JP7547628B2 (ja) 2020-09-29 2024-09-09 南京鋼鉄股▲ふん▼有限公司 低コスト高性能ｑ５００橋梁用鋼板および生産方法

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CN102373387B (zh) * 2011-11-02 2013-05-22 武汉钢铁(集团)公司 大应变冷弯管用钢板及其制造方法
CN103114186B (zh) * 2013-03-15 2015-04-08 济钢集团有限公司 一种易焊接高性能钢板的控制冷却方法
JP2017128795A (ja) * 2016-01-18 2017-07-27 株式会社神戸製鋼所 鍛造用鋼及び大型鍛鋼品
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CN113667897A (zh) * 2021-08-31 2021-11-19 重庆钢铁股份有限公司 一种低温韧性钢及其P、As匹配工艺
CN115287530A (zh) * 2022-06-22 2022-11-04 河钢股份有限公司 高焊接性能700MPa级稀土高强结构钢及其生产方法

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CN102400049B (zh) * 2010-09-07 2014-03-12 鞍钢股份有限公司 一种490级别建筑结构用耐火钢板及其制造方法
WO2016068094A1 (fr) * 2014-10-28 2016-05-06 Ｊｆｅスチール株式会社 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
JPWO2016068094A1 (ja) * 2014-10-28 2017-04-27 Ｊｆｅスチール株式会社 溶接熱影響部の低温靭性に優れる高張力鋼板とその製造方法
JP7547628B2 (ja) 2020-09-29 2024-09-09 南京鋼鉄股▲ふん▼有限公司 低コスト高性能ｑ５００橋梁用鋼板および生産方法

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EP2380997A1 (fr) 2011-10-26
CN101849026B (zh) 2012-07-04
KR20100105821A (ko) 2010-09-30
BRPI0901011B1 (pt) 2019-09-10
BRPI0901011A2 (pt) 2015-11-24
CN101849026A (zh) 2010-09-29
JP4834149B2 (ja) 2011-12-14
KR101189263B1 (ko) 2012-10-09
EP2380997A4 (fr) 2016-12-28
JPWO2010082361A1 (ja) 2012-06-28
EP2380997B1 (fr) 2020-01-08
US20110262298A1 (en) 2011-10-27

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