WO2013088715A1 - Matériau d'acier pour soudage à apport de chaleur élevé - Google Patents

Matériau d'acier pour soudage à apport de chaleur élevé Download PDF

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WO2013088715A1
WO2013088715A1 PCT/JP2012/007953 JP2012007953W WO2013088715A1 WO 2013088715 A1 WO2013088715 A1 WO 2013088715A1 JP 2012007953 W JP2012007953 W JP 2012007953W WO 2013088715 A1 WO2013088715 A1 WO 2013088715A1
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Prior art keywords
haz
welding
steel material
heat input
toughness
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PCT/JP2012/007953
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English (en)
Japanese (ja)
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横田　智之
長谷　和邦
三田尾　眞司
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Ｊｆｅスチール株式会社
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Priority to CN201280061292.9A priority Critical patent/CN103987869B/zh
Priority to BR112014014401-0A priority patent/BR112014014401B1/pt
Priority to KR1020147015959A priority patent/KR101608239B1/ko
Priority to JP2013549120A priority patent/JP5796636B2/ja
Publication of WO2013088715A1 publication Critical patent/WO2013088715A1/fr

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    • 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
    • C22C38/001—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
    • C22C38/04—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present invention is used for various steel structures in the fields of ships, construction, civil engineering, etc., and has a yield stress of 460 MPa or more, particularly a large amount of welding heat input exceeding 300 kJ / cm. It relates to steel materials suitable for high heat input welding.
  • steel structures used in the fields of ships, offshore structures, architecture, steel pipes, etc. are finished into structures having a desired shape by welding. Therefore, from the viewpoint of ensuring safety, these structures have a welded part in addition to ensuring the properties of the steel materials used (mechanical properties-of base), that is, strength and toughness.
  • the toughness of the steel is also required to be excellent.
  • the above ships and steel structures have become increasingly large (becoming large-sized), and steel materials used have been actively promoted to increase (increase strength) and thicken (increase wall thickness). ing.
  • the welding process involves high-efficiency and high heat input welding such as submerged arc welding, electrogas welding, electroslag welding, and electroslag welding.
  • high heat input welding such as submerged arc welding, electrogas welding, electroslag welding, and electroslag welding.
  • a steel material having excellent toughness of the welded portion is required.
  • FIG. 1 is a macrostructure photograph of a cross section of a high heat input weld.
  • both the welded metal produced from the melted parent metal and welding material are mixed almost uniformly in the molten state and solidified. The part exists.
  • On both sides there is a heat affected zone (HAZ) in which the structure and properties of the base material are affected by heat input during welding and the properties and properties of the base material are altered. Furthermore, the state which the base material exists in the both sides is shown.
  • the boundary between the weld metal and the HAZ (broken line in the figure) is generally referred to as a “bond”.
  • the HAZ in the vicinity of the bond part is heated to a high temperature in the vicinity of the melting point, particularly in the heat affected zone, so that the crystal grains become coarse and the toughness is remarkably reduced.
  • the bond portion at a distance from the bond portion, it becomes a fine-grained region and softens, which is a main cause of reduced joint strength.
  • TiN is finely dispersed in steel to suppress the coarsening of austenite grains and to be used as a ferrite transformation nucleus. Yes.
  • a technique aiming at the same effect as described above has been developed by dispersing Ti oxide.
  • Patent Document 1 discloses a technique for controlling the shape of sulfide (sulfide shape control) in order to improve the toughness of the heat affected zone welded with a high heat input exceeding 300 kJ / cm.
  • a technique for optimizing the amount of Ca added to crystallization to crystallize CaS and effectively use it as a ferrite transformation nucleus is disclosed. Since this CaS crystallizes at a lower temperature than the oxide, it can be finely dispersed in the steel.
  • this CaS is used as a nucleus to form ferrite transformation nuclei such as MnS, TiN and BN ( Since ferrite-nucleation-site) is finely dispersed, the structure of the weld heat-affected zone can be made a fine ferrite pearlite structure (ferrite-and-pearlite-structure) to achieve high toughness.
  • Patent Document 1 it has become possible to suppress toughness degradation to some extent due to high heat input welding.
  • Patent Document 2 discloses that in addition to reducing the contents of C and Si, reducing the content of P is effective. Furthermore, in Patent Document 3, by adding Mn actively and reducing P as much as possible, the martensite in the vicinity of the bond portion HAZ can be reduced, and a steel material having a yield stress of 460 MPa grade with excellent toughness can be obtained. It is said.
  • Patent Document 1 is a technique for improving the HAZ toughness of the bond part particularly when a high heat input welding is performed on a steel material having a yield stress of 390 MPa grade. It cannot fully cope with the high heat input HAZ toughness and HAZ softening of the steel material having a yield stress of 460 MPa grade.
  • the technique described in Patent Document 2 targets steel materials with a yield stress of 460 MPa grade, reduces island martensite in the vicinity of the bond part HAZ by reducing the content of C, Si, P, and Ca The HAZ toughness is ensured by adding an appropriate amount and finely dispersing the ferrite transformation nuclei.
  • Patent Document 4 has a high amount of C, and uses a precipitation strengthening element such as Nb or V to take sufficient measures against softening of the HAZ.
  • a precipitation strengthening element such as Nb or V
  • the techniques described in Patent Documents 5 and 6 are techniques for suppressing HAZ softening by using the hardenability of B.
  • Patent Document 5 is premised on the addition of a large amount of Ti, B, and N, and there is a problem in manufacturability, and there is a concern that toughness may be lowered due to solute N in a region where TiN dissolves in the vicinity of the bond portion.
  • Patent Document 6 is premised on Nb-free, and when a steel material with a yield stress of 460 MPa grade is targeted, it is difficult to ensure joint strength.
  • an object of the present invention is to provide a high heat input welding having a yield stress of 460 MPa or more, which is excellent in strength (softening resistance) and toughness of the weld heat-affected zone even when a high heat input welding with a heat input exceeding 300 kJ / cm is applied.
  • the purpose is to provide steel for construction at low cost.
  • the present inventors have an effect on the HAZ toughness near the bond portion and the hardness of the HAZ softened portion when high heat input welding with a heat input exceeding 300 kJ / cm is applied to a high strength steel material having a yield stress of 460 MPa or more.
  • the effect of tissue factor was investigated. As a result, it was found that the abundance of island martensite or martensite has a great influence on each property. That is, regarding the HAZ toughness in the vicinity of the bond part, a small amount of island-like martensite has an adverse effect on the toughness, and conversely, regarding the hardness of the HAZ softened part, the higher the martensite fraction generated there, the higher the hardness. It has been found that the joint strength increases as the height increases. Therefore, the inventors have further studied the relationship between the alloy elements and the abundance of the martensite in the HAZ in the vicinity of the bond portion and the martensite in the HAZ most softened portion.
  • the base metal strength can be effectively increased without generating island martensite that adversely affects the HAZ toughness in the vicinity of the bond part, while the HAZ softened part is effective. It was found that the abundance of martensite was less and the joint strength was disadvantageous. However, on the premise of the active addition of Mn, the island-like martensite generated in the HAZ near the bond part is minimized by appropriately controlling the content of P as an impurity element to 0.012% to 0.03%. The present inventors completed the present invention by finding that the hardness can be effectively improved by increasing the martensite in the HAZ softest part while reducing the amount.
  • the present invention is a high heat input welding characterized in that the martensite in the HAZ softest part structure is 3 to 12% by volume when a high heat input welding with a welding heat input exceeding 300 kJ / cm is performed. Steel material.
  • Steel materials for high heat input welding of the present invention are: C: 0.030 to 0.080%, Si: 0.01 to 0.15%, Mn: 1.80 to 2.60%, P: 0.012 to 0.030%, S: 0.0005 to 0.0040%, Al: 0.005 to 0.100%, Nb: 0.003 to 0.030%, Ti: 0.003 to 0.030%, N : 0.0025 to 0.0070%, B: 0.0003 to 0.0025%, and carbon equivalent C eq represented by the following formula (1) is 0.330 to 0.450 Martens in the heat-affected zone most softened part structure when large heat input welding having a component composition consisting of Fe and inevitable impurities and having a heat input exceeding 300 kJ / cm is included.
  • the steel material for high heat input welding of the present invention is characterized by further containing V: 0.20% or less in addition to the above component composition.
  • the steel material for high heat input welding of the present invention further includes Cu: 1.00% or less, Ni: 1.00% or less, Cr: 0.40% or less, and Mo: 0.4. % Or less selected from 1% or less.
  • the steel material for high heat input welding of the present invention further includes Ca: 0.0005 to 0.0050%, Mg: 0.0005 to 0.0050%, Zr: 0.0010 to 0 One or more selected from 0.0200% and REM: 0.0010 to 0.0200%.
  • the steel material of the present invention is suitably used for ships and large steel structures constructed by high heat input welding such as submerged arc welding, electrogas welding, and electroslag welding.
  • the steel material which is the object of the present invention is a steel material having a plate thickness of 40 mm or more manufactured by hot rolling.
  • the structure of the HAZ softest part, which is a feature of the steel material of the present invention, will be described.
  • the present invention controls the amount of martensite generated in the heat-affected zone (HAZ) of the high heat input weld zone, especially the softest zone where the austenite becomes finer and hardenability decreases due to the austenite. This is a technique for suppressing softening. In order to obtain such an effect, the martensite fraction in the most softened portion of the HAZ needs to be 3% by volume or more.
  • the case where the welding heat input amount exceeds 300 kJ / cm is defined as the large heat input welding.
  • the present invention defines the strength of the weld heat affected zone even if the large heat input welding is performed. It is because it aims at providing the steel material which is excellent in toughness cheaply.
  • the higher the martensite fraction at the position the better.
  • further addition of alloying elements is essential. This results in the generation of island martensite in the vicinity of the bond portion, resulting in a reduction in HAZ toughness in the vicinity of the bond portion.
  • the martensite fraction in the HAZ softest part is 12% by volume or less, such a decrease in toughness in the bond part can be minimized.
  • the abundance of martensite in the HAZ softest part is 3 to 12% by volume. Preferably, it is in the range of 3 to 10%.
  • the HAZ most softened portion refers to a heat-affected zone that becomes an austenite fine grain region separated by about 10 mm from the bond portion as shown in FIG.
  • the HAZ softest part is identified by measuring the Hv Vickers hardness at intervals of 0.5 mm and setting the area showing the minimum hardness as the HAZ softest part.
  • the martensite in the HAZ softest part can be confirmed by polishing the cross section of the weld, etching, and observing with an optical microscope or SEM (scanningscanelectron microscope).
  • the structure of the HAZ softest part is a structure mainly composed of ferrite and containing pearlite, bainite, and the like other than the martensite.
  • C 0.030 to 0.080% C is an element that increases the strength of the steel material, and in order to ensure the strength necessary for structural steel, it is necessary to contain 0.030% or more. On the other hand, if C exceeds 0.080%, island-like martensite is easily generated in the HAZ near the bond portion, so the upper limit is made 0.080%. Preferably, it is 0.035 to 0.070% of range.
  • Si 0.01 to 0.15%
  • Si is an element added as a deoxidizing agent when melting steel, and it is necessary to add 0.01% or more. However, if it exceeds 0.15%, the toughness of the base material is lowered, and island martensite is generated in the vicinity of the bond portion HAZ subjected to high heat input welding, which tends to cause a reduction in toughness. Therefore, Si is set in the range of 0.01 to 0.15%. Preferably, it is 0.03 to 0.12% of range.
  • Mn 1.80 to 2.60%
  • Mn has a tendency to decompose and render harmless by decomposing untransformed austenite generated in the vicinity of the bond part during cooling during high heat input welding into cementite. It is an important element in the invention. In order to secure the required strength and obtain the above-mentioned effects, addition of 1.80% or more is necessary. However, if it exceeds 2.60%, HAZ toughness is conversely reduced. Therefore, Mn is set to 1.80 to 2.60%. Preferably, it is in the range of 1.90 to 2.30%, more preferably in the range of 1.82 to 2.50%.
  • P 0.012 to 0.030%
  • P is contained in an amount of 0.012% or more in order to promote the formation of martensite in the HAZ softest part.
  • the addition of P is limited to 0.030% or less in order to make it difficult to decompose untransformed austenite into cementite in the vicinity of the bond portion and to lower its toughness due to the formation of island martensite.
  • it is 0.022% or less, more preferably 0.020% or less.
  • S is an element necessary for producing MnS or CaS that forms a nucleation site of ferrite. In order to obtain such an effect, it is necessary to contain 0.0005% or more. However, if it exceeds 0.0040%, the toughness of the base material is lowered. Therefore, S is set in the range of 0.0005 to 0.0040%. Preferably, it is in the range of 0.0007 to 0.0035%.
  • Al 0.005 to 0.100%
  • Al is an element added for deoxidation of steel, and it is necessary to contain 0.005% or more. However, if the content exceeds 0.100%, not only the toughness of the base metal but also the toughness of the weld metal is lowered. Therefore, Al is in the range of 0.005 to 0.100%. The range is preferably 0.008 to 0.100%, more preferably 0.010 to 0.100%, and still more preferably 0.010 to 0.060%.
  • Nb 0.003 to 0.030%
  • Nb is an element effective for ensuring the strength of the base material and the hardness of the HAZ softened portion, and consequently the weld joint strength.
  • the content is less than 0.003%, the above effect is small.
  • the content exceeds 0.030%, island martensite is generated in the vicinity of the bond portion HAZ and the toughness is lowered. Therefore, Nb is set in the range of 0.003 to 0.030%. Preferably, it is in the range of 0.005 to 0.027%.
  • Ti 0.003-0.030% Ti precipitates as TiN during solidification, suppresses the coarsening of the austenite grains in the vicinity of the bond portion HAZ, and becomes a transformation nucleus of ferrite and contributes to the increase in toughness. In order to obtain such an effect, addition of 0.003% or more is necessary. On the other hand, if the content exceeds 0.030%, the precipitated TiN becomes coarse and the above effect cannot be obtained. Therefore, Ti is in the range of 0.003 to 0.030%. Preferably, it is 0.006 to 0.025% of range.
  • N 0.0025 to 0.0070%
  • N is an element necessary for the generation of TiN described above, and in order to secure the necessary amount of TiN, it is necessary to contain 0.0025% or more. However, if the content exceeds 0.0070%, the effect of hardenability by the solid solution B is hindered, and the strength of the base material and the hardness of the HAZ most softened portion are lowered. Therefore, N is set in the range of 0.0025 to 0.0070%. Preferably, it is in the range of 0.0030 to 0.0065%.
  • B has the effect of increasing the hardness of the softest portion by exhibiting hardenability in the fine grain region of the weld heat affected zone, that is, the HAZ softening portion.
  • BN is generated in the HAZ near the bond part to reduce the solute N (solute N) and act as a ferrite transformation nucleus, so that it is an element useful for increasing the toughness of the HAZ near the bond part.
  • B is in the range of 0.0003 to 0.0025%.
  • it is in the range of 0.0006 to 0.0020%.
  • Carbon equivalent C eq 0.330 to 0.450
  • the carbon equivalent C eq represented by the following formula (1) is in the range of 0.330 to 0.450.
  • C eq C + Mn / 6 + (Cr + Mo + V) / 5 + (Cu + Ni) / 15 (1)
  • the element symbol in the above formula indicates the content (%) of each element, and the element not contained is 0.
  • the carbon equivalent C eq represented by the formula (1) needs to be in the range of 0.330 to 0.450.
  • the carbon equivalent C eq is less than 0.330, the necessary base material strength cannot be obtained.
  • the carbon equivalent C eq exceeds 0.450, the toughness of the heat affected zone in the vicinity of the bond portion decreases due to high heat input welding.
  • C eq is in the range of 0.370 to 0.420.
  • the steel material of the present invention can contain V as a selective element in the following range in addition to the above essential components.
  • V 0.20% or less
  • V precipitates as VN, contributes to the improvement of the strength and toughness of the base material, and also acts as a ferrite nuclei. Therefore, V can be contained as necessary.
  • addition of 0.04% or more is preferable.
  • the upper limit is preferably 0.20%. More preferably, it is 0.06 to 0.18% of range.
  • the steel material of the present invention can further contain one or more selected from Cu, Ni, Cr and Mo as selective elements in the following range for the purpose of improving the strength.
  • Cu 1.00% or less
  • Mo 0.4% or less
  • Cu, Ni, Cr and Mo are effective elements for increasing the strength of the base material.
  • Mo 0.05 to 0.35% is there.
  • the steel material of the present invention can further contain at least one selected from Ca, Mg, Zr and REM as a selective element in the following range.
  • Ca 0.0005 to 0.0050%
  • Ca can be contained in order to obtain an effect of improving toughness by fixing S and dispersing oxides and sulfides. In order to acquire the said effect, it is preferable to contain at least 0.0005%. However, even if added over 0.0050%, the above effect is only saturated. Therefore, when it contains Ca, it is preferable to set it as 0.0005 to 0.0050% of range. More preferably, it is in the range of 0.0008 to 0.0045%.
  • Mg, Zr, and REM are all elements having an effect of improving toughness due to oxide dispersion.
  • it is necessary to contain 0.0005% or more of Mg and 0.0010% or more of Zr and REM.
  • Mg exceeds 0.0050% and Zr and REM exceed 0.020%, the effect is only saturated. Therefore, when it contains these elements, it is preferable to set it as the said range. More preferably, the ranges are Mg: 0.0005 to 0.0045%, Zr: 0.0050 to 0.018%, and REM: 0.0050 to 0.018%.
  • the balance other than the above components in the steel material of the present invention is Fe and inevitable impurities.
  • the content of other elements is not rejected as long as the effects of the present invention are not impaired.
  • O 0.0050% or less is acceptable.
  • the steel material of the present invention can be produced by a conventionally known method, and the production conditions are not particularly limited. For example, after the hot metal is made into molten steel with a converter or the like, the steel components are adjusted to the above appropriate range by RH degassing or the like, and then the steel piece is made through a continuous casting or ingot-bundling process. Next, the steel slab is reheated and hot-rolled to obtain a steel material having a desired size and then allowed to cool, or after the hot-rolling, accelerated cooling, direct quenching-tempering, reheating quenching-tempering It can be manufactured through a process such as reheating and normalizing-tempering.
  • the 30 mm thick steel plate was subjected to tempering treatment at 500 ° C. for 10 minutes. Thereafter, a round bar tensile test piece having a parallel portion of 14 mm ⁇ ⁇ 85 mm and a distance between gauge points (gauge length) of 70 mm was collected from the thick steel plate so that the longitudinal direction of the test piece coincided with the plate width direction, and the base metal strength ( Yield stress YS, tensile strength TS) were measured.
  • the hardness of the heat-affected zone most softened part greatly affects the welded joint strength. The higher the softened part hardness, the higher the welded joint strength.
  • a small test piece of 3 mm ⁇ ⁇ 10 mm was taken from the thick steel plate, heated to 800 to 1300 ° C., and then subjected to heat treatment to cool 800 to 500 ° C. in 390 sec. .
  • the Vickers hardness HV10 kgf of a small test piece heated and cooled to each temperature of 800 to 1300 ° C. was measured, and the lowest hardness was determined as the softest part hardness.
  • a test piece having a width of 80 mm, a length of 80 mm and a thickness of 15 mm is taken from the thick steel plate, heated to 1450 ° C., and then cooled to 800 to 500 ° C. in 390 sec. Was granted. Thereafter, a 2 mm V notch Charpy specimen was collected and subjected to an appropriate Charpy impact test in the range of ⁇ 100 to 40 ° C. and a ductile fracture ratio of 50%. Fracture transition temperature vTrs was determined and toughness was evaluated.
  • the heat treatment condition corresponds to a heat cycle of a heat-affected zone subjected to electrogas welding with a heat input of 500 kJ / cm.
  • a sample heated to 900 ° C. corresponding to the fine grain region immediately above the transformation point is used among samples heated to 800 to 1300 ° C., and the cross section of the specimen is etched with nital. And revealed the organization.
  • SEM SEM, we photographed tissue images of three fields of view at 1000 times, and image-analyzed them to determine the average area fraction of martensite, which was determined as the martensite volume fraction of the HAZ softest part. did.
  • Table 2 shows the tensile properties (YS, TS) of the base material (thick steel plate) evaluated by the above procedure, the hardness and martensite volume fraction of the HAZ softened part, and the HAZ toughness in the vicinity of the bond part. It was. From Table 2, No. of invention example. Each of the steel sheets 1 to 11 has a martensite fraction of 3 to 11% by volume, the softest part hardness is as high as HV155 or more, and the HAZ toughness near the bond part: all vTrs is -40 ° C. or less, which is excellent. Toughness is obtained.
  • any component is out of the component range of the present invention, and either the HAZ softened portion hardness or the bond portion vicinity HAZ toughness is low.
  • the steel material of the present invention is suitable for use in ships and large steel structures constructed by high heat input welding such as submerged arc welding, electrogas welding, and electroslag welding.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Metallurgy (AREA)
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Abstract

La présente invention concerne un matériau en acier économique pour soudage à apport de chaleur élevé ayant une limite d'élasticité de 460 MPa ou plus présentant d'excellentes résistance (résistance au ramollissement) et ténacité d'une section de soudure affectée par chauffage soumise à soudage à apport de chaleur élevé avec un apport de chaleur de soudage supérieur à 300 kJ/cm. Le matériau d'acier pour soudage à apport de chaleur élevé est caractérisé en ce que le matériau d'acier a une composition de composants comprenant, en % en masse : une quantité fixe de C, Si, Mn, P, et S ; de 0,005 à 0,100 % de Al ; de 0,003 à 0,030 % de Nb ; de 0,003 à 0,030 % de Ti ; de 0,0025 à 0,0070 % de N ; et de 0,0003 à 0,0025 % de B ; la teneur étant telle que l'équivalent en carbone (Ceq) représenté par la formule (1) soit de 0,330 à 0,450 ; le reste comprenant Fe et des impuretés inévitables ; et de 3 à 12 % en volume étant la teneur de martensite dans la structure de la section de ramollissement maximal d'une section affectée par chauffage lorsqu'un soudage à apport de chaleur élevé ayant une chaleur de soudage supérieure à 300 kJ/cm est effectué.
PCT/JP2012/007953 2011-12-14 2012-12-12 Matériau d'acier pour soudage à apport de chaleur élevé WO2013088715A1 (fr)

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Application Number Priority Date Filing Date Title
CN201280061292.9A CN103987869B (zh) 2011-12-14 2012-12-12 大热输入焊接用钢材
BR112014014401-0A BR112014014401B1 (pt) 2011-12-14 2012-12-12 Material de aço para soldagem com alta entrada de calor
KR1020147015959A KR101608239B1 (ko) 2011-12-14 2012-12-12 대입열 용접용 강재
JP2013549120A JP5796636B2 (ja) 2011-12-14 2012-12-12 大入熱溶接用鋼材

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JP2011-273288 2011-12-14

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