JP6110800B2 - Stainless steel flux cored wire - Google Patents
Stainless steel flux cored wire Download PDFInfo
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- JP6110800B2 JP6110800B2 JP2014014164A JP2014014164A JP6110800B2 JP 6110800 B2 JP6110800 B2 JP 6110800B2 JP 2014014164 A JP2014014164 A JP 2014014164A JP 2014014164 A JP2014014164 A JP 2014014164A JP 6110800 B2 JP6110800 B2 JP 6110800B2
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 59
- 239000010935 stainless steel Substances 0.000 title claims description 58
- 230000004907 flux Effects 0.000 title claims description 55
- 238000003466 welding Methods 0.000 claims description 52
- 150000001339 alkali metal compounds Chemical class 0.000 claims description 20
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 13
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 13
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 13
- 150000002222 fluorine compounds Chemical class 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 5
- 239000002893 slag Substances 0.000 description 55
- 229910052751 metal Inorganic materials 0.000 description 26
- 239000002184 metal Substances 0.000 description 26
- 239000011734 sodium Substances 0.000 description 19
- 239000011651 chromium Substances 0.000 description 17
- 230000000694 effects Effects 0.000 description 17
- 239000011324 bead Substances 0.000 description 15
- 239000010936 titanium Substances 0.000 description 15
- 229910001566 austenite Inorganic materials 0.000 description 14
- 229910000859 α-Fe Inorganic materials 0.000 description 14
- 238000006243 chemical reaction Methods 0.000 description 12
- 239000011572 manganese Substances 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 230000007423 decrease Effects 0.000 description 10
- 238000002844 melting Methods 0.000 description 8
- 230000008018 melting Effects 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- 229910052804 chromium Inorganic materials 0.000 description 7
- 238000005538 encapsulation Methods 0.000 description 7
- 150000001875 compounds Chemical class 0.000 description 6
- 238000005336 cracking Methods 0.000 description 6
- 229910052719 titanium Inorganic materials 0.000 description 6
- 238000012546 transfer Methods 0.000 description 6
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 229910052700 potassium Inorganic materials 0.000 description 5
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 4
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000002425 crystallisation Methods 0.000 description 3
- 230000008025 crystallization Effects 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 238000009863 impact test Methods 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 235000019353 potassium silicate Nutrition 0.000 description 3
- 239000004576 sand Substances 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 229910052708 sodium Inorganic materials 0.000 description 3
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 229910052845 zircon Inorganic materials 0.000 description 3
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 3
- 229910000616 Ferromanganese Inorganic materials 0.000 description 2
- ZLMJMSJWJFRBEC-UHFFFAOYSA-N Potassium Chemical compound [K] ZLMJMSJWJFRBEC-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- GEIAQOFPUVMAGM-UHFFFAOYSA-N ZrO Inorganic materials [Zr]=O GEIAQOFPUVMAGM-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 2
- PQXKHYXIUOZZFA-UHFFFAOYSA-M lithium fluoride Chemical compound [Li+].[F-] PQXKHYXIUOZZFA-UHFFFAOYSA-M 0.000 description 2
- 229910001512 metal fluoride Inorganic materials 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000011591 potassium Substances 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Chemical compound [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000004544 sputter deposition Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- IRPGOXJVTQTAAN-UHFFFAOYSA-N 2,2,3,3,3-pentafluoropropanal Chemical compound FC(F)(F)C(F)(F)C=O IRPGOXJVTQTAAN-UHFFFAOYSA-N 0.000 description 1
- KLZUFWVZNOTSEM-UHFFFAOYSA-K Aluminum fluoride Inorganic materials F[Al](F)F KLZUFWVZNOTSEM-UHFFFAOYSA-K 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- 229910001309 Ferromolybdenum Inorganic materials 0.000 description 1
- 229910000863 Ferronickel Inorganic materials 0.000 description 1
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 239000004111 Potassium silicate Substances 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- 239000004115 Sodium Silicate Substances 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- SJKRCWUQJZIWQB-UHFFFAOYSA-N azane;chromium Chemical compound N.[Cr] SJKRCWUQJZIWQB-UHFFFAOYSA-N 0.000 description 1
- RRZKHZBOZDIQJG-UHFFFAOYSA-N azane;manganese Chemical compound N.[Mn] RRZKHZBOZDIQJG-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 229910001610 cryolite Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 239000011737 fluorine Substances 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 239000010436 fluorite Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 229910044991 metal oxide Inorganic materials 0.000 description 1
- 150000004706 metal oxides Chemical class 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 238000005504 petroleum refining Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 1
- 229910052913 potassium silicate Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 235000013024 sodium fluoride Nutrition 0.000 description 1
- 239000011775 sodium fluoride Substances 0.000 description 1
- GROMGGTZECPEKN-UHFFFAOYSA-N sodium metatitanate Chemical compound [Na+].[Na+].[O-][Ti](=O)O[Ti](=O)O[Ti]([O-])=O GROMGGTZECPEKN-UHFFFAOYSA-N 0.000 description 1
- 229910052911 sodium silicate Inorganic materials 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910001928 zirconium oxide Inorganic materials 0.000 description 1
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- Nonmetallic Welding Materials (AREA)
Description
本発明は、ステンレス鋼の溶接に適用され、特に高温環境下において、優れた高温引張強さおよび耐割れ性に優れる溶接金属が得られ、かつ溶接作業性が良好なステンレス鋼溶接用フラックス入りワイヤに関する。 INDUSTRIAL APPLICABILITY The present invention is applied to welding of stainless steel, and in particular, in a high-temperature environment, a weld metal having excellent high-temperature tensile strength and crack resistance is obtained, and a welded flux-cored wire for stainless steel with good workability About.
１９９０年代初頭、石油精製装置の高温環境で使用されるオーステナイト系ステンレス鋼製配管において、Ｂｉを含有したオーステナイト系ステンレス鋼溶接用フラックス入りワイヤで施工された溶接継手で割れの発生が相次いで報告された。特に、７００℃付近の温度域では、実用化後１年以内という短期間に割れが発生するトラブルが報告され、大きな問題となった。この割れの原因として、一般的なステンレス鋼溶接用フラックス入りワイヤには、スラグ剥離性の改善のためにＢｉが酸化物の形で添加されているが、このＢｉを添加した溶接継手は、７００℃以上の温度域に曝された場合、オーステナイト粒界にＢｉが濃化し、再熱割れが発生し、その再熱割れによって短時間で粒界強度が低下し、延性が著しく低下することが判明した。 In the early 1990s, in the austenitic stainless steel piping used in the high temperature environment of petroleum refining equipment, the occurrence of cracks was reported one after another in welded joints constructed with a flux-cored wire for austenitic stainless steel welding containing Bi. It was. In particular, in the temperature range around 700 ° C., a problem that cracking occurred within a short period of time within one year after practical use was reported, which became a big problem. As a cause of this crack, Bi is added in the form of an oxide to improve the slag removability in a general stainless steel welding flux cored wire. When exposed to a temperature range of ℃ or higher, Bi is concentrated in the austenite grain boundary, reheat cracking occurs, and it is found that the reheat cracking reduces the grain boundary strength in a short time and significantly reduces the ductility. did.
このような高温環境化でステンレス鋼溶接用フラックス入りワイヤで溶接した溶接金属の再熱割れ防止のする手段として、Ｂｉ量を１０ｐｐｍ程度にすれば、溶接金属の高温延性に影響がなく、実用上問題ないことが提言され、ＪＩＳでは、Ｂｉ無添加の溶接用フラックス入りワイヤとして、Ｂｉ≦０．００１質量％のワイヤが規定されており、米国石油学会（ＡＰＩ）においても、５５０℃以上で使用される配管の溶接にはＢｉ≦０．００２質量％のワイヤを使用することが推奨されている。このようなＢｉ無添加の溶接用フラックス入りワイヤは、高温強度が高く、耐割れ性が優れることから、高温環境下で使用される化学プラントなどに適用されている。しかし、スラグ剥離性の改善効果を有するＢｉが低く規制されているため、従来の溶接用フラックス入りワイヤと比較すると、スラグ剥離性が悪く、溶接施工の高能率化の観点を満足できないといった問題がある。したがって、Ｂｉを含有した溶接用フラックス入りワイヤと同等の溶接作業性を有し、高温強度が高く、耐割れ性に優れるＢｉ無添加のステンレス鋼溶接用フラックス入りワイヤの開発が望まれている。 As a means for preventing reheat cracking of weld metal welded with a flux-cored wire for stainless steel welding in such a high temperature environment, if the Bi content is about 10 ppm, the hot ductility of the weld metal is not affected and practically used. It is proposed that there is no problem, and JIS stipulates that Bi ≦ 0.001 mass% as a flux-cored wire for welding without additive Bi, and is used at 550 ° C. or higher in the American Petroleum Institute (API). It is recommended to use a wire with Bi ≦ 0.002 mass% for welding of the pipes to be made. Such a Bi-added flux cored wire for welding has high temperature strength and excellent crack resistance, and is therefore applied to chemical plants used in high temperature environments. However, since Bi, which has an effect of improving the slag peelability, is regulated low, there is a problem that the slag peelability is poor compared to the conventional flux-cored wire for welding and the efficiency of welding construction cannot be satisfied. is there. Therefore, the development of a Bi-free stainless steel welding flux-cored wire having welding workability equivalent to that of a Bi-containing welding flux-cored wire, high-temperature strength, and excellent crack resistance is desired.
このように、高温用途用のステンレス鋼溶接用フラックス入りワイヤは種々検討されており、例えば、特許文献１には、ＴｉＯ2、ＳｉＯ2、ＺｒＯ2、金属弗化物、Ａｌ2Ｏ3、ＢｉおよびＢｉ化合物を規定するオーステナイト系ステンレス鋼溶接用フラックス入りワイヤが開示されている。しかし、この溶接用フラックス入りワイヤは、ＺｒＯ2量が多く、溶接金属および溶接スラグ間に窒化物を生成するため、スラグ剥離性が悪いといった課題があった。 As described above, various types of flux-cored wires for welding stainless steel for high temperature applications have been studied. For example, Patent Document 1 discloses TiO 2 , SiO 2 , ZrO 2 , metal fluoride, Al 2 O 3 , Bi, and the like. An austenitic stainless steel welding flux cored wire that defines Bi compounds is disclosed. However, this flux-cored wire for welding has a problem that the amount of ZrO 2 is large and nitride is generated between the weld metal and the weld slag, so that the slag peelability is poor.
また、特許文献２には、Ｏ、Ｎｂ、Ｖ、Ｃ、Ｎ、Ｃｒ、ＴｉＯ2、ＳｉＯ2、Ａｌ2Ｏ3および金属弗化物等を限定した高温用途用ステンレス鋼溶接用フラックス入りワイヤが開示されている。しかし、この溶接用フラックス入りワイヤでは、溶接金属中のＮｂ含有量が多くなり、スラグ剥離性が悪くなる。また、Ｎ含有量が少なくなるので、オーステナイトとフェライトの晶出量によって安定した固溶強化が得られず、溶着金属の引張強さが低くなる。さらには、ＳＵＳ３０４Ｎ２などのオーステナイト系ステンレス鋼に適用した場合、希釈の影響によって溶接金属中のＮ含有量が多くなり、スラグ剥離性が悪くなるという問題があった。 Further, Patent Document 2 discloses a flux-cored wire for welding stainless steel for high-temperature applications in which O, Nb, V, C, N, Cr, TiO 2 , SiO 2 , Al 2 O 3 and metal fluoride are limited. Has been. However, in this flux-cored wire for welding, the Nb content in the weld metal increases, and the slag peelability deteriorates. Further, since the N content is reduced, stable solid solution strengthening cannot be obtained depending on the amount of crystallization of austenite and ferrite, and the tensile strength of the deposited metal is lowered. Furthermore, when applied to austenitic stainless steels such as SUS304N2, there is a problem in that the N content in the weld metal increases due to the influence of dilution, resulting in poor slag removability.
本発明は、ステンレス鋼の溶接に適用され、特に高温環境下において、優れた高温引張強さおよび耐割れ性に優れる溶接金属が得られ、かつ溶接作業性が良好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。 INDUSTRIAL APPLICABILITY The present invention is applied to welding of stainless steel, and in particular, in a high-temperature environment, a weld metal having excellent high-temperature tensile strength and crack resistance is obtained, and a welded flux-cored wire for stainless steel with good workability The purpose is to provide.
本発明者らは、上記の課題を解決するために、各種成分組成の溶接用フラックス入りワイヤを試作して詳細に検討した。その結果、溶接用フラックス入りワイヤ中の成分(金属成分、フラックス成分)を適性化することによって、溶接金属の高温での引張強さ、靭性および耐割れ性が向上し、溶接作業性が良好となることを見出して、本発明を完成した。
本発明の要旨は、次の通りである。
In order to solve the above-mentioned problems, the present inventors have made trials of flux-cored wires for welding having various component compositions and examined them in detail. As a result, by optimizing the components (metal component, flux component) in the flux-cored wire for welding, the tensile strength, toughness and crack resistance at high temperatures of the weld metal are improved, and welding workability is improved. As a result, the present invention was completed.
The gist of the present invention is as follows.
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：０．００５〜０．１０％、
Ｓｉ：０．１〜１．０％、
Ｍｎ：０．５〜４．５％、
Ｎｉ：７〜１２％、
Ｃｒ：１８〜２５％、
Ｍｏ：０．０１〜１．０％、
Ｔｉ：０．１〜０．５％、
Ｎ：０．１〜０．３％、
Ｎｂ：０．０５％以下を含有し、フラックスに、
ＴｉＯ2：４．５〜７．５％、
ＳｉＯ2：０．２〜１．８％、
ＺｒＯ2：０．０１〜０．１０％、
Ａｌ2Ｏ3：０．０１〜０．２０％、
Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種：０．０１〜０．２０％、
弗素化合物のＦ換算値：０．１〜１．０％
を含有し、残部は、Ｆｅおよび不可避不純物からな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 a flux-cored wire for welding stainless steel formed by filling a stainless steel outer shell with a flux, the total amount of the stainless steel outer sheath and the flux in mass% with respect to the total mass of the wire, C: 0.005 to 0.10%,
Si: 0.1 to 1.0%,
Mn: 0.5 to 4.5%,
Ni: 7-12%,
Cr: 18-25%,
Mo: 0.01 to 1.0%,
Ti: 0.1 to 0.5%,
N: 0.1 to 0.3%
Nb: 0.05% or less, in the flux,
TiO 2: 4.5~7.5%,
SiO 2 : 0.2 to 1.8%,
ZrO 2 : 0.01 to 0.10%,
Al 2 O 3: 0.01~0.20%,
Na 1 kind of K 2 O conversion value of terms of Na 2 O values and K alkali metal compound of an alkali metal compound or two 0.01 to 0.20%
F conversion value of fluorine compound: 0.1-1.0%
A flux-cored wire for welding stainless steel, wherein the balance is made of Fe and inevitable impurities.
本発明のステンレス鋼溶接用フラックス入りワイヤによれば、特に高温環境下において、優れた高温引張強さおよび耐割れ性に優れる溶接金属が得られ、かつ溶接作業性が良好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ができる。 According to the stainless steel welding flux-cored wire of the present invention, a stainless steel welding flux that provides a weld metal excellent in high-temperature tensile strength and crack resistance, and has good welding workability, particularly in a high-temperature environment. Cored wire can be provided.
本発明者らは、上記の課題を解決するために、各種成分組成の溶接用フラックス入りワイヤを試作して詳細に検討した。その結果、溶接用フラックス入りワイヤ中のＣ、Ｃｒ、Ｎｉ、Ｍｏを適性化することによって、高温での引張強さ、靭性および耐割れ性が向上することを見出した。 In order to solve the above-mentioned problems, the present inventors have made trials of flux-cored wires for welding having various component compositions and examined them in detail. As a result, it has been found that the tensile strength, toughness and crack resistance at high temperatures are improved by optimizing C, Cr, Ni and Mo in the flux-cored wire for welding.
また、高温で長時間保持した場合、フェライト／オーステナイト粒界へ炭化物やフェライト相中にσ相が析出してフェライト相内が脆化し、高温引張強さが低下するので、フェライト生成元素であるＣｒを適正化することによって、フェライト量を低く抑え、フェライト／オーステナイト粒界中の炭化物やσ相を低減できることを見出した。 In addition, when held at a high temperature for a long time, the σ phase precipitates in the carbide / ferrite phase at the ferrite / austenite grain boundary, the ferrite phase becomes brittle, and the high temperature tensile strength decreases. It has been found that by optimizing the amount of ferrite, the amount of ferrite can be kept low, and carbides and σ phases in the ferrite / austenite grain boundaries can be reduced.
また、Ｃ量を調整してオーステナイト相に適正な炭化物を析出させ、Ｎ量を調整してオーステナイト相に固溶させることで引張強さを向上できることを突き止めたが、それに伴って、靭性が低下したため、さらなる検討を行った。その結果、Ｔｉ量を適正化することで、脱酸を促進させて溶接金属中の酸化物を低減し、靭性を改善できることを見出した。 In addition, it was found that the tensile strength could be improved by adjusting the amount of C to precipitate the appropriate carbide in the austenite phase and adjusting the amount of N to make it dissolve in the austenite phase. Therefore, further investigation was conducted. As a result, it has been found that by optimizing the amount of Ti, deoxidation can be promoted to reduce oxides in the weld metal and improve toughness.
一方、フェライト量が少なくなるとともに、耐割れ性が悪くなる傾向が認められたため、Ｍｎ添加量の適正化も行い、低融点化合物の偏析を低減させ、耐割れ性を改善できることを見出したこと等に基づいて、本発明を完成した。 On the other hand, since the ferrite content decreased and crack resistance tended to deteriorate, it was found that the Mn addition amount was optimized, segregation of low melting point compounds was reduced, and crack resistance could be improved. The present invention has been completed based on the above.
溶接作業性については、従来のＢｉを含有したステンレス鋼溶接用フラックス入りワイヤと比較すると、スラグ剥離性が劣化し、溶接施工の高能率化を満足できないといった問題があり、種々検討した結果、ＴｉＯ2量を適正化し、溶接スラグの熱膨張率を調整して溶接金属と溶接スラグの熱膨張差を増加させることにより、スラグ剥離性を向上できることを見出した。上記の効果は、Ａｌ2Ｏ3、および弗素化合物を適量添加することにより良好にできる。また、アークの安定性およびスパッタ量の低減は、ＴｉＯ2、ＺｒＯ2、ＮａおよびＫのアルカリ金属化合物、弗素化合物およびＮを適量添加することで、また、ビード形状は、Ｓｉ、ＳｉＯ2、Ａｌ2Ｏ3およびＮａおよびＫのアルカリ金属化合物を適量添加することで良好にできる。 As for welding workability, there is a problem that the slag peelability deteriorates and the efficiency of welding work cannot be satisfied, compared with the conventional flux-cored wire for stainless steel welding containing Bi. It was found that the slag peelability can be improved by optimizing the amount of 2 and adjusting the coefficient of thermal expansion of the weld slag to increase the difference in thermal expansion between the weld metal and the weld slag. The above effect can be improved by adding appropriate amounts of Al 2 O 3 and fluorine compounds. Further, the stability of the arc and the amount of sputtering can be reduced by adding an appropriate amount of TiO 2 , ZrO 2 , Na and K alkali metal compounds, fluorine compounds and N, and the bead shape can be Si, SiO 2 , Al It can be improved by adding appropriate amounts of 2 O 3 and alkali metal compounds of Na and K.
本発明の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フラックスの各成分組成それぞれの単独および共存による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を述べる。なお、各成分組成の含有量は、ワイヤ全質量に対する質量％で示す。
まず、ステンレス鋼外皮とフラックスの合計で、以下の通りに限定する。
The flux-cored wire for welding stainless steel of the present invention can be achieved by the synergistic effect of the individual and coexistence of each component composition of the stainless steel sheath and the flux. The reasons and limitations of each component composition are as follows. Give the reason. In addition, content of each component composition is shown by the mass% with respect to the wire total mass.
First, the total of the stainless steel skin and the flux is limited as follows.
［Ｃ：０．００５〜０．１０％］
Ｃは、ステンレス鋼外皮、フェロマンガン、フェロシリコンマンガンおよびグラファイト等から添加され、ＣｒおよびＴｉ炭化物を生成して、溶着金属の高温引張強さを高める効果がある。Ｃが０．００５％未満では、ＣｒおよびＴｉ炭化物の生成が不十分で、高温での引張強さが低くなる。一方、Ｃが０．１０％を超えると、ＣｒおよびＴｉ炭化物が粗大化し、高温に保持した後の靭性が低くなる。従って、Ｃ量は０．００５〜０．１０％とする。
[C: 0.005-0.10%]
C is added from stainless steel skin, ferromanganese, ferrosilicon manganese, graphite, and the like, and produces Cr and Ti carbides, and has the effect of increasing the high-temperature tensile strength of the deposited metal. If C is less than 0.005%, the formation of Cr and Ti carbide is insufficient, and the tensile strength at high temperature is low. On the other hand, when C exceeds 0.10%, Cr and Ti carbides are coarsened, and the toughness after being kept at a high temperature is lowered. Therefore, the C content is 0.005 to 0.10%.
［Ｓｉ：０．１〜１．０％］
Ｓｉは、ステンレス鋼外皮、金属シリコン、フェロシリコンおよびフェロシリコンマンガン等から添加され、ビード形状やスラグ被包性を改善する効果を有する。Ｓｉが０．１％未満では、溶接時の脱酸反応によって形成されるスラグ量が少なく、ビード形状が悪くなる。一方、Ｓｉが１．０％を超えると、スラグ量が過多となり、スラグ被包性が悪くなる。従って、Ｓｉは０．１〜１．０％とする。
[Si: 0.1 to 1.0%]
Si is added from stainless steel skin, metallic silicon, ferrosilicon, ferrosilicon manganese, and the like, and has an effect of improving bead shape and slag encapsulation. If Si is less than 0.1%, the amount of slag formed by the deoxidation reaction during welding is small, and the bead shape becomes poor. On the other hand, if Si exceeds 1.0%, the amount of slag becomes excessive, and the slag encapsulation becomes worse. Therefore, Si is 0.1 to 1.0%.
［Ｍｎ：０．５〜４．５％］
Ｍｎは、ステンレス鋼外皮、金属マンガン、フェロマンガンおよびフェロシリコンマンガン、窒化Ｍｎ等から添加され、低融点化合物の偏析を低減して耐割れ性を改善する効果を有する。Ｍｎが０．５％未満では、オーステナイト粒界に低融点化合物が偏析するため、耐割れ性が悪くなる。一方、Ｍｎが４．５％を超えると、炭化物および窒化物を生成して常温での靭性が低下する。従って、Ｍｎは０．５〜４．５％とする。
[Mn: 0.5 to 4.5%]
Mn is added from stainless steel skin, metal manganese, ferromanganese and ferrosilicon manganese, Mn nitride, etc., and has the effect of reducing segregation of low melting point compounds and improving crack resistance. If Mn is less than 0.5%, the low melting point compound is segregated at the austenite grain boundaries, resulting in poor crack resistance. On the other hand, if Mn exceeds 4.5%, carbides and nitrides are generated and the toughness at normal temperature is lowered. Therefore, Mn is 0.5 to 4.5%.
［Ｎｉ：７〜１２％］
Ｎｉは、ステンレス鋼外皮、金属ニッケルおよびフェロニッケル等から添加され、オーステナイト相を安定化させる元素であり、フェライト量の調整および耐割れ性を改善する効果を有する。Ｎｉが７％未満では、オーステナイトの晶出量が減少してフェライト量が多くなり、常温での靭性が低下する。一方、Ｎｉが１２％を超えると、フェライトの晶出量が少なくなり、低融点化合物の偏析が助長されて耐割れ性が悪くなる。従って、Ｎｉは７〜１２％とする。
[Ni: 7-12%]
Ni is an element that is added from a stainless steel shell, metallic nickel, ferronickel, or the like and stabilizes the austenite phase, and has the effect of adjusting the ferrite content and improving crack resistance. If Ni is less than 7%, the amount of crystallization of austenite decreases, the amount of ferrite increases, and the toughness at room temperature decreases. On the other hand, if Ni exceeds 12%, the amount of ferrite crystallized decreases, segregation of the low melting point compound is promoted, and crack resistance deteriorates. Therefore, Ni is 7 to 12%.
［Ｃｒ：１８〜２５％］
Ｃｒは、ステンレス鋼外皮、金属クロムおよびフェロクロム、窒化Ｃｒ等から添加され、フェライト相を安定化させる元素であり、溶着金属の引張強さを増加させる効果を有する。Ｃｒが１８％未満では、フェライトの晶出量が減少してオーステナイト量が多くなり、常温での引張強さが低下する。一方、Ｃｒが２５％を超えると、Ｃｒ炭化物の生成が多くなり、高温での引張強さが低下する。従って、Ｃｒは１８〜２５％とする。
[Cr: 18-25%]
Cr is an element that is added from a stainless steel shell, metallic chromium and ferrochromium, Cr nitride, and the like and stabilizes the ferrite phase, and has the effect of increasing the tensile strength of the deposited metal. If Cr is less than 18%, the amount of crystallization of ferrite decreases, the amount of austenite increases, and the tensile strength at room temperature decreases. On the other hand, when Cr exceeds 25%, the production of Cr carbide increases, and the tensile strength at high temperature decreases. Therefore, Cr is 18 to 25%.
［Ｍｏ：０．０１〜１．０％］
Ｍｏは、ステンレス鋼外皮、金属モリブデンおよびフェロモリブデン等から添加され、オーステナイト相中に固溶され、引張強さを改善する効果を有する。Ｍｏが０．０１％未満では、固溶強化の効果が得られず、常温での引張強さが低下する。一方、Ｍｏが１．０％を超えると、フェライト中より極めて硬く脆いσ相が析出され、高温に保持した後の靭性が低下する。従って、Ｍｏは０．０１〜１．０％とする。
[Mo: 0.01 to 1.0%]
Mo is added from a stainless steel outer shell, metallic molybdenum, ferromolybdenum, or the like, and is dissolved in the austenite phase and has an effect of improving the tensile strength. If Mo is less than 0.01%, the effect of solid solution strengthening cannot be obtained, and the tensile strength at room temperature decreases. On the other hand, when Mo exceeds 1.0%, an extremely hard and brittle σ phase is precipitated from the ferrite, and the toughness after being kept at a high temperature is lowered. Therefore, Mo is set to 0.01 to 1.0%.
［Ｔｉ：０．１〜０．５％］
Ｔｉは、ステンレス鋼製外皮、金属チタンおよびフェロチタン等から添加され、脱酸を促進させて溶接金属中の酸化物を低減し、靭性を改善する効果を有する。Ｔｉが０．１％未満では、脱酸が不十分で、常温での靭性が低下する。一方、Ｔｉが０．５％を超えると、溶接時に溶滴が粗大に成長し、大粒のスパッタが発生する。従って、Ｔｉは０．１〜０．５％とする。
[Ti: 0.1 to 0.5%]
Ti is added from a stainless steel outer shell, metallic titanium, ferrotitanium, or the like, and has the effect of promoting deoxidation to reduce oxides in the weld metal and improving toughness. When Ti is less than 0.1%, deoxidation is insufficient and toughness at room temperature is lowered. On the other hand, when Ti exceeds 0.5%, droplets grow coarsely during welding, and large spatters are generated. Therefore, Ti is set to 0.1 to 0.5%.
〔Ｎ：０．１〜０．３％〕
Ｎは、ステンレス鋼外皮、窒化クロムおよび窒化マンガン等から添加され、オーステナイト中に固溶され引張強さを向上する効果を有する。Ｎが０．１％未満では、オーステナイト相中に固溶されず、常温での引張強さが低下する。一方、Ｎが０．３％を超えると、溶接時に溶融池に固溶しきれないＮが発生して溶滴移行が円滑に行われず、スパッタ発生量が増加する。従って、Ｎは、０．１〜０．３％とする。
[N: 0.1-0.3%]
N is added from a stainless steel skin, chromium nitride, manganese nitride, or the like, and has the effect of improving the tensile strength by being dissolved in austenite. If N is less than 0.1%, it will not be dissolved in the austenite phase, and the tensile strength at room temperature will decrease. On the other hand, if N exceeds 0.3%, N that cannot be completely dissolved in the molten pool is generated at the time of welding, and droplet transfer is not performed smoothly, and the amount of spatter generated increases. Therefore, N is set to 0.1 to 0.3%.
［Ｎｂ：０．０５％以下］
Ｎｂは、ステンレス鋼外皮に含有されていて、不可避的にワイヤ中に含有される成分であって、含有量が多くなると溶接金属とスラグ間で化合物を生成してスラグ剥離性を悪くする作用があり、少ない方が望ましいく、０．０５％以下（０％を含む）であれば許容できる。好ましくは０．０２%以下である。
[Nb: 0.05% or less]
Nb is a component contained in the stainless steel outer shell and inevitably contained in the wire. When the content is increased, a compound is formed between the weld metal and the slag and the slag peelability is deteriorated. Yes, the smaller one is desirable, and 0.05% or less (including 0%) is acceptable. Preferably it is 0.02% or less.
次に、ワイヤ全質量に対する質量％で、フラックス中に含有する成分組成を、以下の通りに限定する。 Next, the component composition contained in the flux in mass% with respect to the total mass of the wire is limited as follows.
［ＴｉＯ2：４．５〜７．５％］
ＴｉＯ2は、ルチール、酸化チタン、チタン酸ソーダ、チタンスラグ、イルミナイト等から添加される。これらは、溶接スラグの熱膨張率を調整し、溶接金属と溶接スラグの熱膨張差を増加させることによってスラグ剥離性を向上させる。ＴｉＯ2が４．５％未満であると、溶接金属と溶接スラグの熱膨張差が少なくなり、スラグ剥離性が劣化する。一方、ＴｉＯ2が７．５％を超えると、溶滴を被包するスラグ量が過多となり、溶滴の移行が阻害されるためアーク安定性が低下する。従って、ＴｉＯ2は４．５〜７．５％とする。
[TiO 2 : 4.5 to 7.5%]
TiO 2 is added from rutile, titanium oxide, sodium titanate, titanium slag, illuminite or the like. These improve the slag peelability by adjusting the thermal expansion coefficient of the weld slag and increasing the difference in thermal expansion between the weld metal and the weld slag. When TiO 2 is less than 4.5%, the difference in thermal expansion between the weld metal and the weld slag is reduced, and the slag peelability is deteriorated. On the other hand, if TiO 2 exceeds 7.5%, the amount of slag encapsulating the droplets becomes excessive, and the transition of the droplets is hindered, resulting in a decrease in arc stability. Therefore, TiO 2 is set to 4.5 to 7.5%.
［ＳｉＯ2：０．２〜１．８％］
ＳｉＯ2は、珪砂、ジルコンサンド等より添加されスラグ形成剤として作用し、スラグの粘性を調整しスラグ被包性を良好にする効果がある。ＳｉＯ2が０．２％未満であると、スラグの粘性が低くなり、スラグ被包性が悪くなる。一方、ＳｉＯ2が１．８％を超えると、スラグ量が増加して溶接金属とスラグ量とのバランスが悪くなり、ビード形状が劣化する。従って、ＳｉＯ2は０．２〜１．８％とする。
[SiO 2 : 0.2 to 1.8%]
SiO 2 is added from silica sand, zircon sand or the like and acts as a slag forming agent, and has the effect of adjusting the viscosity of the slag and improving the slag encapsulation. When SiO 2 is less than 0.2%, the viscosity of the slag is lowered, and the slag encapsulation is deteriorated. On the other hand, if SiO 2 exceeds 1.8%, the amount of slag increases, the balance between the weld metal and the amount of slag deteriorates, and the bead shape deteriorates. Thus, SiO 2 is set to 0.2 to 1.8%.
〔ＺｒＯ2：０．０１〜０．１０％〕
ＺｒＯ2は、ジルコンサンドおよび酸化ジルコニウム等から添加され、スラグの粘性を調整し、溶滴移行の際に発生するスパッタ発生量を低減する効果を有する。ＺｒＯ2が０．０１％未満であると、スラグの粘性が低くなり、溶滴移行の際に小粒のスパッタが発生する。一方、ＺｒＯ2が０．１０％を超えると、スラグの粘性が高くなり、溶滴が大きく成長し、溶滴移行が円滑に行われずアークが不安定になる。従って、ＺｒＯ2は０．０１〜０．１０％とする。
[ZrO 2 : 0.01 to 0.10%]
ZrO 2 is added from zircon sand, zirconium oxide or the like, and has the effect of adjusting the viscosity of the slag and reducing the amount of spatter generated during droplet transfer. When the ZrO 2 content is less than 0.01%, the viscosity of the slag becomes low, and small particles of spatter are generated during droplet transfer. On the other hand, if ZrO 2 exceeds 0.10%, the viscosity of the slag increases, the droplets grow large, the droplet transfer is not performed smoothly, and the arc becomes unstable. Therefore, ZrO 2 is set to 0.01 to 0.10%.
［Ａｌ2Ｏ3：０．０１〜０．２０％］
Ａｌ2Ｏ3はアルミナから添加され、スラグの融点を調整してビード形状を向上させる効果を有する。Ａｌ2Ｏ3が０．０１％未満であると、スラグの融点が低くなるので、溶接金属とスラグの凝固が不均一となり、ビード形状が劣化する。一方、Ａｌ2Ｏ3が０．２０％を超えると、スラグの融点が高くなり、冷却速度の速いビード部にスラグが残ってスラグ剥離性が悪くなる。従って、Ａｌ2Ｏ3は０．０１〜０．２０％とする。
[Al 2 O 3 : 0.01 to 0.20%]
Al 2 O 3 is added from alumina and has the effect of adjusting the melting point of the slag and improving the bead shape. If the Al 2 O 3 content is less than 0.01%, the melting point of the slag becomes low, so that the solidification of the weld metal and the slag becomes uneven and the bead shape deteriorates. On the other hand, if Al 2 O 3 exceeds 0.20%, the melting point of the slag becomes high, and the slag remains in the bead portion where the cooling rate is fast, so that the slag peelability is deteriorated. Accordingly, Al 2 O 3 is set to 0.01 to 0.20%.
〔Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種：０．０１〜０．２０％〕
ＮａおよびＫのアルカリ金属化合物は、水ガラスのＮａＯ2およびＫ2Ｏ等から添加され、アークを安定にし、スパッタ発生量を低減する効果を有する。Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種が０．０１％未満では、アークが不安定となり、溶滴移行が短絡移行となってスパッタ発生量が増加する。一方、Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種が０．２０％を超えると、スラグの凝固が早くなり、ビード形状が悪くなる。従って、Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種は０．０１〜０．２０％とする。
[Na 1 kind of K 2 O conversion value of terms of Na 2 O values and K alkali metal compound of an alkali metal compound or two 0.01 to 0.20%]
Na and K alkali metal compounds are added from NaO 2 and K 2 O of water glass, etc., and have the effect of stabilizing the arc and reducing the amount of spatter generated. In one or less than two kinds of 0.01% of the K 2 O conversion value of terms of Na 2 O values and K alkali metal compound of the Na alkali metal compound, the arc becomes unstable, droplet transfer and short circuit transfer As a result, the amount of spatter generated increases. On the other hand, if one or two of K 2 O conversion value of terms of Na 2 O values and K alkali metal compound of an alkali metal compound of Na is more than 0.20%, faster solidification of the slag, bead shape Deteriorate. Therefore, one or two K 2 O converted value of the alkali metal compound terms of Na 2 O values and K of the alkali metal compound of Na is set to 0.01 to 0.20 percent.
［弗素化合物のＦ換算値：０．１〜１．０％］
弗素化合物のＦ換算値は、弗化ソーダ、珪弗化カリ、ジルコンフッ化カリ、氷晶石、弗化アルミ、弗化リチウムおよび蛍石等から添加され、アークの安定性を向上する効果を有する。弗素化合物のＦ換算値が０．１％未満では、上述の効果が不十分であり、アークが不安定になる。一方、弗素化合物のＦ換算値が１．０％を超えると、スラグの融点が低下して溶融金属よりスラグの凝固が早くなり、スラグ剥離性が悪くなる。従って、弗素化合物のＦ換算値は０．１〜１．０％とする。
なお、フラックス中に含有される金属酸化物は、金属単体成分の含有量としない。
[F conversion value of fluorine compound: 0.1 to 1.0%]
The fluorine conversion value of the fluorine compound is added from sodium fluoride, potassium silicofluoride, potassium zircon fluoride, cryolite, aluminum fluoride, lithium fluoride, fluorite, etc., and has the effect of improving the stability of the arc. . If the F-converted value of the fluorine compound is less than 0.1%, the above effect is insufficient and the arc becomes unstable. On the other hand, when the F-converted value of the fluorine compound exceeds 1.0%, the melting point of the slag is lowered and the solidification of the slag is faster than the molten metal, and the slag peelability is deteriorated. Therefore, the F converted value of the fluorine compound is set to 0.1 to 1.0%.
Note that the metal oxide contained in the flux is not the content of the single metal component.
残部は、Ｆｅおよび不可避不純物である。Ｆｅは、ステンレス鋼外皮のＦｅ、フラックスの鉄粉、鉄合金（Ｆｅ−Ｓｉ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎ等のフェロアロイ）粉などからのＦｅである。不可避不純物は、Ｐ、Ｓ、Ｂｉなどの不可避に混入される不純物をいい０％であることが望ましいが、０%にするには生産コストが高くなるという問題がある。 The balance is Fe and inevitable impurities. Fe is Fe from stainless steel outer shell, flux iron powder, iron alloy (ferroalloy such as Fe-Si, Fe-Mn, Fe-Si-Mn) powder, and the like. The unavoidable impurities are inevitably mixed impurities such as P, S, and Bi, and are desirably 0%. However, there is a problem that the production cost is increased to achieve 0%.
なお、耐割れ性の観点から、Ｐは０．０４０％以下、Ｓは０．０３０％以下であることが好ましい。また、Ｂｉは、溶接部が高温に長時間保持された場合、オーステナイト粒界にＢｉが濃化し易く、再熱割れを発生させるとともに、短時間で粒界強度が低下して延性が著しく低下させるのでＢｉは、０．００１％以下とすることが好ましい。 From the viewpoint of crack resistance, P is preferably 0.040% or less and S is preferably 0.030% or less. In addition, when Bi is kept at a high temperature for a long time, Bi is likely to be concentrated at the austenite grain boundary, causing reheat cracking, and at the same time, the grain boundary strength is lowered and ductility is significantly reduced. Therefore, Bi is preferably 0.001% or less.
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、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と、例えば、ステンレス鋼外皮を帯鋼から管状に成形する場合、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に丸形に成形し、所定のワイヤ径まで伸線する。この際、成形した外皮シームを溶接してシームレスタイプの溶接用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、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ことができる。いずれも製造方法も、ワイヤ径は０．８〜３．６ｍｍまで製造が可能である。 As mentioned above, although the reason for limitation of the component composition of the flux-cored wire for stainless steel welding of the present invention has been described, when referring to the manufacturing method of the flux-cored wire for welding, for example, when forming a stainless steel skin from a steel strip into a tubular shape, The filled flux that has been blended, 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, the formed outer seam can be welded to form a seamless type flux-cored wire for welding. Further, when the stainless steel skin is a pipe, the pipe can be vibrated to be filled with a flux and drawn to a predetermined wire diameter. In any of the manufacturing methods, the wire diameter can be manufactured up to 0.8 to 3.6 mm.
フラックスは、供給および充填が円滑に行えるように、固着剤（珪酸カリおよび珪酸ソーダの水ガラス）を添加して造粒して用いることもできる。 The flux can be granulated by adding a fixing agent (potassium silicate and sodium silicate water glass) 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に示す化学成分のステンレス鋼外皮を用い、表２−１および表２−２に示す各種成分組成のフラックスを充填し、端面同士を溶接してシームレス状にした後、ワイヤ径１．２ｍｍまで縮径してステンレス鋼溶接用フラックス入りワイヤを試作した。 Using the stainless steel skin of chemical components shown in Table 1, filled with fluxes of various component compositions shown in Table 2-1 and Table 2-2, and welded end faces to make them seamless, then the wire diameter 1.2 mm The flux cored wire for welding stainless steel was made as a prototype.
表２に示すステンレス鋼溶接用フラックス入りワイヤを用い、溶接作業性および機械的性質を調査した。 Using the stainless steel welding flux cored wire shown in Table 2, welding workability and mechanical properties were investigated.
溶接作業性の評価は、表３に示す成分のＳＵＳ３０４Ｌ鋼板を用い、表４に示す溶接条件で下向水平すみ肉溶接を行い、アーク安定性、スパッタ発生量、ビード形状、スラグ被包性およびスラグ剥離性を調査した。なお、それぞれの良否は目視にて判定した。 Evaluation of welding workability was performed by using a SUS304L steel plate having the components shown in Table 3 and performing downward horizontal fillet welding under the welding conditions shown in Table 4, and arc stability, spatter generation amount, bead shape, slag encapsulation, and Slag peelability was investigated. In addition, each quality was determined visually.
溶着金属試験は、表３に示す成分の板厚２０ｍｍ、開先角度１０°を設けたＳＵＳ３０４Ｌ鋼板に２層バタリングを行い、ＪＩＳ Ｚ ３３２３に準拠し、表４に示す溶接条件にて多層盛溶接を行った。溶着金属部より、引張試験片および衝撃試験片を採取し、室温および６５０℃の高温で試験を行った。 In the weld metal test, a SUS304L steel plate having a thickness of 20 mm and a groove angle of 10 ° having the components shown in Table 3 was subjected to two-layer buttering and multilayer welding was performed in accordance with JIS Z 3323 under the welding conditions shown in Table 4. Went. Tensile test pieces and impact test pieces were collected from the weld metal part and tested at room temperature and at a high temperature of 650 ° C.
常温試験は、室温にて引張試験、試験温度−２０℃で衝撃試験行い、引張強さが５２０ＭＰａ以上、吸収エネルギーが３本の平均値で２５Ｊ以上を良好とした。 In the room temperature test, a tensile test at room temperature and an impact test at a test temperature of −20 ° C. were performed, and a tensile strength of 520 MPa or more and an absorption energy of 3 J were average values of 25 J or more.
高温試験は、引張試験は引張試験片を６５０℃まで加熱した直後に試験を行い、引張強さが２５０ＭＰａ以上を良好とし、衝撃試験は衝撃試験片を６５０℃×２ｈ保持し、室温まで空冷した後、試験温度−２０℃で吸収エネルギーが３本の平均値で３０Ｊ以上を良好とした。 In the high temperature test, the tensile test was performed immediately after heating the tensile test piece to 650 ° C., the tensile strength was good at 250 MPa or more, and the impact test was held at 650 ° C. × 2 h and air cooled to room temperature. After that, the test energy was −20 ° C., and the absorbed energy was determined to be 30 J or more with an average value of three.
耐割れ性の評価は、表３に示す成分の板厚２０ｍｍ、開先角度１０°を設けたＳＵＳ３０４Ｌ鋼板を用い、表４に示す溶接条件で多層盛溶接して溶接継手を作製し、該溶接継手を８００℃×７２０ｈ保持し、室温まで空冷した後、ＪＩＳ Ｚ ３１２２に準拠して側曲げ試験片を採取して側曲げ試験を実施し、疵が３ｍｍ以下を良好とした。それら調査結果を表５にまとめて示す。試験結果として総合評価が良好な場合を場合を○、劣る場合を×として示している。 Evaluation of cracking resistance was conducted by using a SUS304L steel plate having a thickness of 20 mm and a groove angle of 10 ° as shown in Table 3 to produce a welded joint by multilayer welding under the welding conditions shown in Table 4. After holding the joint at 800 ° C. × 720 h and air-cooling to room temperature, a side bend test piece was taken according to JIS Z 3122 and a side bend test was performed. The survey results are summarized in Table 5. As a test result, the case where the comprehensive evaluation is good is shown as ◯, and the case where it is inferior is shown as x.
表２−１、表２−２および表５のワイヤＮｏ．１〜１２が本願発明例、ワイヤＮｏ．１３〜２４は比較例である。本願発明であるワイヤＮｏ．１〜１２は、ステンレス鋼外皮とフラックスとの合計のＣ、Ｓｉ、Ｍｎ、Ｎｉ、Ｃｒ、Ｍｏ、Ｔｉ、Ｎおよびフラックス中のＴｉＯ2、ＳｉＯ2、ＺｒＯ2、Ａｌ2Ｏ3、Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種の合計、弗素化合物のＦ換算値が適正であるので、常温および高温での引張強さおよび吸収エネルギーが良好で、耐割れ性も良好であった。また、アーク安定性、ビード形状、スラグ被包性およびスラグ剥離性も良好で、スパッタ発生量も少なく、極めて満足な結果であった。 The wire Nos. In Table 2-1, Table 2-2, and Table 5 were used. 1 to 12 are examples of the present invention, wire No. 13 to 24 are comparative examples. Wire No. which is the present invention. 1 to 12 are the total of C, Si, Mn, Ni, Cr, Mo, Ti, N of the stainless steel outer shell and the flux, and alkalis of TiO 2 , SiO 2 , ZrO 2 , Al 2 O 3 , and Na in the flux Since the total of one or two of the Na 2 O conversion value of the metal compound and the K 2 O conversion value of the alkali metal compound of K and the F conversion value of the fluorine compound are appropriate, the tensile strength at normal temperature and high temperature and Absorption energy was good and crack resistance was also good. Moreover, the arc stability, bead shape, slag encapsulation and slag peelability were good, and the amount of spatter was small, which was a very satisfactory result.
比較例中ワイヤＮｏ．１３は、ステンレス鋼外皮とフラックスとの合計のＳｉが少ないので、ビード形状が不良であった。また、フラックス中のＮａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種の合計が少ないので、スパッタが多かった。さらに、フラックス中の弗素化合物のＦ換算値が少ないので、アークが不安定であった。 In the comparative example, the wire No. No. 13 had a poor bead shape because the total Si of the stainless steel shell and the flux was small. Further, since the one or of the sum of K 2 O converted value of the alkali metal compound terms of Na 2 O values and K of the alkali metal compound of Na in the flux is small, spatter was large. Further, since the F-converted value of the fluorine compound in the flux is small, the arc was unstable.
ワイヤＮｏ．１４は、ステンレス鋼外皮とフラックスとの合計のＳｉが多いので、スラグ被包性が不良であった。また、フラックス中のＮａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種の合計が多いので、ビード形状が不良であった。さらに、フラックス中の弗素化合物のＦ換算値が多いので、スラグ剥離性が不良であった。 Wire No. No. 14 had a poor total slag encapsulating property because there was much Si in the total of the stainless steel skin and the flux. Further, since the one or of the sum of K 2 O converted value of the alkali metal compound terms of Na 2 O values and K of the alkali metal compound of Na in the flux is large, the bead shape was poor. Furthermore, since there were many F conversion values of the fluorine compound in a flux, slag peelability was unsatisfactory.
ワイヤＮｏ．１５は、ステンレス鋼外皮とフラックスとの合計のＭｎが少ないので、耐割れ性が不良であった。また、ステンレス鋼外皮とフラックスとの合計のＴｉが少ないので、常温での靭性が低かった。さらに、フラックス中のＳｉＯ2が少ないので、スラグ被包性が不良であった。また、フラックス中のＺｒＯ2が少ないので、スパッタが多かった。 Wire No. No. 15 had a poor crack resistance because the total Mn of the stainless steel shell and the flux was small. Moreover, since the total Ti of the stainless steel shell and the flux was small, the toughness at room temperature was low. Further, since a small SiO 2 in the flux, the slag encapsulated was poor. In addition, since there is little ZrO 2 in the flux, the sputtering there were many.
ワイヤＮｏ．１６は、ステンレス鋼外皮とフラックスとの合計のＭｎが多いので、常温での靭性が低かった。また、ステンレス鋼外皮とフラックスとの合計のＴｉが多いので、スパッタが多かった。さらに、フラックス中のＳｉＯ2が多いので、ビード形状が不良であった。また、フラックス中のＺｒＯ2が多いので、アークが不安定であった。 Wire No. No. 16 had a low toughness at room temperature because the total Mn of the stainless steel shell and the flux was large. Further, since the total Ti of the stainless steel outer shell and the flux was large, there was much spatter. In addition, because there are many SiO 2 in the flux, the bead shape was poor. In addition, because there are many ZrO 2 in the flux, the arc was unstable.
ワイヤＮｏ．１７は、ステンレス鋼外皮とフラックスとの合計のＣが少ないので、高温での引張強さが低かった。また、ステンレス鋼外皮とフラックスとの合計のＮｉが少ないので、常温での靭性が低かった。さらに、フラックス中のＴｉＯ2が少ないので、スラグ剥離性が不良であった。 Wire No. No. 17 had a low tensile strength at high temperatures because the total C of the stainless steel shell and the flux was small. Moreover, since the total Ni of the stainless steel skin and the flux was small, the toughness at room temperature was low. Furthermore, since less TiO 2 in the flux, the slag removability was poor.
ワイヤＮｏ．１８は、ステンレス鋼外皮とフラックスとの合計のＣが多いので、高温での靭性が低かった。また、ステンレス鋼外皮とフラックスとの合計のＮｉが多いので、耐割れ性が不良であった。さらに、フラックス中のＴｉＯ2が多いので、アークが不安定であった。 Wire No. No. 18 had a low total toughness at a high temperature because the total C of the stainless steel shell and the flux was large. Moreover, since there was much Ni of the sum total of a stainless steel outer_layer | skin and a flux, crack resistance was unsatisfactory. Furthermore, since many TiO 2 in the flux, the arc was unstable.
ワイヤＮｏ．１９は、ステンレス鋼外皮とフラックスとの合計のＮが少ないので、常温での引張強さが低かった。また、フラックス中のＡｌ2Ｏ3が少ないので、ビード形状が不良であった。 Wire No. No. 19 had a low tensile strength at room temperature because the total N of the stainless steel skin and the flux was small. Further, since the small Al 2 O 3 in the flux, the bead shape was poor.
ワイヤＮｏ．２０は、ステンレス鋼外皮とフラックスとの合計のＮが多いので、スパッタが多かった。また、フラックス中のＡｌ2Ｏ3が多いので、スラグ剥離性が不良であった。 Wire No. No. 20 had a lot of spatter because the total N of the stainless steel shell and the flux was large. Also, since there are many Al 2 O 3 in the flux, the slag removability was poor.
ワイヤＮｏ．２１は、ステンレス鋼外皮とフラックスとの合計のＣｒが少ないので、常温での引張強さが低かった。 Wire No. No. 21 had a low tensile strength at room temperature because the total Cr of the stainless steel shell and the flux was small.
ワイヤＮｏ．２２は、ステンレス鋼外皮とフラックスとの合計のＣｒが多いので、高温での引張強さが低かった。 Wire No. No. 22 had a high tensile strength at a high temperature because the total Cr of the stainless steel outer shell and the flux was large.
ワイヤＮｏ．２３は、ステンレス鋼外皮とフラックスとの合計のＭｏが少ないので、常温での引張強さが低かった。 Wire No. No. 23 had a low tensile strength at room temperature because the total Mo of the stainless steel shell and the flux was small.
ワイヤＮｏ．２４は、ステンレス鋼外皮とフラックスとの合計のＭｏが多いので、高温での靭性が低かった。 Wire No. No. 24 had a high toughness at high temperature because there was much Mo in the total of the stainless steel outer shell and the flux.
以上の実施例に示すように、本願発明のステンレス鋼溶接用フラックス入りワイヤでは常温および高温での引張強さおよび吸収エネルギーが良好で、耐割れ性も良好であった。また、アーク安定性、ビード形状、スラグ被包性およびスラグ剥離性も良好で、スパッタ発生量も少なく、溶接作業性が良好となり極めて満足な結果が得られていた。 As shown in the above Examples, the stainless steel welding flux cored wire of the present invention had good tensile strength and absorbed energy at normal temperature and high temperature, and good crack resistance. Also, the arc stability, bead shape, slag encapsulation and slag peelability were good, the amount of spatter was small, welding workability was good, and very satisfactory results were obtained.
Claims (1)
Ｃ：０．００５〜０．１０％、
Ｓｉ：０．１〜１．０％、
Ｍｎ：０．５〜４．５％、
Ｎｉ：７〜１２％、
Ｃｒ：１８〜２５％、
Ｍｏ：０．０１〜１．０％、
Ｔｉ：０．１〜０．５％、
Ｎ：０．１〜０．３％、
Ｎｂ：０．０５％以下を含有し、
フラックスに、
ＴｉＯ２：４．５〜７．５％、
ＳｉＯ２：０．２〜１．８％、
ＺｒＯ２：０．０１〜０．１０％、
Ａｌ２Ｏ３：０．０１〜０．２０％、
Ｎａのアルカリ金属化合物のＮａ2Ｏ換算値およびＫのアルカリ金属化合物のＫ2Ｏ換算値の１種または２種：０．０１〜０．２０％、
弗素化合物のＦ換算値：０．１〜１．０％を含有し、残部は、Ｆｅおよび不可避不純物からな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 welding stainless steel formed by filling the stainless steel outer shell with flux, the mass% of the total mass of the wire, and the total of the stainless steel outer shell and the flux,
C: 0.005-0.10%,
Si: 0.1 to 1.0%,
Mn: 0.5 to 4.5%,
Ni: 7-12%,
Cr: 18-25%,
Mo: 0.01 to 1.0%,
Ti: 0.1 to 0.5%,
N: 0.1 to 0.3%
Nb: 0.05% or less,
To the flux,
TiO 2: 4.5~7.5%,
SiO 2: 0.2~1.8%,
ZrO 2 : 0.01 to 0.10%,
Al 2 O 3: 0.01~0.20%,
Na 1 kind of K 2 O converted value of terms of Na 2 O values and K alkali metal compound of an alkali metal compound or two 0.01 to 0.20%
F-corresponding value of fluorine compound: 0.1 to 1.0%, the balance being made of Fe and inevitable impurities, a stainless steel welding flux cored wire.
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| JP6566928B2 (en) * | 2016-12-07 | 2019-08-28 | 日鉄溶接工業株式会社 | Stainless steel flux cored wire |
| CN109136748B (en) * | 2018-08-02 | 2019-10-29 | 浙江久立特材科技股份有限公司 | A kind of stabilisation type stainless steel seamless pipe and its manufacturing method |
| CN111992924A (en) * | 2020-08-27 | 2020-11-27 | 山东能源重装集团恒图科技有限公司 | 500 MPa-level flux-cored wire and preparation method thereof |
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| JP4584002B2 (en) * | 2005-04-07 | 2010-11-17 | 日鐵住金溶接工業株式会社 | Flux-cored wire for ferritic stainless steel welding |
| KR100774155B1 (en) * | 2006-10-20 | 2007-11-07 | 고려용접봉 주식회사 | Flux cored wire for duplex stainless steel and the manufacturing method thereof |
| JP5138242B2 (en) * | 2007-03-14 | 2013-02-06 | 日鐵住金溶接工業株式会社 | Flux-cored wire for duplex stainless steel welding |
| US8878099B2 (en) * | 2008-05-27 | 2014-11-04 | Nippon Steel & Sumikin Stainless Steel Corporation | Flux cored wire for welding duplex stainless steel which refines solidified crystal grains |
| JP5885618B2 (en) * | 2012-08-09 | 2016-03-15 | 日鐵住金溶接工業株式会社 | Stainless steel flux cored wire |
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