JP5558406B2 - Flux-cored wire for carbon dioxide shielded arc welding - Google Patents
Flux-cored wire for carbon dioxide shielded arc welding Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims description 86
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 title claims description 30
- 229910002092 carbon dioxide Inorganic materials 0.000 title claims description 15
- 239000001569 carbon dioxide Substances 0.000 title claims description 15
- 229910000831 Steel Inorganic materials 0.000 claims description 33
- 239000010959 steel Substances 0.000 claims description 33
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 30
- 239000001257 hydrogen Substances 0.000 claims description 30
- 229910052739 hydrogen Inorganic materials 0.000 claims description 30
- 238000006243 chemical reaction Methods 0.000 claims description 16
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 15
- 230000004907 flux Effects 0.000 claims description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 11
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 9
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 8
- 150000002222 fluorine compounds Chemical class 0.000 claims description 8
- 150000001339 alkali metal compounds Chemical class 0.000 claims description 5
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 description 105
- 239000002184 metal Substances 0.000 description 105
- 239000011324 bead Substances 0.000 description 26
- 238000005336 cracking Methods 0.000 description 24
- 239000002893 slag Substances 0.000 description 18
- 230000000694 effects Effects 0.000 description 16
- 239000007789 gas Substances 0.000 description 11
- 239000010936 titanium Substances 0.000 description 11
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 239000011734 sodium Substances 0.000 description 7
- 230000007423 decrease Effects 0.000 description 6
- 230000001965 increasing effect Effects 0.000 description 6
- 238000000034 method Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 229910052760 oxygen Inorganic materials 0.000 description 6
- 239000007787 solid Substances 0.000 description 6
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 5
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 5
- 239000001301 oxygen Substances 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Chemical compound [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 description 4
- 238000009863 impact test Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 229910052700 potassium Inorganic materials 0.000 description 3
- 239000004576 sand Substances 0.000 description 3
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 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
- 229910002551 Fe-Mn Inorganic materials 0.000 description 2
- 229910017082 Fe-Si Inorganic materials 0.000 description 2
- 229910017133 Fe—Si Inorganic materials 0.000 description 2
- 229910018505 Ni—Mg Inorganic materials 0.000 description 2
- ZLMJMSJWJFRBEC-UHFFFAOYSA-N Potassium Chemical compound [K] ZLMJMSJWJFRBEC-UHFFFAOYSA-N 0.000 description 2
- 229910006639 Si—Mn Inorganic materials 0.000 description 2
- 239000004115 Sodium Silicate Substances 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000005538 encapsulation Methods 0.000 description 2
- 230000002708 enhancing effect Effects 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 239000011591 potassium Substances 0.000 description 2
- 235000019353 potassium silicate Nutrition 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 235000013024 sodium fluoride Nutrition 0.000 description 2
- 239000011775 sodium fluoride Substances 0.000 description 2
- 229910052911 sodium silicate Inorganic materials 0.000 description 2
- 239000003381 stabilizer Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910018134 Al-Mg Inorganic materials 0.000 description 1
- 229910018467 Al—Mg Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910017116 Fe—Mo Inorganic materials 0.000 description 1
- 239000004111 Potassium silicate Substances 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
- 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
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229920003023 plastic Polymers 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 229910052913 potassium silicate 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
- 230000000717 retained effect Effects 0.000 description 1
- 238000007665 sagging Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 229910052708 sodium Inorganic materials 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 1
- 125000000391 vinyl group Chemical group [H]C([*])=C([H])[H] 0.000 description 1
- 229920002554 vinyl polymer Polymers 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Nonmetallic Welding Materials (AREA)
Description
本発明は、炭酸ガスシールドアーク溶接用フラックス入りワイヤに関し、特に、高能率に溶接施工が可能な大入熱及び高パス間温度の溶接施工条件で引張強さが５９０〜７４０ＭＰａ級の高張力鋼を溶接する場合に、全姿勢溶接においての溶接作業性に優れ、機械的性能に優れた溶接金属を得ることができる炭酸ガスシールドアーク溶接用フラックス入りワイヤに関する。 TECHNICAL FIELD The present invention relates to a flux-cored wire for carbon dioxide shielded arc welding, and in particular, a high-tensile steel having a tensile strength of 590 to 740 MPa under welding conditions of high heat input and high-pass temperature capable of high-efficiency welding. It is related with the flux cored wire for carbon dioxide shielded arc welding which can obtain the weld metal which is excellent in welding work nature in all position welding, and excellent in mechanical performance.
近年、建築鉄骨分野において、溶接施工のさらなる能率向上を図るため、大入熱及び高パス間温度の溶接施工条件に対応するガスシールドアーク溶接用ソリッドワイヤが開発されており、その成分組成の一例がＪＩＳ Ｚ３３１２ ＹＧＷ１８に規定されている。このガスシールドアーク溶接用ソリッドワイヤは、溶接金属の強度及び靭性の低下を招くことなく溶接施工が可能な条件として、引張強さが４９０ＭＰａ級の高張力鋼に対して、最大入熱４０ｋＪ／ｃｍ、最高パス間温度３５０℃の溶接施工条件が許容される。また、引張強さが５２０ＭＰａ級の高張力鋼に対しては、最大入熱３０ｋＪ／ｃｍ、最高パス間温度２５０℃の溶接施工条件が許容される。 In recent years, in order to further improve the efficiency of welding work in the field of building steel frames, solid wire for gas shielded arc welding has been developed that supports welding conditions with high heat input and high interpass temperature. Is defined in JIS Z3312 YGW18. This solid wire for gas shielded arc welding has a maximum heat input of 40 kJ / cm with respect to high-tensile steel with a tensile strength of 490 MPa class as a condition that enables welding work without reducing the strength and toughness of the weld metal. Welding conditions with a maximum interpass temperature of 350 ° C. are acceptable. For high-tensile steel with a tensile strength of 520 MPa, welding conditions with a maximum heat input of 30 kJ / cm and a maximum interpass temperature of 250 ° C. are allowed.
このような大入熱及び高パス間温度の溶接施工条件に対応したガスシールドアーク溶接用ソリッドワイヤとしては、例えば、特開平１０−２３０３８７号公報（特許文献１）、特開平１１−９０６７８号公報（特許文献２）及び特開２００１−２８７０８６号公報（特許文献３）等にあるように、Ｍｏ、Ｃｒ等を多く含むものが提案されている。このようなソリッドワイヤによれば、大入熱及び高パス間温度の溶接施工条件においても強度を確保することが可能であるが、ソリッドワイヤの場合、立向上進溶接においては溶融メタルが垂れ易いため、立向上進溶接で良好な溶接作業性を確保しつつ、高能率に溶接施工が可能な溶接施工条件で溶接するのは困難である。 As solid wires for gas shielded arc welding corresponding to such welding conditions of high heat input and high pass temperature, for example, Japanese Patent Application Laid-Open No. 10-230387 (Patent Document 1) and Japanese Patent Application Laid-Open No. 11-90678. As described in (Patent Document 2) and Japanese Patent Application Laid-Open No. 2001-287086 (Patent Document 3), those containing a large amount of Mo, Cr, and the like have been proposed. According to such a solid wire, it is possible to ensure strength even under welding conditions of high heat input and high-pass temperature, but in the case of solid wire, molten metal tends to sag in the vertical improvement welding. For this reason, it is difficult to perform welding under welding conditions that enable high-efficiency welding work while ensuring good welding workability by vertical improvement welding.
フラックス入りワイヤにより立向上進溶接性を向上した例として、特開平９−２６２６９３号公報（特許文献４）、特開２００４−３４０７８号公報（特許文献５）、特開２００８−８７０４４号公報（特許文献６）等に記載のものが提案されている。しかしながら、これらに記載の何れのフラックス入りワイヤも、高能率に溶接施工が可能な溶接入熱２０〜４０ｋＪ／ｃｍ、パス間温度２００〜３５０℃の溶接施工条件において得られる溶接金属の強度及び靭性が充分ではない。 As examples of improving the vertical weldability by the flux-cored wire, JP-A-9-262893 (Patent Document 4), JP-A-2004-34078 (Patent Document 5), JP-A-2008-87044 (Patent Document) Documents described in Document 6) have been proposed. However, the strength and toughness of the weld metal obtained in any of the flux-cored wires described therein can be obtained under welding conditions of welding heat input of 20 to 40 kJ / cm and inter-pass temperature of 200 to 350 ° C. that can be welded with high efficiency. Is not enough.
このような課題に対応するため、本願発明者らは、特開２０１１−２５２９８号公報（特許文献７）で提案しているように、高能率に溶接施工が可能な大入熱及び高パス間温度の溶接施工条件の下で、良好な溶接作業性が得られるとともに、機械的性能に優れた溶接金属が得られるフラックス入りワイヤを開発している。しかし、このフラックス入りワイヤでは、５２０ＭＰａ級高張力鋼に対応できる強度と０℃での靭性とに優れた溶接金属は確保できるが、さらなる高強度鋼に対応できる強度とさらなる低温での靭性とについて、要求される性能を十分確保できていないという問題があった。 In order to cope with such a problem, the inventors of the present application proposed a high heat input and a high pass interval capable of high-efficiency welding as proposed in Japanese Patent Application Laid-Open No. 2011-25298 (Patent Document 7). We are developing flux-cored wires that can achieve good welding workability and temperature-welded metal under high temperature welding conditions. However, with this flux-cored wire, it is possible to secure a weld metal excellent in strength that can handle 520 MPa class high-strength steel and toughness at 0 ° C., but about strength that can handle higher strength steel and toughness at lower temperatures There was a problem that the required performance could not be secured sufficiently.
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、その目的とするところは、シールドガスに炭酸ガスを用い、高能率に溶接施工が可能な溶接入熱２０〜４０ｋＪ／ｃｍ、パス間温度２００〜３５０℃の溶接施工条件において、全姿勢溶接において溶接作業性が良好であり、さらに５９０〜７４０ＭＰａ級の強度と−４０℃で良好な靭性との溶接金属が得られる炭酸ガスシールドアーク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 the object of the present invention is to use welding heat input of 20 to 40 kJ, which uses carbon dioxide as a shielding gas and can be welded with high efficiency. / Cm, under welding conditions of 200 to 350 ° C between passes, welding workability is good in all-position welding, and a weld metal having a strength of 590 to 740 MPa and good toughness at -40 ° C is obtained. An object of the present invention is to provide a flux-cored wire for carbon dioxide shielded arc welding.
本発明の要旨は、鋼製外皮にフラックスを充填してなる炭酸ガスシールドアーク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、Ｃ：０．０３〜０．１０％、Ｓｉ：０．１〜０．４％、Ｍｎ：１．７〜２．８％、Ｍｏ：０．１〜０．３％、Ｎｉ：０．１〜３．０％、Ｍｇ：０．３５〜０．６５％、Ｂ：０．００１０〜０．０１００％、Ｔｉ酸化物のＴｉＯ2換算値：４．８〜６．５％、Ｓｉ酸化物のＳｉＯ2換算値：０．３〜０．８％、Ｚｒ酸化物のＺｒＯ2換算値：０．２〜０．５％、ＡｌのＡｌ2Ｏ3換算値及びＡｌ2Ｏ3の１種又は２種の合計：０．４〜１．２％、アルカリ金属化合物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の１種又は２種の合計：０．０６〜０．２０％を含有し、弗素化合物のＦ換算値が０．０３％以下であり、残部が鉄粉、鉄合金のＦｅ分、鋼製外皮のＦｅ分及び不可避不純物からなることを特徴とする。 The gist of the present invention is that, in a flux-cored wire for carbon dioxide shielded arc welding, in which a steel outer shell is filled with flux, C: 0.03 to 0.10%, Si: 0.0. 1 to 0.4%, Mn: 1.7 to 2.8%, Mo: 0.1 to 0.3%, Ni: 0.1 to 3.0%, Mg: 0.35 to 0.65% B: 0.0010 to 0.0100%, TiO 2 equivalent value of Ti oxide: 4.8 to 6.5%, SiO 2 equivalent value of Si oxide: 0.3 to 0.8%, Zr oxidation ZrO 2 converted value of the product: 0.2 to 0.5%, Al 2 O 3 converted value of Al and the total of one or two of Al 2 O 3 : 0.4 to 1.2%, alkali metal compound Of Na 2 O converted value and K 2 O converted value of one or two kinds: 0.06 to 0.20% in total, F converted value of fluorine compound is 0.03% It is the following, The remainder consists of iron powder, Fe part of an iron alloy, Fe part of a steel outer shell, and an unavoidable impurity.
また、ワイヤの全水素量が２０ｐｐｍ以下であることも特徴とする炭酸ガスシールドアーク溶接用フラックス入りワイヤにある。 Further, the present invention provides a flux-cored wire for carbon dioxide shielded arc welding, wherein the total hydrogen content of the wire is 20 ppm or less.
本発明に係る炭酸ガスシールドアーク溶接用フラックス入りワイヤによれば、高能率に溶接施工が可能な大入熱及び高パス間温度の溶接施工条件で５９０〜７４０ＭＰａ級高張力鋼を溶接した場合でも、全姿勢溶接においてアークが安定であるとともにスパッタ発生量が少なく、ビード形状及びスラグ剥離性など良好な溶接作業性が得られ、かつ、機械的性能、特に−４０℃での靭性が良好な溶接金属を得ることが可能となる。 According to the flux-cored wire for carbon dioxide shielded arc welding according to the present invention, even when 590 to 740 MPa class high-tensile steel is welded under the welding conditions of high heat input and high-pass temperature enabling high-efficiency welding. In all position welding, the arc is stable, the amount of spatter is small, good welding workability such as bead shape and slag peelability is obtained, and mechanical performance, particularly toughness at -40 ° C is good. It becomes possible to obtain a metal.
本発明者らは、高能率に溶接施工が可能な大入熱及び高パス間温度の溶接施工条件で溶接した場合においても、全姿勢溶接での溶接作業性が良好であるとともに、強度及び低温靭性をはじめとした機械的性能に優れた溶接金属を得るべく、フラックス入りワイヤの成分組成について種々検討を行った。 The inventors of the present invention have good welding workability in all-position welding as well as strength and low temperature even when welding is performed under the welding conditions of high heat input and high-pass temperature capable of highly efficient welding. In order to obtain a weld metal with excellent mechanical performance including toughness, various investigations were made on the composition of the flux-cored wire.
この結果、最大入熱量４０ｋＪ／ｃｍ、最高パス間温度３５０℃で高能率に溶接施工が可能な条件で多層盛溶接した場合において、十分な溶接金属の強度及び低温靭性を確保するためには、ワイヤ中のＣ、Ｍｎ、Ｍｏを適正量とすることにより溶接金属の強度を確保し、さらにＳｉを低く制限し、Ｍｇ、Ｎｉ、Ｂを適正量とすることによって良好な溶接金属の強度及び低温靭性が得られることが判明した。 As a result, in order to ensure sufficient weld metal strength and low-temperature toughness when multi-layer welding is performed under conditions where the maximum heat input is 40 kJ / cm and the temperature between the maximum passes is 350 ° C. and can be welded with high efficiency, Strength of weld metal is ensured by making C, Mn, and Mo in the wire proper, and Si is restricted to a low level. It has been found that toughness can be obtained.
また、全姿勢溶接における溶接作業性は、ＴｉＯ2、ＳｉＯ2、ＺｒＯ2、Ａｌ、Ａｌ2Ｏ3、Ｎａ2Ｏ及びＫ2Ｏを適正量にすると共に、弗素化合物を低減することによって良好になることを見出した。 In addition, the welding workability in all-position welding is improved by making TiO 2 , SiO 2 , ZrO 2 , Al, Al 2 O 3 , Na 2 O and K 2 O appropriate amounts and reducing fluorine compounds. I found out that
以下、本発明に係るフラックス入りワイヤの成分（以下、ワイヤ成分という。）と、その組成の限定理由について説明する。なお、各ワイヤ成分は、フラックス入りワイヤの鋼製外皮又はフラックスの少なくとも一方に含有されるものである。以下の説明において、各ワイヤ成分の組成は、各ワイヤ成分の鋼製外皮とフラックスとでの合計質量をワイヤ全質量に対する質量％での割合で表すこととし、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。 Hereinafter, the components of the flux-cored wire according to the present invention (hereinafter referred to as wire components) and the reasons for limiting the composition will be described. Each wire component is contained in at least one of the steel outer sheath or flux of the flux-cored wire. In the following description, the composition of each wire component is represented by the total mass of the steel outer sheath and the flux of each wire component as a percentage by mass% with respect to the total mass of the wire. It shall be described and expressed.
［Ｃ：０．０３〜０．１０％］
Ｃは、溶接金属の焼入れ性を高め、溶接金属の強度及び低温靭性を確保するうえで重要な元素である。ワイヤ成分のＣが０．０３％未満では、必要な溶接金属の強度及び低温靭性が得られない。一方、ワイヤ成分のＣが０．１０％を超えると、溶接金属の高温割れ感受性が高くなり、クレータ割れ等の高温割れが生じやすくなる。また、溶接金属の強度が過度に高くなり溶接金属の低温靭性がかえって低下する。従って、ワイヤ成分のＣは０．０３〜０．１０％とする。なお、ワイヤ成分のＣ源としては、鋼製外皮中のＣ、フラックス中のＣ単体、鉄粉及び金属粉中のＣ等がある。
[C: 0.03-0.10%]
C is an important element for enhancing the hardenability of the weld metal and ensuring the strength and low temperature toughness of the weld metal. If the C of the wire component is less than 0.03%, the required weld metal strength and low temperature toughness cannot be obtained. On the other hand, if the C of the wire component exceeds 0.10%, the hot metal is susceptible to high temperature cracking, and high temperature cracking such as crater cracking is likely to occur. In addition, the strength of the weld metal becomes excessively high, and the low temperature toughness of the weld metal is reduced. Therefore, C of the wire component is set to 0.03 to 0.10%. Examples of the C source of the wire component include C in the steel outer shell, C alone in the flux, C in iron powder and metal powder, and the like.
［Ｓｉ：０．１〜０．４％］
Ｓｉは、溶接金属の酸素量を低下させて溶接金属の低温靭性を向上させるうえで重要な元素であるが、大入熱及び高パス間温度での溶接施工条件においては、溶接金属中のＳｉが過多であると、再熱部においてマルテンサイトと残留オーステナイトの混合組織（以下、ＭＡという。）の生成が促進され、かえって溶接金属の低温靭性が低下してしまう。しかしながら、ワイヤ成分のＳｉが０．４％以下であれば、−４０℃における靭性について許容できる範囲となる。一方、ワイヤ成分のＳｉが０．１％未満では、脱酸効果が不足するためブローホール等の気孔欠陥が発生する。従って、ワイヤ成分のＳｉは０．１〜０．４％とする。なお、ワイヤ成分のＳｉ源としては、鋼製外皮中のＳｉ、フラックス中のＦｅ−Ｓｉ、Ｆｅ−Ｓｉ−Ｍｎのような合金中のＳｉ等がある。
[Si: 0.1 to 0.4%]
Si is an important element for reducing the oxygen content of the weld metal and improving the low temperature toughness of the weld metal. However, in welding conditions with a large heat input and a high interpass temperature, Si in the weld metal If it is excessive, the formation of a mixed structure of martensite and retained austenite (hereinafter referred to as MA) is promoted in the reheated portion, and the low-temperature toughness of the weld metal is deteriorated. However, if Si of the wire component is 0.4% or less, the toughness at −40 ° C. is acceptable. On the other hand, when the wire component Si is less than 0.1%, the deoxidation effect is insufficient, and pore defects such as blow holes are generated. Therefore, Si of the wire component is set to 0.1 to 0.4%. Examples of the Si source of the wire component include Si in the steel outer shell, Si in an alloy such as Fe-Si and Fe-Si-Mn in a flux, and the like.
［Ｍｎ：１．７〜２．８％］
Ｍｎは、溶接金属の酸素量を下げて必要な溶接金属の低温靭性を得ると共に、溶接金属の焼き入れ性を高めて溶接金属の強度を確保する上で重要な元素である。ワイヤ成分のＭｎが１．７％未満であると、大入熱及び高パス間温度の溶接施工条件の下ではＭｎによる充分な効果が得られず、溶接金属の強度及び低温靭性の低下を招く。ワイヤ成分のＭｎが２．８％を超えると、溶接金属の強度が過度に高くなり溶接金属の低温靭性がかえって低下する。従って、ワイヤ成分のＭｎは１．７〜２．８％とする。ワイヤ成分のＭｎ源としては、鋼製外皮中のＭｎ、フラックス中の金属Ｍｎ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎのような合金中のＭｎ等がある。
[Mn: 1.7 to 2.8%]
Mn is an important element for reducing the oxygen content of the weld metal to obtain the necessary low temperature toughness of the weld metal and enhancing the hardenability of the weld metal to ensure the strength of the weld metal. If the Mn of the wire component is less than 1.7%, sufficient effects due to Mn cannot be obtained under the welding conditions of high heat input and high pass temperature, leading to a decrease in the strength and low temperature toughness of the weld metal. . If the Mn of the wire component exceeds 2.8%, the strength of the weld metal becomes excessively high, and the low temperature toughness of the weld metal decreases. Therefore, the Mn of the wire component is set to 1.7 to 2.8%. Examples of the Mn source of the wire component include Mn in a steel outer shell, metal Mn in a flux, Mn in an alloy such as Fe—Mn, Fe—Si—Mn, and the like.
［Ｍｏ：０．１〜０．３％］
Ｍｏは、Ｍｎと同様に微量添加で溶接金属の焼入れ性を高める元素であり、特に、大入熱及び高パス間温度の溶接施工条件の下で強度を確保するために必須となる元素である。ワイヤ成分のＭｏが０．１％未満であると、必要な溶接金属の強度が得られず溶接金属の低温靭性も低下する。一方、ワイヤ成分のＭｏが０．３％を超えると、溶接金属の強度が高くなりすぎ溶接金属の低温靭性がかえって低下する。従って、ワイヤ成分のＭｏは０．１〜０．３％とする。なお、ワイヤ成分のＭｏ源としては、金属Ｍｏ、Ｆｅ−Ｍｏのような合金中のＭｏ等がある。
[Mo: 0.1 to 0.3%]
Mo, like Mn, is an element that enhances the hardenability of the weld metal by adding a small amount, and in particular, is an element that is indispensable to ensure strength under welding conditions of high heat input and high pass temperature. . If the Mo content of the wire component is less than 0.1%, the required weld metal strength cannot be obtained, and the low temperature toughness of the weld metal also decreases. On the other hand, if the Mo of the wire component exceeds 0.3%, the strength of the weld metal becomes too high, and the low temperature toughness of the weld metal is lowered. Therefore, Mo of the wire component is set to 0.1 to 0.3%. In addition, as Mo source of a wire component, there are Mo in an alloy such as metal Mo and Fe—Mo.
［Ｎｉ：０．１〜３．０％］
Ｎｉは、溶接金属の強度及び低温靭性を向上させる効果がある。ワイヤ成分のＮｉが０．１％未満では、その効果が不十分となり、溶接金属の強度及び低温靭性の低下を招く。ワイヤ成分のＮｉが３．０％を超えると、溶接金属の強度が過度に上昇し溶接金属の低温靭性がかえって低下する。従って、ワイヤ成分のＮｉは０．１〜３．０％とする。なお、ワイヤ成分のＮｉ源としては、金属Ｎｉ、Ｎｉ−Ｍｇのような合金中のＮｉ等がある。
[Ni: 0.1 to 3.0%]
Ni has the effect of improving the strength and low temperature toughness of the weld metal. If Ni of the wire component is less than 0.1%, the effect becomes insufficient, and the strength and low temperature toughness of the weld metal are reduced. If the wire component Ni exceeds 3.0%, the strength of the weld metal excessively increases and the low-temperature toughness of the weld metal decreases. Therefore, Ni of the wire component is set to 0.1 to 3.0%. Note that the Ni source of the wire component includes metal Ni, Ni in an alloy such as Ni—Mg, and the like.
［Ｍｇ：０．３５〜０．６５％］
Ｍｇは、強脱酸剤として溶接金属の酸素を低減することにより溶接金属の低温靭性を向上させる効果がある。特に、大入熱及び高パス間温度の溶接施工条件では、溶融プールが大きくなって他の脱酸剤（Ｃ、Ｓｉ、Ｍｎ）の消耗が多いため、主にＭｇで脱酸して溶接金属の低温靭性を確保する。ワイヤ成分のＭｇが０．３５％未満であると、溶接金属の酸素が多くなって溶接金属の低温靭性が低下する。一方、ワイヤ成分のＭｇが０．６５％を超えると、スパッタ発生量が多くなる。従って、ワイヤ成分のＭｇは０．３５〜０．６５％とする。なお、ワイヤ成分のＭｇ源としては、金属Ｍｇ、Ａｌ−Ｍｇ、Ｎｉ−Ｍｇのような合金中のＭｇ等がある。
[Mg: 0.35-0.65%]
Mg has the effect of improving the low temperature toughness of the weld metal by reducing the oxygen of the weld metal as a strong deoxidizer. In particular, under welding conditions of high heat input and high pass temperature, the molten pool becomes large and the consumption of other deoxidizers (C, Si, Mn) is large. Ensure low temperature toughness. If the wire component Mg is less than 0.35%, oxygen in the weld metal increases and the low-temperature toughness of the weld metal decreases. On the other hand, when the wire component Mg exceeds 0.65%, the amount of spatter generated increases. Therefore, Mg of the wire component is set to 0.35 to 0.65%. The Mg source of the wire component includes Mg in an alloy such as metal Mg, Al—Mg, and Ni—Mg.
［Ｂ：０．００１０〜０．０１００％］
Ｂは、微量の添加により溶接金属の焼入れ性を高めて、溶接金属の低温靭性を向上させる効果がある。ワイヤ成分のＢが０．００１０％未満では、その効果が不十分となり、溶接金属の低温靭性の低下を招く。ワイヤ成分のＢが０．０１００％を超えると、溶接金属の高温割れ感受性が高くなり、クレータ割れ等の高温割れが生じやすくなる。また、溶接金属の強度が過大となり溶接金属の低温靭性がかえって低下する。従って、ワイヤ成分のＢは０．００１０〜０．０１００％とする。なお、Ｂの効果は、金属単体、合金又は酸化物による何れでも発揮することができるため、フラックスに添加する場合の形態は自由である。
[B: 0.0010 to 0.0100%]
B has the effect of increasing the hardenability of the weld metal by adding a small amount and improving the low temperature toughness of the weld metal. If B of the wire component is less than 0.0010%, the effect is insufficient, and the low temperature toughness of the weld metal is reduced. When B of the wire component exceeds 0.0100%, the hot metal is susceptible to high temperature cracking, and high temperature cracking such as crater cracking is likely to occur. In addition, the strength of the weld metal becomes excessive and the low temperature toughness of the weld metal is reduced. Therefore, B of the wire component is set to 0.0010 to 0.0100%. In addition, since the effect of B can be exhibited by any of a single metal, an alloy, or an oxide, the form when added to the flux is arbitrary.
［Ｔｉ酸化物のＴｉＯ2換算値：４．８〜６．５％］
ルチール、チタンスラグ等のＴｉ酸化物は、アーク安定剤であるとともにビード形状を良好にする効果がある。また、Ｔｉ酸化物は、溶融スラグの粘性と融点を適度なものとすることにより、立向上進溶接で溶融メタルが垂れるのを防止する効果がある。さらに、Ｔｉ酸化物は、一部がＴｉ酸化物として溶接金属に歩留り、溶接金属のミクロ組織を微細化して溶接金属の低温靭性を向上させる効果がある。Ｔｉ酸化物のＴｉＯ2換算値が４．８％未満であると、アークが不安定となりスパッタ発生量が多くなるとともに、ビード形状も不良となる。また、立向上進溶接で溶融メタルが垂れるようになる。一方、Ｔｉ酸化物のＴｉＯ2換算値が６．５％を超えると、アークが安定してスパッタ発生量も少なくなるが、多層盛溶接でスラグ量が多くなり、スラグ剥離性が不良となる。また、溶接金属へのＴｉ酸化物の歩留りが過剰になり、非金属介在物が多くなって溶接金属の低温靭性が低下する。従って、Ｔｉ酸化物のＴｉＯ2換算値は４．８〜６．５％とする。
[TiO 2 converted value of Ti oxides: 4.8 to 6.5%]
Ti oxides such as rutile and titanium slag are an arc stabilizer and have an effect of improving the bead shape. In addition, the Ti oxide has an effect of preventing the molten metal from dripping in the vertical improvement welding by making the viscosity and melting point of the molten slag moderate. Furthermore, the Ti oxide partly has a yield as a Ti oxide in the weld metal, and has the effect of reducing the microstructure of the weld metal and improving the low temperature toughness of the weld metal. When the TiO 2 conversion value of the Ti oxide is less than 4.8%, the arc becomes unstable, the amount of spatter generated increases, and the bead shape becomes poor. In addition, the molten metal drips during the vertical improvement welding. On the other hand, if the TiO 2 equivalent value of the Ti oxide exceeds 6.5%, the arc becomes stable and the amount of spatter generated decreases, but the amount of slag increases by multi-layer welding, resulting in poor slag peelability. Moreover, the yield of the Ti oxide to the weld metal becomes excessive, and the non-metallic inclusions are increased, so that the low temperature toughness of the weld metal is lowered. Therefore, the TiO 2 equivalent value of the Ti oxide is 4.8 to 6.5%.
［Ｓｉ酸化物のＳｉＯ2換算値：０．３〜０．８％］
珪砂やジルコンサンド、珪酸ソーダ等のＳｉ酸化物は、大入熱及び高パス間温度の溶接施工条件においても溶融スラグの粘性を高め、特に、立向上進溶接でメタル垂れが発生するのを防止してビード形状を平滑にする効果がある。Ｓｉ酸化物のＳｉＯ2換算値が０．３％未満であると、溶融スラグの粘性が低くなり、立向上進溶接でメタル垂れが発生し易くなることにより、ビード形状が凸形となり平滑なビード形状が得られない。一方、０．８％を超えると、溶接金属中のＭＡ生成が促進され、溶接金属の低温靭性が低下する。従って、Ｓｉ酸化物のＳｉＯ2換算値は０．３〜０．８％とする。
[SiO 2 converted value of Si oxide: 0.3 to 0.8%]
Si oxides such as silica sand, zircon sand, and sodium silicate increase the viscosity of molten slag even under welding conditions with high heat input and high pass temperature, and prevent metal dripping from occurring especially during vertical welding. This has the effect of smoothing the bead shape. When the SiO 2 equivalent value of the Si oxide is less than 0.3%, the viscosity of the molten slag becomes low, and metal dripping is likely to occur during vertical welding, so that the bead shape becomes convex and a smooth bead. The shape cannot be obtained. On the other hand, if it exceeds 0.8%, MA production in the weld metal is promoted, and the low temperature toughness of the weld metal is lowered. Therefore, the SiO 2 equivalent value of the Si oxide is set to 0.3 to 0.8%.
［Ｚｒ酸化物のＺｒＯ2換算値：０．２〜０．５％］
ジルコンサンド、酸化ジルコン等のＺｒ酸化物は、溶融スラグの凝固温度を高くして立向上進溶接で溶融メタルを垂れにくくする効果がある。Ｚｒ酸化物のＺｒＯ2換算値が０．２％未満であると、立向上進溶接で溶融メタルが垂れ易くなることにより、ビード形状が凸形となり平滑なビード形状が得られない。一方、０．５％を超えると、スラグ巻込みが発生し易くなる。従って、Ｚｒ酸化物のＺｒＯ2換算値は０．２〜０．５％とする。
[ZrO 2 converted value of Zr oxide: 0.2 to 0.5%]
Zr oxides such as zircon sand and zircon oxide have the effect of increasing the solidification temperature of the molten slag and making it difficult for the molten metal to sag in the vertical improvement welding. If the ZrO 2 conversion value of the Zr oxide is less than 0.2%, the molten metal is likely to sag in the vertical improvement welding, and the bead shape becomes convex and a smooth bead shape cannot be obtained. On the other hand, if it exceeds 0.5%, slag entrainment tends to occur. Therefore, the ZrO 2 conversion value of the Zr oxide is 0.2 to 0.5%.
［ＡｌのＡｌ2Ｏ3換算値及びＡｌ2Ｏ3の１種又は２種の合計：０．４〜１．２％］
Ａｌは、酸化物となって、Ａｌ2Ｏ3とともに溶融スラグの粘性及び凝固点を調整することによって、スラグ被包性を高めてビード形状を良好にする効果がある。ＡｌのＡｌ2Ｏ3換算値及びＡｌ2Ｏ3の１種又は２種の合計が０．４％未満であると、立向上進溶接で溶融メタルが垂れ易くなることによりビード形状が凸形となり、平滑なビード形状が得られない。一方、１．２％を超えると、溶接金属中に非金属介在物として残留して溶接金属の低温靭性が低下する。従って、ＡｌのＡｌ2Ｏ3換算値及びＡｌ2Ｏ3の１種又は２種の合計は０．４〜１．２％とする。なお、ワイヤ成分のＡｌ源としては、金属Ａｌ、Ｆｅ−Ａｌのような合金中のＡｌ等がある。
[Total of Al or Al 2 O 3 converted value of Al and one or two of Al 2 O 3 : 0.4 to 1.2%]
Al becomes an oxide and has the effect of improving the slag encapsulation and improving the bead shape by adjusting the viscosity and freezing point of the molten slag together with Al 2 O 3 . If the Al 2 O 3 conversion value of Al and the total of one or two of Al 2 O 3 is less than 0.4%, the bead shape becomes convex due to the fact that molten metal tends to sag during vertical welding. A smooth bead shape cannot be obtained. On the other hand, if it exceeds 1.2%, it remains as a non-metallic inclusion in the weld metal and the low temperature toughness of the weld metal is lowered. Therefore, the Al 2 O 3 conversion value of Al and the total of one or two of Al 2 O 3 is 0.4 to 1.2%. The Al source of the wire component includes Al in an alloy such as metal Al and Fe—Al.
［アルカリ金属化合物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の１種又は２種の合計：０．０６〜０．２０％］
カリ長石、珪酸ソーダや珪酸カリからなる水ガラスの固質成分、弗化ソーダや珪弗化カリ等の弗素化合物からのＮａ及びＫは、アーク安定剤及びスラグ形成剤として作用する。アルカリ金属化合物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の１種又は２種の合計が０．０６％未満であると、アークが不安定となりスパッタ発生量が多くなると共に、ビード外観が劣化する。一方、０．２０％を超えると、スラグ剥離性が不良となる。また、立向上進溶接で溶融メタルが垂れやすくなる。従って、アルカリ金属化合物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の１種又は２種の合計は０．０６〜０．２０％とする。
[Total of one or two kinds of Na 2 O equivalent value and K 2 O equivalent value of the alkali metal compound: 0.06 to 0.20%]
Solid components of water glass composed of potassium feldspar, sodium silicate and potassium silicate, and Na and K from fluorine compounds such as sodium fluoride and potassium silicofluoride act as arc stabilizers and slag forming agents. When one or two of the sum of terms of Na 2 O values and K 2 O converted value of the alkali metal compound is less than 0.06%, the arc becomes large amount of occurrence of spatter becomes unstable, bead appearance deterioration To do. On the other hand, if it exceeds 0.20%, the slag peelability becomes poor. In addition, the molten metal tends to sag during the vertical improvement welding. Accordingly, the total of one or two of the alkali metal compound Na 2 O equivalent value and K 2 O equivalent value is 0.06 to 0.20%.
［弗素化合物のＦ換算値：０．０３％以下］
弗化ソーダや珪弗化カリ等の弗素化合物は、アークの指向性を高めて安定した溶融プールを形成する効果があるが、大入熱及び高パス間温度の溶接施工条件においては、弗素化合物のＦ換算値が０．０３％超であると、スパッタ発生量が多くなる。従って、弗素化合物のＦ換算値は０．０３％以下とする。
[F conversion value of fluorine compound: 0.03% or less]
Fluorine compounds such as sodium fluoride and potassium silicofluoride have the effect of increasing the directivity of the arc to form a stable molten pool. However, under the conditions of welding with high heat input and high interpass temperature, fluorine compounds If the F-converted value exceeds 0.03%, the amount of spatter generated increases. Therefore, the F-converted value of the fluorine compound is 0.03% or less.
［全水素量：２０ｐｐｍ以下］
ワイヤ中の水素は、溶接金属の拡散性水素源となるので、耐低温割れ性を高める観点からできるだけ低減することが好ましい。ワイヤ中の全水素量が２０ｐｐｍを超えると、拡散性水素量（ＪＩＳ Ｚ３１１８）が４ｍｌ／１００ｇを超えるので、多層盛溶接をした場合に低温割れ感受性が高まり、低温割れの可能性が大きくなる。従って、ワイヤ中の全水素量は２０ｐｐｍ以下とすることが好ましい。なお、ワイヤ中の全水素量は、不活性ガス融解熱伝導度法等により測定することができる。また、拡散性水素量は、ＪＩＳ Ｚ３１１８に記載の方法により測定することができる。
[Total hydrogen content: 20 ppm or less]
Since hydrogen in the wire serves as a diffusible hydrogen source for the weld metal, it is preferable to reduce it as much as possible from the viewpoint of improving cold cracking resistance. When the total amount of hydrogen in the wire exceeds 20 ppm, the amount of diffusible hydrogen (JIS Z3118) exceeds 4 ml / 100 g, so that the sensitivity to cold cracking is increased when multi-layer welding is performed, and the possibility of cold cracking is increased. Therefore, the total amount of hydrogen in the wire is preferably 20 ppm or less. The total amount of hydrogen in the wire can be measured by an inert gas melting thermal conductivity method or the like. The amount of diffusible hydrogen can be measured by the method described in JIS Z3118.
なお、本発明に係る炭酸ガスシールドアーク溶接用フラックス入りワイヤのその他の成分は、成分調整のために添加した鉄粉、鋼製外皮のＦｅ分、鉄合金（Ｆｅ−Ｓｉ、Ｆｅ−Ｍｎ等）のＦｅ分及び不可避不純物である。 The other components of the flux-cored wire for carbon dioxide shielded arc welding according to the present invention include iron powder added for component adjustment, Fe content of steel outer sheath, iron alloy (Fe-Si, Fe-Mn, etc.) Fe content and inevitable impurities.
また、本発明に係る炭酸ガスシールドアーク溶接用フラックス入りワイヤは、鋼製外皮をパイプ状に成形し、その内部にフラックスを充填した構造である。本発明に係るフラックス入りワイヤの種類としては、鋼製外皮に継ぎ目が無いワイヤと、鋼製外皮に継ぎ目を有するワイヤとに大別できる。鋼製外皮に継ぎ目がないワイヤは、例えば、予め管状に成形されたパイプ内に開口部から粉状のフラックスを充填し、所定の断面寸法まで伸線加工するか、鋼製フープを管状に湾曲成形しながら内部に粉状のフラックスを充填し、次いで合わせ目を溶接してから所定の断面寸法まで伸線加工して製造される。鋼製外皮に継ぎ目があるワイヤは、例えば、鋼製フープを管状に湾曲成形しながら内部に粉状のフラックスを充填し、次いで所定の断面寸法まで伸線加工して製造される。本発明においては、何れの断面構造のワイヤを採用してもよい。 The flux-cored wire for carbon dioxide shielded arc welding according to the present invention has a structure in which a steel outer shell is formed into a pipe shape and the flux is filled therein. The types of the flux-cored wires according to the present invention can be roughly classified into a wire having no seam in the steel outer shell and a wire having a seam in the steel outer shell. For a wire that has no seam in the steel outer sheath, for example, a powder shaped flux is filled from an opening into a pipe that has been previously formed into a tubular shape, and is drawn to a predetermined cross-sectional dimension, or a steel hoop is bent into a tubular shape. It is manufactured by filling a powdery flux inside while forming, then welding the seam, and then drawing to a predetermined cross-sectional dimension. A wire having a seam in a steel outer shell is manufactured, for example, by filling a powdery flux inside while bending a steel hoop into a tubular shape, and then drawing to a predetermined cross-sectional dimension. In the present invention, a wire having any cross-sectional structure may be adopted.
なお、鋼製外皮に貫通した継ぎ目の無いワイヤは、ワイヤの全水素量を低減することを目的として、６５０〜１０００℃の温度域で焼鈍する熱処理が可能であるうえ、製造後の吸湿がないことから、拡散性水素量を低減して耐低温割れ性の向上を容易に実現できるので、より好ましい。鋼製外皮に継ぎ目を有するワイヤは、耐低温割れ性の向上を図る場合、水素含有量の低いフラックスの選定が必要である。 In addition, the seamless wire that penetrates the steel outer sheath can be heat-treated by annealing in a temperature range of 650 to 1000 ° C. for the purpose of reducing the total hydrogen content of the wire, and does not absorb moisture after manufacturing. Therefore, it is more preferable because the amount of diffusible hydrogen can be reduced and the low temperature cracking resistance can be easily improved. For a wire having a seam in a steel outer shell, it is necessary to select a flux having a low hydrogen content in order to improve cold cracking resistance.
また、本発明に係るガスシールドアーク溶接用フラックス入りワイヤは、シールドガスとして炭酸ガスを使用するガスシールドアーク溶接に用いられる。これは、炭酸ガスがアルゴンを主成分とする混合ガスより安価であることと、大入熱溶接においてアルゴンを主成分とする混合ガスよりシールド性の確保が容易であるという利点があるためである。 The flux-cored wire for gas shielded arc welding according to the present invention is used for gas shielded arc welding using carbon dioxide as a shielding gas. This is because carbon dioxide gas has the advantage that it is cheaper than a mixed gas containing argon as a main component, and that shielding properties are easier to secure than a mixed gas containing argon as a main component in large heat input welding. .
以下、本発明の効果を実施例により具体的に説明する。 Hereinafter, the effect of the present invention will be described in detail with reference to examples.
実施例では、まず、ＪＩＳ Ｇ３１４１に記載のＳＰＣＣを鋼製外皮として使用して、下記の表１に示すワイヤＮｏ．１〜２５の成分組成のフラックス入りワイヤを試作した。各試作ワイヤのワイヤ径は１．４ｍｍとした。ワイヤＮｏ．２３〜２５を除く各試作ワイヤは、伸線加工の途中で６５０〜８００℃の温度域で焼鈍を実施した。このうち、鋼製外皮に継ぎ目を有するワイヤＮｏ．４，５及び２１は、Ａｒ雰囲気中で焼鈍した後、ワイヤ製造後にビニール製の袋に封入して溶接時まで保管した。また、ワイヤＮｏ．２３〜２５は、焼鈍及びビニール製の袋への封入は実施しなかった。鋼製外皮に継ぎ目の無いワイヤは、ワイヤ表面に銅めっきを施した。なお、表１において、フラックス入りワイヤの成分組成が本発明において規定した範囲外であるものについては下線を付すこととした。 In Examples, first, SPCC described in JIS G3141 was used as a steel outer sheath, and wire Nos. Shown in Table 1 below were used. A flux-cored wire having a component composition of 1 to 25 was manufactured. The diameter of each prototype wire was 1.4 mm. Wire No. Each prototype wire except 23 to 25 was annealed in the temperature range of 650 to 800 ° C. during the drawing process. Of these, the wire No. having a seam in the steel outer sheath. Nos. 4, 5 and 21 were annealed in an Ar atmosphere, sealed in a vinyl bag after wire production, and stored until welding. In addition, wire No. In Nos. 23 to 25, annealing and encapsulation in a plastic bag were not performed. Wires that were seamless to the steel skin were plated with copper on the wire surface. In Table 1, those in which the component composition of the flux-cored wire is outside the range defined in the present invention are underlined.
各試作ワイヤは、その各試作ワイヤを実際に用いて、高能率に溶接施工が可能な溶接入熱３５〜４０ｋＪ／ｃｍ、パス間温度２００〜３５０℃の溶接施工条件の下で立向上進多層溶接を行った時の溶接作業性と、溶接後に得られる溶接金属の機械的性能及び拡散性水素量を調査した。また、各試作ワイヤは、溶接金属の耐低温割れ性を調査するため、後述の溶接割れ試験を行なった。 Each prototype wire is a multi-layer that can be improved under the welding conditions of 35 to 40 kJ / cm welding heat input and 200 to 350 ° C between passes, which can be welded efficiently by using each prototype wire. We investigated the welding workability when welding, the mechanical performance and diffusible hydrogen content of the weld metal obtained after welding. Each prototype wire was subjected to a weld cracking test described later in order to investigate the low temperature cracking resistance of the weld metal.
立向上進多層溶接は、板厚２５ｍｍの建築構造用鋼であり引張強さが５９０ＭＰａ級の鋼ＳＡ４４０Ｂを試験体として用い、その試験体について開先角度３５度、ルート間隔７ｍｍとしたうえで裏当てを配置した条件として、下記の表２に示す溶接条件の下で、試験体を各試作ワイヤによりガスシールドアーク溶接することにより行った。立向上進多層溶接では、アークの安定性、スパッタの発生状態、ビード形状及びスラグ剥離性を調査して、その調査結果に基づき各試作ワイヤを評価した。 Multi-layer welding is a steel for building structures with a plate thickness of 25 mm, and steel 440 B with a tensile strength of 590 MPa is used as a test specimen. The test specimen has a groove angle of 35 degrees and a root interval of 7 mm. As a condition for placing the abutment, the test specimen was subjected to gas shield arc welding with each prototype wire under the welding conditions shown in Table 2 below. In the vertical improvement multi-layer welding, the arc stability, spatter generation state, bead shape and slag peelability were investigated, and each prototype wire was evaluated based on the investigation results.
立向上進多層溶接により得られた溶接金属は、溶接金属の板厚中央部から引張試験片（ＪＩＳ Ｚ２２４１ １０号）及びシャルピー衝撃試験片（ＪＩＳ Ｚ２２４２ Ｖノッチ試験片）を採取して、それぞれＪＩＳ Ｚ２２４１に記載の方法及びＪＩＳ Ｚ２２４２に記載の方法に準拠して引張試験及びシャルピー衝撃試験を行ない、その試験結果に基づき各試作ワイヤを評価した。このとき、シャルピー衝撃試験は、試験温度を−４０℃として各試作ワイヤにつき三回分の試験を行ない、各試験により得られた吸収エネルギーの平均値を求めることとした。引張強さは５９０〜７４０ＭＰａの範囲内、吸収エネルギーの平均値は７０Ｊ以上を合格とした。 The weld metal obtained by vertical multi-layer welding was obtained by collecting a tensile test piece (JIS Z2241 No. 10) and a Charpy impact test piece (JIS Z2242 V-notch test piece) from the center of the weld metal thickness. A tensile test and a Charpy impact test were performed based on the method described in Z2241 and the method described in JIS Z2242, and each prototype wire was evaluated based on the test results. At this time, in the Charpy impact test, the test temperature was set to −40 ° C., the test was performed three times for each prototype wire, and the average value of the absorbed energy obtained by each test was determined. The tensile strength was within a range of 590 to 740 MPa, and the average value of absorbed energy was 70 J or more.
拡散性水素量は、ＪＩＳ Ｚ３１１８に記載の方法に準拠して測定した。拡散性水素量は４ｍｌ／１００ｇ以下を良好とした。ワイヤの全水素量は、（株）堀場製作所製の水素分析装置（ＥＭＧＡ−６２１）を用いて測定した。 The amount of diffusible hydrogen was measured according to the method described in JIS Z3118. The amount of diffusible hydrogen was 4 ml / 100 g or less. The total hydrogen content of the wire was measured using a hydrogen analyzer (EMGA-621) manufactured by Horiba, Ltd.
溶接割れ試験は、ＪＩＳ Ｚ３１５７のＵ形溶接割れ試験方法に準拠して行うこととし、板厚３５ｍｍの建築構造用鋼であり引張強さが５９０ＭＰａ級の鋼ＳＡ４４０Ｂを試験体として試験板を製作し、下記の表３に示す溶接条件の下で試験板の開先を各試験ワイヤによりガスシールドアーク溶接し、溶接後４８時間経過した試験体について、表面割れ及び断面割れ（５断面）の発生有無を浸透探傷試験（ＪＩＳ Ｚ２３４３）により調査することで行なった。 The weld crack test shall be conducted in accordance with the U-shaped weld crack test method of JIS Z3157. A test plate was manufactured using steel SA440B with a thickness of 35 mm and a tensile strength of 590 MPa class steel SA440B. The presence or absence of occurrence of surface cracks and cross-sectional cracks (5 cross-sections) on the specimens that were gas-shielded arc welded to the test plate with each test wire under the welding conditions shown in Table 3 below and 48 hours after welding Was examined by a penetrant flaw detection test (JIS Z2343).
以上の試験結果を表４にまとめて示す。なお、表４において、評価対象とした数値が合格又は良好でないものについては下線を付すこととした。 The above test results are summarized in Table 4. In addition, in Table 4, it was decided that the numerical value made into the evaluation object was underlined about what passed or was not favorable.
表１及び表４中のワイヤＮｏ．１〜１０が本発明例、ワイヤＮｏ．１１〜２５は比較例である。本発明例であるワイヤＮｏ．１〜１０は、フラックス入りワイヤの成分組成が本発明において規定した条件を満足しているので、アークが安定であり、スパッタ発生量が少なく、ビードの垂れがなく、ビード形状及びスラグ剥離性が良好であり、溶接金属の引張強さ及び吸収エネルギーが目標とする性能を満足した。また、ワイヤＮｏ．１〜１０は、ワイヤ中の全水素量が本発明において規定した条件を満足しているので、拡散性水素量が少なく、Ｕ形溶接割れ試験で割れが発生しないなど、極めて満足な結果であった。 In Table 1 and Table 4, the wire No. 1 to 10 are examples of the present invention, wire Nos. 11 to 25 are comparative examples. In the present invention, the wire No. 1 to 10, since the composition of the flux-cored wire satisfies the conditions specified in the present invention, the arc is stable, the amount of spatter is small, the bead does not sag, the bead shape and the slag peelability are The tensile strength and absorbed energy of the weld metal satisfied the target performance. In addition, wire No. Nos. 1 to 10 are extremely satisfactory results such that the total hydrogen amount in the wire satisfies the conditions specified in the present invention, so that the amount of diffusible hydrogen is small and cracks do not occur in the U-shaped weld crack test. It was.
これに対して、比較例であるワイヤＮｏ．１１は、Ｃが少ないので溶接金属の引張強さが低く、溶接金属の吸収エネルギーも低値であった。また、ＳｉＯ2換算値が少ないので、メタル垂れが発生してビード形状が凸ビードとなった。 In contrast, the wire No. No. 11 had low C, so the tensile strength of the weld metal was low, and the absorbed energy of the weld metal was also low. Further, since the SiO 2 conversion value was small, metal dripping occurred and the bead shape became a convex bead.
ワイヤＮｏ．１２は、Ｃが多いのでクレータ部に割れが発生し、溶接金属の引張強さが高く、溶接金属の吸収エネルギーが低値であった。また、ＴｉＯ2換算値が少ないので、アークが不安定となりスパッタの発生量が多く、メタル垂れが発生してビード形状が凸ビードとなった。 Wire No. In No. 12, since there was much C, the crater part was cracked, the tensile strength of the weld metal was high, and the absorbed energy of the weld metal was low. Further, since the TiO 2 conversion value is small, the arc becomes unstable, the amount of spatter generated is large, metal dripping occurs, and the bead shape becomes a convex bead.
ワイヤＮｏ．１３は、Ｓｉが少ないので、溶接金属の脱酸が不十分となりブローホールが発生した。また、ＡｌのＡｌ2Ｏ3換算値及びＡｌ2Ｏ3の合計が多いので、溶接金属の吸収エネルギーが低値であった。 Wire No. In No. 13, since there was little Si, deoxidation of the weld metal was insufficient and blow holes were generated. Further, since the total amount of Al in terms of Al 2 O 3 and Al 2 O 3 is large, the absorbed energy of the weld metal was low.
ワイヤＮｏ．１４は、Ｓｉが多いので、溶接金属の吸収エネルギーが低値であった。また、ＺｒＯ2換算値が多いので、スラグ巻込みが発生した。 Wire No. No. 14 has a large amount of Si, so the absorbed energy of the weld metal was low. Further, since the terms of ZrO 2 value is large, slag inclusion occurs.
ワイヤＮｏ．１５は、Ｍｎが少ないので、溶接金属の引張強さが低かった。また、Ｍｇが少ないので、溶接金属の酸素量が高くなり吸収エネルギーが低値であった。 Wire No. No. 15 had a low Mn, so the tensile strength of the weld metal was low. Moreover, since there was little Mg, the oxygen amount of the weld metal became high and the absorbed energy was low.
ワイヤＮｏ．１６は、Ｍｎが多いので、溶接金属の引張強さが高く、溶接金属の吸収エネルギーが低値であった。また、ＺｒＯ2換算値が少ないので、メタル垂れが発生してビード形状が凸ビードとなった。 Wire No. Since No. 16 had a large amount of Mn, the tensile strength of the weld metal was high, and the absorbed energy of the weld metal was low. Further, since the ZrO 2 converted value was small, metal dripping occurred and the bead shape became a convex bead.
ワイヤＮｏ．１７は、Ｍｏが少ないので、溶接金属の引張強さが低く、溶接金属の吸収エネルギーも低値であった。また、ＡｌのＡｌ2Ｏ3換算値が低いので、メタル垂れが発生してビード形状が凸ビードになった。 Wire No. Since No. 17 had little Mo, the tensile strength of the weld metal was low, and the absorbed energy of the weld metal was also low. Moreover, since the Al 2 O 3 conversion value of Al was low, metal sagging occurred and the bead shape became a convex bead.
ワイヤＮｏ．１８は、Ｍｏが多いので、溶接金属の引張強さが高く、溶接金属の吸収エネルギーが低値であった。また、ワイヤ中の全水素量が高いので、拡散性水素量が多く、Ｕ形溶接割れ試験で低温割れが発生した。 Wire No. Since No. 18 had a lot of Mo, the tensile strength of the weld metal was high, and the absorbed energy of the weld metal was low. Further, since the total amount of hydrogen in the wire was high, the amount of diffusible hydrogen was large, and cold cracking occurred in the U-shaped weld cracking test.
ワイヤＮｏ．１９は、Ｎｉが少ないので溶接金属の吸収エネルギーが低値であった。また、Ｋ2Ｏ換算値が少ないので、アークが不安定となりスパッタ発生量が多く、ビード外観も不良であった。 Wire No. In No. 19, since the amount of Ni is small, the absorbed energy of the weld metal was low. Further, since the K 2 O conversion value is small, the arc becomes unstable, the amount of spatter generated is large, and the bead appearance is also poor.
ワイヤＮｏ．２０は、Ｎｉが多いので、溶接金属の引張強さが高く、溶接金属の吸収エネルギーが低値であった。また、ワイヤ中の全水素量が高いので、拡散性水素量が多く、Ｕ形溶接割れ試験で低温割れが発生した。 Wire No. No. 20 had a large amount of Ni, so the tensile strength of the weld metal was high, and the absorbed energy of the weld metal was low. Further, since the total amount of hydrogen in the wire was high, the amount of diffusible hydrogen was large, and cold cracking occurred in the U-shaped weld cracking test.
ワイヤＮｏ．２１は、Ｍｇが多いので、スパッタ発生量が多かった。また、Ｎａ2Ｏ換算値及びＫ2Ｏ換算値の合計が多いので、スラグ剥離性が不良であり、メタル垂れが発生してビード形状が凸ビードになった。 Wire No. Since No. 21 had a large amount of Mg, the amount of spatter generated was large. Further, since the terms of Na 2 O values and K sum is often the 2 O converted value, a slag removability poor bead shape becomes convex bead metal dripping occurs.
ワイヤＮｏ．２２は、Ｂが少ないので、溶接金属の吸収エネルギーが低値であった。また、Ｆ換算値が多いので、スパッタ発生量が多かった。 Wire No. No. 22 had a low B, so the absorbed energy of the weld metal was low. Moreover, since there were many F conversion values, the amount of spatter generation was large.
ワイヤＮｏ．２３は、Ｂが多いので、クレータ割れが生じ、溶接金属の強度が高く、溶接金属の吸収エネルギーが低値であった。また、ワイヤ中の全水素量が高いので、拡散性水素量が多く、Ｕ形溶接割れ試験で低温割れが発生した。 Wire No. No. 23 had a large amount of B, so crater cracking occurred, the strength of the weld metal was high, and the absorbed energy of the weld metal was low. Further, since the total amount of hydrogen in the wire was high, the amount of diffusible hydrogen was large, and cold cracking occurred in the U-shaped weld cracking test.
ワイヤＮｏ．２４は、ＴｉＯ2換算値が多いのでスラグ剥離性が不良であり、溶接金属の吸収エネルギーも低値であった。また、ワイヤ中の全水素量が高いので、拡散性水素量が多く、Ｕ形溶接割れ試験で低温割れが発生した。 Wire No. No. 24 had a poor slag removability because of its large TiO 2 conversion value, and the absorbed energy of the weld metal was also low. Further, since the total amount of hydrogen in the wire was high, the amount of diffusible hydrogen was large and cold cracking occurred in the U-shaped weld cracking test.
ワイヤＮｏ．２５は、ＳｉＯ2換算値が多いので、溶接金属の吸収エネルギーが低値であった。また、ワイヤ中の全水素量が高いので、拡散性水素量が多く、Ｕ形溶接割れ試験で低温割れが発生した。 Wire No. Since No. 25 has a large SiO 2 converted value, the absorbed energy of the weld metal was low. Further, since the total amount of hydrogen in the wire was high, the amount of diffusible hydrogen was large, and cold cracking occurred in the U-shaped weld cracking test.
Claims (2)
ワイヤ全質量に対する質量％で、
Ｃ：０．０３〜０．１０％、
Ｓｉ：０．１〜０．４％、
Ｍｎ：１．７〜２．８％、
Ｍｏ：０．１〜０．３％、
Ｎｉ：０．１〜３．０％、
Ｍｇ：０．３５〜０．６５％、
Ｂ：０．００１０〜０．０１００％、
Ｔｉ酸化物のＴｉＯ2換算値：４．８〜６．５％、
Ｓｉ酸化物のＳｉＯ2換算値：０．３〜０．８％、
Ｚｒ酸化物のＺｒＯ2換算値：０．２〜０．５％、
ＡｌのＡｌ2Ｏ3換算値及びＡｌ2Ｏ3の１種又は２種の合計：０．４〜１．２％、
アルカリ金属化合物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の１種又は２種の合計：０．０６〜０．２０％を含有し、
弗素化合物のＦ換算値が０．０３％以下であり、
残部が鉄粉、鉄合金のＦｅ分、鋼製外皮のＦｅ分及び不可避不純物からなること
を特徴とする炭酸ガスシールドアーク溶接用フラックス入りワイヤ。 In the flux-cored wire for carbon dioxide shielded arc welding formed by filling flux in the steel outer sheath,
% By mass relative to the total mass of the wire
C: 0.03-0.10%,
Si: 0.1 to 0.4%,
Mn: 1.7-2.8%,
Mo: 0.1 to 0.3%,
Ni: 0.1 to 3.0%,
Mg: 0.35-0.65%,
B: 0.0010 to 0.0100%,
TiO 2 conversion value of Ti oxide: 4.8 to 6.5%,
SiO 2 converted value of Si oxide: 0.3 to 0.8 percent,
ZrO 2 conversion value of Zr oxide: 0.2 to 0.5%,
Al 2 O 3 conversion value of Al and total of one or two of Al 2 O 3 : 0.4 to 1.2%,
One or two of the sum of terms of Na 2 O values and K 2 O converted value of the alkali metal compound: containing from 0.06 to 0.20%,
F conversion value of fluorine compound is 0.03% or less,
A flux-cored wire for carbon dioxide shielded arc welding, wherein the balance is composed of iron powder, Fe content of an iron alloy, Fe content of a steel outer sheath, and inevitable impurities.
を特徴とする請求項１に記載の炭酸ガスシールドアーク溶接用フラックス入りワイヤ。 The flux-cored wire for carbon dioxide shielded arc welding according to claim 1, wherein the total hydrogen content of the wire is 20 ppm or less.
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| KR101784275B1 (en) * | 2016-02-11 | 2017-10-11 | 한국기술교육대학교 산학협력단 | Method for welding alloy steel and carbon steel |
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