WO2010134353A1 - 溶接用鋼材およびその製造方法 - Google Patents
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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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
- B23K35/3066—Fe as the principal constituent with Ni as next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
- B23K35/3073—Fe as the principal constituent with Mn as next major constituent
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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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
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- 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
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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
- 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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
Definitions
- the present invention relates to a welding steel material excellent in CTOD characteristics of a weld heat affected zone (HAZ) in welding from small heat input to medium heat input, and a method for producing the same.
- the present invention relates to a steel material for welding with excellent CTOD characteristics of the FL part and the IC part where the toughness is most deteriorated in welding from small heat input to medium heat input, and a manufacturing method thereof.
- the present application includes Japanese Patent Application No. 2009-124614 filed in Japan on May 22, 2009, Japanese Patent Application No. 2009-123428 filed in Japan on May 21, 2009, and August 21, 2009. The priority is claimed on the basis of Japanese Patent Application No. 2009-192387 filed in Japan, the contents of which are incorporated herein by reference.
- the CTOD characteristics of the weld heat affected zone are as follows: FL part [Fusion Line: boundary between WM (welded metal) and HAZ (weld heat affected zone)] and IC part [Intercritical HAZ: HAZ and BM (base material)]
- FL part Fusion Line: boundary between WM (welded metal) and HAZ (weld heat affected zone)
- IC part Intercritical HAZ: HAZ and BM (base material)
- the test results at two positions (notch portions) of [Boundary of] are evaluated. However, so far, only the FL portion, which has been considered to have the lowest CTOD characteristics, has been evaluated.
- the CTOD characteristic of the FL part is sufficient, the CTOD characteristic of the IC part is also sufficient, so it was not necessary to evaluate the CTOD characteristic of the IC part.
- a relatively large amount of O is contained.
- an element that stabilizes austenite and enhances hardenability is added in a certain amount or more.
- the IC part of the steel material in a harsh environment of about ⁇ 60 ° C. while ensuring the properties required for the structural material for welding (for example, the strength and toughness of the base material and the CTOD value of the FL part). It is difficult to secure the CTOD value of.
- the present invention provides a CTOD characteristic of the FL part at ⁇ 60 ° C. in welding (for example, multi-layer welding) from small heat input to medium heat input (for example, 1.5 to 6.0 kJ / mm at a plate thickness of 50 mm).
- the present invention provides a high-strength steel material having excellent CTOD (fracture toughness) characteristics in which the CTOD characteristics of the IC portion are sufficient and a method for producing the same.
- the present inventors diligently studied a method for improving the CTOD characteristics of both the FL portion and the IC portion of the welded portion where the toughness is most deteriorated by welding from small heat input to medium heat input.
- the present inventors are most important in reducing non-metallic inclusions, and in particular, reducing O (oxygen in steel). I found it essential. Further, the present inventors have found that since intragranular ferrite (IGF) is reduced by reducing O, it is necessary to reduce alloy elements that deteriorate the CTOD characteristics of the FL portion. Furthermore, the present inventors have found that in order to improve the CTOD characteristics of the IC part, it is effective to reduce the hardness in addition to the reduction of oxygen in the steel. Based on the above findings, the present inventors have completed the present invention.
- IGF intragranular ferrite
- the gist of the present invention is as follows.
- the welding steel material according to one embodiment of the present invention has a mass%, a C content [C] of 0.010% to 0.065%, and a Si content [Si] of 0. 0.05% or more and 0.20% or less of Si, Mn content [Mn] of 1.52% or more and 2.70% or less of Mn, and Ni content [Ni] of 0.10% or more and 1.
- a method for producing a welding steel according to one aspect of the present invention comprises producing the welding steel according to (1) or (2) above by continuous casting and heating to a temperature of 950 to 1100 ° C. Heat treatment.
- a steel material excellent in HAZ toughness in welding from small heat input to medium heat input can be provided.
- a steel material excellent in CTOD characteristics (low temperature toughness) of the FL part and the IC part where the toughness is most deteriorated by welding such as multi-layer welding from low heat input to medium heat input can be provided. Therefore, it is possible to provide a steel material having high strength and high toughness for structures used in severe environments such as offshore structures and earthquake resistant buildings.
- the CTOD of the FL part and the IC part at ⁇ 60 ° C. in welding from low heat input to medium heat input (for example, 1.5 to 6.0 kJ / mm at a plate thickness of 50 mm).
- medium heat input for example, 1.5 to 6.0 kJ / mm at a plate thickness of 50 mm.
- O oxygen in steel
- an oxide-based nonmetallic inclusion represented by Ti oxide is used as a transformation nucleus of intragranular ferrite (IGF). It was necessary to add some amount of O. According to the research of the present inventor, in order to improve the CTOD characteristics of the FL part and the IC part at ⁇ 60 ° C., it is necessary to reduce oxide-based nonmetallic inclusions.
- FIG. 1 shows the relationship between the CTOD characteristics (T ⁇ c0.1 (FL) ) of the FL equivalent reproduction HAZ and the steel component parameter P CTOD .
- the steel component parameter P CTOD represented by the formula (1) is used to test a number of molten steels in a laboratory and analyze the CTOD characteristics (T ⁇ c0.1 (FL) ) of the HA equivalent reproduction HAZ and the steel components. This is an empirical formula derived as follows.
- the CTOD characteristic (T ⁇ c0.1 (FL) ) of ⁇ 110 ° C. or lower is the target level (T ⁇ c0.1 ) as a structural steel material based on the knowledge obtained in many experiments. (FL) ⁇ ⁇ 110 ° C.).
- a CTOD ( ⁇ c) value of 0.25 mm or more can be secured stably at ⁇ 60 ° C. in the FL notch test of an actual joint of a steel sheet having a thickness of 50 to 100 mm. From FIG. 1, it can be seen that, in the FL equivalent reproduction HAZ, in order to make T ⁇ c0.1 (FL) ⁇ 110 ° C. or less, it is necessary to control the steel component parameter P CTOD to 0.065% or less. In addition, as the CTOD ( ⁇ c) value is larger, the toughness (for example, energy absorption due to plastic strain) is higher.
- the FL equivalent reproduction HAZ is a part corresponding to the heat input amount of the FL part of the test piece subjected to the FL equivalent reproduction thermal cycle shown below.
- This FL equivalent thermal cycle treatment (triple cycle) was performed on the test piece having a cross section of 10 mm ⁇ 20 mm under the following conditions.
- 1st cycle Maximum heating temperature 1400 ° C (between 800 and 500 ° C is cooled in 22 seconds)
- 2nd cycle Maximum heating temperature of 760 ° C (cooling between 760 and 500 ° C in 22 seconds)
- 3rd cycle Maximum heating temperature 500 ° C (cooling between 500-300 ° C in 60 seconds) As shown in FIG.
- the position of the FL notch 7 in the welded portion 2 is the FL portion 5 at the boundary between the HAZ 4 and the WM 3.
- T ⁇ c0.1 (FL) is the temperature at which the lowest value of the obtained CTOD (.delta.c) values obtained using three test pieces for each test temperature exceeds 0.1 mm (° C.).
- T ⁇ c0.1 (FL) needs to be ⁇ 110 ° C. or lower as described above.
- the present inventors have found that reducing the hardness in addition to reducing the oxygen in the steel is effective for improving the CTOD characteristics of the IC part.
- FIG. 2 shows the relationship between the CTOD characteristics of a test piece subjected to a reproduction thermal cycle equivalent to ICHAZ (Intercritical HAZ), which will be described later, and the hardness of the reproduction HAZ equivalent to ICHAZ.
- FIG. 3 shows the relationship between the steel component hardness parameter CeqH and the hardness of the reproduced HAZ equivalent to ICHAZ.
- the HAZ hardness (Vickers test with a load of 10 kgf) is It is necessary to make it Hv176 or less. Therefore, it can be seen from FIG. 3 that the steel component hardness parameter CeqH needs to be controlled to 0.235% or less. In order to further reduce the hardness, the steel component hardness parameter CeqH is preferably 0.225% or less.
- the steel component hardness parameter CeqH is an empirical formula obtained by multiple regression of the characteristics (hardness) of steel and the components.
- CeqH [C] + [Si] /4.16+ [Mn] /14.9+ [Cu] /12.9+ [Ni] /105+1.12 [Nb] + [V] /1.82 (2 ) Is defined.
- [C], [Si], [Mn], [Cu], [Ni], [Nb], and [V] are the contents of C, Si, Mn, Cu, Ni, Nb, and V in the steel. (Mass%). For example, when Cu is not contained, the Cu content is 0%.
- C 0.010 to 0.065%
- the C content [C] exceeds 0.065%, the properties of the welded HAZ deteriorate and the CTOD properties at ⁇ 60 ° C. are not sufficient. Therefore, the upper limit of the C content [C] is 0.065%. Therefore, the C content [C] is 0.015% or more and 0.065% or less.
- Si 0.05-0.20%
- the Si content [Si] the better.
- the Al content [Al] is limited as will be described later, a Si content [Si] of 0.05% or more is necessary for deoxidation.
- the Si content [Si] exceeds 0.20%, the HAZ toughness is impaired, so the upper limit of the Si content [Si] is 0.20%. Accordingly, the Si content [Si] is 0.05% or more and 0.20% or less.
- the Si content [Si] is preferably 0.15% or less or 0.13% or less.
- Mn 1.52 to 2.70%
- Mn is an inexpensive element that has a large effect of optimizing the microstructure. Moreover, there is little possibility of harming HAZ toughness by addition of Mn. From these points, it is preferable that the amount of Mn added is large. However, if the Mn content exceeds 2.70%, the hardness of ICAZ increases and the toughness deteriorates. Therefore, the upper limit of the Mn content [Mn] is 2.70%. Further, when the Mn content [Mn] is less than 1.52%, the effect of improving the microstructure is small, so the lower limit of the Mn content [Mn] is 1.52%. Therefore, the Mn content [Mn] is 1.52% or more and 2.70% or less. In order to further improve the HAZ toughness, the Mn content [Mn] is preferably 1.55% or 1.6% or more, and more preferably 1.7% or more.
- Ni 0.10 to 1.50%
- Ni is an element that does not significantly deteriorate the HAZ toughness, improves the strength and toughness of the base material, and does not increase the hardness of ICHAZ.
- Ni is an expensive alloy element, and if it is excessively contained in steel, it may cause surface defects. Therefore, the upper limit of the Ni content [Ni] is 1.50%.
- the Ni content [Ni] is 0.10% or more and 1.50% or less.
- the Ni content [Ni] is preferably 0.20% or more, and is 0.30% or more. It is more preferable. Furthermore, in order to provide weather resistance to the steel material, the Ni content [Ni] is preferably 0.40% or more, and more preferably 0.50% or more. In order to prevent surface flaws more reliably, the Ni content [Ni] is preferably 1.20% or less, and more preferably 1.0% or less. In the case where the strength and toughness of the base material can be sufficiently secured by adding other elements, the Ni content [Ni] is most preferably 0.80% or less in order to further secure the economy. As will be described later, when Cu is added as necessary, the Ni content [Ni] is 1 ⁇ 2 or more of the Cu content [Cu] in order to suppress Cu cracking of the slab. It is preferable.
- Mn Mn
- Ni Ni
- P and S are elements that reduce toughness and are contained as inevitable impurities. Therefore, it is necessary to reduce both the P content [P] and the S content [S] in order to ensure the base material toughness and the HAZ toughness.
- the upper limit of P content [P] and the upper limit of S content [S] are 0.008% and 0.005%, respectively.
- the P content [P] is preferably limited to 0.005% or less
- the S content [S] is preferably limited to 0.003% or less.
- Al 0.004% or less (excluding 0%)
- the Al content [Al] is preferably as small as possible because it is necessary to generate a Ti oxide. However, since there are restrictions on industrial production, the upper limit of the Al content [Al] is 0.004%.
- Ti 0.005 to 0.015% Ti produces Ti oxide and refines the microstructure. However, when there is too much Ti content [Ti], Ti will produce
- Nb 0.010% or less (including 0%) Nb may be contained as an impurity and improves the strength and toughness of the base material, but decreases the HAZ toughness.
- the range of Nb content [Nb] in which the HAZ toughness is not significantly lowered is 0.010% or less. Therefore, the Nb content [Nb] is limited to 0.010% or less. In order to further improve the HAZ toughness, the content is preferably limited to 0.002% or less (including 0%).
- the O content [O] is essential to be 0.0010% or more in order to secure the amount of Ti oxide generated as IGF nuclei in the FL part.
- the O content [O] is limited to a range of 0.0015% to 0.0045%.
- the O content [O] is preferably 0.0030% or less, and more preferably 0.0028% or less.
- N 0.002 to 0.006% N is necessary to produce Ti nitride.
- the N content [N] is less than 0.002%, the effect of generating Ti nitride is small.
- the N content [N] exceeds 0.006%, surface flaws occur during the production of steel slabs, so the upper limit of the N content [N] is 0.006%. Therefore, the N content [N] is 0.002% or more and 0.006% or less.
- the N content [N] is preferably 0.005% or less.
- Mg 0.0003 to 0.003%
- Mg is an important alloying element of the present invention, and is added mainly as a deoxidizer or a sulfide-forming element.
- Mg content [Mg] is added so as to be 0.003% or less, coarse oxides or sulfides are not generated, and a preferable base material and HAZ toughness can be obtained. Further, in order to sufficiently expect the formation of oxides necessary as pinning particles, addition of 0.0003% or more is necessary. Therefore, the range of Mg content [Mg] is set to 0.0003 to 0.003%.
- Ca 0.0003 to 0.003% Ca suppresses the generation of elongated MnS by generating sulfides, and improves the properties in the thickness direction of the steel material, particularly the lamellar resistance. Furthermore, Ca is an important element of the present invention because it has the same effect as Mg. In order to sufficiently obtain the above effects, 0.0003% or more must be added. Further, when the Ca content [Ca] is limited to 0.003% or less, the number of coarse oxides of Ca is suppressed, and the number of ultrafine oxides or sulfides can be sufficiently obtained.
- Mg and Ca are added simultaneously, but both are powerful deoxidizing elements.
- the total content of Mg and Ca is 0.0030% or less, the formation of coarse inclusions can be more effectively suppressed, and sufficient toughness can be obtained with a margin.
- Cu 0.50% or less (including 0%) Cu is an element that does not significantly deteriorate the HAZ toughness, improves the strength and toughness of the base material, and does not increase the hardness of ICHAZ too much. If sufficient strength of the steel material is ensured by elements such as C, Mn, and Ni, it is not always necessary to add Cu. Cu may be added in response to a request for strength or the like. However, Cu is a relatively expensive alloy element, and the above-mentioned effect is small as compared with Ni, and increases the risk of Cu cracking of the slab due to addition of too much. Therefore, the Cu content [Cu] is limited to 0.50% or less. You may restrict
- the Cu content [Cu] is twice the Ni content [Ni] in order to prevent Cu cracking of the slab.
- the following is preferable.
- the solid solubility limit of Cu in ferrite ( ⁇ Fe) is small, ⁇ Cu may be precipitated in the weld HAZ depending on the thermal history of welding, which may lower the low temperature toughness. If the Cu content [Cu] is 0.03% or less, the low-temperature toughness of the product can be ensured more reliably. In particular, when using a welding method with a large amount of heat, the low temperature toughness can be ensured more reliably if the Cu content [Cu] is 0.01% or less.
- V 0.020% or less (including 0%) V is effective for improving the strength of the base material. Therefore, V may be added as necessary. However, if V exceeding 0.020% is added, the HAZ toughness is greatly reduced. Therefore, the V content [V] is limited to 0.020% or less. In order to sufficiently suppress the decrease in HAZ toughness, it is preferable to limit the V content [V] to 0.010%. If the strength of the steel material is sufficiently ensured by elements such as C, Mn, and Ni, it is not always necessary to add V. Even when V is selectively added for reasons of strength, it is preferable to suppress the V content [V] as much as possible. Therefore, the V content [V] is more preferably 0.005% or less.
- the welding steel material of the present invention contains or restricts the above components, and the balance contains iron and inevitable impurities.
- the steel plate of the present invention contains, in addition to the above components, other alloy elements for the purpose of further improving the corrosion resistance and hot workability of the steel plate itself, or as an unavoidable impurity from secondary materials such as scrap. May be.
- other alloy elements Cr, Mo, B, Ca, Mg, Sb, Sn, As, etc.
- other alloy elements Cr, Mo, B, Ca, Mg, Sb, Sn, As, etc.
- the content of each of these elements includes 0%.
- the Cr content [Cr] is preferably 0.1% or less, more preferably 0.05% or less, and most preferably 0.02% or less. preferable.
- Mo decreases HAZ toughness
- the Mo content [Mo] is preferably 0.05% or less, more preferably 0.03% or less, and most preferably 0.01% or less. preferable.
- B increases HAZ hardness and decreases HAZ toughness
- the B content [B] is preferably 0.0005% or less, more preferably 0.0003% or less, and 0.0002% Most preferably:
- the Sb content [Sb] is preferably 0.005% or less, more preferably 0.003% or less, and most preferably 0.001% or less.
- the Sn content [Sn] is preferably 0.005% or less, more preferably 0.003% or less, and most preferably 0.001% or less.
- the As content [As] is preferably 0.005% or less, more preferably 0.003% or less, and most preferably 0.001% or less.
- REM has an effect of suppressing the formation of Ti oxide, the REM content [REM] is preferably 0.005% or less, more preferably 0.003% or less, and 0.001% Most preferably:
- the welding steel material of the present invention contains or restricts the above components as steel components, and the balance consists of iron and unavoidable impurities.
- the minimum dimension (for example, plate thickness) of the steel material is preferably 6 mm or more. In consideration of the use as a structural material, the minimum dimension (for example, plate thickness) of the steel material may be 100 mm or less.
- a slab is manufactured from the above-mentioned steel (molten steel) by a continuous casting method.
- the cooling rate (solidification rate) of molten steel is high, and a large amount of fine Ti oxide and Ti nitride can be generated in the slab.
- the reheating temperature of the slab needs to be 950 ° C. or higher and 1100 ° C. or lower.
- the Ti nitride becomes coarse, the toughness of the base material deteriorates, and it is difficult to improve the HAZ toughness.
- the lower limit of the reheating temperature is 950 ° C. Therefore, it is necessary to perform rolling at a temperature of 950 ° C. or higher and 1100 ° C. or lower.
- a processing heat treatment is performed.
- the rolling temperature is controlled within a narrow range according to the steel components, and then water cooling is performed as necessary.
- the austenite grains can be refined and the microstructure can be refined, and the strength and toughness of the steel material can be improved.
- the thickness (minimum dimension) of the final steel material is controlled to be 6 mm or more by rolling.
- thermomechanical treatment it is possible to produce a steel material having not only the HAZ toughness during welding but also the toughness of the base material.
- thermomechanical method is preferably a method combining controlled rolling and accelerated cooling. Note that after producing the steel, even when reheated to purposes Ar 3 following transformation point temperature, such as the dehydrogenation and strength optimization, characteristics of the steel material is not impaired.
- Thick steel plates of various steel components were manufactured through the steps of converter, continuous casting, and thick plate (rolling), and the base material strength tensile test and the weld joint CTOD test were performed on these thick steel plates.
- the welded joint used for the CTOD test was produced with a welding heat input of 4.5 to 5.0 kJ / mm by the submerged arc welding (SAW) method used as a general test welding.
- SAW submerged arc welding
- the FL part 5 of this welded joint is formed using a K groove so that the weld penetration line (FL) 9 is substantially perpendicular to the end surface of the thick steel plate.
- notch position (FL notch 7 and IC notch 8) is the FL portion (boundary between WM3 and HAZ4) 5 or the IC portion (boundary between HAZ4 and BM1) 6, as shown in FIGS. 4A and 4B.
- five tests were performed at ⁇ 60 ° C. for each of the FL notch 7 and the IC notch 8.
- Tables 1 and 2 show the chemical components of the steel, and Tables 3 and 4 show the manufacturing conditions of the thick steel plate (base material), the properties of the base material (BM), and the properties of the welded joint.
- CR Controlled rolling (rolling at the optimum temperature range to improve the strength and toughness of steel)
- ACC controlled rolling-accelerated cooling (steel material is water-cooled to 400-600 ° C after controlled rolling and allowed to cool)
- DQ Quenching and tempering immediately after rolling (Steel material is water cooled to 200 ° C or less immediately after rolling and then tempered)
- ⁇ c (av) is an average value of CTOD values of five tests
- ⁇ c (min) is a CTOD value of five tests. Indicates the lowest value.
- the yield strength (YS) was 430 N / mm 2 (MPa) or more, the tensile strength was 502 N / mm 2 (MPa) or more, and the base material strength was sufficient.
- the CTOD value ( ⁇ c) at ⁇ 60 ° C. the minimum CTOD value ⁇ c (min) of the FL notch is 0.42 mm or more, and the minimum CTOD value ⁇ c (min) of the IC notch is 0.60 mm or more. Excellent fracture toughness.
- the comparative example has the same strength as the example, but the CTOD value is inferior to that of the example, and is not suitable as a steel material used in a severe environment.
- the comparative steel 10 has a high Al amount
- the comparative steel 11 has no addition of Mg and Ca
- the comparative steel 12 has a high Si amount
- the comparative steel 13 has an excessive amount of Mg + Ca and an excessive amount of Nb. Since the comparative steel 14 is high and the amount of Ca is excessive and the amount of V is excessive, PCTOD and CeqH are high, so both have low CTOD values.
- the CTOD value of the IC notch is a low value. Since the comparative steel 32 has a high Al content, the PCTD and CeqH values are appropriate, but the structure control in the vicinity of the FL is insufficient and the CTOD value of the FL notch is low. Since the comparative steel 33 has an excessive amount of Mg + Ca and high PCTOD and CeqH values, both FL and IC notches have low CTOD values. Since the comparative steel 34 has an excessive amount of Si, no addition of Mg and Ca, and a high CeqH value, both the FL and IC notches have low CTOD values. Since the comparative steel 35 has an excessive amount of V and the comparative steel 22 has an excessive amount of Nb, the CeqH is high, and the CT notch value of the IC notch is particularly low.
- the CTOD value ( ⁇ c) at ⁇ 60 ° C. has a minimum CTOD value ⁇ c (min) at the FL notch of less than 0.43 mm, and the minimum value of the CTOD value at the IC notch ⁇ c (min) was less than 0.60 mm, and fracture toughness was not sufficient.
- FIG. 5 shows a summary of the relationship between the steel component hardness parameter CeqH in Tables 1 to 4 and the CTOD ( ⁇ c) value at ⁇ 60 ° C. in the IC part. As shown in FIG.
- the CTOD value in the IC notch is suppressed by suppressing the steel component hardness parameter CeqH to 0.235% or less.
- a steel material having a minimum value ⁇ c (min) of 0.25 mm or more could be produced.
- the minimum value ⁇ c (min) of the CTOD value is A steel material of 0.25 mm or more could not be manufactured (for example, Comparative Examples 8 and 37).
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Abstract
Description
本願は、2009年5月22日に、日本に出願された特願2009-124614号、2009年5月21日に、日本に出願された特願2009-123428号、および、2009年8月21日に、日本に出願された特願2009-192387号に基づき優先権を主張し、その内容をここに援用する。
(2) 上記(1)に記載の溶接用鋼材において、Cu含有量[Cu]を0.03~0.24%、Ni含有量[Ni]を0.10~0.49%、にさらに制限してもよい。
(3) 上記(1)または(2)に記載の溶接用鋼材において、MgとCaの合計含有量を0.0030%以下にさらに制限してもよい。
(4) 本発明の一態様にかかる溶接用鋼の製造方法は、上記(1)または(2)に記載の溶接用鋼材を連続鋳造により製造し、950~1100℃の温度に加熱して加工熱処理する。
PCTOD=[C]+[V]/3+[Cu]/22+[Ni]/67・・・(1)
ここで、[C]、[V]、[Cu]、[Ni]は、それぞれ、鋼中のC、V、Cu、Niの含有量(質量%)である。例えば、Cuが含有されない場合には、Cu含有量は、0%である。
1st cycle:最高加熱温度1400℃(800~500℃間を22secで冷却)
2nd cycle:最高加熱温度760℃(760~500℃間を22secで冷却)
3rd cycle:最高加熱温度500℃(500~300℃間を60secで冷却)
図4A中に示すように、溶接部2におけるFLノッチ7の位置は、HAZ4とWM3との境界のFL部5である。FLノッチによる以下のCTOD試験では、荷重とこのFL部5の開口変位との関係を測定した。
この試験片をBS5762法(British Standards)のCTOD試験によって評価し、図1のTδc0.1(FL)が得られている。ここで、Tδc0.1(FL)は、各試験温度で3本の試験片を用いて得られたCTOD(δc)値の最低値が0.1mmを超える温度(℃)である。なお、CTOD試験における板厚の影響を考慮すると、板厚50~100mmの鋼板の実継手のFLノッチ部(FL部)において、-60℃で安定して0.25mm以上のCTOD(δc)値を確保するためには、上述したようにTδc0.1(FL)を-110℃以下にする必要がある。
1st cycle:最高加熱温度950℃(800~500℃間を20secで冷却)
2nd cycle:最高加熱温度770℃(770~500℃間を22secで冷却)
3rd cycle:最高加熱温度450℃(450~300℃間を65secで冷却)
図4B中に示すように、溶接部2におけるICノッチ8の位置は、母材1とHAZ4との境界のIC部(ICHAZ部)6である。ICノッチによるCTOD試験では、荷重とこのIC部6の開口変位との関係を測定した。
CeqH=[C]+[Si]/4.16+[Mn]/14.9+[Cu]/12.9+[Ni]/105+1.12[Nb]+[V]/1.82・・・(2)
と定義される。なお、[C]、[Si]、[Mn]、[Cu]、[Ni]、[Nb]、[V]は、鋼中のC、Si、Mn、Cu、Ni、Nb、Vの含有量(質量%)である。例えば、Cuが含有されない場合には、Cu含有量は、0%である。
十分な強度を得るために、0.010%以上のCを含有させる必要がある。しかしながら、0.065%超のC含有量[C]では、溶接HAZの特性が劣化し、-60℃のCTOD特性が十分でない。そのため、C含有量[C]の上限は、0.065%である。したがって、C含有量[C]は、0.015%以上0.065%以下である。
良好なHAZ靭性を得るため、Si含有量[Si]は、少ないほど好ましい。しかしながら、後述するようにAl含有量[Al]を制限しているため、脱酸上0.05%以上のSi含有量[Si]が必要である。しかしながら、0.20%超のSi含有量[Si]では、HAZ靭性を害するため、Si含有量[Si]の上限は、0.20%である。したがって、Si含有量[Si]は、0.05%以上0.20%以下である。より良好なHAZ靭性を得るために、Si含有量[Si]は、0.15%以下または0.13%以下であることが好ましい。
Mnは、ミクロ組織を適正化する効果が大きい安価な元素である。また、Mnの添加によって、HAZ靭性を害する可能性は少ない。これらの点からは、Mnの添加量が多いのが好ましい。しかしながら、2.70%超のMn含有量では、ICHAZの硬さが増加し、靭性が劣化する。そのため、Mn含有量[Mn]の上限は、2.70%である。また、Mn含有量[Mn]が1.52%未満では、ミクロ組織を向上する効果が少ないので、Mn含有量[Mn]の下限は、1.52%である。したがって、Mn含有量[Mn]は、1.52%以上2.70%以下である。よりHAZ靭性を改善するためには、Mn含有量[Mn]は、1.55%又は1.6%以上であることが好ましく、より好ましくは、1.7%以上である。
Niは、HAZ靭性をあまり劣化させず、母材の強度及び靭性を向上させ、ICHAZの硬さをあまり増加させない元素である。しかしながら、Niは、高価な合金元素であり、鋼中に過剰に含まれると表面瑕を生じさせることがある。そのため、Ni含有量[Ni]の上限は、1.50%である。一方で、上述のNi添加の効果を十分に享受するためには、少なくとも0.10%のNiを含有する必要がある。したがって、Ni含有量[Ni]は、0.10%以上1.50%以下である。ICHAZの硬さをあまり増加させることなく、母材の強度及び靭性をより向上するために、Ni含有量[Ni]は、0.20%以上であることが好ましく、0.30%以上であることがより好ましい。さらに、鋼材に耐候性を付与するためには、Ni含有量[Ni]は、0.40%以上であることが好ましく、0.50%以上であることがさらに好ましい。また、表面疵をより確実に防止するためには、Ni含有量[Ni]は、1.20%以下であることが好ましく、1.0%以下であることがより好ましい。他元素の添加により母材の強度及び靭性を十分に確保できる場合には、より経済性を確保するために、Ni含有量[Ni]は、0.80%以下であることが最も好ましい。なお、後述するように、Cuを必要に応じ添加する場合には、鋳片のCu割れを抑制するために、Ni含有量[Ni]は、Cu含有量[Cu]の1/2以上であることが好ましい。
S:0.005%以下(0%を含む)
P及びSは、靭性を低下させ、不可避的不純物として含有される元素である。そのため、P含有量[P]及びS含有量[S]は、母材靭性及びHAZ靭性を確保するためともに低下させる必要がある。しかしながら、工業生産的な制約があるため、P含有量[P]の上限及びS含有量[S]の上限は、それぞれ0.008%及び0.005%である。より良好なHAZ靭性を得るために、P含有量[P]を0.005%以下に制限することが好ましく、S含有量[S]を0.003%以下に制限することが好ましい。
Al含有量[Al]は、Ti酸化物を生成させる必要があるため、少ないほど好ましい。しかしながら、工業生産的に制約があるため、Al含有量[Al]の上限は、0.004%である。
Tiは、Ti酸化物を生成させミクロ組織を微細化させる。しかしながら、Ti含有量[Ti]が多すぎると、Tiは、TiCを生成してHAZ靭性を劣化させる。そのため、Ti含有量[Ti]は、0.005%以上0.015%以下が適正な範囲である。よりHAZ靭性を改善するために、Ti含有量[Ti]は、0.013%以下であることが好ましい。
Nbは、不純物として含有される場合があり、母材の強度及び靭性を向上させるが、HAZ靭性を低下させる。HAZ靭性が著しく低下しないNb含有量[Nb]の範囲は、0.010%以下である。そのため、Nb含有量[Nb]を0.010%以下に制限する。よりHAZ靭性を改善させるためには、0.002%以下(0%を含む)に制限することが好ましい。
O含有量[O]は、FL部のIGF生成核としてのTiの酸化物の生成量を確保するために、0.0010%以上であることが必須である。しかし、O含有量[O]が多すぎると、酸化物のサイズおよび個数が過大になるためIC部のCTOD特性が劣化する。そのため、O含有量[O]を0.0015%以上0.0045%以下の範囲に制限した。より良好なHAZ靭性を得るために、O含有量[O]は、0.0030%以下であることが好ましく、0.0028%以下であることがより好ましい。
Nは、Ti窒化物を生成させるために必要である。しかしながら、N含有量[N]が0.002%未満では、Ti窒化物を生成させる効果が少ない。また、N含有量[N]が0.006%超では、鋼片製造時に表面疵が発生するため、N含有量[N]の上限は、0.006%である。したがって、N含有量[N]は、0.002%以上0.006%以下である。より良好なHAZ靭性を得るために、N含有量[N]は、0.005%以下であることが好ましい。
Mgは本発明の重要な合金元素であり、主に脱酸剤あるいは硫化物生成元素として添加される。Mg含有量[Mg]が0.003%以下になるように添加されると、粗大な酸化物あるいは硫化物が生成せず、好ましい母材およびHAZ靭性が得られる。また、ピニング粒子として必要な酸化物の生成を十分に期待するため、0.0003%以上の添加が必要である。従って、Mg含有量[Mg]の範囲を0.0003~0.003%とする。
Caは硫化物を生成することにより伸長MnSの生成を抑制し、鋼材の板厚方向の特性、特に耐ラメラテア性を改善する。さらに、CaはMgと同様な効果を有していることから、本発明の重要な元素である。上記の効果を十分に得るため、0.0003%以上の添加が必要である。また、Ca含有量[Ca]を0.003%以下に制限すると、Caの粗大酸化物個数が抑制され、超微細な酸化物あるいは硫化物の個数が十分に得られる。
Cuは、HAZ靭性をあまり劣化させず、母材の強度及び靭性を向上させ、ICHAZの硬さもあまり増加させない元素である。CやMn、Ni等の元素により鋼材の強度を十分に確保すれば、Cuを必ずしも添加する必要はない。強度等の要請に応じ、Cuを添加してもよい。しかし、Cuは、比較的高価な合金元素であり、Niに比べると上述の効果が小さく、多過ぎる添加によって鋳片のCu割れが生じる危険性を高める。そのため、Cu含有量[Cu]を0.50%以下に制限する。必要に応じて、0.24%以下又は0.10%以下に制限してもよい。加えて、鋼中にCuを添加したり、不純物としてCuを含んだりする場合には、鋳片のCu割れを防止するために、Cu含有量[Cu]をNi含有量[Ni]の2倍以下にすることが好ましい。また、Cuのフェライト(αFe)中への固溶限が小さいため、溶接の熱履歴によっては溶接HAZ中にεCuが析出し、低温靭性を低下させる可能性がある。Cu含有量[Cu]を0.03%以下にすれば、製品の低温靭性をより確実に担保できる。特に大熱量の溶接方法を用いる場合等は、Cu含有量[Cu]を0.01%以下にすれば、さらに確実に低温靭性が確保できる。
Vは、母材強度を向上させるために有効である。そのため、必要に応じ、Vを添加してもよい。しかし、0.020%を超えるVを添加すると、HAZ靭性が大きく低下する。そのため、V含有量[V]を、0.020%以下に制限する。HAZ靭性の低下を十分に抑えるためには、V含有量[V]を0.010%に制限することが好ましい。CやMn、Ni等の元素により鋼材の強度を十分に確保すれば、Vを必ずしも添加する必要はない。強度上の理由から選択的にVを添加する場合であっても、V含有量[V]を極力少なく抑えることが好ましい。したがって、V含有量[V]は、0.005%以下であることがより好ましい。
MoはHAZ靭性を低下させるため、Mo含有量[Mo]は、0.05%以下であることが好ましく、0.03%以下であることがより好ましく、0.01%以下であることが最も好ましい。
BはHAZ硬さを高め、HAZ靭性を低下させるため、B含有量[B]は、0.0005%以下であることが好ましく、0.0003%以下であることがより好ましく、0.0002%以下であることが最も好ましい。
SnはHAZ靭性を損なうため、Sn含有量[Sn]は、0.005%以下であることが好ましく、0.003%以下であることがより好ましく、0.001%以下であることが最も好ましい。
AsはHAZ靭性を損なうため、As含有量[As]は、0.005%以下であることが好ましく、0.003%以下であることがより好ましく、0.001%以下であることが最も好ましい。
REMはTi酸化物の生成を抑制する効果があるため、REM含有量[REM]は、0.005%以下であることが好ましく、0.003%以下であることがより好ましく、0.001%以下であることが最も好ましい。
CR:制御圧延(鋼材の強度及び靭性を改善するために最適な温度域での圧延)
ACC:制御圧延-加速冷却(制御圧延後400℃~600℃の温度域まで鋼材を水冷し、放冷)
DQ:圧延直後焼入れ-焼戻し(圧延直後に200℃以下の温度まで鋼材を水冷した後、焼戻し)
また、表3及び4中の溶接継手のCTOD試験結果において、δc(av)は、5本の試験のCTOD値の平均値を、δc(min)は、5本の試験のうちのCTOD値の最低値を示す。
比較鋼32はAl量が高いため、PCTODおよびCeqH値は適正であるが、FL近傍の組織制御が不十分となってFLノッチのCTOD値が低い。
比較鋼33はMg+Ca量が過剰、かつPCTODおよびCeqH値も高いため、FL、ICノッチともCTOD値が低い値である。
比較鋼34はSi量が過剰で、Mg、Caも無添加であり、CeqH値も高いため、FL、ICノッチともCTOD値が低い値である。
比較鋼35はV量が過剰なため、比較鋼22はNb量が過剰なため、CeqHが高くなり、特にICノッチのCTOD値が低い値となっている。
表1~表4中の鋼成分硬さパラメーターCeqHとIC部における-60℃でのCTOD(δc)値との関係を纏めた結果を図5に示す。図5に示すように、鋼中の各成分及び鋼成分パラメーターPCTODが上記条件を満足する場合には、鋼成分硬さパラメーターCeqHを0.235%以下に抑えることによって、ICノッチにおけるCTOD値の最小値δc(min)が0.25mm以上の鋼材を製造することができた。なお、鋼成分硬さパラメーターCeqHが0.235%以下であっても、鋼中の各成分及び鋼成分パラメーターPCTODが上記条件を満足しない場合には、CTOD値の最小値δc(min)が0.25mm以上の鋼材を製造することができなかった(例えば、比較例8及び37)。
Claims (4)
- 質量%で、
C含有量[C]が、0.010%以上0.065%以下のCと、
Si含有量[Si]が、0.05%以上0.20%以下のSiと、
Mn含有量[Mn]が、1.52%以上2.70%以下のMnと、
Ni含有量[Ni]が、0.10%以上1.50%以下のNiと、
Ti含有量[Ti]が、0.005%以上0.015%以下のTiと、
O含有量[O]が、0.0010%以上0.0045%以下のOと、
N含有量[N]が、0.002%以上0.006%以下のNと、
Mg含有量[Mg]が、0.0003%以上0.003%以下のMgと、
Ca含有量[Ca]が、0.0003%以上0.003%以下のCaと、
を含有し、残部が鉄および不可避的不純物を含み、
P含有量[P]を0.008%以下、
S含有量[S]を0.005%以下、
Al含有量[Al]を0.004%以下、
Nb含有量[Nb]を0.010%以下、
Cu含有量[Cu]を0.50%以下、
V含有量[V]を0.020%以下
に制限し、
鋼成分パラメーターPCTODが、
PCTOD=[C]+[V]/3+[Cu]/22+[Ni]/67・・・(1)
と定義され、
鋼成分硬さパラメーターCeqHが、
CeqH=[C]+[Si]/4.16+[Mn]/14.9+[Cu]/12.9+[Ni]/105+1.12[Nb]+[V]/1.82・・・(2)
と定義されるとき、
前記PCTODが0.065%以下、かつ、前記CeqHが0.235%以下であることを特徴とする溶接用鋼材。 - 請求項1に記載の溶接用鋼材であって、
Cu含有量[Cu]を0.03以下
にさらに制限することを特徴とする溶接用鋼材。 - MgとCaの合計含有量を0.0030%以下にさらに制限することを特徴とする請求項1または2に記載の溶接用鋼材。
- 請求項1または2に記載の成分のスラブを連続鋳造により製造し、
950~1100℃の温度に加熱して加工熱処理する、
ことを特徴とする溶接用鋼の製造方法。
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
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JP2010536248A JP4705696B2 (ja) | 2009-05-21 | 2010-05-21 | 溶接用鋼材およびその製造方法 |
CN2010800030774A CN102197154A (zh) | 2009-05-21 | 2010-05-21 | 焊接用钢材及其制造方法 |
EP20100777589 EP2400041B1 (en) | 2009-05-21 | 2010-05-21 | Steel material for welding and method for producing same |
BRPI1014830-2A BRPI1014830B1 (pt) | 2009-05-21 | 2010-05-21 | Aço para estrutura soldada |
RU2011146832/02A RU2470085C9 (ru) | 2009-05-21 | 2010-05-21 | Сталь для сварной конструкции и способ ее получения |
KR1020117009636A KR101160028B1 (ko) | 2009-05-21 | 2010-05-21 | 용접용 강재 및 그 제조 방법 |
US13/138,790 US8920713B2 (en) | 2009-05-21 | 2010-05-21 | Steel for welded structure and producing method thereof |
CA2757223A CA2757223C (en) | 2009-05-21 | 2010-05-21 | Steel for welded structure and producing method thereof |
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Cited By (3)
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JP2013256699A (ja) * | 2012-06-13 | 2013-12-26 | Nippon Steel & Sumitomo Metal Corp | 溶接性、溶接熱影響部靭性に優れた厚手高強度鋼板およびその製造方法 |
EP2784168A4 (en) * | 2011-11-25 | 2015-11-11 | Nippon Steel & Sumitomo Metal Corp | STEEL MATERIAL FOR WELDING |
US9403242B2 (en) | 2011-03-24 | 2016-08-02 | Nippon Steel & Sumitomo Metal Corporation | Steel for welding |
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TWI534271B (zh) | 2009-05-19 | 2016-05-21 | 新日鐵住金股份有限公司 | 熔接用鋼材 |
CN103998636B (zh) * | 2012-12-13 | 2015-07-22 | 新日铁住金株式会社 | 焊接用钢材 |
EP3447162B1 (en) * | 2016-04-21 | 2020-12-30 | Nippon Steel Corporation | Thick steel plate |
KR101899694B1 (ko) * | 2016-12-23 | 2018-09-17 | 주식회사 포스코 | 저온 충격인성 및 ctod 특성이 우수한 후강판 및 그 제조방법 |
CN108103398B (zh) * | 2017-12-07 | 2021-06-25 | 新疆八一钢铁股份有限公司 | 一种460Mpa级高强度高耐候钢板的生产方法 |
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JP2013256699A (ja) * | 2012-06-13 | 2013-12-26 | Nippon Steel & Sumitomo Metal Corp | 溶接性、溶接熱影響部靭性に優れた厚手高強度鋼板およびその製造方法 |
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US8920713B2 (en) | 2014-12-30 |
BRPI1014830B1 (pt) | 2022-09-27 |
EP2400041A1 (en) | 2011-12-28 |
KR101160028B1 (ko) | 2012-06-25 |
RU2470085C1 (ru) | 2012-12-20 |
RU2470085C9 (ru) | 2013-09-20 |
BRPI1014830A2 (pt) | 2016-09-27 |
EP2400041A4 (en) | 2012-10-17 |
JP4705696B2 (ja) | 2011-06-22 |
CA2757223C (en) | 2013-03-05 |
KR20110060959A (ko) | 2011-06-08 |
JPWO2010134353A1 (ja) | 2012-11-08 |
TWI365915B (en) | 2012-06-11 |
US20120027637A1 (en) | 2012-02-02 |
EP2400041B1 (en) | 2015-05-20 |
CN102197154A (zh) | 2011-09-21 |
CA2757223A1 (en) | 2010-11-25 |
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