JP5885618B2 - Stainless steel flux cored wire - Google Patents
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- JP5885618B2 JP5885618B2 JP2012177070A JP2012177070A JP5885618B2 JP 5885618 B2 JP5885618 B2 JP 5885618B2 JP 2012177070 A JP2012177070 A JP 2012177070A JP 2012177070 A JP2012177070 A JP 2012177070A JP 5885618 B2 JP5885618 B2 JP 5885618B2
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- 230000004907 flux Effects 0.000 title claims description 64
- 229910001220 stainless steel Inorganic materials 0.000 title claims description 53
- 239000010935 stainless steel Substances 0.000 title claims description 52
- 229910052751 metal Inorganic materials 0.000 claims description 44
- 239000002184 metal Substances 0.000 claims description 44
- 239000002893 slag Substances 0.000 claims description 44
- 238000003466 welding Methods 0.000 claims description 39
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 13
- 229910001512 metal fluoride Inorganic materials 0.000 claims description 13
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 11
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 10
- 229910052760 oxygen Inorganic materials 0.000 claims description 10
- 229910045601 alloy Inorganic materials 0.000 claims description 4
- 239000000956 alloy Substances 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 239000003795 chemical substances by application Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 9
- 239000000843 powder Substances 0.000 description 9
- 239000011734 sodium Substances 0.000 description 9
- 239000011324 bead Substances 0.000 description 8
- 238000005452 bending Methods 0.000 description 7
- 239000007789 gas Substances 0.000 description 7
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- 229910017060 Fe Cr Inorganic materials 0.000 description 5
- 229910002544 Fe-Cr Inorganic materials 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 5
- 235000019353 potassium silicate Nutrition 0.000 description 5
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 239000010953 base metal Substances 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000005538 encapsulation Methods 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 229910002551 Fe-Mn Inorganic materials 0.000 description 3
- 239000004111 Potassium silicate Substances 0.000 description 3
- 239000004115 Sodium Silicate Substances 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000010433 feldspar Substances 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 3
- 229910052913 potassium silicate Inorganic materials 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 229910052911 sodium silicate Inorganic materials 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- -1 Fe-Cr nitride Chemical class 0.000 description 2
- CDBYLPFSWZWCQE-UHFFFAOYSA-L Sodium Carbonate Chemical compound [Na+].[Na+].[O-]C([O-])=O CDBYLPFSWZWCQE-UHFFFAOYSA-L 0.000 description 2
- 229910052797 bismuth Inorganic materials 0.000 description 2
- 239000003610 charcoal Substances 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- 239000000377 silicon dioxide Substances 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- 229910016569 AlF 3 Inorganic materials 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical group F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 1
- KWYUFKZDYYNOTN-UHFFFAOYSA-M Potassium hydroxide Chemical compound [OH-].[K+] KWYUFKZDYYNOTN-UHFFFAOYSA-M 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- GEIAQOFPUVMAGM-UHFFFAOYSA-N ZrO Inorganic materials [Zr]=O GEIAQOFPUVMAGM-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- DLHONNLASJQAHX-UHFFFAOYSA-N aluminum;potassium;oxygen(2-);silicon(4+) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[O-2].[O-2].[O-2].[Al+3].[Si+4].[Si+4].[Si+4].[K+] DLHONNLASJQAHX-UHFFFAOYSA-N 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- AOWKSNWVBZGMTJ-UHFFFAOYSA-N calcium titanate Chemical compound [Ca+2].[O-][Ti]([O-])=O AOWKSNWVBZGMTJ-UHFFFAOYSA-N 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- NJLLQSBAHIKGKF-UHFFFAOYSA-N dipotassium dioxido(oxo)titanium Chemical compound [K+].[K+].[O-][Ti]([O-])=O NJLLQSBAHIKGKF-UHFFFAOYSA-N 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229940072033 potash Drugs 0.000 description 1
- BWHMMNNQKKPAPP-UHFFFAOYSA-L potassium carbonate Substances [K+].[K+].[O-]C([O-])=O BWHMMNNQKKPAPP-UHFFFAOYSA-L 0.000 description 1
- 235000015320 potassium carbonate Nutrition 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000004544 sputter deposition Methods 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 229910052882 wollastonite Inorganic materials 0.000 description 1
- 239000010456 wollastonite Substances 0.000 description 1
Description
本発明は、高強度オーステナイト系ステンレス鋼のガスシールドアーク溶接に用いるフラックス入りワイヤに関し、特にＮを多く含有する高強度オーステナイト系ステンレス鋼の溶接において、母材と同等の高い引張強さが得られ、スラグの剥離性等を向上させることで良好な溶接作業性を確保する上で好適なステンレス鋼溶接用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 flux-cored wire used for gas shielded arc welding of high-strength austenitic stainless steel, and in particular, in high-strength austenitic stainless steel containing a large amount of N, high tensile strength equivalent to that of a base material can be obtained. The present invention relates to a flux-cored wire for welding stainless steel suitable for ensuring good welding workability by improving the slag releasability and the like.
ＳＵＳ３０４等に代表されるオーステナイト系ステンレス鋼は、その優れた耐食性、引張強さ及び靭性から、化学プラントやケミカルタンカー、建築構造物等に適用されている。最近ではＳＵＳ３０４に、Ｎを添加して高強度化を図ったＳＵＳ３０４Ｎ２やＳＵＳ３０４Ｎ２Ａ等の適用範囲が広まり、構造物の薄板化、軽量化が図られ、特に建築構造物への適用が進められている。 Austenitic stainless steel represented by SUS304 and the like is applied to chemical plants, chemical tankers, building structures and the like because of its excellent corrosion resistance, tensile strength and toughness. Recently, the range of application of SUS304N2 and SUS304N2A, etc., in which N is added to SUS304 to increase its strength has been widened, and the structure has been made thinner and lighter, and is particularly being applied to building structures. .
このようなＮを含有させたステンレス鋼としてのＳＵＳ３０４Ｎ２及びＳＵＳ３０４Ｎ２Ａ等に対する溶接材料として、例えば特許文献１、２に開示されているステンレス鋼溶接用フラックス入りワイヤが開発され実用化されている。 As welding materials for such SUS304N2 and SUS304N2A as stainless steel containing N, for example, flux cored wires for stainless steel welding disclosed in Patent Documents 1 and 2 have been developed and put to practical use.
特に、この特許文献１では、オーステナイト系ステンレス鋼の溶接において母材と同等の優れた強度特性を発揮させるため、ワイヤ中のＣ、Ｍｎ、Ｃｒ、Ｎｉの合金成分及びＮのガス成分量をそれぞれ適正範囲に制御し、かつ充填すべきフラックス中に主としてスラグ剤を含有させたフラックス入りワイヤが開示されている。 In particular, in Patent Document 1, in order to exhibit excellent strength characteristics equivalent to the base metal in welding of austenitic stainless steel, the alloy components of C, Mn, Cr, Ni and the amount of gas component of N in the wire are respectively set. A flux-cored wire that is controlled within an appropriate range and contains a slag agent mainly in the flux to be filled is disclosed.
また特許文献２では、Ｎｉを始めとした金属成分の含有率やスラグ成分の含有率を限定することにより、スラグの被包性や剥離性を向上させたフラックス入りワイヤが開示されている。 Patent Document 2 discloses a flux-cored wire that improves the slag encapsulation and peelability by limiting the content of metal components including Ni and the content of slag components.
しかし、特許文献１に開示されているフラックス入りワイヤは、Ｎｉ量がワイヤ全重量に対して９．５〜１１．５％と多いため、溶着金属の引張強さが低いという問題点があった。また特許文献１の開示技術では、スラグ剤にＺｒＯ2を含有するため、スラグの良好な剥離性を確保することができず、溶接作業性の向上が図れないという問題点もあった。 However, the flux-cored wire disclosed in Patent Document 1 has a problem that the tensile strength of the weld metal is low because the amount of Ni is as large as 9.5 to 11.5% with respect to the total weight of the wire. . Further, in the disclosed technique of Patent Document 1, since ZrO 2 is contained in the slag agent, there is a problem in that good slag releasability cannot be ensured and welding workability cannot be improved.
特許文献２に開示されているフラックス入りワイヤは、ワイヤ全重量に対してＮｉが９．０〜１４．０％もの多量に亘り含有するため、溶着金属の引張強さが低いという問題点もあった。また特許文献２の開示技術では、ＳｉＯ2の含有量がワイヤ全重量に対して０．１〜０．５％と少ないため、スラグ剥離性が十分ではなく、溶接作業性の向上が図れないという問題点もあった。。 The flux-cored wire disclosed in Patent Document 2 has a problem that the tensile strength of the weld metal is low because Ni is contained in a large amount of 9.0 to 14.0% with respect to the total weight of the wire. It was. Further, in the disclosed technique of Patent Document 2, since the content of SiO 2 is as small as 0.1 to 0.5% with respect to the total weight of the wire, the slag removability is not sufficient and the welding workability cannot be improved. There was also a problem. .
そこで本発明は、上述した問題点に鑑みて案出されたものであり、高強度オーステナイト系ステンレス鋼のガスシールドアーク溶接に用いるフラックス入りワイヤに関し、特にＮを多量に含有するオーステナイト系ステンレス鋼の溶接において、母材と同等の高い引張強さが得られ、スラグ剥離性等を向上させることで良好な溶接作業性を確保することが可能なステンレス鋼溶接用フラックス入りワイヤを提供することを目的とする。 Therefore, the present invention has been devised in view of the above-described problems, and relates to a flux-cored wire used for gas shielded arc welding of high-strength austenitic stainless steel, particularly of austenitic stainless steel containing a large amount of N. An object of the present invention is to provide a flux-cored wire for stainless steel welding that has a high tensile strength equivalent to that of the base material in welding and can ensure good welding workability by improving slag peelability and the like. And
本発明者らは、前記課題を解決するためにＮを多量に含有するオーステナイト系ステンレス鋼ＳＵＳ３０４Ｎ２及びＳＵＳ３０４Ｎ２Ａ等を、フラックス入りワイヤを用いてガスシールドアーク溶接した場合に、スラグの剥離性が良好で、かつ得られる溶接金属が母材と同等の引張強さが得られるステンレス鋼溶接用フラックス入りワイヤについて種々検討を行った。 In order to solve the above problems, the present inventors have good slag releasability when austenitic stainless steels SUS304N2 and SUS304N2A containing a large amount of N are gas shielded arc welded using a flux-cored wire. In addition, various studies were made on flux-cored wires for stainless steel welding, in which the obtained weld metal has the same tensile strength as that of the base metal.
その結果、Ｎｉ量を低減して溶着金属及び継手溶接金属のフェライト量を多くすることによって、溶接金属の引張強さを高くできることを新たに見出した。しかし、Ｎｉ量を低減させただけでは安定した高い引張強さが得られず、母材の希釈を受けた溶接継手では、母材よりも低い引張強さになることが確認された。 As a result, it has been newly found that the tensile strength of the weld metal can be increased by reducing the amount of Ni and increasing the amount of ferrite in the weld metal and joint weld metal. However, it was confirmed that a stable high tensile strength could not be obtained only by reducing the amount of Ni, and that a weld joint that had undergone dilution of the base metal had a lower tensile strength than the base metal.
このため、侵入型固溶強化元素であるＣの適正添加を行い、引張強さの向上を図った。しかし、Ｃを単純に添加しただけでは炭化物を析出して靭性が劣化する。そこで、Ｃの固溶度を高めると共に、溶接作業性に悪影響を及ぼすことがないＭｎを適量添加して引張強さ、靭性及び溶接作業性のバランスを保ったワイヤ成分系を確立した。 Therefore, proper addition of C, which is an interstitial solid solution strengthening element, was performed to improve the tensile strength. However, if C is simply added, carbides precipitate and the toughness deteriorates. Accordingly, a wire component system was established in which the solid solubility of C was increased and an appropriate amount of Mn that did not adversely affect welding workability was added to maintain a balance between tensile strength, toughness, and welding workability.
さらに、Ｎを含有させたステンレス鋼の溶接で、スラグ剥離性等をより向上させるため、スラグ剤の成分系等を種々検討した結果、スラグ剥離性劣化の原因となるＡｌ2Ｏ3及びＺｒＯ2をできる限り添加せず、ガラス質で滑らかなスラグを形成するＳｉＯ2を積極的に添加することによって良好なスラグ剥離性が得られることを検証した。 Furthermore, in order to further improve the slag releasability and the like in welding of stainless steel containing N, Al 2 O 3 and ZrO 2 that cause deterioration of slag releasability as a result of various investigations on the component system of the slag agent It was verified that good slag removability can be obtained by positively adding SiO 2 that forms vitreous and smooth slag.
本発明は以上の知見によりなされたもので、その要旨とするところは、ステンレス鋼外皮にフラックスを充填してなるステンレス鋼溶接用フラックス入りワイヤにおいて、ワイヤ全質量に対する質量％で、ステンレス鋼外皮とフラックスの合計で、Ｃ：０．０３〜０．１５％、Ｓｉ：０．１５〜０．７％、Ｍｎ：２〜５％、Ｎｉ：７〜９％、Ｃｒ：２０〜２５％、Ｎ：０．１〜０．３％を含有し、フラックスに、ＴｉＯ2：３〜８％、ＳｉＯ2：０．５〜２％、金属弗化物の１種または２種以上の合計：０．１〜３．０％を含有し、Ａｌ2Ｏ3及びＺｒＯ2の１種又は２種の合計：０．１％以下、かつスラグ剤成分の合計：５〜１０％、フラックス充填率：１５〜２７％で、残部はステンレス外皮のＦｅ分、フラックスの合金鉄中のＦｅ分、鉄粉及び不可避不純物であることを特徴とする。 The present invention has been made based on the above knowledge, and the gist of the present invention is that, in a flux-cored wire for welding stainless steel formed by filling a stainless steel outer shell with flux, in mass% with respect to the total mass of the wire, Total flux: C: 0.03-0.15%, Si: 0.15-0.7%, Mn: 2-5%, Ni: 7-9%, Cr: 20-25%, N: It contains 0.1 to 0.3%, and the flux contains TiO 2 : 3 to 8%, SiO 2 : 0.5 to 2%, a total of one or more metal fluorides: 0.1 to 0.2% Containing 3.0%, total of one or two of Al 2 O 3 and ZrO 2 : 0.1% or less, and total of slag component: 5 to 10%, flux filling ratio: 15 to 27% The balance is the Fe content of the stainless steel outer shell, the Fe content in the alloy iron of the flux, It is characterized by powder and inevitable impurities.
また本発明は、上述した構成に加えて、ステンレス鋼外皮とフラックスの合計でＮｂ：０．０１〜０．５％と、フラックスに金属Ｂｉ及び酸化ＢｉのＢｉ換算値の１種又は２種の合計：０．０１〜０．１５％との何れか一方または両方を更に含有することを特徴とする。 The present invention, in addition to the above-described configuration, the sum of stainless steel outer skin and the flux Nb: 0.01 to 0.5% and, of Bi converted value of metal Bi and Bi oxide to the flux of one or two Total: Any one or both of 0.01 to 0.15% is further contained.
さらに本発明は、上述した構成に加えて、フラックスにＮａ2Ｏ及びＫ2Ｏの１種又は２種の合計：０．０２〜０．２０％を含有することも特徴とする。 Furthermore, in addition to the above-described configuration, the present invention is characterized in that the flux contains a total of 0.02 to 0.20% of one or two of Na 2 O and K 2 O.
上述した構成からなる本発明に係るステンレス鋼溶接用フラックス入りワイヤによれば、Ｎを多量に含有するオーステナイト系ステンレス鋼のガスシールドアーク溶接に適用することにより、アークを安定させてスパッタ発生量を低減させ、スラグの剥離性を向上させるとともに良好なビード形状が得られ、溶接欠陥がなく母材と同等の高い引張強さが得られるとともに延性及び靭性の良好な溶接継手を得ることができる。 According to the flux-cored wire for welding stainless steel according to the present invention having the above-described configuration, by applying it to gas shielded arc welding of austenitic stainless steel containing a large amount of N, the arc is stabilized and the amount of spatter generated is reduced. Thus, it is possible to improve the slag peelability and obtain a good bead shape, to obtain a welded joint having good weldability and ductility and toughness while obtaining high tensile strength equivalent to that of the base material without welding defects.
以下、本発明の実施の形態としてのステンレス鋼溶接用フラックス入りワイヤについて詳細に説明する。 Hereinafter, a stainless steel welding flux cored wire as an embodiment of the present invention will be described in detail.
本発明を適用したステンレス鋼溶接用フラックス入りワイヤは、ステンレス鋼外皮および充填フラックスの各成分組成それぞれの共存による単独および相乗効果によりなし得たものであるが、以下にそれぞれの各成分組成の添加理由および限定理由について説明する。なお、各成分の含有量は、フラックス入りワイヤ全質量に対する質量％で表すこととし、その質量％を表すときには単に％と記載して表すこととする。 The flux-cored wire for stainless steel welding to which the present invention is applied can be achieved by a single effect and a synergistic effect due to the coexistence of each component composition of the stainless steel sheath and the filling flux. The reason and limitation reason will be described. The content of each component is expressed by mass% with respect to the total mass of the flux-cored wire, and when expressing the mass%, it is simply expressed as%.
ステンレス鋼外皮とフラックスの合計でＣ：０．０３〜０．１５％
Ｃは、溶接継手の引張強さを向上させる効果がある。Ｃが０．０３％未満の場合、Ｎｉが適量であっても溶接継手の引張強さが低くなる。一方、Ｃが０．１５％を超えると、溶着金属の靭性が低下する。従って、ステンレス鋼外皮とフラックスの合計でＣは０．０３〜０．１５％とする。なお、Ｃ源として、ステンレス鋼外皮に含まれる成分の他、フラックスから高炭Ｆｅ−Ｍｎ、高炭Ｆｅ−Ｃｒ等のＣ含有鉄合金粉末から添加できる。
C: 0.03 to 0.15% in total of stainless steel hull and flux
C has an effect of improving the tensile strength of the welded joint. When C is less than 0.03%, the tensile strength of the welded joint is lowered even if Ni is in an appropriate amount. On the other hand, when C exceeds 0.15%, the toughness of the deposited metal decreases. Therefore, C is 0.03 to 0.15% in total of the stainless steel skin and the flux. In addition to the components contained in the stainless steel skin, the C source can be added from a C-containing iron alloy powder such as high-carbon Fe—Mn and high-carbon Fe—Cr from the flux.
ステンレス鋼外皮とフラックスの合計でＳｉ：０．１５〜０．７％
Ｓｉは、脱酸剤として作用し、溶着金属の酸素量を低減して良好な延性が得られる。Ｓｉが０．１５％未満であると、溶着金属の伸びが低くなる。一方、Ｓｉが０．７％を超えると、Ｓｉ系酸化物が溶接金属内に介在物として分散析出し、溶接継手の曲げ延性が劣化する。従って、ステンレス鋼外皮とフラックスの合計でＳｉは０．１５〜０．７％とする。なお、Ｓｉ源として、ステンレス鋼外皮に含まれる成分の他、フラックスからＦｅ−Ｓｉ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉末から添加できる。
Total of stainless steel outer shell and flux Si: 0.15-0.7%
Si acts as a deoxidizer and reduces the amount of oxygen in the deposited metal to obtain good ductility. When Si is less than 0.15%, the elongation of the deposited metal is lowered. On the other hand, when Si exceeds 0.7%, Si-based oxides are dispersed and deposited as inclusions in the weld metal, and the bending ductility of the welded joint deteriorates. Therefore, Si is 0.15 to 0.7% in total of the stainless steel skin and the flux. In addition to the components contained in the stainless steel skin, the Si source can be added from an alloy powder such as Fe-Si, Fe-Si-Mn, etc. from the flux.
ステンレス鋼外皮とフラックスの合計でＭｎ：２〜５％
Ｍｎは、Ｃの固溶度を高くする。Ｍｎが２％未満では、Ｃの歩留りが低くなり溶接継手の引張強さが低くなる。一方、Ｍｎが５％を超えると、ＭｎＳの過度の析出を促して靭性が低下する。従って、ステンレス鋼外皮とフラックスの合計でＭｎは２〜５％とする。なお、Ｍｎ源として、ステンレス鋼外皮に含まれる成分の他、フラックスから金属Ｍｎ、Ｆｅ−Ｍｎ、高炭Ｆｅ−Ｍｎ等の金属粉末から添加できる。
Mn: 2-5% in total of stainless steel shell and flux
Mn increases the solid solubility of C. If Mn is less than 2%, the yield of C will be low and the tensile strength of the welded joint will be low. On the other hand, if Mn exceeds 5%, excessive precipitation of MnS is promoted and toughness is lowered. Therefore, Mn is 2 to 5% in total of the stainless steel skin and the flux. In addition to the components contained in the stainless steel shell, the Mn source can be added from a metal powder such as metal Mn, Fe—Mn, high charcoal Fe—Mn, etc. from the flux.
ステンレス鋼外皮とフラックスの合計でＮｉ：７〜９％
Ｎｉは、オーステナイト相を安定化させ、延性が良好な溶着金属が得られる。Ｎｉが７％未満では、オーステナイト相の安定が不十分で、溶着金属の伸びが低くなる。一方、Ｎｉが９％を超えると、フェライト相の晶出を抑制して溶着金属のフェライト量が少なく、引張強さが低くなる。従って、ステンレス鋼外皮とフラックスの合計でＮｉは７〜９％とする。なお、Ｎｉ源として、ステンレス鋼外皮に含まれる成分の他、フラックスから金属Ｎｉ等の金属粉末から添加できる。
Ni: 7-9% in total of stainless steel shell and flux
Ni stabilizes the austenite phase and provides a weld metal with good ductility. If Ni is less than 7%, the stability of the austenite phase is insufficient, and the elongation of the deposited metal becomes low. On the other hand, if Ni exceeds 9%, crystallization of the ferrite phase is suppressed, the amount of ferrite in the weld metal is small, and the tensile strength is low. Therefore, Ni is 7 to 9% in total of the stainless steel skin and the flux. In addition to the components contained in the stainless steel shell, the Ni source can be added from metal powder such as metal Ni from the flux.
ステンレス鋼外皮とフラックスの合計でＣｒ：２０〜２５％
Ｃｒは、安定したフェライト相を晶出し、ＰやＳ等の低融点化合物を析出させる元素を固溶させて高温割れを防止する。Ｃｒが２０％未満では、フェライト相の晶出量が少なくなって割れが発生しやすい。一方、Ｃｒが２５％を超えると、Ｃｒ炭化物をフェライト粒内及び粒界に析出させて曲げ延性が劣化する。従って、ステンレス鋼外皮とフラックスの合計でＣｒは２０〜２５％とする。なお、Ｃｒ源として、ステンレス鋼外皮に含まれる成分の他、フラックスから金属Ｃｒ、Ｆｅ−Ｃｒ、高炭Ｆｅ−Ｃｒ、窒化Ｆｅ−Ｃｒ等の金属粉末から添加できる。
The sum of stainless steel shell and flux is Cr: 20-25%
Cr crystallizes a stable ferrite phase and dissolves an element that precipitates a low melting point compound such as P or S to prevent hot cracking. If Cr is less than 20%, the amount of crystallization of the ferrite phase decreases and cracks are likely to occur. On the other hand, if Cr exceeds 25%, Cr carbide precipitates in the ferrite grains and in the grain boundaries, and the bending ductility deteriorates. Therefore, Cr is 20 to 25% in total of the stainless steel skin and the flux. In addition to the components contained in the stainless steel shell, the Cr source can be added from a metal powder such as metal Cr, Fe—Cr, high charcoal Fe—Cr, or nitrided Fe—Cr from a flux.
ステンレス鋼外皮とフラックスの合計でＮ：０．１〜０．３％
Ｎは、オーステナイト相の固溶強化を行い、安定した高い引張強さの溶着金属が得られる。Ｎが０．１％未満では、溶着金属の引張強さが低くなる。一方、Ｎが０．３％を超えると、固溶できないＮが気泡となってブローホールが発生する。従って、ステンレス鋼外皮とフラックスの合計でＮは０．１〜０．３％とする。なお、Ｎ源として、ステンレス鋼外皮に含まれる成分の他、フラックスから窒化Ｍｎ、窒化Ｆｅ−Ｃｒ等の金属粉末から添加できる。
The total of stainless steel hull and flux N: 0.1-0.3%
N performs solid solution strengthening of the austenite phase, and a stable high tensile strength weld metal is obtained. If N is less than 0.1%, the tensile strength of the weld metal is low. On the other hand, if N exceeds 0.3%, N that cannot be dissolved becomes bubbles and blowholes are generated. Therefore, N is 0.1 to 0.3% in total of the stainless steel skin and the flux. In addition to the components contained in the stainless steel shell, the N source can be added from a metal powder such as Mn nitride, Fe-Cr nitride, etc. from the flux.
フラックスに含有するＴｉＯ 2 ：３〜８％
ＴｉＯ2は、被包性が良好なスラグを形成してビード形状を良好にする。ＴｉＯ2が３％未満では、その効果が十分に得られずビード形状が凸状となる。一方、ＴｉＯ2が８％を超えると、アーク長が長くなり溶滴の離脱を阻害してスパッタが多発する。従って、フラックスに含有するＴｉＯ2は３〜８％とする。なお、ＴｉＯ2源として、ルチール、イルミナイト、チタンスラグ、チタン酸カルシウム、チタン酸カリウム等を使用する。
TiO 2 contained in flux : 3-8%
TiO 2 forms a slag with good encapsulation and makes the bead shape good. If TiO 2 is less than 3%, the effect cannot be sufficiently obtained, and the bead shape becomes convex. On the other hand, if TiO 2 exceeds 8%, the arc length becomes long and the detachment of the droplets is inhibited, resulting in frequent spattering. Therefore, TiO 2 contained in the flux to 3-8%. In addition, as a TiO 2 source, rutile, illuminite, titanium slag, calcium titanate, potassium titanate, or the like is used.
フラックスに含有するＳｉＯ 2 ：０．５〜２％
ＳｉＯ2は、スラグをガラス質として砕けやすくするのでスラグ剥離性を良好とする。ＳｉＯ2が０．５％未満では、スラグのガラス化が不十分であるので除去しにくく剥離性が悪くなる。一方、ＳｉＯ2が２％を超えると、アークの安定性が劣化して溶接作業が悪くなる。従って、フラックスに含有するＳｉＯ2は０．５〜２％とする。ＳｉＯ2源として、珪砂、珪灰石、カリ長石、ソーダ長石、珪酸カリ、珪酸ソーダ等から添加できる。
SiO 2 contained in the flux : 0.5-2%
Since SiO 2 makes the slag vitrified easily, it makes the slag peelable good. If SiO 2 is less than 0.5%, the slag is insufficiently vitrified, so that it is difficult to remove and the peelability becomes poor. On the other hand, if SiO 2 exceeds 2%, the stability of the arc deteriorates and the welding operation becomes worse. Thus, SiO 2 contained in the flux is 0.5 to 2%. As the SiO 2 source, silica sand, wollastonite, potassium feldspar, soda feldspar, potassium silicate, sodium silicate, or the like can be added.
フラックスに含有する金属弗化物の1種又は２種以上の合計：０．１〜３．０％
金属弗化物は、アークの安定性を良好にする。特にＮ含有ステンレス鋼の溶接では、溶着金属に固溶されないＮがＮ2ガスとしてアーク雰囲気に放出されてアークを緊縮させてアーク安定性を阻害する。従って、アーク安定性を向上させる金属弗化物の添加は必須となる。金属弗化物の1種又は２種以上の合計が０．１％未満では、アーク状態が不安定となる。一方、金属弗化物の1種又は２種以上の合計が３．０％を超えると、溶滴が爆発移行となりやすくスパッタが多発する。従って、金属弗化物の1種又は２種以上の合計は、０．１〜３．０％とする。金属弗化物源として、ＡｌＦ3、ＮａＦ、Ｋ2ＺｒＦ6、ＬｉＦ等を使用する。
Total of one or more metal fluorides contained in the flux: 0.1 to 3.0%
Metal fluorides improve the arc stability. In particular, in the welding of N-containing stainless steel, N that is not solid-dissolved in the deposited metal is released as N 2 gas into the arc atmosphere, and the arc is contracted to inhibit arc stability. Therefore, the addition of a metal fluoride that improves the arc stability is essential. If the total of one or more metal fluorides is less than 0.1%, the arc state becomes unstable. On the other hand, if the total of one or more of the metal fluorides exceeds 3.0%, the droplets are liable to explode and spatter frequently occurs. Accordingly, the total of one or more metal fluorides is 0.1 to 3.0%. As the metal fluoride source, AlF 3 , NaF, K 2 ZrF 6 , LiF or the like is used.
フラックスに含有するＡｌ 2 Ｏ 3 及びＺｒＯ 2 の１種又は２種の合計：０．１％以下
Ａｌ2Ｏ3及びＺｒＯ2は、Ｎと結合して、スラグ剥離性を劣化させる窒化物を生成するのでできる限り低い方が好ましい。従って、Ａｌ2Ｏ3及びＺｒＯ2の１種又は２種の合計は０．１以下とする。Ａｌ2Ｏ3源として、カリ長石、ソーダ長石、珪砂等に含まれる不純物があり、できる限りＡｌ2Ｏ3含有量の低いフラックス原料を使用する。また、ＺｒＯ2源として、ルチール等に含まれる不純物があるが、できる限りＺｒＯ2含有量が低いフラックス原料を使用する。
Total of one or two of Al 2 O 3 and ZrO 2 contained in the flux : 0.1% or less Al 2 O 3 and ZrO 2 combine with N to form nitrides that degrade slag removability Therefore, the lower one is preferable. Therefore, the total of one or two of Al 2 O 3 and ZrO 2 is 0.1 or less. As an Al 2 O 3 source, there are impurities contained in potash feldspar, soda feldspar, silica sand, etc., and a flux raw material having as low an Al 2 O 3 content as possible is used. Further, as a ZrO 2 source, there is an impurity contained in rutile or the like, but a flux raw material having a ZrO 2 content as low as possible is used.
スラグ剤成分の合計：５〜１０％
酸化物及び金属弗化物からなるスラグ成分剤の合計は、被包性が良好なスラグを形成してビード形状を良好する。この効果は５％以上添加することによって得られる。一方、スラグ剤成分の合計が１０％を超えると、溶滴にスラグ剤が絡み合って溶滴移行状態が不安定でスパッタの発生量が多くなる。従って、スラグ剤の合計は５〜１０％とする。
Total slag component: 5-10%
The total of the slag component agents composed of oxide and metal fluoride forms a slag with good encapsulating properties and a good bead shape. This effect can be obtained by adding 5% or more. On the other hand, when the total of the slag agent components exceeds 10%, the slag agent is entangled with the droplets, the droplet transfer state is unstable, and the amount of spatter generated increases. Therefore, the total amount of the slag agent is 5 to 10%.
フラックス充填率：１５〜２７％
ステンレス鋼外皮へのフラックス充填率が１５％未満では、ステンレス鋼外皮の肉厚が厚くなり、溶滴の離脱がスムーズに行われずに溶滴が離脱する際に大きなスパッタが発生する。一方、フラックス充填率が２７％を超えると、ワイヤ製造時に断線が生じやすく生産性が悪くなる。従って、フラックス充填率は１５〜２７％とする。充填率の増減は、鉄粉やＳＵＳ３０４Ｌステンレス粉末等を使用して調整することができる。
Flux filling rate: 15-27%
When the flux filling rate into the stainless steel outer shell is less than 15%, the thickness of the stainless steel outer shell becomes thick and large spatter is generated when the droplets are released without being smoothly released. On the other hand, if the flux filling rate exceeds 27%, disconnection is likely to occur during wire production, and the productivity is deteriorated. Therefore, the flux filling rate is 15 to 27%. The increase / decrease in the filling rate can be adjusted using iron powder, SUS304L stainless steel powder, or the like.
以降の成分の限定については、本発明を適用したステンレス鋼溶接用フラックス入りワイヤにおいて必須にはならない。 The limitation of the subsequent components is not essential in the stainless steel welding flux cored wire to which the present invention is applied.
ステンレス鋼外皮とフラックスの合計でＮｂ：０．０１〜０．５％
Ｎｂは、微量の添加で引張強さを向上させる。Ｎｂが０．０１％未満であると、引張強さ向上の効果がない。一方、Ｎｂが０．５％を超えると、高温割れが生じやすくなる。また、ＮｂＣが析出して靭性を劣化させる。従って、ステンレス鋼外皮とフラックスの合計でＮｂは０．０１〜０．５％とする。なお、Ｎｂ源として、ステンレス鋼外皮に含まれる成分の他、フラックスから金属Ｎｂ、Ｆｅ−Ｎｂ等の金属粉末から添加できる。
Nb: 0.01 to 0.5% in total of stainless steel outer shell and flux
Nb improves the tensile strength when added in a small amount. If Nb is less than 0.01%, there is no effect of improving the tensile strength. On the other hand, if Nb exceeds 0.5%, hot cracking tends to occur. Moreover, NbC precipitates and deteriorates toughness. Therefore, Nb is 0.01 to 0.5% in total of the stainless steel outer shell and the flux. In addition to the components contained in the stainless steel shell, the Nb source can be added from a metal powder such as metal Nb or Fe—Nb from a flux.
フラックスに含有する金属Ｂｉ及び酸化ＢｉのＢｉ換算値の１種又は２種の合計：０．０１〜０．１５％
Ｂｉは、スラグ剥離性を向上させる。Ｂｉ換算値が０．０１％未満であると、スラグ剥離性を向上させる効果は得られない。一方、Ｂｉ換算値が０．１５％を超えると、高温割れが生じやすくなる。またＢｉ換算値が０．１５％を超えると、靭性を劣化させる。従って、フラックスに含有する金属Ｂｉ及び酸化ＢｉのＢｉ換算値の１種又は２種の合計は０．０１〜０．１５％とする。
Total of one or two of Bi converted values of metal Bi and oxidized Bi contained in the flux: 0.01 to 0.15%
Bi improves slag peelability. The effect which improves slag peelability is not acquired as Bi conversion value is less than 0.01%. On the other hand, when the Bi equivalent value exceeds 0.15%, hot cracking is likely to occur. Moreover, when Bi converted value exceeds 0.15%, toughness will be deteriorated. Accordingly, the total of one or two of Bi converted values of metal Bi and oxidized Bi contained in the flux is set to 0.01 to 0.15%.
フラックスに含有するＮａ 2 Ｏ及びＫ 2 Ｏの１種又は２種の合計：０．０２〜０．２０％
Ｎａ2Ｏ及びＫ2Ｏは、アークを安定にしてスパッタの発生を抑制する。Ｎａ2Ｏ及びＫ2Ｏの１種又は２種の合計が０．０２％未満であると、アークを安定にする効果が得られない。一方、Ｎａ2Ｏ及びＫ2Ｏの１種又は２種の合計が０．２０％を超えると、スパッタの発生量が増加する。なお、Ｎａ2Ｏ及びＫ2Ｏ源は、珪酸ソーダ及び珪酸カリからなる水ガラスから添加できる。
Total of one or two of Na 2 O and K 2 O contained in the flux : 0.02 to 0.20%
Na 2 O and K 2 O stabilize the arc and suppress the occurrence of sputtering. If the total of one or two of Na 2 O and K 2 O is less than 0.02%, the effect of stabilizing the arc cannot be obtained. On the other hand, when the total of one or two of Na 2 O and K 2 O exceeds 0.20%, the amount of spatter generated increases. Na 2 O and K 2 O sources can be added from water glass made of sodium silicate and potassium silicate.
以上、本発明のステンレス鋼溶接用フラックス入りワイヤの成分組成の限定理由を述べたが、その他の成分として、Ｃｕ：０．５％以下、Ｍｏ：０．５％以下の範囲で機械性能の調整として添加することができる。また、耐割れ性確保の観点から、低融点介在物の析出を促進するＰ及びＳは、Ｐ：０．０４０％以下、Ｓ：０．０３０％以下であることが好ましい。また、その他スラグ剤として、ＦｅＯ、Ｆｅ2Ｏ3、ＣａＯ、ＭｇＯ、ＭｎＯ等をアーク安定性やスパッタの発生防止、スラグ剥離性向上を目的として合計で０．５％以下の範囲で適宜添加調整することができる。 The reason for limiting the component composition of the flux-cored wire for welding stainless steel according to the present invention has been described above. However, as other components, adjustment of mechanical performance is within a range of Cu: 0.5% or less and Mo: 0.5% or less. Can be added as Further, from the viewpoint of ensuring crack resistance, P and S that promote precipitation of low melting point inclusions are preferably P: 0.040% or less and S: 0.030% or less. As other slag agents, FeO, Fe 2 O 3 , CaO, MgO, MnO, etc. are added and adjusted as appropriate within a total range of 0.5% or less for the purpose of arc stability, prevention of spatter generation, and improvement of slag peelability. can do.
本発明のステンレス鋼溶接用フラックス入りワイヤの製造方法について言及する。例えばステンレス鋼外皮を帯鋼より管状に成形する場合には、配合、撹拌、乾燥した充填フラックスをＵ形に成形した溝に満たした後丸形に成形し、所定のワイヤ径まで伸線する。この際、整形した外皮シームを溶接することで、シームレスタイプのフラックス入りワイヤとすることもできる。またステンレス鋼外皮がパイプの場合には、パイプを振動させてフラックスを充填し、所定のワイヤ径まで伸線する。 Reference is made to the method for producing a flux-cored wire for welding stainless steel of the present invention. For example, when a stainless steel skin is formed into a tubular shape from a steel strip, the filling flux mixed, stirred, and dried is filled into a U-shaped groove, then formed into a round shape, and drawn to a predetermined wire diameter. At this time, a seamless type flux-cored wire can be obtained by welding the shaped outer seam. When the stainless steel sheath is a pipe, the pipe is vibrated, filled with flux, and drawn to a predetermined wire diameter.
充填フラックスは、供給、充填が円滑に行えるように、水ガラス（珪酸カリおよび珪酸ソーダの水溶液）を添加造粒して用いることもできる。 The filling flux can be used by adding and granulating water glass (aqueous solution of potassium silicate and sodium silicate) so that supply and filling can be performed smoothly.
以下、実施例により本発明を詳細に説明する。 Hereinafter, the present invention will be described in detail by way of examples.
表１に示す化学成分のオーステナイト系ステンレス鋼外皮（Ｗ１、Ｗ２）を用いて表２に示す各種組成のステンレス鋼溶接用フラックス入りワイヤを試作した。ちなみに、この表２における「ワイヤ全質量に対する質量％」は、表１に示すオーステナイト系ステンレス鋼外皮（Ｗ１、Ｗ２）にフラックスを充填したステンレス鋼外皮とフラックスの合計の量における、ワイヤ全質量に対する質量％を意味するものである。なお、試作したワイヤ径は、直径１．２ｍｍとした。 Using the austenitic stainless steel skins (W1, W2) having the chemical components shown in Table 1, flux-cored wires for welding stainless steel having various compositions shown in Table 2 were produced. Incidentally, “mass% with respect to the total mass of the wire” in Table 2 is based on the total mass of the wire in the total amount of the austenitic stainless steel outer shell (W1, W2) shown in Table 1 filled with the flux and the flux. It means mass%. The trial wire diameter was 1.2 mm.
溶着金属試験は、ＪＩＳ Ｚ ３３２３に従いＳＭ４９０Ａ鋼に２層バタリングを行った開先を用いて溶接を行い、引張試験及び衝撃試験を実施した。 In the weld metal test, welding was performed using a groove obtained by performing two-layer buttering on SM490A steel in accordance with JIS Z 3323, and a tensile test and an impact test were performed.
溶接継手性能は、表３に示す板厚１２ｍｍのＳＵＳ３０４Ｎ２Ａ鋼を用い、開先角度６０°、ギャップ３ｍｍ、裏当て金ありの溶接継手を下向姿勢にて作製した。溶接継手は、ＪＩＳ Ｚ ３１０６に従ってＸ線透過試験を実施し、割れ及びブローホール発生状況の調査を行った。溶接継手の機械性能は、ＪＩＳ Ｚ ３１２１に従い１Ａ号試験片にて継手引張試験を行った。また、ＪＩＳ Ｚ ３１２２に従い、溶接継手の表曲げ試験を行った。溶着金属性能は、引張強さ：６９０ＭＰａ以上、伸び：２０％以上、衝撃試験−２０℃における吸収エネルギー（ｖＥ−２０℃）：１５Ｊ以上を良好とした。溶接継手のＸ線透過試験は、きずの像の分類をＪＩＳ Ｚ ３１０４に基づいて行い、第１種１類を良好とした。溶接継手の機械性能は、継手の引張強さ：６９０ＭＰａ以上、表曲げ試験：無欠陥を良好とした。 As for the weld joint performance, SUS304N2A steel having a thickness of 12 mm shown in Table 3 was used, and a weld joint with a groove angle of 60 °, a gap of 3 mm, and a backing metal was produced in a downward posture. The welded joint was subjected to an X-ray transmission test according to JIS Z 3106, and the occurrence of cracks and blowholes was investigated. As for the mechanical performance of the welded joint, a joint tensile test was performed using a No. 1A test piece in accordance with JIS Z 3121. Moreover, according to JIS Z 3122, the surface bending test of the welded joint was done. As for the weld metal performance, tensile strength: 690 MPa or more, elongation: 20% or more, impact test −20 ° C. absorbed energy (vE-20 ° C.): 15 J or more were considered good. In the X-ray transmission test of the welded joint, the classification of the flaw image was performed based on JIS Z 3104, and the first kind and the first kind were considered good. As for the mechanical performance of the welded joint, the tensile strength of the joint: 690 MPa or more and the surface bending test: no defect were considered good.
溶接作業性は、表３に示すＳＵＳ３０４Ｎ２Ａ鋼を用いて水平すみ肉溶接を行い、アーク安定性、スパッタの多少、スラグ剥離性及びビード形状を調べた。なお、溶着金属試験、溶接継手試験及び溶接作業性の調査の溶接電流は１８０〜２５０Ａ、シールドガス：ＣＯ2で実施した。それらの結果を表４にまとめて示す。 For welding workability, horizontal fillet welding was performed using SUS304N2A steel shown in Table 3, and the arc stability, the degree of spatter, the slag peelability, and the bead shape were examined. In addition, the welding current of the welding metal test, the welded joint test, and the investigation of the welding workability was carried out with 180 to 250 A and shield gas: CO 2 . The results are summarized in Table 4.
表２および表４中のワイヤＮｏ．１〜１３が本願発明例、ワイヤＮｏ．１４〜２６は比較例である。本願発明例であるワイヤＮｏ．１〜１３は、Ｃ、Ｓｉ、Ｍｎ、Ｎｉ、Ｃｒ、Ｎ、ＴｉＯ2、ＳｉＯ2、金属弗化物の合計、Ａｌ2Ｏ3とＺｒＯ2の合計、スラグ剤成分の合計及びフラックスの充填率が本発明において規定した範囲に含まれているため、溶着金属の引張強さ、伸び及び吸収エネルギーが高く、溶接継手のＸ線透過試験結果、引張強さ及び曲げ性能も良好で、アークが安定でスパッタの発生が少なく、スラグ剥離性及びビード形状も良好である等、極めて満足な結果であった。なお、Ｎｂを適量含むワイヤＮｏ．４、５、８及びワイヤＮｏ．１１は、溶着金属及び溶接継手の引張強さが高く、Ｂｉを適量含むワイヤＮｏ．３、５、１０及びワイヤＮｏ．１３は、スラグ剥離性が非常に良好であった。さらに、Ｎａ2Ｏ及びＫ2Ｏの１種又は２種を適量含むワイヤＮｏ．１、４、６、７、９、１０及びワイヤＮｏ．１１は、アークが非常に安定していた。 In Table 2 and Table 4, the wire No. 1 to 13 are examples of the present invention, wire Nos. 14 to 26 are comparative examples. Wire No. which is an example of the present invention. 1 to 13 are C, Si, Mn, Ni, Cr, N, TiO 2 , SiO 2 , total of metal fluorides, total of Al 2 O 3 and ZrO 2 , total of slag agent components, and flux filling rate Since it is included in the range specified in the present invention, the tensile strength, elongation and absorbed energy of the weld metal are high, the X-ray transmission test results of the welded joint, the tensile strength and bending performance are good, and the arc is stable. The results were extremely satisfactory, such as low spatter generation and good slag peelability and bead shape. Note that a wire No. containing an appropriate amount of Nb. 4, 5, 8 and wire no. No. 11 is a wire no. 3, 5, 10 and wire no. No. 13 had very good slag peelability. Furthermore, a wire No. containing an appropriate amount of one or two of Na 2 O and K 2 O is used. 1, 4, 6, 7, 9, 10 and wire no. In No. 11, the arc was very stable.
比較例中ワイヤＮｏ．１４は、Ｃが少ないので、溶接継手の引張強さが低かった。また、ＴｉＯ2が多いので、スパッタの発生量が多かった。 In the comparative example, the wire No. No. 14 had less C, so the tensile strength of the welded joint was low. Further, since the amount of TiO 2 was large, the amount of spatter generated was large.
ワイヤＮｏ．１５は、Ｃが多いので、溶着金属の吸収エネルギーが低かった。また、ＴｉＯ2が少ないので、スラグの被包性が悪くビード形状が不良であった。 Wire No. Since No. 15 had a lot of C, the absorbed energy of the deposited metal was low. Further, since TiO 2 is less, the bead shape poor encapsulation of the slag was poor.
ワイヤＮｏ．１６は、Ｓｉが少ないので、溶着金属の伸びが低かった。また、金属弗化物の合計が多いので、スパッタ発生量が多かった。 Wire No. Since No. 16 had little Si, the elongation of the weld metal was low. Further, since the total amount of metal fluoride was large, the amount of spatter generated was large.
ワイヤＮｏ．１７は、Ｓｉが高いので、曲げ試験で割れが生じた。また、金属弗化物の合計が少ないので、アークが不安定であった。なお、Ｎａ2Ｏが少ないので、アークを安定にする効果は得られなかった。 Wire No. Since No. 17 was high in Si, cracks occurred in the bending test. Also, the arc was unstable because the total amount of metal fluoride was small. Since Na 2 O is less, the effect of stabilizing the arc could not be obtained.
ワイヤＮｏ．１８は、Ｍｎが少ないので、溶接継手の引張強さが低かった。また、ＳｉＯ2が多いので、アークが不安定であった。 Wire No. No. 18 had low Mn, so the tensile strength of the welded joint was low. In addition, since the SiO 2 is large, the arc was unstable.
ワイヤＮｏ．１９は、Ｍｎが多いので、溶着金属の吸収エネルギーが低かった。また、ＳｉＯ2が少ないので、スラグ剥離性が悪かった。なお、Ｂｉが少ないので、スラグ剥離性を向上する効果は得られなかった。 Wire No. No. 19 had a high Mn content, so the absorbed energy of the weld metal was low. Further, since SiO 2 is small, the slag removability is poor. In addition, since there was little Bi, the effect which improves slag peelability was not acquired.
ワイヤＮｏ．２０は、Ｎｉが少ないので、溶着金属の伸びが低かった。また、スラグ剤成分の合計が多いので、スパッタの発生量が多かった。 Wire No. In No. 20, since the amount of Ni was small, the elongation of the deposited metal was low. Further, since the total amount of slag agent components is large, the amount of spatter generated is large.
ワイヤＮｏ．２１は、Ｎｉが多いので、溶着金属及び溶接継手の引張強さが低かった。また、スラグ剤成分の合計が少ないので、スラグ被包性が悪くビード形状が不良であった。さらに、Ｂｉが多いので、割れが生じ、溶着金属の吸収エネルギーも低かった。 Wire No. Since No. 21 has a lot of Ni, the tensile strength of the weld metal and the welded joint was low. Moreover, since the sum total of the slag agent component was small, the slag encapsulation was poor and the bead shape was poor. Furthermore, since there was much Bi, the crack occurred and the absorbed energy of the deposited metal was low.
ワイヤＮｏ．２２は、Ｃｒが少ないので、割れが発生した。また、フラックス充填率が低いので、スパッタの発生量が多かった。 Wire No. Since No. 22 had little Cr, the crack generate | occur | produced. Further, since the flux filling rate was low, the amount of spatter generated was large.
ワイヤＮｏ．２３は、Ｃｒが多いので、曲げ試験で割れが生じた。また、フラックス充填率が高いので、生産時に断線が生じて生産性が悪かった。 Wire No. Since No. 23 had a large amount of Cr, cracking occurred in the bending test. Moreover, since the flux filling rate was high, disconnection occurred during production, resulting in poor productivity.
ワイヤＮｏ．２４は、Ｎｂが多いので、割れが発生し、溶着金属の吸収エネルギーも低かった。また、Ａｌ2Ｏ3とＺｒＯ2の合計が多いので、スラグ剥離性が悪かった。 Wire No. Since No. 24 had a large amount of Nb, cracks occurred and the absorbed energy of the weld metal was low. Further, since the Al 2 O 3 and the sum of ZrO 2 is large, the slag removability is poor.
ワイヤＮｏ．２５は、Ｎが少ないので、溶着金属及び溶接継手の引張強さが低かった。また、Ｎｂが少ないので、溶接金属の引張強さの向上効果は得られなかった。 Wire No. No. 25 had low N, so the tensile strength of the weld metal and the welded joint was low. Moreover, since there is little Nb, the improvement effect of the tensile strength of a weld metal was not acquired.
ワイヤＮｏ．２６は、Ｎが多いので、ブローホールが発生した。また、Ｎａ2ＯとＫ2Ｏの合計が多いので、スパッタの発生量が多かった。 Wire No. No. 26 had a large amount of N, so blow holes were generated. Further, since the total amount of Na 2 O and K 2 O was large, the amount of spatter generated was large.
Claims (3)
ワイヤ全質量に対する質量％で、ステンレス鋼外皮とフラックスの合計で、
Ｃ：０．０３〜０．１５％、
Ｓｉ：０．１５〜０．７％、
Ｍｎ：２〜５％、
Ｎｉ：７〜９％、
Ｃｒ：２０〜２５％、
Ｎ：０．１〜０．３％を含有し、
さらに、フラックスに、
ＴｉＯ2：３〜８％、
ＳｉＯ2：０．５〜２％、
金属弗化物の１種または２種以上の合計：０．１〜３．０％を含有し、
Ａｌ2Ｏ3及びＺｒＯ2の１種又は２種の合計：０．１％以下、かつスラグ剤成分の合計：５〜１０％、
フラックス充填率：１５〜２７％で、残部はステンレス鋼外皮のＦｅ分、フラックスの合金鉄中のＦｅ分、鉄粉及び不可避不純物であることを特徴とするステンレス鋼溶接用フラックス入りワイヤ。 In the flux-cored wire for stainless steel welding formed by filling the stainless steel outer shell with flux,
It is the mass% with respect to the total mass of the wire.
C: 0.03-0.15%,
Si: 0.15 to 0.7%,
Mn: 2 to 5%
Ni: 7-9%,
Cr: 20 to 25%,
N: 0.1 to 0.3% is contained,
Furthermore, in flux,
TiO 2: 3~8%,
SiO 2 : 0.5-2%
A total of one or more metal fluorides: 0.1 to 3.0%,
Total of one or two of Al 2 O 3 and ZrO 2 : 0.1% or less, and the total of slag component: 5 to 10%,
A flux-cored wire for welding stainless steel, characterized in that the flux filling ratio is 15 to 27%, and the balance is the Fe content of the stainless steel skin, the Fe content in the alloy iron of the flux, iron powder, and inevitable impurities.
Ｎｂ：０．０１〜０．５％と、フラックスに金属Ｂｉ及び酸化ＢｉのＢｉ換算値の１種又は２種の合計：０．０１〜０．１５％との何れか一方または両方を更に含有することを特徴とする請求項１に記載のステンレス鋼溶接用フラックス入りワイヤ。 It is the mass% with respect to the total mass of the wire.
Nb: 0.01 to 0.5% and one or both of the total of one or two of Bi converted values of metal Bi and oxidized Bi: 0.01 to 0.15% are further contained in the flux. The flux-cored wire for welding stainless steel according to claim 1.
フラックスにＮａ2Ｏ及びＫ2Ｏの１種又は２種の合計：０．０２〜０．２０％を更に含有することを特徴とする請求項１又は２に記載のステンレス鋼溶接用フラックス入りワイヤ。 % By mass relative to the total mass of the wire
One or two of the total of Na 2 O and K 2 O in the flux: 0.02 to 0.20% further flux-cored wire for stainless steel welding according to claim 1 or 2, characterized in that it contains .
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