CN106392369B - Ni-based alloy flux-cored wire - Google Patents
Ni-based alloy flux-cored wire Download PDFInfo
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- CN106392369B CN106392369B CN201610355993.3A CN201610355993A CN106392369B CN 106392369 B CN106392369 B CN 106392369B CN 201610355993 A CN201610355993 A CN 201610355993A CN 106392369 B CN106392369 B CN 106392369B
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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
- B23K35/3033—Ni as the principal 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
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
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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
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/3601—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest with inorganic compounds as principal constituents
- B23K35/3602—Carbonates, basic oxides or hydroxides
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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
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/362—Selection of compositions of fluxes
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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
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/368—Selection of non-metallic compositions of core materials either alone or conjoint with selection of soldering or welding materials
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
The invention provides a Ni-based alloy flux-cored wire which is not easy to generate high-temperature cracks during welding and can obtain welding metal with good tensile ductility even if the welding metal contains a large amount of hydrogen. The Ni-based alloy flux-cored wire is a Ni-based alloy flux-cored wire with a flux wrapped in a sheath, and the whole welding wire comprises the following components: the total amount of Ni, Cr, Mo, Mn, W, Fe, Al contained in a predetermined amount in terms of B in one or both of the B compound and the B alloy is 0.005 mass% or more and 0.030 mass% or less, and C, Si, P, S, Ti, and Nb are each a predetermined value or less, based on the total mass of the wire.
Description
Technical Field
The present invention relates to a Ni-based alloy flux-cored wire used for welding 9% Ni steel, various high Ni alloys, and the like.
Background
A thick steel plate of 9% Ni steel having excellent low-temperature toughness is used for an LNG (Liquefied Natural Gas) storage tank or the like, and a Ni-based alloy welding material having excellent low-temperature toughness is used for welding the 9% Ni steel. The Ni-based alloy welding material is required to have high low-temperature toughness in a state after welding without heat treatment after welding.
In a special welding material such as a Ni-based alloy welding material, a shielded arc welding using a Ni-based alloy flux-cored wire and a TIG (Tungsten Inert Gas) welding are often performed, but in recent years, a Gas shielded arc welding using a Ni-based alloy flux-cored wire is often performed in order to expect higher operation efficiency.
Based on this situation, numerous inventions relating to Ni-based alloy flux-cored wires have been disclosed. For example, patent document 1 discloses a Ni-based alloy flux-cored wire in which the amount of C in the metal sheath is limited and a predetermined amount of a deoxidizing component is added. Patent document 1 describes that the Ni-based alloy flux-cored wire can prevent solidification cracking of the weld metal and stabilize the arc during the welding operation, thereby obtaining excellent high-temperature cracking resistance and welding operability.
In the present specification, "weld metal" means a metal obtained by melting a deposited metal and a molten base material and solidifying the melted metal during welding when welding is performed. In the present specification, "deposited metal" refers to a metal that is transferred from a welding filler (welding wire), which is a metal material added during welding, to a welded portion.
Further, patent documents 2 and 3 disclose a Ni-based alloy flux-cored wire in which the composition of the entire wire or the compositions of the entire wire and the sheath are limited to predetermined ranges. Patent document 2 describes that the Ni-based alloy flux-cored wire can be excellent in high-temperature cracking resistance and welding workability. Further, patent document 3 describes that the Ni-based alloy flux-cored wire can provide a weld metal having excellent crack resistance and can further improve welding workability.
Documents of the prior art
Patent document
Patent document 1: japanese laid-open patent publication No. 2015-085366
Patent document 2: japanese patent laid-open publication No. 2005-59077
Patent document 3: japanese laid-open patent publication No. 9-314382
Disclosure of Invention
Technical problem to be solved by the invention
The Ni-based alloy welding material has the following problems: the trace amount of hydrogen contained in the weld metal decreases the mechanical properties of the weld metal at room temperature, particularly the tensile elongation at break.
The same applies to the case where the welding material itself absorbs moisture if stored for a long period of time in a high-temperature and high-humidity environment, and moisture contained in the welding material is transferred to the weld metal during welding, or moisture remains in the base metal.
For the above reasons, weld metal lacking tensile ductility (tensile elongation at break) is sometimes formed.
However, none of the inventions described in patent documents 1 to 3 can improve the insufficient tensile ductility due to the large amount of hydrogen contained in the weld metal.
In addition, since the Ni-based alloy has a completely austenitic structure, it tends to have high susceptibility to high-temperature cracking and poor high-temperature cracking resistance. Therefore, the Ni-based alloy flux-cored wire is required to have excellent high-temperature cracking resistance, i.e., to be less likely to cause high-temperature cracking during welding.
The present invention has been made in view of the above circumstances, and an object thereof is to provide a Ni-based alloy flux-cored wire which is less likely to cause hot cracking during welding and can obtain a weld metal having good tensile ductility even when the weld metal contains a large amount of hydrogen.
Means for solving the problems
The Ni-based alloy flux-cored wire of the present invention for solving the above-described technical problems is a Ni-based alloy flux-cored wire in which a flux is enclosed in a sheath, and the entire composition of the wire is, relative to the total mass of the wire, Ni: 50 to 70 mass% of Cr: 1 to 15 mass% of Mo: 10 to 20 mass%, Mn: 1.5 to 5.5 mass%, W: 1.5 to 5.0 mass% inclusive, Fe: 2.0 to 8.0 mass% inclusive, Al: 0.01 to 0.40 mass% inclusive, and the total of B-equivalent amounts of either or both of the B compound and the B alloy: 0.005 mass% or more and 0.030 mass% or less, C: 0.050% by mass or less of Si: 0.15 mass% or less, P: 0.015% by mass or less, S: 0.010 mass% or less, Ti: 0.20% by mass or less, Nb: 0.03 mass% or less.
As described above, since the Ni-based alloy flux-cored wire of the present invention contains a predetermined amount of B with respect to the total mass of the wire, a weld metal having good tensile ductility (good tensile elongation at break) can be obtained even when the weld metal after welding contains a large amount of hydrogen due to exposure to a high-temperature and high-humidity environment. In addition, in the Ni-based alloy flux-cored wire of the present invention, the content of C, Si, P, S, Ti, Nb, and the like is limited to the total mass of the wire and the content of Al is set to a predetermined range, so that the decrease in high-temperature cracking resistance can be suppressed.
In the Ni-based alloy flux-cored wire of the present invention, the flux preferably contains TiO in the total mass of the wire2: 3.0 to 10.0 mass% or less of SiO2: 0.1 to 4.0 mass% ZrO2: 0.5 to 2.0 mass% of a metal fluoride: 0.01 to 1.5 mass% in terms of F.
Thus, the Ni-based alloy flux-cored wire of the present invention contains TiO in a predetermined amount based on the total mass of the wire2And metal fluorides, so that arc stability can be improved. In addition, the Ni-based alloy flux-cored wire of the present invention contains a predetermined amount of SiO based on the total mass of the wire2And ZrO2Therefore, the welding operability can be improved.
In the Ni-based alloy flux-cored wire of the present invention, the sheath preferably contains Ni: 60 mass% or more, Mo: 8 to 22 mass% of Cr: 1 to 15 mass%.
In this way, the Ni-based alloy flux-cored wire of the present invention contains a predetermined amount of Ni with respect to the total mass of the sheath, and therefore can maintain the uniformity of the weld metal. In addition, since the Ni-based alloy flux-cored wire of the present invention contains a predetermined amount of Mo in the total mass of the sheath, the strength of the weld metal can be ensured. Further, since the Ni-based alloy flux-cored wire of the present invention contains Cr in a predetermined amount with respect to the total mass of the sheath, the corrosion resistance and strength of the weld metal can be improved.
Effects of the invention
The Ni-based alloy flux-cored wire of the present invention is less likely to cause hot cracking during welding in the welding of 9% Ni steel or Ni-based alloy, and can obtain a weld metal having good tensile ductility even when the weld metal contains a large amount of hydrogen.
Drawings
Fig. 1 is a graph showing the relationship between the total amount of B converted in one or both of the compound B and the alloy B (indicated as "total amount of B converted" in fig. 1), the tensile elongation at break of the deposited metal, and whether or not hot cracking occurs under predetermined welding conditions, with respect to the total mass of the wire. The horizontal axis represents the total amount (mass%) of B in terms of B, and the vertical axis represents the tensile elongation at break (%) of the deposited metal. The specified welding conditions were current 280A, voltage 34V, welding speed 500mm/min (labeled as "280V-34V-500 mm/min." in FIG. 1).
Fig. 2 is a cross-sectional view showing a groove shape for welding a room-temperature tensile test piece for collecting deposited metal.
Fig. 3 is a cross-sectional view showing a collection position of a tensile test piece used in a room-temperature tensile test of a deposited metal.
Fig. 4 is a cross-sectional view showing a structure of a material to be welded which is welded in a hot crack test.
Detailed Description
Hereinafter, embodiments of the Ni-based alloy flux-cored wire (hereinafter, may be simply referred to as "wire") according to the present invention will be described in detail.
The welding wire is a Ni-based alloy flux-cored welding wire with a flux wrapped in a sheath. Hereinafter, the outer skin is described in detail, and the outer skin is formed of an Ni-based alloy. The Ni-based alloy is an alloy whose main component (component having the largest content) is Ni. The wire of the present invention can be drawn to have a diameter of 1.2mm (the actual diameter includes an error range of the nominal diameter), for example, but is not limited thereto, and any diameter can be suitably used as long as it is a wire diameter used as a Ni-based alloy flux-cored wire.
In the welding wire of the present invention, the entire composition of the welding wire contains Ni: 50 to 70 mass% of Cr: 1 to 15 mass% of Mo: 10 to 20 mass%, Mn: 1.5 to 5.5 mass%, W: 1.5 to 5.0 mass% inclusive, Fe: 2.0 to 8.0 mass% inclusive, Al: 0.01 to 0.40 mass% inclusive, and the total of B-equivalent amounts of either or both of the B compound and the B alloy: 0.005 mass% or more and 0.030 mass% or less.
In the welding wire of the present invention, the composition of the entire welding wire is, relative to the total mass of the welding wire, C: 0.050% by mass or less of Si: 0.15 mass% or less, P: 0.015% by mass or less, S: 0.010 mass% or less, Ti: 0.20% by mass or less, Nb: 0.03 mass% or less.
The components and composition of the welding wire will be described below.
(Ni in the entire welding wire is 50 to 70 mass% based on the total mass of the welding wire)
Ni is alloyed with various metals to impart excellent mechanical properties and corrosion resistance to weld metals. However, if the Ni content in the wire is less than 50 mass% with respect to the total mass of the wire, excellent mechanical properties and corrosion resistance of the weld metal cannot be obtained. On the other hand, if the Ni content in the wire exceeds 70 mass% with respect to the total mass of the wire, the content of other alloying elements becomes insufficient, and mechanical properties cannot be secured. Therefore, the Ni content is 50 mass% or more and 70 mass% or less with respect to the total mass of the wire. The Ni source in the welding wire of the present invention includes an Ni-based alloy forming the outer layer, metallic Ni that may be contained (possibly contained) in the flux, an Ni — Mo alloy, and the like, and in the present invention, the value obtained by converting the content thereof into Ni is defined as the Ni content.
(Cr in the entire welding wire is 1 to 15 mass% based on the total mass of the welding wire.)
Cr has an effect of improving the corrosion resistance and strength of the weld metal. However, if the Cr content in the wire is less than 1 mass% with respect to the total mass of the wire, this effect cannot be obtained. On the other hand, if the Cr content in the wire exceeds 15 mass% with respect to the total mass of the wire, the high temperature cracking resistance is lowered. Therefore, the Cr content is 1 mass% or more and 15 mass% or less with respect to the total mass of the wire. The Cr source in the wire of the present invention includes Ni-based alloy forming the outer layer, metallic Cr that may be contained in the flux, Fe — Cr alloy, and the like, and in the present invention, the value obtained by converting the content thereof into Cr is defined as the Cr content.
(Mo in the entire welding wire: 10 to 20 mass% inclusive of the total mass of the welding wire.)
Mo has the effect of improving the corrosion resistance and strength of the weld metal. However, if the Mo content in the wire is less than 10 mass% with respect to the total mass of the wire, the corrosion resistance and strength of the weld metal cannot be ensured. On the other hand, if the Mo content in the wire exceeds 20 mass% with respect to the total mass of the wire, the high temperature cracking resistance is lowered. Therefore, the Mo content is 10 mass% or more and 20 mass% or less with respect to the total mass of the wire. The Mo source in the wire of the present invention includes Ni-based alloy forming the outer layer, Mo metal which may be contained in the flux, Fe — Mo alloy, and the like, and in the present invention, the value obtained by converting the content thereof into Mo is defined as the Mo content.
(Mn in the entire welding wire is 1.5 mass% or more and 5.5 mass% or less based on the total mass of the welding wire)
Mn forms a low melting point compound with Ni to bind to S, which reduces high temperature cracking resistance, and has an effect of making S harmless. However, if the Mn content in the wire is less than 1.5 mass% with respect to the total mass of the wire, the effect of making S harmless cannot be obtained. On the other hand, if the Mn content in the wire exceeds 5.5 mass% with respect to the total mass of the wire, the slag removability is lowered. Therefore, the Mn content is 1.5 mass% or more and 5.5 mass% or less with respect to the total mass of the wire. The Mn source in the wire of the present invention includes Ni-based alloy forming the outer layer, Mn which is a metal that may be contained in the flux, Fe — Mn alloy, and the like, and in the present invention, the value obtained by converting the content thereof into Mn is defined as the Mn content.
(W in the entire welding wire is 1.5 mass% or more and 5.0 mass% or less based on the total mass of the welding wire)
W is a component for improving the strength of the weld metal. However, if the W content in the wire is less than 1.5 mass% with respect to the total mass of the wire, the strength of the weld metal cannot be ensured. On the other hand, if the W content in the wire exceeds 5.0 mass% with respect to the total mass of the wire, the high temperature cracking resistance is lowered. Therefore, the W content is 1.5 mass% or more and 5.0 mass% or less with respect to the total mass of the wire. In the present invention, the W source in the welding wire includes Ni-based alloy forming the outer layer, metal W, Fe-W alloy which may be contained in the flux, and the content thereof is defined as W content in terms of W.
(Fe in the entire welding wire is 2.0 mass% or more and 8.0 mass% or less based on the total mass of the welding wire.)
Fe is a component that ensures ductility of the weld metal. If the Fe content in the wire is less than 2.0 mass% with respect to the total mass of the wire, the ductility of the weld metal cannot be ensured. On the other hand, if the Fe content in the wire exceeds 8.0 mass% with respect to the total mass of the wire, the high temperature cracking resistance is lowered. Therefore, the Fe content is 2.0 mass% or more and 8.0 mass% or less with respect to the total amount of the wire. The Fe source in the wire of the present invention includes Ni-based alloy forming the outer layer, metallic Fe that may be contained in the flux, Fe-Mn alloy, Fe-Cr alloy, Fe-Mo alloy, Fe-Ti alloy, etc., and in the present invention, the value obtained by converting the content thereof to Fe is defined as Fe content.
(Al in the entire welding wire is 0.01 to 0.40 mass% based on the total mass of the welding wire)
al contained in the wire has an action of reducing the amount of dissolved oxygen in the molten metal as a deoxidizing component, suppressing the reaction of "C + O ═ CO (gas)", and reducing the amount of generated pores, but if it is excessively added, high-temperature cracking resistance is deteriorated. As described later, the present invention is a flux-cored wire to which B is actively added, but when B is actively added, the high-temperature cracking property of the wire tends to decrease. In the invention, the following are found: the Al content in the wire is 0.01 mass% or more and 0.40 mass% or less based on the total mass of the wire, whereby the high-temperature cracking resistance of the weld metal can be ensured. Therefore, the Al content is 0.01 mass% or more and 0.40 mass% or less with respect to the total mass of the wire. The Al source in the welding wire of the present invention includes Ni-based alloy forming the outer layer, metallic Al that may be contained in the flux, Fe — Al alloy, and the like, and in the present invention, the value obtained by converting the content thereof into Al is defined as the Al content. However, the Al content is the content of Al derived from metallic Al and Al alloy dissolved in sulfuric acid, and does not include Al derived from Al insoluble in sulfuric acid2O3And the like.
(total of B-equivalent amounts of either or both of the B compound and the B alloy in the entire welding wire: 0.005 to 0.030 mass% based on the total mass of the welding wire.)
In the present invention, B is actively added, i.e., at least one of a B compound and a B alloy is actively added. Conventionally, B is a component causing high-temperature cracking as in P, S, Bi. In particular, in welding using a Ni-based alloy flux-cored wire, since welding is performed at a high current and a high speed as compared with the shielded arc welding, special attention needs to be paid to high-temperature cracks, and it is often necessary to suppress B in order to obtain a sound weld metal.
However, the present inventors have conducted extensive studies to find that the chemical composition does not decrease in the high-temperature cracking property even if B is actively added (see fig. 1), and that a good range of tensile elongation at break can be obtained even when the weld metal contains a large amount of hydrogen due to exposure to a high-temperature and high-humidity environment.
Fig. 1 is a graph showing the relationship between the tensile elongation at break of the deposited metal and the occurrence of hot cracking under predetermined welding conditions, the sum of the B-equivalent amounts of either one or both of the B compound and the B alloy with respect to the total mass of the wire. The horizontal axis represents the total amount (mass%) of B in terms of B, and the vertical axis represents the tensile elongation at break (%) of the deposited metal. FIG. 1 is described in detail in the section of [ example ].
If the total of the B-equivalent amounts of either or both of the B compound and the B alloy in the wire is less than 0.005 mass% based on the total mass of the wire, when the weld metal contains a large amount of hydrogen, the tensile elongation at break of the weld metal decreases. When the total amount of the B-equivalent amount of either one or both of the B compound and the B alloy in the wire exceeds 0.030 mass% based on the total mass of the wire, high-temperature cracking is likely to occur. Therefore, the total of the B-equivalent amounts of either one or both of the B compound and the B alloy is 0.005 mass% or more and 0.030 mass% or less with respect to the total mass of the wire. In addition, the total amount of B in terms of one or both of the B compound and the B alloy in the wire is preferably 0.010 mass% or more with respect to the total mass of the wire from the viewpoint of obtaining a higher tensile elongation at break of the weld metal, and is preferably 0.020 mass% or less from the viewpoint of obtaining a higher high-temperature cracking property. As the compound B, B is mentioned2O3Oxides, etc. As the B alloy, Fe-B alloy, etc. may be mentioned. The B compound and the B alloy may be added to the flux.
(C in the entire welding wire: 0.050% by mass or less based on the total mass of the welding wire.)
C is an inevitable impurity present in the welding wire. If the C content in the wire exceeds 0.050 mass% with respect to the total mass of the wire, the high temperature crack resistance is lowered. Therefore, the C content is defined to be 0.050% by mass or less (including 0% by mass) with respect to the total mass of the wire. The C source in the welding wire of the present invention includes C which is an inevitable impurity contained in the Ni-based alloy forming the outer layer, the alloy which may be contained in the flux, and the slag forming agent, and the total amount of these is defined as the C content.
(Si in the entire welding wire: 0.15 mass% or less based on the total mass of the welding wire.)
Si is an inevitable impurity present in the wire. If the Si content in the wire exceeds 0.15 mass% with respect to the total mass of the wire, the high temperature cracking resistance is lowered. Therefore, the Si content is defined to be 0.15 mass% or less (including 0 mass%) with respect to the total mass of the wire. The content of Si in the wire of the present invention is the content of Si derived from metal Si and Si alloy dissolved in hydrochloric acid and nitric acid, and does not include Si derived from SiO not dissolved in acid2And the like.
(P in the entire welding wire: 0.015 mass% or less based on the total mass of the welding wire) (S in the entire welding wire: 0.010 mass% or less based on the total mass of the welding wire)
P and S are inevitable impurities present in the welding wire. If the P content in the wire exceeds 0.015 mass% and/or the S content exceeds 0.010 mass% based on the total mass of the wire, low-melting compounds of these elements and Ni are generated in grain boundaries, and the high-temperature cracking resistance is lowered. Therefore, the P content is defined as 0.015 mass% or less (including 0 mass%) with respect to the total mass of the wire, and the S content is defined as 0.010 mass% or less (including 0 mass%) with respect to the total mass of the wire.
(Ti in the entire welding wire: 0.20 mass% or less based on the total mass of the welding wire.)
Ti contained in the wire has a deoxidizing component similar to Al and dissolves in the molten metalThe oxygen storage amount decreases, the reaction of "C + O ═ CO (gas)" is suppressed, and the amount of generated pores is reduced. As described above, the present invention is a flux-cored wire to which B is positively added, but when B is positively added, the high-temperature cracking property of the wire tends to decrease. In the present invention, high-temperature cracking resistance is ensured by adding a predetermined amount of Al as described above, and high-temperature cracking resistance of the weld metal can be ensured more reliably by containing a predetermined amount of Ti in addition to Al. However, since excessive addition of Ti as described above deteriorates the high-temperature cracking resistance, the Ti content is limited to 0.20 mass% or less (including 0 mass%) based on the total mass of the wire in order to prevent this. In the present invention, the Ti source in the wire includes a Ni-based alloy forming the outer layer, metallic Ti that may be contained in the flux, an Fe — Ti alloy, and the like, and the content thereof is defined as the Ti content in terms of Ti. However, the Ti content is the content of Ti derived from a metal Ti or Ti alloy dissolved in sulfuric acid, and does not include Ti derived from TiO insoluble in sulfuric acid2And the like.
(Nb in the entire welding wire: 0.03 mass% or less based on the total mass of the welding wire.)
Nb is an inevitable impurity present in the wire. If the Nb content in the wire exceeds 0.03 mass% based on the total mass of the wire, the Nb combines with Ni to generate a low-melting-point compound, and therefore, the high-temperature cracking resistance is lowered. Therefore, the Nb content is defined to be 0.03 mass% or less (including 0 mass%) with respect to the total mass of the wire.
The remainder of the flux includes, for example, Ni, Cr, Mo, Mn, W, Fe, Al, Cu, N, Al2O3MgO, and the like. For example, Ni, Cr, Mo, Mn, W, Fe, and Al may be contained in the sheath, but may be added from the flux so as to satisfy a predetermined range with respect to the total mass of the wire. As the addition form, Ni, Cr, Mo, Mn, W, Fe, Al, Cu may be added in the form of respective metal powders, or may be added in the form of an iron alloy (Fe-alloy). C. Si, P, S, Nb are impurities in the flux.
(preferred form of the flux)
The welding wire of the present invention preferably contains TiO in the total mass of the above-described flux welding wire2: 3.0 to 10.0 mass% or less of SiO2: 0.1 to 4.0 mass% ZrO2: 0.5 to 2.0 mass% of a metal fluoride: 0.01 to 1.5 mass% in terms of F.
(TiO in flux)2: 3.0 to 10.0 mass% based on the total mass of the welding wire
TiO2Added for improved arc stability. As TiO2Sources, including rutile, ilmenite and the like, which are defined as TiO in the present invention2The amount is converted to a value. If TiO2If the amount of the flux is less than 3.0 mass% based on the total mass of the wire, the effect of stabilizing the arc cannot be obtained. On the other hand, if TiO2If the amount of slag exceeds 10.0 mass% based on the total mass of the wire, the amount of slag increases, and slag inclusion tends to occur in the welded portion. Thus, TiO2The amount is preferably 3.0 mass% or more and 10.0 mass% or less based on the total mass of the wire.
(SiO in flux)2: 0.1 to 4.0 mass% based on the total mass of the welding wire
SiO2The coating property is improved by adjusting the viscosity of the welding slag. As SiO2Sources including wollastonite, feldspar, and mica, among others. If SiO2If the total mass of the welding wire is less than 0.1 mass%, the covering property of the slag is insufficient, and the welding workability is deteriorated. On the other hand, if SiO2If the amount of slag exceeds 4.0 mass% based on the total mass of the welding wire, the amount of slag increases, and slag inclusion tends to occur. Thus, SiO2The amount is preferably 0.1 mass% or more and 4.0 mass% or less based on the total mass of the wire.
(ZrO in flux)2: 0.5 to 2.0 mass% based on the total mass of the welding wire
ZrO2In order to improve welding workability in a vertical posture by increasing a melting point of the slagAnd (4) adding. As ZrO2Sources including zircon sand, zircon powder, and the like. If ZrO of2If the amount of the slag is less than 0.5 mass% based on the total mass of the welding wire, the amount of the slag is insufficient, and the covering property of the slag is poor. On the other hand, if ZrO2If the amount of slag exceeds 2.0 mass% based on the total mass of the wire, the amount of slag increases, and slag inclusion tends to occur in the welded portion. Thus, ZrO2The amount is preferably 0.5 mass% or more and 2.0 mass% or less based on the total mass of the wire.
(metal fluoride in flux: 0.01 to 1.5 mass% in terms of F relative to the total mass of the wire.)
The metal fluoride has the effect of improving the arc stability and improving the fluidity of the slag. As the metal fluoride source, LiF, NaF, KF, Na are included3AlF6、K2SiF6、K2TiF6And the like. If the amount of the metal fluoride is less than 0.01 mass% in terms of F based on the total mass of the wire, the above-described effects cannot be sufficiently obtained, and the arc stability is lowered. On the other hand, if the metal fluoride exceeds 1.5 mass% in terms of F with respect to the total mass of the wire, the viscosity of the slag decreases, and the molten pool tends to sag in a vertical posture. Therefore, the metal fluoride is preferably 0.01 mass% or more and 1.5 mass% or less in terms of F with respect to the total mass of the wire.
(Jacket)
In the welding wire of the present invention, it is preferable that the sheath contains Ni: 60 mass% or more, Mo: 8 to 22 mass% of Cr: 1 to 15 mass%.
(Ni in the outer skin: 60 mass% or more based on the total mass of the outer skin)
The reason why the Ni-based alloy is used as the sheath metal is to suppress the addition of the alloy from the flux without impairing the uniformity of the weld metal and without causing an excessive filling amount of the flux. If the Ni content in the sheath is less than 60 mass%, the components other than Ni are inevitably increased, but Cr, Mo, etc. in the sheath deteriorate the wire drawability of the sheath, and the productivity is lowered. When the Ni content in the sheath exceeds 80 mass%, all components other than Ni must be added to the flux so that the flux filling ratio (the ratio of the flux mass to the total mass of the wire) becomes excessive. If the flux filling rate is excessive, the wire is difficult to be drawn in the manufacturing process, and productivity is reduced. Therefore, the Ni content in the outer skin is preferably suppressed to 80 mass% or less with respect to the total mass of the outer skin. Therefore, the Ni content in the sheath is preferably 60 mass% or more, and preferably 80 mass% or less, with respect to the total mass of the sheath.
(Mo in the outer skin: 8 to 22 mass% based on the total mass of the outer skin.)
Mo has an effect of securing the strength of the weld metal. If the Mo content in the sheath is less than 8 mass% with respect to the total mass of the sheath, Mo must be added from the flux to obtain the strength of the weld metal, and the flux filling rate becomes excessive. On the other hand, if the Mo content in the outer skin exceeds 22 mass% with respect to the total mass of the outer skin, the hot workability of the outer skin is lowered, and therefore, the outer skin is difficult to be formed. Therefore, the Mo content in the outer skin is preferably 8 mass% or more and 22 mass% or less with respect to the total mass of the outer skin.
(Cr in the outer skin is 1 to 15 mass% based on the total mass of the outer skin)
Cr has an effect of improving the corrosion resistance and strength of the weld metal. If the Cr content in the outer skin is less than 1 mass% with respect to the total mass of the outer skin, these effects cannot be obtained. On the other hand, if the Cr content in the outer skin exceeds 15 mass% with respect to the total mass of the outer skin, the hot workability of the outer skin is lowered, and therefore, the outer skin is difficult to be formed. Therefore, the Cr content in the outer skin is preferably 1 mass% or more and 15 mass% or less with respect to the total mass of the outer skin.
(other Components of the outer skin: Ti, Al, Mg)
Examples of other components of the outer skin include: ti: the outer skin is 0.002 mass% or more and 0.40 mass% or less with respect to the total mass of the outer skin; al: the outer skin is 0.03 to 0.40 mass% based on the total mass of the outer skin; mg: the amount of the sheath is 0.004 to 0.025 mass% based on the total mass of the sheath.
Ti, Al, and Mg in the outer shell have an effect of reducing the amount of dissolved oxygen in the molten metal as a deoxidizing component, suppressing the reaction of "C + O ═ CO (gas)", and reducing the amount of generated pores. When only one of Ti, Al, and Mg is contained as the other component of the outer skin, if the Ti content in the outer skin is less than 0.002 mass% with respect to the total mass of the outer skin, or the Al content is less than 0.03 mass% with respect to the total mass of the outer skin, or the Mg content is less than 0.004 mass% with respect to the total mass of the outer skin, the effect cannot be obtained. On the other hand, if the Ti content in the sheath exceeds 0.40 mass% with respect to the total mass of the sheath, or the Al content exceeds 0.40 mass% with respect to the total mass of the sheath, or the Mg content exceeds 0.025 mass% with respect to the total mass of the sheath, the hot workability of the sheath is lowered, and thus the shaping of the sheath becomes difficult. Therefore, the Ti content in the sheath is preferably 0.002 mass% or more and 0.40 mass% or less with respect to the total mass of the sheath, the Al content in the sheath is preferably 0.03 mass% or more and 0.40 mass% or less with respect to the total mass of the sheath, and the Mg content in the sheath is preferably 0.004 mass% or more and 0.025 mass% or less with respect to the total mass of the sheath.
(other Components of the outer skin: C)
C in the outer skin exists as an inevitable impurity. C in the outer skin becomes CO gas during welding and causes generation of blowholes. In order to avoid this, the C content in the outer skin is preferably 0.020% by mass or less (including 0% by mass) with respect to the total mass of the outer skin.
(other component of the outer skin: Si)
The Si in the sheath is present as an unavoidable impurity. Si in the outer skin generates a low-melting-point compound during welding, and therefore, high-temperature cracking resistance is reduced. In order to avoid this, the Si content in the sheath is preferably 0.15 mass% or less (including 0 mass%) with respect to the total mass of the sheath.
(other ingredients in the outer skin: remainder)
The remainder may contain, for example: mn: 4.0 mass% or less of Fe with respect to the total mass of the outer skin: 7.0 mass% or less with respect to the total mass of the outer skin, W: the content of the inorganic particles is 4.0 mass% or less (including 0 mass%) based on the total mass of the outer skin. However, if the Mn content in the outer skin exceeds 4.0 mass% with respect to the total mass of the outer skin, or the W content exceeds 4.0 mass%, the hot workability of the outer skin is lowered, and therefore, the outer skin is difficult to be formed. If the Fe content in the outer skin exceeds 7.0 mass%, the high temperature cracking resistance is lowered.
Further, as other components in the outer skin, inevitable impurities may be cited. Examples of the inevitable impurities include P, S, Cu, Nb, V, N, and the like, in addition to C, Si described above. The allowable content of P was 0.010 mass%, the allowable content of S was 0.010 mass%, the allowable content of Cu was 0.01 mass%, the allowable content of Nb was 0.10 mass%, the allowable content of V was 0.10 mass%, and the allowable content of N was 0.010 mass% (both inclusive of 0 mass%).
In the welding wire of the present invention, the flux filling rate is preferably 15 mass% or more and 30 mass% or less, more preferably 20 mass% or more and 25 mass% or less, with respect to the total mass of the welding wire.
The welding wire of the present invention has the above-described composition, and therefore, is less likely to cause high-temperature cracking during welding, and can provide a weld metal having good tensile ductility even when the weld metal contains a large amount of hydrogen due to exposure to a high-temperature and high-humidity environment or the like.
Therefore, the welding wire of the present invention can be suitably used for welding low-temperature steels such as 9% Ni steel and various high-Ni alloys using Ar + CO2Gas shielded arc welding of mixed gases, and the like.
Examples
Hereinafter, examples satisfying the requirements of the present invention and comparative examples not satisfying the requirements of the present invention will be compared, and a welding wire of the present invention will be specifically described.
A belt of Ni-based alloy having a composition shown in Table 1 and having a thickness of 0.4mm and a width of 9.0mm was bent to form cylindrical outer skins (Nos. A and B). Flux containing flux components (nos. i and II) shown in table 2 was contained in these sheaths, and Ni-based alloy flux-cored wires (nos. 1 to 18) having compositions shown in table 3 were produced as a whole (flux filling ratio: 20 to 25%). The wire was drawn into a diameter of 1.2mm, and then heated by energization to reduce the water content in the wire to 400ppm or less, thereby obtaining a test wire.
TABLE 1
[ TABLE 1]
[ TABLE 2]
The metal component of 1) is Ni, Cr, Mo, Mn, W, Fe, Al and Cu.
[ TABLE 3 ]
No.1 to No.18 test wires were used to perform [1] a room temperature tensile test of deposited metal and [2] a FISCO crack test as a high temperature crack test.
[1] Room temperature tensile test of deposited metal
The tensile elongation at break of the deposited metal was measured and determined by performing a room temperature tensile test of the deposited metal (JIS Z3111: 2005, "method for tensile and impact test of deposited metal"). The room temperature tensile test of the deposited metal was performed in the following manner.
As shown in fig. 2, a bevel was formed on the bevel face of an SM490 steel sheet having a thickness of 20mm such that the bevel angle was 45 °, and the bevel was subjected to a pre-weld (welding) with a test wire to form a pre-weld layer 2. Then, the base materials 1 subjected to the pre-edge welding are arranged so that the root gap becomes 12mm, and the shim plate 3 (steel material) whose surface is also subjected to the pre-edge welding is arranged on the side where the groove is narrow. The groove was cut in accordance with JIS Z3111: 2005, welding to produce a deposited metal. Then, tensile test 4 (A1 in JIS Z3111: 2005) was collected from the produced deposited metal in accordance with the procedure shown in FIG. 3, and the above test was carried out.
The welding conditions comprise welding current of 200A, voltage of 29V and welding speed of 300-400 mm/min. Since the wire was simulated to be excessively hygroscopic and about 10ppm hydrogen was contained in the deposited metal, the wire was measured using a wire electrode set at 8: 2 volume ratio of 98% Ar-2% H2Gas and 100% CO2A shielding gas for the gas. The flow rate of the shielding gas was 25L/min.
The criterion for determining the tensile elongation at break of the deposited metal is a numerical value (%) showing the tensile elongation at break, 40% or more is excellent, 35% or more and less than 40% is good, 30% or more and less than 35% is Δ (no practical problem), and less than 30% is x (no practical problem). The tensile elongation at break of the deposited metal was ∈ and ∘ as good, and Δ and × as bad. Although Δ has no practical problem at all, Δ is a failure because the object of the present invention is to improve a product having higher performance.
[2] High temperature crack test
The high temperature cracking resistance was evaluated by conducting a high temperature cracking test (JIS Z3155: 1993 "C-clamp restraint butt weld cracking test Method" (Method of FISCO test)). The high temperature cracking test was performed in the following manner.
Using the base material (20 mm in thickness, 125mm in width, and 300mm in length) having the composition shown in Table 4, the slope was formed to half the thickness so that the groove angle of the base material 10 became 60 degrees, as shown in FIG. 4. Then, the distance between the base material 10 and the base material 10 was adjusted to 2mm, and the thickness was adjusted in accordance with JIS Z3155: 1993. For the welding, a test wire was used, and a single pass welding was performed by an automatic welding machine to confirm the presence or absence of cracks in the weld metal portions other than the arcing (japanese text: ス タ ー ト) and the craters.
[ TABLE 4 ]
The welding conditions for the high temperature crack test were as follows: current 280A, voltage 34V, welding speed is 500mm/min, and 80% Ar-20% CO is used as protective gas2The flow rate of the shielding gas was 25L/min.
In the determination of the high temperature crack test, the total crack length of the weld metal portion excluding the arcing and the crater was regarded as "excellent" (excellent), the total crack length thereof was regarded as "good" (good) when it exceeded 0mm and was less than 1mm, the total crack length thereof was regarded as "Δ" (practically no problem), and the total crack length thereof was regarded as "poor" (poor) when it was not less than 1mm and was not less than 3 mm. The high temperature cracking resistance was ∈ and ℃ ∈ and Δ and × were no. In the present invention, Δ is regarded as a failure for the same reason as described above.
The results of determination of tensile elongation at break and the results of determination of high-temperature crack resistance of the deposited metal were regarded as excellent, and the results of determination of either were regarded as good. On the other hand, the case where at least one of the determination result of the tensile elongation at break and the determination result of the high temperature crack resistance of the weld metal is Δ or × is taken as the overall evaluation x (failure).
Table 5 shows the results of determination of tensile elongation at break, the results of determination of high-temperature crack resistance, and the overall evaluation of the deposited metal.
Fig. 1 is a graph showing the results of measurement of tensile elongation at break and determination of high-temperature cracking resistance of the deposited metal in the obtained test wires of nos. 1 to 12 and 14 to 18, and the sum of the amounts of B converted in either one or both of the B compound and the B alloy with respect to the total mass of the wire. As is clear from fig. 1: if the total amount of B (the total amount of either or both of the B compound and the B alloy) is 0.030 mass% or less, high-temperature cracking does not occur even when welding is performed under the welding conditions (280A-34V-500 mm/min.) of the high-temperature cracking test, and if the total amount of B exceeds 0.030 mass%, high-temperature cracking occurs.
[ TABLE 5 ]
As shown in table 5, the test wires of nos. 1 to 6 satisfying the requirements of the present invention both had good results in terms of tensile elongation at break and high-temperature crack resistance of the deposited metal, and had a comprehensive evaluation of "excellent" or "good". In particular, in the test wires of nos. 1 to 4, since the total of the B equivalent amounts of either one or both of the B compound and the B alloy with respect to the total mass of the wire is in a preferable range, the results of the determination of the tensile elongation at break and the results of the determination of the high temperature crack resistance of the deposited metal are both excellent, and the overall evaluation is also excellent. That is, the test wires of nos. 1 to 4 were confirmed to be more preferable.
On the other hand, the results of the No.7 to 18 test wires that do not satisfy the requirements of the present invention are: the tensile elongation at break and the high temperature cracking resistance of the deposited metal were not satisfactory. The Gross scores of the test wires of Nos. 7 to 18 were all X.
Specifically, in the test wires of nos. 7 to 10, the total of B equivalent amounts of either or both of the B compound and the B alloy with respect to the total mass of the wire was too low, and therefore the tensile elongation at break of the deposited metal was reduced.
In the test wires of nos. 11 to 13, the total of the B equivalent amounts of either or both of the B compound and the B alloy with respect to the total mass of the wire was too high, and therefore, the high-temperature cracking resistance was lowered.
In the test wire of No.14, the Al content based on the total mass of the wire was too high, and the high-temperature cracking resistance did not reach the acceptable level.
In the test wire of No.15, the Ti content based on the total mass of the wire was too high, and therefore the high-temperature crack resistance did not reach the acceptable level.
In the test wire of No.16, since both the Si content and the S content were too high relative to the total mass of the wire, the high-temperature cracking resistance did not reach the acceptable level.
In the test wire of No.17, the C content and the P content were too high relative to the total mass of the wire, and therefore the high-temperature cracking resistance did not reach the acceptable level.
In the test wire of No.18, the Nb content was too high based on the total mass of the wire, and the high temperature cracking resistance was not satisfactory.
Although the welding wire of the present invention has been described in detail with reference to the embodiments and examples, the gist of the present invention is not limited to these contents, and the scope of the right of the present invention should be broadly construed based on the scope of the claims. It is needless to say that the contents of the present invention can be widely changed or modified based on the above description.
Description of the symbols
1. 10 base material
2 pre-edge-stacking welding layer
3 backing board
4 tensile test piece
Claims (2)
1. A Ni-based alloy flux-cored wire excellent in high-temperature crack resistance and tensile elongation at break at room temperature, characterized in that the Ni-based alloy flux-cored wire is a Ni-based alloy flux-cored wire in which a flux is enclosed in a sheath, and the composition of the entire wire is such that the total mass of the wire is
Ni: 50 to 70 mass% inclusive,
Cr: 1 to 15 mass% inclusive,
Mo: 10 to 20 mass% inclusive,
Mn: 1.5 to 5.5 mass% inclusive,
W: 1.5 to 5.0 mass% inclusive,
Fe: 2.0 to 8.0 mass%,
Al: 0.01 to 0.40 mass% inclusive,
The total of the B-equivalent amounts of either one or both of the B compound and the B alloy: 0.005 to 0.030 mass%,
C: 0.050% by mass or less,
Si: 0.15 mass% or less,
P: less than 0.015 mass%,
S: 0.010 mass% or less,
Ti: 0.20 mass% or less,
Nb: 0.03 mass% or less of a surfactant,
And the flux contains in relation to the total mass of the welding wire
TiO2: 3.0 to 10.0 mass% inclusive,
SiO2: 0.1 to 4.0 mass% inclusive,
ZrO2: 0.5 to 2.0 mass% inclusive,
Metal fluoride: 0.01 to 1.5 mass% in terms of F.
2. The Ni-based alloy flux-cored wire of claim 1, wherein the sheath contains relative to the total mass of the sheath
Ni: 60 mass% or more,
Mo: 8 to 22 mass% inclusive,
Cr: 1 to 15 mass%.
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| JP7010675B2 (en) * | 2017-11-24 | 2022-01-26 | 株式会社神戸製鋼所 | Flux-filled wire for gas shielded arc welding and welding method |
| JP7244340B2 (en) * | 2019-04-22 | 2023-03-22 | 株式会社神戸製鋼所 | Ni-based alloy flux-cored wire |
| CN109894772B (en) * | 2019-04-29 | 2021-03-19 | 重庆大学 | Flux-cored wire for skin layer of large-scale hot-forging die with fist-shaped bionic structure and preparation method of flux-cored wire |
| JP7401345B2 (en) * | 2020-02-28 | 2023-12-19 | 株式会社神戸製鋼所 | Ni-based alloy flux-cored wire |
| CN113478115B (en) * | 2021-06-21 | 2022-12-09 | 西安理工大学 | Arc cladding flux-cored wire and preparation method thereof |
| CN115255718B (en) * | 2022-09-06 | 2023-08-18 | 兰州理工大学 | Nickel-based alloy welding wire and preparation method and application thereof |
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|---|---|---|---|---|
| JP2000117488A (en) * | 1998-08-10 | 2000-04-25 | Kobe Steel Ltd | Ni-BASED ALLOY FLUX-CORED WIRE |
| CN101036963A (en) * | 2006-03-16 | 2007-09-19 | 联合工艺公司 | Nickel alloy welding wire |
| CN103358050A (en) * | 2012-03-30 | 2013-10-23 | 株式会社日立制作所 | An Ni-based alloy for a welding material, a welding wire and a welding rod employing the material, and a welding power |
| CN104588912A (en) * | 2013-10-31 | 2015-05-06 | 株式会社神户制钢所 | Ni based alloy flux cored wire |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPS6380994A (en) * | 1986-06-17 | 1988-04-11 | Kobe Steel Ltd | Ni base flux-cored wire for gas shielded arc welding |
| JPH09314382A (en) | 1996-05-29 | 1997-12-09 | Kobe Steel Ltd | Flux-cored wire for welding ni alloy |
| JP4154885B2 (en) * | 2000-11-16 | 2008-09-24 | 住友金属工業株式会社 | Welded joint made of Ni-base heat-resistant alloy |
| JP4173076B2 (en) | 2003-08-18 | 2008-10-29 | 株式会社神戸製鋼所 | Ni-based alloy flux cored wire |
| JP4970802B2 (en) * | 2006-02-02 | 2012-07-11 | 株式会社神戸製鋼所 | Ni-based alloy flux cored wire |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000117488A (en) * | 1998-08-10 | 2000-04-25 | Kobe Steel Ltd | Ni-BASED ALLOY FLUX-CORED WIRE |
| CN101036963A (en) * | 2006-03-16 | 2007-09-19 | 联合工艺公司 | Nickel alloy welding wire |
| CN103358050A (en) * | 2012-03-30 | 2013-10-23 | 株式会社日立制作所 | An Ni-based alloy for a welding material, a welding wire and a welding rod employing the material, and a welding power |
| CN104588912A (en) * | 2013-10-31 | 2015-05-06 | 株式会社神户制钢所 | Ni based alloy flux cored wire |
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| JP2017030018A (en) | 2017-02-09 |
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