WO2007049367A1 - Joint de soudure et son procede de production - Google Patents

Joint de soudure et son procede de production Download PDF

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Publication number
WO2007049367A1
WO2007049367A1 PCT/JP2006/300340 JP2006300340W WO2007049367A1 WO 2007049367 A1 WO2007049367 A1 WO 2007049367A1 JP 2006300340 W JP2006300340 W JP 2006300340W WO 2007049367 A1 WO2007049367 A1 WO 2007049367A1
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welded joint
welding
metal
weld
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PCT/JP2006/300340
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English (en)
Japanese (ja)
Inventor
Tomoya Kawabata
Kazushige Arimochi
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Sumitomo Metal Industries, Ltd.
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Publication of WO2007049367A1 publication Critical patent/WO2007049367A1/fr

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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
    • B23K9/00—Arc welding or cutting
    • B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded

Definitions

  • the present invention relates to a welded joint and a method for manufacturing the same.
  • welded joints and their manufacturing methods that are assumed to be used in a low-temperature environment of -60 ° C or lower, more specifically, liquefied petroleum gas (hereinafter referred to as “LPG”) or liquefied natural gas (hereinafter referred to as “LPG”).
  • LPG liquefied petroleum gas
  • LPG liquefied natural gas
  • LNG liquefied natural gas
  • the present invention relates to a welded joint capable of ensuring safety and a manufacturing method thereof.
  • a base material (material steel) for producing a so-called “low temperature tank” for storing LPG, LNG, etc. is required to have excellent fracture toughness for ensuring safety.
  • the so-called “9% Ni steel” containing 9% Ni by mass used in LNG tanks is the storage temperature of LNG—base metal and welded joints at 165 ° C Resistance to fracture, such as brittle fracture propagation stopping properties, is required. For this reason, in order to improve the properties of the base material, the chemical composition has been improved by reducing the content of impurity elements such as P and S, and the C content, and quenching (Q) -2 phase.
  • the so-called “three-stage heat treatment method” of zone quenching (L) —tempering (T) has been applied to optimize the metal structure.
  • austenitic welding materials are generally used from the viewpoint of ensuring resistance to fracture, that is, fracture safety.
  • SMAW force sideways welding
  • SAW submerged arc welding
  • vertical welding force TIG welding, for which automatic TIG welding has been applied, has a low welding speed, and improvement of power in terms of efficiency has been desired.
  • Patent Documents 1 to 3 disclose a technique aimed at improving the welding speed by using a 1 torch and 2 electrodes
  • Non-Patent Document 1 discloses the technique of the above 1 torch and 2 electrodes. Is applied to prestressed concrete LNG tanks! RU [0006] TIG welding is excellent in that the bead shape is beautiful and the necessity for rework after welding is low. However, even with the technology that has achieved the two-electrode method described above, a reduction in efficiency due to multilayer welding is inevitable.
  • Non-Patent Document 2 describes a high-heat-input electrified port gas arc welding (hereinafter also referred to as "EGW"!
  • thick-walled members can now be constructed by single-layer welding.
  • Non-Patent Document 3 describes an example in which electroslag welding is applied to welding of a building structure, in particular, welding of a diaphragm portion of a box column.
  • Patent Document 1 Japanese Patent Laid-Open No. 9-277052
  • Patent Document 2 Japanese Patent Laid-Open No. 9-277055
  • Patent Document 3 Japanese Patent Application Laid-Open No. 9 295154
  • Non-Patent Document 1 Kobayashi, Yuki, Ushio, Tanaka, Ueno, Yamashita: “Development and practical application of two-electrode high-efficiency TIG welding method (SE DAR— TIG)”, Proceedings of Welding Structure Symposium 2002, 411 ⁇ 4 14 The page
  • Non-Patent Document 2 Minagawa, Ishida, Funatsu, Imai: “Yield Strength 390MPa Steel Plate for Adult Heat Welding for Large Container Ships”, Nippon Steel Technical Report No. 380 (2004), pages 6-8
  • Non-Patent Document 3 Zanki, Onishi, Otake, Okaguchi, Yokoyama, Hatano: “Development of high-performance HT590 steel sheet for construction with excellent weldability”, Sumitomo Metals Vol. 50 (1998) No. 1, pages 43-47 Disclosure of the invention
  • the object of the present invention is to provide high heat input welding for so-called “9% Ni steel” for high efficiency welding. It is to provide a welded joint capable of ensuring fracture safety even when applied and a method for manufacturing the same.
  • GMAW gas metal arc welding
  • the CTOD value is an amount calculated for macro deformation level force, basically, the greater the difference in hardness between the weld metal and HAZ, the smaller the CTOD value. If this is recorded numerically, it can be expressed as follows. That is, the Vickers hardness of the weld metal (hereinafter referred to as “HV”) and the Vickers hardness of the weld heat affected zone (hereinafter referred to as “HV”)
  • the D value decreases significantly.
  • the amount of inclusions in the weld metal depends on the type of gas used as the shielding gas. to be influenced. In other words, oxygen (o) and carbon dioxide (CO) are abundant in the shielding gas component.
  • oxygen will melt into the weld metal through an arc reaction at a high temperature, and further, it will crystallize or precipitate as an oxide.
  • Base material is mass%, C: 0.01 to 0.2%, Si: 0.01 to: L 0%, Mn: 0.1 to 2.0%, Ni: 6 0 to: L0. 0% and A1: 0.005 to 0.1%, the balance is a welded joint consisting of Fe and impurities, gas metal arc welding using austenitic filler metal Alternatively, a welded joint that is joined by electret gas arc welding and has a weld metal structure of austenite and satisfies the following formulas (1) and (2).
  • HV is the Vickers hardness of the weld metal and HV is the Vickers hardness of the heat affected zone.
  • the base material is selected from Cu: 1% or less, Cr: 1% or less, Mo: 1% or less, and B: 0.005% or less instead of part of Fe 1
  • a method for manufacturing a welded joint characterized in that gas metal arc welding or elect mouth gas arc welding is performed with a deviation of 20% or less.
  • “Pickers hardness” refers to an average value of Vickers hardness measured at a plurality of locations on a weld metal or weld heat affected zone.
  • the “Pickers hardness of weld metal” is calculated from the Vickers hardness stamped multiple times on the lZ4t line (where “t” indicates the plate thickness) of the weld metal.
  • the "Vickers hardness of the weld heat affected zone” should be an average value based on the Pickers hardness stamped in the area between the "bond part” and the "bond part force is also lmm away from the base metal”. What is necessary is just to calculate.
  • the "welded metal structure” refers to the structure of every part of the weld metal.
  • the structure of the weld metal is austenite” means that no matter what part of the weld metal is observed, it becomes austenite! /.
  • the welded joint of the present invention has good fracture toughness, in particular, good CTOD characteristics, and can ensure great resistance to brittle fracture, so that welding of a tank for storing a low-temperature liquid is possible. Fittings, especially 165 ° C, can be used as welded joints for LNG tanks that store cryogenic LNG. This welded joint can be obtained relatively easily by the method of the present invention in which high heat input welding is applied to so-called “9% Ni steel” and can achieve high efficiency in welding. It is beneficial.
  • Fig. 1 shows a V-groove force with a groove angle of 5 ° on one side and a root gap of 5mm on a 25% -thick 9% Ni steel base material having the chemical composition specified in the present invention.
  • Hastelloy TGS-709S registered trademark
  • the C needs to be contained in an amount of 0.01% or more in view of ensuring strength.
  • the toughness is lowered.
  • the toughness is markedly lowered. Therefore, the content of C is set to 0.01 to 0.2%.
  • the upper limit of the C content is preferably 0.1%.
  • Si is an element that has a deoxidizing action and improves strength, and a content of 0.01% or more is necessary. However, if the content is too large, the weld joint toughness will decrease. In particular, when the Si content exceeds 1.0%, the toughness of the welded joint is significantly reduced. Therefore, the content of Si was set to 0.01 to: L 0%. From the viewpoint of ensuring good weld joint toughness, the upper limit of the Si content is preferably 0.50%.
  • Mn is an element that improves strength and toughness, and should be contained by 0.1% or more. However, if the content is too large, the weldability deteriorates and the characteristics of the base metal and the welded joint become non-uniform. In particular, if the Mn content exceeds 2.0%, the weldability deteriorates remarkably, and the characteristics of the base metal and the welded joint become more uneven. Therefore, the Mn content was set to 0.1 to 2.0%. The upper limit of the Mn content is preferably 1.0%.
  • Ni has the effect of improving strength and toughness at the same time, and tanks for storing low-temperature liquids, especially-165 ° C!
  • LNG tanks for storing cryogenic LNG It is an element that is indispensable for the base material, and its content must be 6.0% or more. However, if the content exceeds 10.0, the effect is saturated and the cost increases. Therefore, the Ni content was 6.0 to L0.
  • A1 A1: 0.005-0.1%
  • A1 is a deoxidizing element and must be contained in an amount of 0.005% or more to ensure the cleanliness of the steel. There is a point. However, if the content is too high, coarse Al 2 O may be generated or welded.
  • the content was set to 0.005-0. 1%.
  • the lower the A1 content the more advantageous the toughness of the welded joint. Therefore, when the toughness of the welded joint is more important, the upper limit of the A1 content is preferably 0.05%. If the upper limit of A1 content is kept as low as 0.05%, it is possible to prevent deterioration of slab surface quality during continuous fabrication caused by A1N.
  • the chemical composition of the base material of the welded joint according to the present invention (1) is defined as containing the elements at C force A within the above-mentioned range, with the balance being Fe and impurity forces. did.
  • the chemical composition of the base material of the welded joint according to the present invention may optionally contain elements shown in Group 1 to Group 3 described later, instead of a part of Fe, if necessary. May be good.
  • Group 1 Cu: l% or less, Cr: l% or less, Mo: 1% or less, and B: 0.005% or less
  • Cu has the effect of increasing strength. However, if the Cu content exceeds 1%, weldability is impaired. Therefore, the Cu content is set to 1% or less. In order to surely obtain the effect of Cu described above, the content is preferably 0.1% or more. Therefore, the more desirable Cu content is 0.1-1%.
  • Cr has an effect of increasing strength. However, if the Cr content exceeds 1%, the weldability is impaired. Therefore, the Cr content is set to 1% or less. In order to obtain the above-described effects with certainty, the content is preferably set to 0.1% or more. Therefore, the more desirable Cr content is 0.1 to 1%.
  • Mo has an effect of increasing strength. However, if the Mo content exceeds 1%, weldability is impaired. Therefore, the Mo content is set to 1% or less. In order to reliably obtain the above-described effect of Mo, the content is preferably set to 0.1% or more. Therefore, the more desirable Mo content is 0.1-1%.
  • B has an effect of increasing strength. That is, B has an effect of improving strength by praying to the grain boundaries. However, if the B content exceeds 0.005%, the toughness is impaired. Therefore, the B content is set to 0.005% or less. In addition, in order to reliably obtain the effect of B described above Therefore, it is preferable that the content is 0.0005% or more. Therefore, the more preferable B content is 0.0005 to 0.005%.
  • Second group V: 0.1% or less, Nb: 0.1% or less, Ti: 0.1% or less, and Zr: 0.05% or less
  • V has the effect of increasing the toughness by refining the structure, and is especially effective for refining the structure when manufacturing the base material by online accelerated cooling.
  • the content of V is set to 0.1% or less.
  • the content is preferably set to 0.005% or more. Therefore, the more desirable V content is 0.005-0. 1%.
  • Nb has the effect of increasing the toughness by refining the structure, and is particularly effective in refining the structure when producing a base material by online accelerated cooling.
  • the Nb content is set to 0.1% or less.
  • the content is preferably 0.005% or more. Therefore, the more desirable Nb content is 0.005-0. 1%.
  • Ti has the effect of increasing the toughness by refining the structure, and is particularly effective in refining the structure when producing a base material by online accelerated cooling.
  • the Ti content is set to 0.1% or less.
  • the content is preferably set to 0.005% or more. Therefore, the more desirable Ti content is 0.005-0. 1%.
  • Zr has the effect of increasing the toughness by refining the structure, and is particularly effective for refining the structure when manufacturing the base material by online accelerated cooling.
  • the Zr content is set to 0.05% or less.
  • the content is preferably set to 0.003% or more. Good. Therefore, the more desirable Zr content is 0.003-0.05%.
  • V, Nb, Ti and Zr, or a combination of two or more may be contained.
  • Group 3 Ca: 0.005% or less
  • Ca has the effect of preventing the formation of MnS and improving the thickness direction characteristics of the base metal, and in particular, increasing the Charpy absorbed energy value in the thickness direction of the base material.
  • the Ca content exceeds 0.005%, the cleanliness of the steel is impaired. Therefore, the Ca content is set to 0.005% or less.
  • the content thereof is 0.0005% or more. Therefore, the more desirable Ca content is 0.0005 to 0.005%.
  • the chemical composition of the base material of the welded joint according to the present invention (2) is replaced with a part of Fe of the base material of the welded joint according to the present invention (1).
  • it is specified to contain one or more selected from Cr: 1% or less, Mo: 1% or less, and B: 0.005% or less.
  • the chemical composition of the base material of the welded joint according to the present invention (3) is replaced with a part of Fe of the base material of the welded joint in the present invention (1) or the present invention (2), V: 0.1% or less, Nb: 0.1% or less, Ti: 0.1% or less, and Zr: 0.05% or less.
  • the chemical composition of the base material of the welded joint according to the present invention (4) is replaced with a part of Fe of the base material of the welded joint in any of the present invention (1) to the present invention (3). Therefore, it was specified that Ca: 0.005% or less.
  • the welded joint of the present invention welded by GMAW or EGW, for example, under the conditions described later, by combining the base material (9% Ni steel) having the chemical composition described in the section (A) and an austenitic filler metal, for example.
  • the structure of the weld metal becomes austenite.
  • the Vickers hardness must be 250 or less.
  • the strength (hardness) of materials including austenitic materials increases. Elongation will decrease. This is because the increase in strength is based on a mechanism that reduces elongation, such as an increase in dislocation density. And the Vickers hardness of the weld metal, that is, HV force 3 ⁇ 4
  • the "Vickers hardness of the weld metal” may be calculated from the Vickers hardness obtained by stamping a plurality of times with the lZ4t line of the weld metal part.
  • the CTOD value which is a measure of resistance to brittle fracture, is an amount calculated from the macro deformation level force.
  • the CTOD test generally does not end with brittle fracture unless the HAZ brittle fracture resistance is extremely bad.
  • the weld metal In order not to end with brittle fracture, the weld metal must have a lower hardness than the HAZ. In other words, "HV ⁇ HV"
  • CTOD value decreases as the difference in Vickers hardness between the weld metal and HAZ increases. Above all, the value of “HV-HV” is great for fracture characteristics of welded joints, especially CTOD characteristics.
  • Figure 1 shows 0.05% C-0. 7% Mn-0. 25% Si-9. 0% Ni—0.025%
  • A1 V-groove force with 5 ° groove angle on one side and root gap of 5mm is applied to Ni steel base metal, and Hastelloy TGS—709S (registered trademark), an Ni-based alloy, is used as an austenitic filler metal.
  • Hastelloy TGS—709S registered trademark
  • an Ni-based alloy is used as an austenitic filler metal.
  • the "Vickers hardness of the weld heat affected zone” includes a plurality of regions between the "bond portion” and the "point separated from the bond portion lmm toward the base metal side".
  • the average value may be calculated from the Vickers hardness obtained by stamping.
  • the welded joint of the present invention can be used at room temperature and has good fracture toughness characteristics even at low temperatures, it should also be used as a welded joint used to manufacture low-temperature tanks that store LPG, LNG, etc. Can do. More specifically, it can be used even in a low temperature environment of 60 ° C or lower.
  • the welded joint according to the present invention (5) should be used in a low temperature environment of 60 ° C or lower.
  • the heat input during welding is set to 4. OkjZmm or more, and the fraction of CO and O in the shielding gas is set to 20% or less.
  • the upper limit of the heat input during welding is not particularly specified, it is better to set it to 30. OkjZmm considering the actual plate thickness of the LNG tank.
  • the welded joints of the present inventions (1) to (4) can be used as the welded joint of the present invention (5) used in the use environment described in the section (D).
  • the austenitic filler material for example, a Ni-based alloy hastelloy (registered trademark) material or inconel (registered trademark) material can be used.
  • the 9% Ni steel plate which is the base material, can be manufactured, for example, as follows. The following description is merely an example of the production method and does not limit the scope of the present invention.
  • Ni steel which has been subjected to component adjustment, is continuously forged under general conditions to form a slab, which is then transported to a plate factory.
  • the slab that arrives at the plate factory is reheated to 1050 ° C, for example, in a heating furnace.
  • Heating furnace power The extracted slab is reverse-rolled by a hot rolling mill to a predetermined thickness.
  • Q-L-T For the cut steel sheet, for example, Q-L-T, where the quenching (Q) temperature is 810 ° C, the two-phase quenching (L) temperature is 580 ° C, and the tempering (T) temperature is 500 ° C.
  • the so-called “three-stage heat treatment” is performed.
  • Q-T treatment is performed at a quenching (Q) temperature of 810 ° C and a tempering (T) temperature of 500 ° C.
  • Example 1 Using a steel plate with the chemical composition shown in Table 1 and the mechanical properties shown in Table 2 and a thickness of 25 mm, a V groove force of 5 ° on one side and a root gap of 5 mm was applied to GMAW and Welded by EGW and investigated the weld joint performance.
  • Steels 1 to 17 in Table 1 are steels of the present invention examples whose chemical compositions satisfy the conditions defined in the present inventions (1) to (4).
  • steels X1 to X5 are comparative steels whose chemical compositions also deviate from the conditional forces defined in the present invention.
  • the 25 mm steel plate which is the base material, was subjected to a tensile test by rolling the slab at the heating temperature and rolling finishing temperature shown in Table 2, and then quenching and tempering at various temperatures. The one with a tensile strength of about 690 to 735 MPa at 590 to 630 MPa was selected.
  • Table 2 shows the quenching and tempering temperatures when the tensile properties described above were obtained.
  • a V-notch test piece with a width of 10 mm specified in JIS Z 2202 (1998) was taken from the position of plate thickness 1Z4 in parallel with the rolling direction, and a Charpy impact test was conducted at –196 ° C to absorb the absorption energy ( vE-196).
  • Type 4 of the CTOD test in Table 2 shows that the stable ductile crack grows by 0.2 mm or more.
  • Hastelloy TGS-709S registered trademark
  • Ni-based alloy having the chemical composition shown in Table 3.
  • Table 4 shows welding methods and heat input amounts for the respective base materials. In all cases, He gas alone (100% He) was used as the shielding gas used during welding.
  • the weaving was investigated and the Vickers hardness (HV) of the heat affected zone was measured.
  • the Vickers hardness of the weld metal is the average value of three points of Vickers hardness obtained by stamping at a test force of 9.807N at a pitch of 0.5mm on the lZ4t line of the weld metal. It was.
  • the HAZ Vickers hardness is about 12mm from the bond part to the lmm part, and the weld part is 14t line at the bond part (immediately above the fusion line), and 0.5mm away from the bond part to the base metal side.
  • the point and bond part force are also on the base metal side. 1.
  • Test force at a point separated by Omm 9. Vickers hardness is measured at 807N, and these three points are averaged to obtain HV.
  • a smooth round bar tensile test piece with a parallel part diameter of 6 mm, a gauge distance of 25 mm and a gripping part of M10 was taken from the position of about 1Z4 of the plate thickness, and a tensile test was conducted at room temperature. % Resistance (0.2% PS) and tensile strength (TS) were determined.
  • a notch is introduced into the so-called “fusion line” bond part, and a standard “BX 2B” type bending test specimen with the total thickness defined in BS 7448 -partl (1991) as B is used, similar to the base metal.
  • a three-point bending CTOD test was conducted at 165 ° C to investigate the limit CTOD value ⁇ c and the type of CTOD test.
  • the pass / fail criterion was set to 0.8 mm as the limit CTOD value based on the CTOD test results of TIG welded joints so far.
  • Table 4 shows the results of the above tests together.
  • Type 4 of the CTOD test in Table 4 means that the stable ductile crack grows 0.2 mm or more, but then brittle fracture occurs, and the brittle fracture occurrence point becomes the maximum load. It means that a brittle fracture does not occur up to the maximum load and the crack propagates in a ductile manner.
  • the asterisk (*) indicates that the conditions specified in the present invention are not met, and the ** mark indicates that the target of 0.8 mm has not been achieved.
  • base materials X1 to X5 whose chemical composition deviates from the conditions specified in the present invention are inferior in toughness, and in particular, base material XI has a critical CTOD value ⁇ c of 0.051 mm and brittle fracture. Because of its low resistance to, the CTOD test type was a type including brittle fracture4.
  • the welded joints with test numbers 1 to 17 that satisfy the conditions specified in the present invention (1) to (4) have a critical CTOD value ⁇ c exceeding lmm, which is large against brittle fracture. It can be seen that it has resistance.
  • the welded joints with test numbers 18 to 22 where the chemical composition of the base material deviated from the conditions stipulated in the present invention were all subjected to brittle fracture due to the brittleness of the HAZ structure itself.
  • the limit CTOD value Sc has not reached the low target of 0.8 mm.
  • the root angle is 5 ° on one side using steel plates of Steel 1 and Steel 3 as the base material.
  • V-groove machining with a gap of 5 mm was performed, and welding was performed using a solid wire with a diameter of 1.6 mm of a filler metal having the chemical composition shown in Table 5.
  • filler metals A to C shown in Table 5 are austenitic base, Stelloy (registered trademark), Inconel 625 (registered trademark), and martensitic base metal wires, respectively.
  • the measurement method is the same as in [Example 1].
  • the welded joints with test numbers 23 to 43 that satisfy the conditions specified in the present invention have a critical CD value ⁇ c exceeding lmm and have a high resistance to brittle fracture. Gawaka.
  • the target of 0.8mm has not been reached.
  • Test No. 44 welded joint has a value of (HV -HV) exceeding 200, and the limit CT
  • OD value Sc is as low as 0.241mm.
  • the welded joint with test number 45 has an HV value exceeding 250 and a critical CTOD value of ⁇
  • the welded joint with test number 46 had a CO fraction of more than 20% in the shielding gas.
  • the critical CTOD value ⁇ c is as low as 0.123 mm.
  • the weld joint with test number 47 had an O fraction in the shielding gas of more than 20%.
  • the limit CTOD value ⁇ c is as low as 0.120 mm.
  • the weld joint with test number 48 uses martensitic code C as the filler metal, so that the weld metal structure formed by welding becomes a martensite structure and becomes HV.
  • the welded joint of the present invention has good fracture toughness, in particular, good CTOD characteristics and great resistance to brittle fracture, a welded joint for tanks for storing low-temperature liquids, -With 165 ° C! As a welded joint of LNG tank for storing cryogenic LNG Can be used.
  • This welded joint can be obtained relatively easily by the method of the present invention in which high heat input welding is applied to so-called “9% Ni steel”, and high efficiency of welding can be realized.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Mechanical Engineering (AREA)
  • Arc Welding In General (AREA)

Abstract

La présente invention concerne un joint de soudure en métal de base comprenant de 0,01 à 0,2 % de C, de 0,01 à 1,0 % de Si, de 0,1 à 2,0 % de Mn, de 6,0 à 10,0 % de Ni, de 0,005 à 0,1 % d’Al, le complément étant constitué de Fe et d’impuretés, lié par soudure à l’arc électrogaz ou par soudure à l’arc gaz-métal en utilisant une charge Ϝ, le métal soudé ayant une structure Ϝ, et lorsque DVMS se rapporte à la dureté Vickers du métal soudé et DVPAC se rapporte à la dureté Vickers de la partie affectée par la chaleur de soudure, les relations « DVPAC ≤ 250 » et « 0 ≤ DVPAC - DVMS ≤ 200 » étant vérifiées. Ce joint de soudure, ayant d’excellentes caractéristiques CTOD et une forte résistance à la rupture fragile, peut être utilisé comme un joint de soudure de réservoirs destinés à stocker un liquide de basse température, plus particulièrement comme un joint de soudure de réservoir de GNL destiné à stocker des GNL dont la température est extrêmement basse de l’ordre de -165 °C.
PCT/JP2006/300340 2005-10-26 2006-01-13 Joint de soudure et son procede de production WO2007049367A1 (fr)

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CN103320719A (zh) * 2013-06-19 2013-09-25 宝山钢铁股份有限公司 低成本可大热输入焊接高强韧性钢板及其制造方法
EP3156171A1 (fr) * 2015-10-14 2017-04-19 CRS Holdings, Inc. Produit consommable pour le soudage haute résistance à base d'un système métallurgique à 10 % d'acier au nickel
CN109477178A (zh) * 2016-08-04 2019-03-15 株式会社神户制钢所 电弧点焊方法和焊丝

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JP6693186B2 (ja) * 2016-03-11 2020-05-13 日本製鉄株式会社 引張強度および靭性に優れた低温用ニッケル含有鋼板の製造方法
JP7477763B2 (ja) 2020-07-08 2024-05-02 日本製鉄株式会社 低温用Ｎｉ鋼を用いた溶接継手の製造方法及びこれにより得られた溶接継手
CN117177831A (zh) * 2021-04-28 2023-12-05 杰富意钢铁株式会社 电弧焊接头和电弧焊方法
JP7188648B1 (ja) * 2021-12-17 2022-12-13 日本製鉄株式会社 低温用ニッケル含有鋼溶接継手
JP2024062502A (ja) * 2022-10-25 2024-05-10 三菱造船株式会社 低温ガス用タンク、低温ガス用タンクの製造方法

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CN103320719A (zh) * 2013-06-19 2013-09-25 宝山钢铁股份有限公司 低成本可大热输入焊接高强韧性钢板及其制造方法
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