JP5763859B1 - Ni-based alloy flux cored wire - Google Patents
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 56
- 239000000956 alloy Substances 0.000 title claims abstract description 56
- 230000004907 flux Effects 0.000 title claims abstract description 44
- 239000000843 powder Substances 0.000 claims abstract description 53
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- 229910052751 metal Inorganic materials 0.000 claims description 43
- 239000002184 metal Substances 0.000 claims description 43
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 19
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical group [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 19
- 229910052720 vanadium Inorganic materials 0.000 claims description 13
- 229910052757 nitrogen Inorganic materials 0.000 claims description 10
- 229910004762 CaSiO Inorganic materials 0.000 claims description 9
- 229910052758 niobium Inorganic materials 0.000 claims description 9
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 229910052715 tantalum Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 5
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- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 238000006243 chemical reaction Methods 0.000 claims description 2
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- 238000003466 welding Methods 0.000 abstract description 76
- 229910052759 nickel Inorganic materials 0.000 abstract description 18
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 abstract 2
- 229910052882 wollastonite Inorganic materials 0.000 abstract 1
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- 238000005336 cracking Methods 0.000 description 40
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 12
- 239000002893 slag Substances 0.000 description 12
- 239000010955 niobium Substances 0.000 description 11
- 229910000831 Steel Inorganic materials 0.000 description 9
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- 238000011156 evaluation Methods 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
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- 229910004261 CaF 2 Inorganic materials 0.000 description 2
- 229910004298 SiO 2 Inorganic materials 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
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- 150000001247 metal acetylides Chemical class 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
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- 229910016569 AlF 3 Inorganic materials 0.000 description 1
- 229910016036 BaF 2 Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910019589 Cr—Fe Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 101100513612 Microdochium nivale MnCO gene Proteins 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
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- 238000011835 investigation Methods 0.000 description 1
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- PQXKHYXIUOZZFA-UHFFFAOYSA-M lithium fluoride Inorganic materials [Li+].[F-] PQXKHYXIUOZZFA-UHFFFAOYSA-M 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
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- 239000011733 molybdenum Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
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- 239000001301 oxygen Substances 0.000 description 1
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- 239000002994 raw material Substances 0.000 description 1
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- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Inorganic materials [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000004544 sputter deposition Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
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- 239000011593 sulfur Substances 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
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Abstract
【課題】 全姿勢溶接において良好な作業性を有し、耐ブローホール性、耐高温割れ性を高めることができるＮｉ基合金フラックス入りワイヤを提供する。【解決手段】 ＮｉまたはＮｉ基合金を主成分とする外皮内に、非金属粉末と金属粉末を含むフラックス粉末を充填する。フラックス粉末中の非金属粉末は、フラックス入りワイヤの全質量に対して、８００℃以上の温度で焼成したＴｉＯ2を４〜６質量％、合成された複酸化物であるＣａＳｉＯ3を０．１〜３質量％、ＺｒＯ2を０．５〜２質量％、金属弗化物を０．１〜２質量％、炭酸塩を０．０５〜１質量％、Ｔｉ及びＡｌのいずれか一種または両種もしくはＴｉ及びＡｌの合金が、フラックス入りワイヤの全質量に対するＴｉ及びＡｌの質量％換算値の合計で０．０５〜１質量％含有する。【選択図】図１PROBLEM TO BE SOLVED: To provide a Ni-based alloy flux cored wire having good workability in all-position welding and capable of improving blow hole resistance and hot crack resistance. SOLUTION: Flux powder containing non-metallic powder and metallic powder is filled in the outer skin mainly composed of Ni or Ni-based alloy. The non-metallic powder in the flux powder is composed of 4 to 6% by mass of TiO2 baked at a temperature of 800 ° C. or higher and 0.1 to 3 of CaSiO3, which is a synthesized double oxide, with respect to the total mass of the flux-cored wire. % By mass, 0.5-2% by mass of ZrO2, 0.1-2% by mass of metal fluoride, 0.05-1% by mass of carbonate, one or both of Ti and Al, or Ti and Al This alloy contains 0.05 to 1% by mass as a total of the mass% converted values of Ti and Al with respect to the total mass of the flux-cored wire. [Selection] Figure 1
Description
本発明は、耐食性、耐熱性が要求される構造物及びＬＮＧタンク等の極低温構造物の溶接に使用されるＮｉ基合金フラックス入りワイヤに関するものである。 The present invention relates to a Ni-based alloy flux-cored wire used for welding a structure requiring corrosion resistance and heat resistance and a cryogenic structure such as an LNG tank.
フラックス入りワイヤを用いるガスシールドアーク溶接法は、被覆アーク溶接法、ＴＩＧ溶接法と比較して、種々の点で溶接効率がよい。そのため、近年、その適用が拡大しており、Ｎｉ基合金においても、フラックスを用いたガスシールドアーク溶接法の適用が拡大している。 The gas shielded arc welding method using a flux-cored wire has better welding efficiency in various respects as compared with the coated arc welding method and the TIG welding method. Therefore, in recent years, the application has been expanded, and the application of the gas shield arc welding method using a flux has also been expanded in Ni-based alloys.
例えば、９％Ｎｉ鋼のような極低温用鋼の溶接に、Ｎｉ基合金フラックス入りワイヤが使用されつつある。具体的には、従来から行われている屋根骨等のタンク本体以外の適用のみならず、ＬＮＧ貯蔵タンクの工期の短縮化を考慮して、タンク本体への適用も検討され始めている。特に、タンク本体への適用に際しては、溶接部の更なる健全性向上が要求される。 For example, Ni-based alloy flux-cored wires are being used for welding cryogenic steels such as 9% Ni steel. Specifically, in addition to conventional applications other than the tank main body such as roof bone, application to the tank main body is being considered in consideration of shortening the construction period of the LNG storage tank. In particular, when applied to the tank body, further improvement in the soundness of the welded portion is required.
特開平８−３０９５８３号（特許文献１）には、９％Ｎｉ鋼用フラックス入りワイヤを極低温用鋼の溶接に用いた場合の耐割れ性、全姿勢作業性等に関する知見が示されている。また、特開平１０−１８０４８６号（特許文献２）、特開平１０−２９６４８６号（特許文献３）には、Ｎｉ基合金外皮内にフラックス粉末が充填されたＮｉ基合金フラックス入りワイヤが示されている。フラックス粉末には、Ｍｏ等の金属粉末に加えて、非金属粉末としてＴｉＯ2等の金属酸化物やＣａＦ2等の金属弗化物が用いられている。 Japanese Patent Laid-Open No. 8-309583 (Patent Document 1) discloses knowledge about crack resistance, all-position workability and the like when a 9% Ni steel flux cored wire is used for welding cryogenic steel. . Japanese Patent Laid-Open No. 10-180486 (Patent Document 2) and Japanese Patent Laid-Open No. 10-296486 (Patent Document 3) show a Ni-based alloy flux-cored wire in which a Ni-based alloy outer shell is filled with flux powder. Yes. The flux powder, in addition to metal powder such as Mo, a metal oxide or metal fluoride such as CaF 2 of TiO 2 or the like is used as a metal powder.
しかしながら、特許文献１に開示されたＮｉ基合金フラックス入りワイヤは、炭酸塩量が多く、全姿勢用ワイヤとしての溶接作業性（スパッタ防止、スラグ剥離性向上等）が充分ではない。また、特許文献２及び特許文献３に開示されたＮｉ基合金フラックス入りワイヤでは、溶接性能のうち耐高温割れ性については開示されているものの、耐ブローホール性については何ら開示されていない。
However, the Ni-based alloy flux cored wire disclosed in
このように、従来のＮｉ基合金フラックス入りワイヤでは、全姿勢溶接で要求される溶接性能および溶接作業性等の諸条件を全て満たすことはできなかった。 Thus, the conventional Ni-based alloy flux cored wires could not satisfy all conditions such as welding performance and welding workability required in all-position welding.
本発明の目的は、全姿勢溶接におけるアーク安定性、スパッタ防止、ビード形状、スラグ剥離性を改善し、さらに耐ブローホール性、耐高温割れ性等の諸性能を高めることができるＮｉ基合金フラックス入りワイヤを提供することにある。 The object of the present invention is to improve the arc stability, spatter prevention, bead shape, slag peelability in all-position welding, and further improve various performances such as blowhole resistance and hot crack resistance. It is to provide a corrugated wire.
本発明のＮｉ基合金フラックス入りワイヤは、ＮｉまたはＮｉ基合金を主成分とする外皮と、外皮内に充填されたフラックス粉末とを備えている。フラックス粉末には、非金属粉末と金属粉末が含有されている。フラックス粉末中の非金属粉末は、フラックス入りワイヤの全質量に対して、８００℃以上の温度で焼成したＴｉＯ2を４〜６質量％、合成された複酸化物としてＣａＳｉＯ3を０．１〜３質量％、ＺｒＯ2を０．５〜２質量％、金属弗化物を０．１〜２質量％、炭酸塩を０．０５〜１質量％、それぞれ含有している。また、フラックス粉末中の金属粉末は、チタン（Ｔｉ）及びアルミニウム（Ａｌ）のいずれか一種または両種からなる金属、もしくはＴｉ及びＡｌの合金が、フラックス入りワイヤの全質量に対するＴｉ及びＡｌの質量％換算値の合計で０．０５〜１質量％含有している。 The Ni-based alloy flux-cored wire of the present invention includes an outer skin mainly composed of Ni or an Ni-based alloy, and flux powder filled in the outer skin. The flux powder contains non-metallic powder and metallic powder. The non-metallic powder in the flux powder is composed of 4 to 6% by mass of TiO 2 baked at a temperature of 800 ° C. or higher with respect to the total mass of the flux-cored wire, and 0.1 to 0.1 of CaSiO 3 as a synthesized double oxide. 3% by mass, 0.5-2% by mass of ZrO 2 , 0.1-2% by mass of metal fluoride and 0.05-1% by mass of carbonate are contained. Further, the metal powder in the flux powder is a metal composed of one or both of titanium (Ti) and aluminum (Al), or an alloy of Ti and Al, and the mass of Ti and Al with respect to the total mass of the flux-cored wire. It contains 0.05-1 mass% in the sum total of% conversion value.
このような非金属粉末と金属粉末を含むフラックス粉末を、ＮｉまたはＮｉ基合金を主成分とする外皮に充填したＮｉ基合金フラックス入りワイヤは、全姿勢溶接における諸性能（アーク安定性、スパッタ防止、ビード形状、スラグ剥離性、耐ブローホール性、耐高温割れ性、低温靱性等）を同時に維持することができる。 Ni-based alloy flux-cored wires filled with such a non-metallic powder and a flux powder containing metal powder in the outer skin mainly composed of Ni or Ni-based alloy have various performances (arc stability, spatter prevention) , Bead shape, slag peelability, blowhole resistance, hot crack resistance, low temperature toughness, etc.) can be maintained at the same time.
なお、Ｔｉ及びＡｌの合金としては、Ｔｉ及びＡｌを含むＦｅ基合金粉末を用いることができる。このようなＦｅ基合金粉末を用いても、全姿勢溶接におる諸性能を発揮することができ、しかもこのＦｅ基合金粉末は安価であるため、フラックス入りワイヤの製造コストを小さくすることができる。 As an alloy of Ti and Al, Fe-based alloy powder containing Ti and Al can be used. Even when such an Fe-based alloy powder is used, various performances in all-position welding can be exhibited, and since this Fe-based alloy powder is inexpensive, the manufacturing cost of the flux-cored wire can be reduced. .
また、本発明のＮｉ基合金フラックス入りワイヤ中の水分量は、３００ｐｐｍ以下に制限することが好ましい。フラックス入りワイヤ中の水分量をこのような数値範囲に調整することにより、全姿勢溶接における諸性能を確実に向上させることができる。なお、このような水分量の規定は、Ｎｉ基合金フラックス入りワイヤにおいて、発明者らが、充填フラックスの組成及びフラックス入りワイヤ中の水分量が溶接金属性能へ及ぼす影響を調査し、その調査結果により得られた知見を基になされたものである。 Moreover, it is preferable to restrict | limit the moisture content in the Ni-based alloy flux cored wire of this invention to 300 ppm or less. By adjusting the amount of moisture in the flux-cored wire to such a numerical range, various performances in all-position welding can be reliably improved. In addition, in the regulation of such moisture amount, in the Ni-based alloy flux-cored wire, the inventors investigated the influence of the composition of the filling flux and the moisture content in the flux-cored wire on the weld metal performance, and the results of the investigation It was made based on the knowledge obtained by this.
なお、本発明のＮｉ基合金フラックス入りワイヤを用いて作製した溶着金属は、その溶着金属中に、ケイ素（Ｓｉ）：０．１１〜０．３６質量％、マンガン（Ｍｎ）：１．３８〜１．７２質量％、クロム（Ｃｒ）：１２．１〜１４．８質量％、モリブデン（Ｍｏ）：１２．０〜１４．６質量％、タングステン（Ｗ）：１．７〜３．９質量％、アルミニウム（Ａｌ）：０．０４〜０．３１質量％、チタン（Ｔｉ）：０．０１〜０．１７質量％、鉄（Ｆｅ）：４．６〜６．９質量％、バナジウム族元素としてバナジウム（Ｖ）、ニオブ（Ｎｂ）及びタンタル（Ｔａ）の少なくとも１種以上：各０．１２〜１．００質量％、不可避不純物として炭素（Ｃ）：０．０３０質量％未満、リン（Ｐ）：０．０１０質量％未満、硫黄（Ｓ）：０．０１０質量％未満及び窒素（Ｎ）：０．０４０質量％未満が含まれており、残部がニッケル（Ｎｉ）である。また、バナジウム族元素の含有量は、下記（１）乃至（３）式の少なくとも１式の条件を満たしている。なお、下記（１）乃至（３）式は、Ｖ、Ｎｂ及びＴａが属するバナジウム族元素と不可避不純物として含まれるＣ及びＮとの関係で成立する式である。 In addition, the weld metal produced using the Ni-based alloy flux cored wire of the present invention includes silicon (Si): 0.11 to 0.36 mass%, manganese (Mn): 1.38 to the weld metal. 1.72 mass%, chromium (Cr): 12.1 to 14.8 mass%, molybdenum (Mo): 12.0 to 14.6 mass%, tungsten (W): 1.7 to 3.9 mass% , Aluminum (Al): 0.04 to 0.31 mass%, titanium (Ti): 0.01 to 0.17 mass%, iron (Fe): 4.6 to 6.9 mass%, as vanadium group element At least one or more of vanadium (V), niobium (Nb) and tantalum (Ta): 0.12 to 1.00% by mass of each, carbon (C) as an inevitable impurity: less than 0.030% by mass, phosphorus (P) : Less than 0.010 mass%, sulfur (S): 0.010 mass Less and nitrogen (N): less than 0.040 wt% are included, the balance nickel (Ni). Further, the content of the vanadium group element satisfies the condition of at least one of the following formulas (1) to (3). The following formulas (1) to (3) are formulas established by the relationship between the vanadium group element to which V, Nb and Ta belong and C and N contained as inevitable impurities.
Ｖ≧（４×Ｃ＋３×Ｎ） ・・・・・（１）
Ｎｂ≧（７×Ｃ＋６×Ｎ） ・・・・・（２）
Ｔａ≧（１５×Ｃ＋１２×Ｎ）・・・・・（３）
溶着金属がこのような条件を満たす場合には、全姿勢溶接における諸性能を維持した上で、該諸性能の中でも特に耐高温割れ性および低温靱性を向上させることができる。
V ≧ (4 × C + 3 × N) (1)
Nb ≧ (7 × C + 6 × N) (2)
Ta ≧ (15 × C + 12 × N) (3)
When the weld metal satisfies such a condition, it is possible to improve the hot crack resistance and the low temperature toughness among the various performances while maintaining various performances in all-position welding.
以下、本発明のＮｉ基合金フラックス入りワイヤの実施の形態について詳細に説明する。本例のＮｉ基合金フラックス入りワイヤでは、ＮｉまたはＮｉ基合金を主成分とする外皮内にフラックス粉末及び金属粉末が充填されている。フラックス粉末には、フラックス入りワイヤの全質量に対して、８００℃以上の温度で焼成したＴｉＯ2が４〜６質量％、合成された複酸化物としてＣａＳｉＯ3が０．１〜３質量％、ＺｒＯ2が０．５〜２質量％、金属弗化物が０．１〜２質量％、炭酸塩が０．０５〜１質量％、それぞれ含有されている。また、金属粉末には、Ｔｉ及びＡｌのいずれか一種または両種からなる金属、もしくはＴｉ及びＡｌの合金が、フラックス入りワイヤの全質量に対するＴｉ及びＡｌの質量％換算値の合計で０．０５〜１質量％、含有されている。 Hereinafter, embodiments of the Ni-based alloy flux cored wire of the present invention will be described in detail. In the Ni-based alloy flux-cored wire of this example, flux powder and metal powder are filled in the outer skin mainly composed of Ni or Ni-based alloy. In the flux powder, 4 to 6% by mass of TiO 2 baked at a temperature of 800 ° C. or higher with respect to the total mass of the flux-cored wire, 0.1 to 3% by mass of CaSiO 3 as a synthesized double oxide, ZrO 2 is contained in an amount of 0.5 to 2% by mass, metal fluoride is contained in an amount of 0.1 to 2% by mass, and carbonate is contained in an amount of 0.05 to 1% by mass. Further, in the metal powder, a metal composed of one or both of Ti and Al, or an alloy of Ti and Al is 0.05 in terms of the total mass converted value of Ti and Al with respect to the total mass of the flux-cored wire. ˜1% by mass is contained.
フラックス入りワイヤの外皮には、ＮｉまたはＮｉ基合金を使用する。Ｎｉ基合金としては、Ｎｉ−Ｃｒ合金、Ｎｉ−Ｃｒ−Ｆｅ合金、Ｎｉ−Ｃｒ−Ｍｏ合金等を用いることができる。なお、Ｎｉとは純Ｎｉをいう。 Ni or a Ni-based alloy is used for the outer skin of the flux-cored wire. As the Ni-based alloy, a Ni—Cr alloy, a Ni—Cr—Fe alloy, a Ni—Cr—Mo alloy, or the like can be used. Ni refers to pure Ni.
次にフラックス粉末に含まれる非金属粉末中のＴｉＯ2は、アークの安定性やスラグの被包性が良好となるため添加する。なお、ＴｉＯ2の添加量が少ないとこれらの特性が充分に得られず、ＴｉＯ2の添加量が多いと耐高温割れ性やスラグ剥離性が低下する傾向があるため、ＴｉＯ2の添加量は４〜６質量％に規制する。さらに、本例で用いるＴｉＯ2は、天然原料であるＴｉＯ2を８００℃以上の温度で焼成し、天然のＴｉＯ2に存在する結晶化した水分を低減させている。このように焼成したＴｉＯ2を用いることにより、良好な溶接金属の機械的性質や、溶接割れ防止効果が得られる。また、フラックス入りワイヤ中の水分量低減に寄与でき、フラックス入りワイヤ中の水分量を３００ｐｐｍ以下に制御することができるため、耐ブローホール性に優れたフラックス入りワイヤが得られる。 Next, TiO 2 in the non-metallic powder contained in the flux powder is added because the arc stability and slag encapsulation are improved. Incidentally, the addition amount of TiO 2 is less not these characteristics are sufficiently obtained, since the amount of TiO 2 is large and the resistance to hot cracking and the slag removability tends to decrease, the addition amount of TiO 2 is It is restricted to 4 to 6% by mass. Furthermore, the TiO 2 used in this example is obtained by firing TiO 2 , which is a natural raw material, at a temperature of 800 ° C. or higher to reduce crystallized water present in natural TiO 2 . By using TiO 2 thus fired, good mechanical properties of weld metal and an effect of preventing weld cracking can be obtained. Moreover, since it can contribute to the moisture content reduction in a flux cored wire and the moisture content in a flux cored wire can be controlled to 300 ppm or less, the flux cored wire excellent in blowhole resistance can be obtained.
合成された複酸化物であるＣａＳｉＯ3は、ＳｉＯ2を添加した場合と比較して溶接金属中の酸素量を下げることができ、溶接金属の耐高温割れ性や低温靱性を高める効果がある。ただし、ＣａＳｉＯ3の添加量は、少ないと上記の効果が得られず、多いとアークが不安定となりスパッタが増加する傾向があるため、０．１〜３質量％に規制する。 CaSiO 3 , which is a synthesized double oxide, can reduce the amount of oxygen in the weld metal as compared with the case where SiO 2 is added, and has the effect of increasing the hot crack resistance and low temperature toughness of the weld metal. However, if the addition amount of CaSiO 3 is small, the above effect cannot be obtained. If the addition amount is large, the arc becomes unstable and the sputtering tends to increase.
ＺｒＯ2は、スラグの粘性や凝固速度を調整するため添加する。ＺｒＯ2の添加量が適正な場合は、全姿勢溶接においてビードの垂れが抑制され、ビード形状が良好になる。なお、添加量が不足するとその効果が得られず、また添加量が多すぎるとスラグの粘性過剰や凝固速度の増加により、溶接金属中にブローホールが多く残存する傾向がある。そのため、ＺｒＯ2の添加量は、０．５〜２質量％に規制する。 ZrO 2 is added to adjust the viscosity and solidification rate of the slag. When the amount of ZrO 2 added is appropriate, bead sag is suppressed in all-position welding, and the bead shape is improved. In addition, when the addition amount is insufficient, the effect cannot be obtained, and when the addition amount is too large, there is a tendency that many blowholes remain in the weld metal due to excessive viscosity of the slag and increase in the solidification rate. Therefore, the amount of ZrO 2 added is restricted to 0.5-2% by mass.
金属弗化物は、溶融温度が低く、スラグの流動性や剥離性を向上させる。また、耐ブローホール性や溶融金属の精錬機能により、溶接金属の靱性を向上させることができる。ただし、金属弗化物の添加量が少ないと上記の効果が得られず、金属弗化物の添加量が多いとアークの吹付けが強くなりスパッタ発生や全姿勢溶接時のビードの垂れの原因となる。そのため、金属弗化物の添加量は、０．１〜２質量％に規制する。なお、金属弗化物としては、ＣａＦ2、ＮａＦ、ＬｉＦ、ＢａＦ2、ＡｌＦ3、ＭｇＦ2等を用いることができる。 Metal fluoride has a low melting temperature and improves slag fluidity and peelability. Further, the toughness of the weld metal can be improved by the blowhole resistance and the molten metal refining function. However, if the amount of metal fluoride added is small, the above effect cannot be obtained, and if the amount of metal fluoride added is large, arc spraying becomes strong, causing spatter generation and bead dripping during all-position welding. . Therefore, the addition amount of metal fluoride is restricted to 0.1 to 2% by mass. As the metal fluoride, CaF 2 , NaF, LiF, BaF 2 , AlF 3 , MgF 2 or the like can be used.
炭酸塩は、アークの吹付けを強くする機能を有する。また、溶接熱により分解したＣＯ2ガスがアーク中の水蒸気分圧を下げ、溶接金属中の水素を下げたり、ＣＯ2ガスのシールド効果により、ブローホール発生を抑制する。そのため、炭酸塩の添加量が少ないと上記の効果が得られず、炭酸塩の添加量が多いとスパッタ発生や全姿勢溶接時のビードの垂れの原因となる。そのため、炭酸塩の添加量は、０．０５〜１質量％に規制する。炭酸塩としては、ＣａＣＯ3、ＢａＣＯ3、ＭｎＣＯ3、Ｌｉ2ＣＯ3、ＳｒＣＯ3等を用いることができる。 Carbonate has a function of strengthening the arc spray. In addition, CO 2 gas decomposed by welding heat lowers the partial pressure of water vapor in the arc, lowers the hydrogen in the weld metal, and suppresses the generation of blowholes by the shielding effect of CO 2 gas. For this reason, if the added amount of carbonate is small, the above effect cannot be obtained, and if the added amount of carbonate is large, it causes spattering and bead dripping during all-position welding. Therefore, the addition amount of carbonate is regulated to 0.05 to 1% by mass. As the carbonate, CaCO 3 , BaCO 3 , MnCO 3 , Li 2 CO 3 , SrCO 3 or the like can be used.
フラックス粉末に含まれる金属粉末中のＴｉ及び／またはＡｌもしくはそれらを含む合金は、脱酸剤としての効果が強く、溶接金属の低温靱性向上にも寄与する。そのため、この添加量が少ないと効果が得られず、添加量が多いとＮｉと金属間化合物を生成し、延性、靱性の低下や、耐高温割れ性の低下を引き起こす傾向があり、また、スパッタの発生原因となる。そのため、この添加量は、Ｔｉ及びＡｌの質量％換算値の合計で０．０５〜１質量％に規制する。なお、本例では、Ｔｉ及びＡｌを含む合金として、入手し易く安価な鉄（Ｆｅ）系合金粉末を用いた。 Ti and / or Al in the metal powder contained in the flux powder or an alloy containing them has a strong effect as a deoxidizer and contributes to the improvement of the low temperature toughness of the weld metal. Therefore, if this addition amount is small, the effect cannot be obtained, and if the addition amount is large, Ni and an intermetallic compound are formed, and there is a tendency that ductility, toughness and hot cracking resistance are reduced, Cause the occurrence of Therefore, this addition amount is regulated to 0.05 to 1% by mass as a total of the mass% converted values of Ti and Al. In this example, an iron (Fe) -based alloy powder that is easily available and inexpensive is used as an alloy containing Ti and Al.
本例のＮｉ基合金フラックス入りワイヤは、得られる溶着金属中に、Ｓｉ：０．１１〜０．３６質量％、Ｍｎ：１．３８〜１．７２質量％、Ｃｒ：１２．１〜１４．８質量％、Ｍｏ：１２．０〜１４．６質量％、Ｗ：１．７〜３．９質量％、Ａｌ：０．０４〜０．３１質量％、Ｔｉ：０．０１〜０．１７質量％、Ｆｅ：４．６〜６．９質量％、バナジウム族元素としてＶ、Ｎｂ及びＴａの少なくとも１種以上：各０．１２〜１．００質量％、不可避不純物としてＣ：０．０３０質量％未満、Ｐ：０．０１０質量％未満、Ｓ：０．０１０質量％未満及びＮ：０．０４０質量％未満を含み、かつ残部がＮｉである。バナジウム属元素は、炭素及び窒素との親和力が強いため、炭素及び窒素と結合し、粒内及び粒界に炭化物（ＶＣ、ＮｂＣ、ＴａＣ）及び窒化物（ＶＮ、ＮｂＮ、ＴａＮ）を生成する。これらの炭化物や窒化物は、いわゆる多パス溶接における熱サイクルで生じる粒界移動がピン止め効果により抑制され、結晶粒界を複雑化し、その結果、耐再熱割れ性を向上させる。ただし、バナジウム属元素の各添加量が少な過ぎると、上記の効果が得られず、バナジウム属元素の各添加量が多すぎるとＮｉと低融点化合物を生成するため、耐凝固割れ性が低下する。なお、再熱割れ及び凝固割れは、いずれも溶接時における高温下で発生する高温割れの一種であり、その発生メカニズムの相違により分類される。また、バナジウム属元素の過剰添加は、低温靱性も低下する。そのため、バナジウム族元素の含有量は、さらに下記（１）〜（３）式の少なくとも１式の条件を満たすように規制する。 The Ni-based alloy flux cored wire of this example has Si: 0.11 to 0.36 mass%, Mn: 1.38 to 1.72 mass%, and Cr: 12.1 to 14 in the obtained weld metal. 8% by mass, Mo: 12.0 to 14.6% by mass, W: 1.7 to 3.9% by mass, Al: 0.04 to 0.31% by mass, Ti: 0.01 to 0.17% by mass %, Fe: 4.6-6.9% by mass, at least one of V, Nb and Ta as vanadium group elements: 0.12-1.00% by mass each, C: 0.030% by mass as inevitable impurities Less than P, less than 0.010% by mass, S: less than 0.010% by mass and N: less than 0.040% by mass, with the balance being Ni. Since vanadium elements have a strong affinity for carbon and nitrogen, they combine with carbon and nitrogen to generate carbides (VC, NbC, TaC) and nitrides (VN, NbN, TaN) in the grains and at grain boundaries. In these carbides and nitrides, grain boundary movement that occurs in a thermal cycle in so-called multi-pass welding is suppressed by the pinning effect, complicating the grain boundaries, and as a result, improving reheat cracking resistance. However, if the amount of each vanadium element added is too small, the above effect cannot be obtained. If the amount of each vanadium element added is too large, Ni and a low-melting point compound are formed, so that the solidification cracking resistance decreases. . Note that reheat cracking and solidification cracking are both types of hot cracks that occur at high temperatures during welding, and are classified according to differences in their generation mechanisms. In addition, excessive addition of vanadium elements also lowers the low temperature toughness. Therefore, the content of the vanadium group element is further regulated so as to satisfy the condition of at least one of the following formulas (1) to (3).
Ｖ≧（４×Ｃ＋３×Ｎ） ・・・・・（１）
Ｎｂ≧（７×Ｃ＋６×Ｎ） ・・・・・（２）
Ｔａ≧（１５×Ｃ＋１２×Ｎ）・・・・・（３）
なお、上記（１）〜（３）式は、Ｖ、Ｎｂ、及びＴａが属するバナジウム族元素と炭素及び窒素との関係で成立する式である。具体的には、数式（１）〜（３）のＣ、Ｎの係数は、Ｖ、Ｎｂ、Ｔａと炭素、窒素との原子量の比より求めた係数である。そのため、バナジウム族元素として、Ｖを用いる場合は、上記（１）式の条件を満たし、Ｎｂを用いる場合は、上記（２）式の条件を満たし、Ｔａを用いる場合は、上記（３）式の条件を満たすように、バナジウム族元素の添加量を規制することにより、高温割れ（再熱割れ、凝固割れの両者）を効果的に防ぎ、かつ極めて良好な低温靱性を発揮することができる。
V ≧ (4 × C + 3 × N) (1)
Nb ≧ (7 × C + 6 × N) (2)
Ta ≧ (15 × C + 12 × N) (3)
The above formulas (1) to (3) are formulas established by the relationship between the vanadium group element to which V, Nb, and Ta belong, and carbon and nitrogen. Specifically, the coefficients of C and N in the formulas (1) to (3) are coefficients obtained from the ratio of atomic weights of V, Nb, Ta, carbon, and nitrogen. Therefore, when V is used as the vanadium group element, the condition of the above expression (1) is satisfied, when Nb is used, the condition of the above expression (2) is satisfied, and when Ta is used, the above expression (3) is satisfied. By regulating the addition amount of the vanadium group element so as to satisfy the above condition, hot cracking (both reheat cracking and solidification cracking) can be effectively prevented, and extremely good low temperature toughness can be exhibited.
以下、図面を参照しながら、かつ、実施例及び比較例を用いて、本発明の効果を具体的に説明する。図１は、本例のＮｉ基合金フラックス入りワイヤの断面図である。この例では、外皮１とこの外皮１内に配置されたフラックス粉末２とを有している。外皮１は、表１に示すようなＮｉまたはＮｉ基合金からなり、径方向の厚みが約０．２〜０．３ｍｍの管状の形状を有している。外皮１は、細長い外皮用金属板（フープ）が筒状に成型されて構成されており、長手方向の両端部が相互に重なる合わせ目１ｃ、１ｄを有している。
Hereinafter, the effects of the present invention will be specifically described with reference to the drawings and using examples and comparative examples. FIG. 1 is a cross-sectional view of the Ni-based alloy flux cored wire of this example. In this example, it has the
フラックス粉末２は、非金属粉末と金属粉末とが混合されている。非金属粉末には、上述のＴｉＯ2、ＺｒＯ2等の酸化物、ＣａＳｉＯ3等の複酸化物、金属弗化物、炭酸塩等が含まれている。また、金属粉末には、上述のように、Ｔｉ及びＡｌを含むＦｅ系合金粉末が用いられている。
The
図１に示すＮｉ基合金フラックス入りワイヤは、例えば、特開２００３−１０３３９４号公報等に示される公知の方法により製造することができる。なお、図１に示すフラックス入りワイヤは合わせ目を有する外皮を用いた例であるが、合わせ目を有しない外皮を用いたフラックス入りワイヤ（シームレスワイヤ）にも本発明を適用できるのはもちろんである。 The Ni-based alloy flux cored wire shown in FIG. 1 can be manufactured by a known method disclosed in, for example, Japanese Patent Application Laid-Open No. 2003-103394. The flux-cored wire shown in FIG. 1 is an example using an outer skin having a seam, but it goes without saying that the present invention can also be applied to a flux-cored wire (seamless wire) using an outer skin without a seam. is there.
次に本発明の実施例及び比較例について説明する。表１は、外皮（フープ）を構成するＮｉおよびＮｉ基合金の化学組成を示す表である。また、表２は、外皮に充填するフラックスの化学組成及びフラックス入りワイヤ中の水分量を示す表である。さらに、表３は、得られた溶着金属の化学成分を示す表である。なお、表３中の「（１）（２）（３）式」列は、請求項４に記載上記（１）〜（３）の３式のうち、いずれか１式以上を満たしていれば○、いずれの式も満たさなければ×と記載した。 Next, examples and comparative examples of the present invention will be described. Table 1 is a table showing the chemical composition of Ni and Ni-based alloy constituting the outer skin (hoop). Moreover, Table 2 is a table | surface which shows the chemical composition of the flux with which an outer shell is filled, and the moisture content in a flux cored wire. Furthermore, Table 3 is a table | surface which shows the chemical component of the obtained weld metal. The column “(1) (2) (3)” in Table 3 satisfies any one or more of the three formulas (1) to (3) described in claim 4. ○, if none of the formulas were satisfied, it was marked as x.
表１〜表３に示す実施例及び比較例について、溶接技術の分野で一般に用いられる各種試験により、溶接性能を確認した。
［溶接作業性試験］
溶接作業性試験は、下向姿勢及び立向姿勢（上進）のすみ肉溶接にて判定を行った。下向姿勢は溶接作業性を評価する上で基本的な溶接姿勢であり、また立向姿勢は溶接速度を遅くするため、ビードが垂れ易く、その点、上向姿勢より厳しい条件となること、また、構造物の溶接には立向姿勢（上進）が広く採用されていることから、全姿勢溶接の評価姿勢として採用した。下向姿勢とは、溶接軸がほぼ水平な継手に対して、上方から下を向いて行う溶接姿勢であり、立向姿勢（上進）とは、溶接軸がほぼ鉛直な継手に対して下から上に向かって鉛直にビードを置く溶接姿勢である。シールドガスには、８０％Ａｒ＋２０％ＣＯ2を用いた。下向姿勢のすみ肉溶接は、溶接電流２００Ａ、アーク電圧３０Ｖ、溶接速度３０ｃｍ／ｍｉｎの溶接条件にて、立向姿勢（上進）のすみ肉溶接は、溶接電流１５０Ａ、アーク電圧２５Ｖ、溶接速度８〜１２ｃｍ／ｍｉｎの溶接条件にて、それぞれ溶接を行った。
About the Example and comparative example which are shown in Table 1-Table 3, welding performance was confirmed by various tests generally used in the field of welding technology.
[Welding workability test]
In the welding workability test, determination was made by fillet welding in a downward posture and a vertical posture (upward). The downward posture is a basic welding posture for evaluating welding workability, and the vertical posture makes the bead droop easily because it slows the welding speed, and in that respect, the condition is more severe than the upward posture. In addition, since the vertical posture (advancing) is widely used for welding structures, it was adopted as the evaluation posture for all-position welding. A downward posture is a welding posture in which the welding axis is directed downward from above with respect to a joint with a substantially horizontal welding axis, and an upright posture (upward) is a downward posture with respect to a joint with a welding axis substantially vertical. This is a welding posture in which a bead is placed vertically from the top to the bottom. As the shielding gas, 80% Ar + 20% CO 2 was used. Fillet welding in the downward posture is welding current of 200A, arc voltage 30V, welding speed 30cm / min, fillet welding in the vertical posture (upward) is welding current 150A, arc voltage 25V, welding Welding was performed under welding conditions at a speed of 8 to 12 cm / min.
溶接作業性は、下向姿勢および立向姿勢において、アーク安定性、スパッタ防止、ビード形状、スラグ剥離の観点から評価した。 Welding workability was evaluated from the viewpoints of arc stability, spatter prevention, bead shape, and slag peeling in a downward posture and a vertical posture.
溶接作業性の評価は、◎：非常に良い、○：良い、△：やや劣る、×：劣る、の基準により判定した。また、各項目の評価を、◎：３点、○：２点、△：１点、×：０点、の基準により点数化し、得られた点数の合計から総合評価を行った。総合評価は、合計点が８点以上を合格とした。
［放射線透過試験］
溶接部の放射線透過試験は、図２（ａ）に示す開先内を、下向姿勢、立向姿勢にて溶接し、図２（ｂ）に示す開先内を、横向姿勢にて溶接した。放射線透過試験に横向姿勢を追加した理由は、横向姿勢では他のいかなる姿勢より溶接速度を速くするため、凝固速度が早く、ブローホールが残存し易くなり、放射線透過試験では最も厳しい条件となるためである。横向姿勢とは、溶接軸がほぼ水平な継手に対して、横方向にビードを置く溶接姿勢である。これらの溶接により得られた溶接部を、ＪＩＳ Ｚ ３１０６に準拠して、ブローホールの有無を確認した。ブローホールの判定は、以下の評価基準に基づいて行い、第１種のきず（丸いブローホール及びこれに類するきず）の判定で、１類、２類を合格とした。なお、継手作製ができなかったものは１類〜４類のいずれにも該当しないものとして扱った。
Welding workability was evaluated based on the following criteria: ◎: very good, ○: good, △: slightly inferior, ×: inferior. The evaluation of each item was scored on the basis of ◎: 3 points, ○: 2 points, Δ: 1 point, x: 0 points, and comprehensive evaluation was performed from the total of the obtained points. In the comprehensive evaluation, the total score was 8 points or more.
[Radiation transmission test]
In the radiation transmission test of the welded portion, the inside of the groove shown in FIG. 2 (a) was welded in a downward posture and a vertical posture, and the inside of the groove shown in FIG. 2 (b) was welded in a horizontal posture. . The reason for adding the lateral orientation to the radiation transmission test is that, in the lateral orientation, the welding speed is higher than in any other orientation, so the solidification rate is high and blowholes are likely to remain. It is. The horizontal posture is a welding posture in which a bead is placed in a horizontal direction with respect to a joint whose welding axis is substantially horizontal. The welds obtained by these weldings were checked for blowholes in accordance with JIS Z 3106. The determination of the blowhole was performed based on the following evaluation criteria, and the first type and the second type were determined to be acceptable in the determination of the first type of flaw (round blowhole and similar flaws). In addition, what was not able to produce joints was handled as what does not correspond to any of 1st-4th class.
１類：きず点数２点以下
２類：きず点数３〜６点
３類：きず点数７〜１２点
４類：きず点数が３類よりも多いもの
なお、きず点数はきずの長径及び個数により算定される点数で、少ない方が評価が高い。
［溶接割れ試験］
溶接割れ試験として、多層盛Ｔ形すみ肉の段削り試験を行った。具体的には、図３に示すように、間隔Ｇを隔ててＴ字形に配置された２つの板材３、４を、拘束ビード５と試験ビード６〜１１により接合し、試験ビード表面から表面下１０ｍｍの位置まで、１ｍｍピッチで段削りを行い、クレータ以外での割れの有無を染色浸透探傷試験方法により調査した。溶接条件は、溶接電流２００Ａ、アーク電圧３０Ｖ、溶接速度５０ｃｍ／ｍｉｎとし、間隔Ｇは１ｍｍとした。
1 type: 2 or
[Weld crack test]
As a weld cracking test, a multi-layer T-shaped fillet test was performed. Specifically, as shown in FIG. 3, two
溶接割れ試験では、多パス溶接による「再熱割れ」及び「凝固割れ」の発生から耐高温割れ性を評価した。具体的には、耐高温割れ性の評価は、再熱割れ及び凝固割れのいずれも発生しなかった場合は「極めて良好」と判定し、再熱割れまたは凝固割れのいずれかの発生に止まった場合は「概ね良好」と判定し、再熱割れ及び凝固割れのいずれも発生した場合は「不良」と判定した。
［衝撃試験］
溶着金属の衝撃試験では、図４に示す９％Ｎｉ鋼母材の開先内を溶接し、ＪＩＳ Ｚ ３１１１に準拠して、４号試験片１２を採取し、−１９６℃の液体窒素中に１０分間保持した後、シャルピー衝撃試験機にて試験を行った。試験片数は３本で、その平均値にて評価を行った。衝撃試験では、溶着金属の吸収エネルギー（Ｊ）を比較して、溶着金属の低温靱性を評価した。溶着金属（低温靱性）の評価は、吸収エネルギーが８５Ｊ以上の場合は「極めて良好」と判定し、吸収エネルギーが４０Ｊ以上かつ８５Ｊ未満の場合は「概ね良好」と判定し、吸収エネルギーが４０Ｊ未満の場合は「不良」と判定した。
In the weld cracking test, the hot cracking resistance was evaluated from the occurrence of “reheat cracking” and “solidification cracking” by multi-pass welding. Specifically, in the evaluation of hot cracking resistance, if neither reheat cracking nor solidification cracking occurred, it was judged as “very good” and only reheat cracking or solidification cracking occurred. The case was judged as “substantially good”, and when both reheat cracking and solidification cracking occurred, it was judged as “bad”.
[Shock test]
In the weld metal impact test, the inside of the groove of the 9% Ni steel base material shown in FIG. 4 was welded, and the No. 4 test piece 12 was sampled according to JIS Z 3111 and placed in liquid nitrogen at −196 ° C. After holding for 10 minutes, the test was conducted with a Charpy impact tester. The number of test pieces was three, and the average value was evaluated. In the impact test, the low-temperature toughness of the weld metal was evaluated by comparing the absorbed energy (J) of the weld metal. The evaluation of the weld metal (low temperature toughness) is judged as “very good” when the absorbed energy is 85 J or more, and judged as “substantially good” when the absorbed energy is 40 J or more and less than 85 J, and the absorbed energy is less than 40 J. In the case of, it was determined as “bad”.
上記の溶接作業性試験、溶接部の放射線透過試験、溶接割れ試験、溶着金属の衝撃試験の結果を表４に示す。なお、表４の溶接割れ試験において、再熱割れ及び凝固割れが共に発生した場合は「高温割れ」と表記した。 Table 4 shows the results of the above-described welding workability test, the radiation transmission test of the welded portion, the weld cracking test, and the impact test of the weld metal. In the weld cracking test in Table 4, when both reheat cracking and solidification cracking occurred, they were indicated as “hot cracking”.
実施例１〜２５、及び比較例１〜１３は、いずれもＮｉ基合金フラックス入りワイヤである（実施例１〜１２及び比較例１〜１３は耐食・耐熱用途に用いられ、実施例１３〜２５は後述するＬＮＧタンク等の極低温構造物の溶接に用いられる）。実施例１〜２５のフラックス入りワイヤを用いた溶接では、下向姿勢、立向姿勢での溶接作業性、耐ブローホール性、耐高温割れ性、低温靱性について、いずれも良好な結果が得られた。 Examples 1 to 25 and Comparative Examples 1 to 13 are all Ni-based alloy flux-cored wires (Examples 1 to 12 and Comparative Examples 1 to 13 are used for corrosion resistance and heat resistance, and Examples 13 to 25 are used. Is used for welding a cryogenic structure such as an LNG tank described later). In the welding using the flux-cored wires of Examples 1 to 25, good results were obtained for the downward posture, the welding workability in the vertical posture, the blowhole resistance, the hot crack resistance, and the low temperature toughness. It was.
これに対して、比較例１（炭酸塩が規制値を超える場合）では、スパッタが多発し、立向姿勢において溶融金属が垂れてビード断面形状が凸となりビード形状が不良となった。 On the other hand, in Comparative Example 1 (when the carbonate exceeds the regulation value), spatter frequently occurred, the molten metal dripped in the standing posture, the bead cross-sectional shape became convex, and the bead shape became poor.
比較例２（ＴｉＯ2が規制値を超える場合）では、スラグの剥離性がわずかに低下した。また、耐溶接割れ性が著しく低下した（再熱割れ及び凝固割れが共存した）。また、吸収エネルギーも極端に低下した。 In Comparative Example 2 (when TiO 2 exceeds the regulation value), the slag peelability slightly decreased. In addition, the resistance to weld cracking was remarkably reduced (reheat cracking and solidification cracking coexisted). Also, the absorbed energy was extremely reduced.
比較例３（ＴｉＯ2が規制値を下回り、金属弗化物が規制値を超える場合）では、スパッタが多発し、立向姿勢において溶融金属が垂れてビード断面形状が凸となりビード形状が不良となった。また、比較例３では、下向姿勢、立向姿勢に限らず、アークが不安定で、スパッタが多発した。 In Comparative Example 3 (when TiO 2 falls below the regulation value and metal fluoride exceeds the regulation value), spatter frequently occurs, the molten metal droops in the upright position, the bead cross-sectional shape becomes convex, and the bead shape becomes poor. It was. In Comparative Example 3, the arc was unstable and spatter occurred frequently, not limited to the downward posture and the vertical posture.
比較例４（ＣａＳｉＯ3が無添加で、その代わりにＳｉＯ2を含有する場合）では、耐溶接割れ性が著しく低下した（再熱割れ及び凝固割れが共存した）。また、吸収エネルギーも極端に低下した。 In Comparative Example 4 (when CaSiO 3 was not added and SiO 2 was contained instead), the weld crack resistance was remarkably reduced (reheat cracking and solidification crack coexisted). Also, the absorbed energy was extremely reduced.
比較例５（ＣａＳｉＯ3が規制値を超える場合）では、スパッタが多発し、立向姿勢でのアークが不安定であった。 In Comparative Example 5 (when CaSiO 3 exceeds the regulation value), spatter frequently occurred and the arc in an upright posture was unstable.
比較例６（ＺｒＯ2が無添加の場合）では、立向姿勢において、スパッタが多発し、また溶融金属が垂れてビード断面形状が凸となりビード形状が不良となった。 In Comparative Example 6 (in the case where ZrO 2 was not added), spatter frequently occurred in the standing posture, and the molten metal dripped, the bead cross-sectional shape became convex, and the bead shape became poor.
比較例７（ＺｒＯ2が規制値を超える場合）では、立向姿勢で、スパッタが多発し、スラグの剥離性がわずかに低下した。また、凝固速度が速くなりすぎて、横向姿勢でブローホールが多発した。 In Comparative Example 7 (when ZrO 2 exceeds the regulation value), spatter frequently occurred in the standing posture, and the slag peelability slightly decreased. In addition, the solidification rate became too fast, and blow holes occurred frequently in the horizontal posture.
比較例８（未焼成のＴｉＯ2を使用した場合）では、フラックス入りワイヤ中の水分量が多くなり（３００ｐｐｍを超え）、ブローホールが多発した。また耐溶接割れ性が著しく低下した（再熱割れ及び凝固割れが共存した）。また、吸収エネルギーも極端に低下した。 In Comparative Example 8 (when unsintered TiO 2 was used), the amount of moisture in the flux-cored wire increased (exceeding 300 ppm), and blowholes occurred frequently. In addition, the weld crack resistance was remarkably reduced (reheat cracking and solidification cracking coexisted). Also, the absorbed energy was extremely reduced.
比較例９（炭酸塩が規制値より少ない場合）では、アークの吹付けが弱くなり、立向姿勢の作業性が若干低下し、横向姿勢でブローホールが多発した。 In Comparative Example 9 (when carbonate was less than the regulation value), arc spraying was weakened, workability in the standing posture was slightly lowered, and blowholes occurred frequently in the lateral posture.
比較例１０（ＴｉＯ2が規制値より少ない場合）では、立向姿勢の作業性が若干低下した。 In Comparative Example 10 (when TiO 2 is less than the regulation value), the workability of the standing posture is slightly lowered.
比較例１１（未焼成のＴｉＯ2を使用し、金属弗化物が無添加の場合）では、フラックス入りワイヤ中の水分量が多くなり（３００ｐｐｍを超え）、ブローホールが多発した。また耐溶接割れ性が著しく低下した（再熱割れ及び凝固割れが共存した）。また、吸収エネルギーも極端に低下した。 In Comparative Example 11 (when unfired TiO 2 was used and no metal fluoride was added), the amount of moisture in the flux-cored wire increased (over 300 ppm), and blowholes occurred frequently. In addition, the weld crack resistance was remarkably reduced (reheat cracking and solidification cracking coexisted). Also, the absorbed energy was extremely reduced.
比較例１２（金属粉末としてのＴｉ、Ａｌが規制値を超える場合）では、下向姿勢でスパッタが多発した。また、得られた溶着金属の耐溶接割れ性が著しく低下した（再熱割れ及び凝固割れが共存した）。また、吸収エネルギーも極端に低下した。 In Comparative Example 12 (when Ti and Al as the metal powder exceeded the regulation value), spatter occurred frequently in a downward posture. Moreover, the weld crack resistance of the obtained deposited metal was remarkably lowered (reheat cracking and solidification cracking coexisted). Also, the absorbed energy was extremely reduced.
比較例１３（金属粉末としてのＴｉ、Ａｌが規制値より少ない場合）では、立向姿勢での溶接作業性が若干低下した。また、脱酸効果がなく、横向姿勢でブローホールが多発した。 In Comparative Example 13 (when Ti and Al as the metal powder were less than the regulation values), the welding workability in the vertical posture was slightly lowered. In addition, there was no deoxidation effect, and blowholes occurred frequently in a horizontal posture.
実施例１〜２５の中で、実施例１３〜２５は、ＬＮＧタンク等の極低温構造物に用いられる９％Ｎｉ鋼の溶接に使用されるＮｉ基合金フラックス入りワイヤを対象とするものである。９％Ｎｉ鋼用溶接材料は、極低温での靱性が優れていることに加え、耐高温割れ性に優れていることが重要である。このような観点から、９％Ｎｉ鋼の溶接に使用されるＮｉ基合金フラックス入りワイヤにおいて、耐高温割れ性及び低温靱性に対するバナジウム属元素の添加効果を確認したところ、以下の結果が得られた。 Among Examples 1 to 25, Examples 13 to 25 are intended for Ni-based alloy flux-cored wires used for welding of 9% Ni steel used for cryogenic structures such as LNG tanks. . It is important that the 9% Ni steel welding material has excellent high temperature crack resistance in addition to excellent toughness at extremely low temperatures. From such a viewpoint, in the Ni-based alloy flux cored wire used for welding of 9% Ni steel, the effect of adding the vanadium element on the hot crack resistance and the low temperature toughness was confirmed, and the following results were obtained. .
特に、実施例１３〜１８［バナジウム族元素の含有量が規制値を満たしており、かつ、数式（１）、（２）、（３）の条件を満たしている場合］のフラックス入りワイヤを用いた溶接では、耐高温割れ性および低温靱性はいずれも「極めて良好」であった。 In particular, the flux-cored wires of Examples 13 to 18 [when the content of the vanadium group element satisfies the regulation value and satisfies the conditions of the formulas (1), (2), and (3)] are used. In the conventional welding, both the hot crack resistance and the low temperature toughness were “very good”.
これに対して、実施例１９、２２（Ｖ、Ｎｂ、Ｔａが、いずれも規制値より少ない場合）、実施例２０、２１、２５［バナジウム族元素の含有量は規制値を満たしているが、数式（１）、（２）、（３）のいずれも満たしていない場合］、実施例２３、２４（Ｖ、Ｎｂが規制値を超える場合）のフラックス入りワイヤを用いた溶接では、耐高温割れ性および低温靱性はいずれも「概ね良好」にとどまった。 On the other hand, Examples 19 and 22 (when V, Nb, and Ta are all less than the regulation value), Examples 20, 21, and 25 [the vanadium group element content satisfies the regulation value, When none of the mathematical formulas (1), (2), and (3) is satisfied], welding using the flux-cored wires of Examples 23 and 24 (when V and Nb exceed the regulation values), high temperature cracking resistance Both low-temperature toughness and low-temperature toughness remained “substantially good”.
このように、実施例１〜２５のフラックス入りワイヤを用いた溶接では、下向姿勢、立向姿勢での溶接作業性、耐ブローホール性、耐高温割れ性、及び衝撃性能は、いずれも良好な結果となり、特に実施例１３〜１８は、実施例１９〜２５と比較して、耐高温割れ性、及び衝撃性能が向上することが判った。 As described above, in welding using the flux-cored wires of Examples 1 to 25, all of the downward attitude, the welding workability in the vertical attitude, the blowhole resistance, the high temperature crack resistance, and the impact performance are all good. It turned out that it became a good result, and especially Examples 13-18 improved hot cracking resistance and impact performance compared with Examples 19-25.
以上、本発明の実施の形態について具体的に説明したが、本発明はこれらの実施の形態および実施例に限定されるものではなく、本発明の技術的思想に基づく変更が可能であるのは勿論である。 Although the embodiments of the present invention have been specifically described above, the present invention is not limited to these embodiments and examples, and modifications based on the technical idea of the present invention are possible. Of course.
本発明のＮｉ基合金フラックス入りワイヤは、フラックス入りワイヤの全質量に対して、８００℃以上の温度で焼成したＴｉＯ2を４〜６質量％、合成された複酸化物としてＣａＳｉＯ3を０．１〜３質量％、ＺｒＯ2を０．５〜２質量％、金属弗化物を０．１〜２質量％、炭酸塩を０．０５〜１質量％、それぞれ含有する非金属粉末と、Ｔｉ及びＡｌのいずれか一種または両種からなる金属、もしくはＴｉ及びＡｌの合金が、フラックス入りワイヤの全質量に対するＴｉ及びＡｌの質量％換算値の合計で０．０５〜１質量％含有する金属粉末とが含まれるフラックス粉末が、ＮｉまたはＮｉ基合金を主成分とする外皮に充填されているため、全姿勢溶接における諸性能（アーク安定性、スパッタ防止、ビード形状、スラグ剥離性、耐ブローホール性、耐高温割れ性等）を同時に向上させ、さらに良好な低温靱性を確保できる。 Ni based alloy flux-cored wire of the present invention is, with respect to the total mass of the flux cored wire, the TiO 2 4 to 6 wt% calcined at 800 ° C. or higher, combined with CaSiO 3 as a mixed oxide 0. 1 to 3% by weight, ZrO 2 0.5 to 2% by weight, metal fluoride 0.1 to 2% by weight, carbonate 0.05 to 1% by weight, non-metallic powder, Ti and A metal powder containing any one or both of Al, or an alloy of Ti and Al containing 0.05 to 1% by mass in terms of a mass% converted value of Ti and Al with respect to the total mass of the flux-cored wire; Since the flux powder containing Ni is filled in the outer skin mainly composed of Ni or Ni-based alloy, various performances (arc stability, anti-spatter, bead shape, slag peelability, blow-proof resistance) Le resistance, resistance to hot cracking, etc.) at the same time to improve and ensure a better low temperature toughness.
Claims (4)
前記フラックス粉末中の前記非金属粉末には、前記フラックス入りワイヤの全質量に対して、８００℃以上の温度で焼成したＴｉＯ2：４〜６質量％、合成されたＣａＳｉＯ3の複酸化物：０．１〜３質量％、ＺｒＯ2：０．５〜２質量％、金属弗化物：０．１〜２質量％、炭酸塩：０．０５〜１質量％が含まれており、
前記フラックス粉末中の前記金属粉末には、Ｔｉ及びＡｌのいずれか一種または両種からなる金属、もしくはＴｉ及びＡｌの合金が、前記フラックス入りワイヤの全質量に対するＴｉ及びＡｌの質量％換算値の合計で０．０５〜１質量％含まれていることを特徴とするＮｉ基合金フラックス入りワイヤ。 A Ni-based alloy flux-cored wire comprising an outer skin mainly composed of Ni or a Ni-based alloy and a flux powder filled in the outer skin and containing a non-metallic powder and a metal powder,
In the non-metallic powder in the flux powder, TiO 2 baked at a temperature of 800 ° C. or higher with respect to the total mass of the flux-cored wire: 4 to 6 mass%, synthesized CaSiO 3 double oxide: 0.1 to 3% by mass, ZrO 2 : 0.5 to 2% by mass, metal fluoride: 0.1 to 2% by mass, carbonate: 0.05 to 1% by mass,
In the metal powder in the flux powder, a metal composed of one or both of Ti and Al, or an alloy of Ti and Al is a mass% conversion value of Ti and Al with respect to the total mass of the flux-cored wire. A Ni-based alloy flux cored wire characterized by containing 0.05 to 1% by mass in total.
前記Ｖ、Ｎｂ及びＴａが属するバナジウム族元素と前記不可避不純物として含まれるＣ及びＮとの間で、含有する前記バナジウム族元素の種類に応じて下記（１）乃至（３）式の少なくとも１式の関係が成立する請求項１乃至３のいずれか１項に記載のＮｉ基合金フラックス入りワイヤ。
Ｖ≧（４×Ｃ＋３×Ｎ） ・・・・・（１）
Ｎｂ≧（７×Ｃ＋６×Ｎ） ・・・・・（２）
Ｔａ≧（１５×Ｃ＋１２×Ｎ）・・・・・（３）
In the weld metal obtained by the flux-cored wire, Si: 0.11 to 0.36 mass%, Mn: 1.38 to 1.72 mass%, Cr: 12.1 to 14.8 mass%, Mo: 12.0 to 14.6% by mass, W: 1.7 to 3.9% by mass, Al: 0.04 to 0.31% by mass, Ti: 0.01 to 0.17% by mass, Fe: 4. 6 to 6.9% by mass, at least one of V, Nb, and Ta as vanadium group elements: 0.12 to 1.00% by mass each, C: less than 0.030% by mass as inevitable impurities, P: 0.0. less than 010 wt%, S: less than 0.010 mass% and N: contains less than 0.040 wt%, and contains Ni as balance,
Between the vanadium group element to which V, Nb, and Ta belong and C and N contained as the inevitable impurities, at least one of the following formulas (1) to (3) according to the type of the vanadium group element to be contained The Ni-based alloy flux cored wire according to any one of claims 1 to 3, wherein the relationship is established .
V ≧ (4 × C + 3 × N) (1)
Nb ≧ (7 × C + 6 × N) (2)
Ta ≧ (15 × C + 12 × N) (3)
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| CN111451602A (en) * | 2020-05-09 | 2020-07-28 | 邱振强 | Digging, replacing, welding and repairing equipment for iron castings |
| CN112509645A (en) * | 2020-11-10 | 2021-03-16 | 鞍钢股份有限公司 | Method for calculating addition amount of alloy powder raw materials of flux-cored wire |
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| CN115922141A (en) * | 2022-12-05 | 2023-04-07 | 北京工业大学 | Metal-cored welding wire for GH3030 high-temperature alloy with high cracking resistance |
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04319093A (en) * | 1991-04-16 | 1992-11-10 | Nippon Oil & Fats Co Ltd | Flux cored wire for nickel alloy 'hastelloy c-276(r)' welding |
| JPH07116891A (en) * | 1993-01-29 | 1995-05-09 | Kobe Steel Ltd | Ni-based alloy flux cored wire |
| JPH08309583A (en) * | 1995-05-17 | 1996-11-26 | Nippon Steel Corp | Flux cored wire for 9% ni steel |
| JPH10180486A (en) * | 1996-12-25 | 1998-07-07 | Nippon Steel Corp | Flux-cored wire for 9% ni steel |
| JPH10296486A (en) * | 1997-05-02 | 1998-11-10 | Nippon Steel Corp | Flux cored wire for welding 9% nickel steel |
| JP2000117488A (en) * | 1998-08-10 | 2000-04-25 | Kobe Steel Ltd | Ni-BASED ALLOY FLUX-CORED WIRE |
| JP2000343276A (en) * | 1999-06-01 | 2000-12-12 | Kobe Steel Ltd | Ni-BASED ALLOY FLUX-CORED WIRE |
| JP2000343277A (en) * | 1999-06-04 | 2000-12-12 | Nippon Steel Corp | Nickel base alloy flux-cored wire excellent in weldability at whole posture |
| JP2009056478A (en) * | 2007-08-30 | 2009-03-19 | Nippon Welding Rod Kk | WIRE FILLED WITH Ni-BASED ALLOY FLUX |
-
2015
- 2015-02-16 JP JP2015027171A patent/JP5763859B1/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04319093A (en) * | 1991-04-16 | 1992-11-10 | Nippon Oil & Fats Co Ltd | Flux cored wire for nickel alloy 'hastelloy c-276(r)' welding |
| JPH07116891A (en) * | 1993-01-29 | 1995-05-09 | Kobe Steel Ltd | Ni-based alloy flux cored wire |
| JPH08309583A (en) * | 1995-05-17 | 1996-11-26 | Nippon Steel Corp | Flux cored wire for 9% ni steel |
| JPH10180486A (en) * | 1996-12-25 | 1998-07-07 | Nippon Steel Corp | Flux-cored wire for 9% ni steel |
| JPH10296486A (en) * | 1997-05-02 | 1998-11-10 | Nippon Steel Corp | Flux cored wire for welding 9% nickel steel |
| JP2000117488A (en) * | 1998-08-10 | 2000-04-25 | Kobe Steel Ltd | Ni-BASED ALLOY FLUX-CORED WIRE |
| JP2000343276A (en) * | 1999-06-01 | 2000-12-12 | Kobe Steel Ltd | Ni-BASED ALLOY FLUX-CORED WIRE |
| JP2000343277A (en) * | 1999-06-04 | 2000-12-12 | Nippon Steel Corp | Nickel base alloy flux-cored wire excellent in weldability at whole posture |
| JP2009056478A (en) * | 2007-08-30 | 2009-03-19 | Nippon Welding Rod Kk | WIRE FILLED WITH Ni-BASED ALLOY FLUX |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111451602A (en) * | 2020-05-09 | 2020-07-28 | 邱振强 | Digging, replacing, welding and repairing equipment for iron castings |
| CN112509645A (en) * | 2020-11-10 | 2021-03-16 | 鞍钢股份有限公司 | Method for calculating addition amount of alloy powder raw materials of flux-cored wire |
| CN112509645B (en) * | 2020-11-10 | 2023-09-26 | 鞍钢股份有限公司 | Calculation method for addition amount of flux-cored wire alloy powder raw materials |
| CN115922141A (en) * | 2022-12-05 | 2023-04-07 | 北京工业大学 | Metal-cored welding wire for GH3030 high-temperature alloy with high cracking resistance |
| CN115890061A (en) * | 2022-12-27 | 2023-04-04 | 西安智能再制造研究院有限公司 | TiC and VC reinforced laser surfacing layer and preparation method thereof |
| CN116275706A (en) * | 2023-05-24 | 2023-06-23 | 北京煜鼎增材制造研究院有限公司 | High-energy beam fuse deposition additive preparation method of nickel-based superalloy |
| CN116275706B (en) * | 2023-05-24 | 2023-08-11 | 北京煜鼎增材制造研究院股份有限公司 | High-energy beam fuse deposition additive preparation method of nickel-based superalloy |
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