JP2018114515A - Coated electrode for low hydrogen type fillet welding - Google Patents
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- 238000003466 welding Methods 0.000 title claims abstract description 92
- 239000001257 hydrogen Substances 0.000 title claims abstract description 22
- 229910052739 hydrogen Inorganic materials 0.000 title claims abstract description 22
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims abstract description 21
- 229910052751 metal Inorganic materials 0.000 claims abstract description 46
- 239000002184 metal Substances 0.000 claims abstract description 46
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- 238000006243 chemical reaction Methods 0.000 claims abstract description 23
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- 238000000576 coating method Methods 0.000 claims description 26
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 11
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 11
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 9
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 239000003517 fume Substances 0.000 abstract description 15
- 239000000843 powder Substances 0.000 abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 239000002893 slag Substances 0.000 description 54
- 239000011324 bead Substances 0.000 description 40
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 24
- 239000011734 sodium Substances 0.000 description 22
- 230000000694 effects Effects 0.000 description 14
- 239000010936 titanium Substances 0.000 description 14
- 238000005538 encapsulation Methods 0.000 description 13
- 239000000395 magnesium oxide Substances 0.000 description 12
- 239000007921 spray Substances 0.000 description 9
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 8
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 8
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- 235000019353 potassium silicate Nutrition 0.000 description 5
- 229910052710 silicon Inorganic materials 0.000 description 5
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 238000001035 drying Methods 0.000 description 4
- 239000010433 feldspar Substances 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 3
- 229910006639 Si—Mn Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
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- 229910052759 nickel Inorganic materials 0.000 description 3
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- 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
- 101100513612 Microdochium nivale MnCO gene Proteins 0.000 description 2
- KWYUFKZDYYNOTN-UHFFFAOYSA-M Potassium hydroxide Chemical compound [OH-].[K+] KWYUFKZDYYNOTN-UHFFFAOYSA-M 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000010445 mica Substances 0.000 description 2
- 229910052618 mica group Inorganic materials 0.000 description 2
- 229940072033 potash Drugs 0.000 description 2
- 235000015320 potassium carbonate Nutrition 0.000 description 2
- BWHMMNNQKKPAPP-UHFFFAOYSA-L potassium carbonate Substances [K+].[K+].[O-]C([O-])=O BWHMMNNQKKPAPP-UHFFFAOYSA-L 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 2
- IXPNQXFRVYWDDI-UHFFFAOYSA-N 1-methyl-2,4-dioxo-1,3-diazinane-5-carboximidamide Chemical compound CN1CC(C(N)=N)C(=O)NC1=O IXPNQXFRVYWDDI-UHFFFAOYSA-N 0.000 description 1
- 229910016569 AlF 3 Inorganic materials 0.000 description 1
- 229910016036 BaF 2 Inorganic materials 0.000 description 1
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- 239000004111 Potassium silicate Substances 0.000 description 1
- CDBYLPFSWZWCQE-UHFFFAOYSA-L Sodium Carbonate Chemical compound [Na+].[Na+].[O-]C([O-])=O CDBYLPFSWZWCQE-UHFFFAOYSA-L 0.000 description 1
- 239000004115 Sodium Silicate Substances 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 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
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000005587 bubbling Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
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- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000004898 kneading Methods 0.000 description 1
- 235000013372 meat Nutrition 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
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- 150000002830 nitrogen compounds Chemical class 0.000 description 1
- 238000010943 off-gassing Methods 0.000 description 1
- 239000003973 paint 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
- 239000002244 precipitate Substances 0.000 description 1
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- 239000004576 sand Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 239000000661 sodium alginate Substances 0.000 description 1
- 235000010413 sodium alginate Nutrition 0.000 description 1
- 229940005550 sodium alginate Drugs 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
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- 230000006641 stabilisation Effects 0.000 description 1
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- 238000009834 vaporization Methods 0.000 description 1
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- 238000005493 welding type Methods 0.000 description 1
Abstract
Description
本発明は、プライマ塗装鋼板のすみ肉溶接において、特に耐ピット性に優れ、ヒューム発生量が少なく、良好なビード形状が得られるなど溶接作業性が良好で、溶接金属の機械的性質に優れ、かつ、生産性にも優れる低水素系すみ肉溶接用被覆アーク溶接棒に関する。 In the fillet welding of the primer coated steel sheet, the present invention is particularly excellent in pit resistance, less fume generation, good bead shape such as good bead shape, excellent mechanical properties of the weld metal, The present invention also relates to a coated arc welding rod for low hydrogen fillet welding that is excellent in productivity.
近年、建築、橋梁及び船舶などの溶接構造物の大型化に伴って４９０ＭＰａｇ級高張力鋼の厚板の鋼板が使用されているが、大気または海洋地域などの過酷な環境下で長時間使用される箇所では、鋼板表面に防錆を目的にプライマを塗装したプライマ塗装鋼板が広く使用されている。 In recent years, 490 MPag class high-strength steel plates have been used along with the increase in the size of welded structures such as buildings, bridges and ships, but they have been used for a long time in harsh environments such as the atmosphere or marine areas. The primer-coated steel sheet in which a primer is coated on the steel sheet surface for the purpose of rust prevention is widely used.
このような厚板のプライマ塗装鋼板を用いた溶接構造物の溶接では、複雑な構造物の溶接が可能で溶接能率が高く、溶接部の機械的性質を確保できるグラビティ溶接での太径の低水素系すみ肉溶接用被覆アーク溶接棒が使用されることが多い。しかし、プライマ塗装鋼板のすみ肉溶接の場合では、溶接時に鋼板表面に塗装したプライマが蒸気化されてピットが多発しやすくなり、またヒューム発生量も多いなど溶接作業性が悪くなるという問題点がある。 In welding of welded structures using such thick primer-coated steel sheets, welding of complex structures is possible, welding efficiency is high, and mechanical properties of the welded part can be ensured. Coated arc welding rods for hydrogen fillet welding are often used. However, in the case of fillet welding of primer coated steel sheet, the primer coated on the steel sheet surface during vaporization is vaporized and pits are likely to occur frequently. is there.
また、グラビティ溶接での低水素系すみ肉溶接用被覆アーク溶接棒は、１パス溶接での溶着量を確保するために通常の被覆アーク溶接棒に比べて太径心線で被覆外径が大きく長尺であるから、生産時に被覆割れなどが発生しやすいなど生産性が悪くなるという問題点もある。 In addition, the coated arc welding rod for low hydrogen fillet welding in gravity welding has a large core diameter and a large coating outer diameter compared to a normal coated arc welding rod in order to secure the amount of welding in one-pass welding. Since it is long, there is also a problem that productivity is deteriorated, for example, coating cracks are likely to occur during production.
このような状況下において、グラビティ溶接で耐ピット性に優れ、ヒューム発生量が少ないなど溶接作業性が良好で、溶接部の機械的性質に優れ、かつ、生産性にも優れた低水素系すみ肉溶接用被覆アーク溶接棒が従来において提案されている。 Under such circumstances, low hydrogen-based corners with excellent weldability, such as excellent pit resistance and low fume generation in gravity welding, excellent welded mechanical properties, and excellent productivity. Conventionally, a coated arc welding rod for meat welding has been proposed.
例えば、特許文献１には、被覆剤中のＴｉＯ2、ＳｉＯ2、ＭｇＣＯ3、ＭｎＣＯ3含有量の比を規定することで、耐ピット性など溶接作業性が改善された低水素系被覆アーク溶接棒が開示されている。特許文献１に記載された低水素系被覆アーク溶接棒によれば、通常のプライマ塗装鋼板の溶接における耐ピット性は改善できる。しかし、ウォッシュプライマ塗装鋼板を溶接した場合には十分な耐ピット性が得られなくなるという問題点がある。また、特許文献１の記載の技術では、ヒューム発生量の低減などの良好な溶接作業性は得られない。また特許文献１の記載の技術では、生産時に被覆割れが生じるなどの問題点もある。 For example, Patent Document 1 discloses a low hydrogen-based coated arc welding in which welding workability such as pit resistance is improved by defining the ratio of the content of TiO 2 , SiO 2 , MgCO 3 , and MnCO 3 in the coating agent. A bar is disclosed. According to the low hydrogen-based coated arc welding rod described in Patent Document 1, the pit resistance in welding of a normal primer-coated steel sheet can be improved. However, there is a problem that sufficient pit resistance cannot be obtained when a wash primer-coated steel sheet is welded. Further, the technique described in Patent Document 1 cannot provide good welding workability such as a reduction in the amount of fume generated. In addition, the technique described in Patent Document 1 has a problem that a coating crack occurs during production.
また、特許文献２及び特許文献３には、被覆剤中にグラファイト、活性炭または炭素を含む合金鉄及び窒素化合物を適量添加することにより、溶接時にガス放出による溶融池中にバブリングを発生させて耐ピット性が改善できる被覆アーク溶接棒が開示されている。特許文献２及び特許文献３に記載された被覆アーク溶接棒によれば、通常のプライマ塗装鋼板の溶接における耐ピット性の改善が得られるものの、特許文献１と同様、ウォッシュプライマ塗装鋼板を溶接する場合には十分な耐ピット性が得られず、ヒューム発生量が多くなるなど良好な溶接作業性は得られない。また、生産時に被覆割れが生じるなど良好な生産性も得られない。 Further, in Patent Document 2 and Patent Document 3, by adding an appropriate amount of graphite, activated carbon or carbon-containing alloy iron and nitrogen compound in the coating agent, bubbling is generated in the molten pool due to outgassing during welding, and resistance to resistance is increased. A coated arc welding rod capable of improving the pit property is disclosed. According to the coated arc welding rods described in Patent Document 2 and Patent Document 3, although improvement in pit resistance in welding of a normal primer coated steel sheet can be obtained, as in Patent Document 1, a wash primer coated steel sheet is welded. In such a case, sufficient pit resistance cannot be obtained, and good welding workability such as an increased amount of fumes cannot be obtained. In addition, good productivity such as coating cracks during production cannot be obtained.
さらに、特許文献４には、被覆剤中に金属弗化物、ＭｇＯ、ＴｉＯ2、ＳｉＯ2、弗素四ケイ素雲母を適量添加することで、スラグの流動性を向上させて溶接作業性、特にヒューム発生量を低減するとともに、金属炭酸塩及びＴｉ、Ａｌ、Ｍｇ、Ｓｉ及びＳｉＣの１種以上を適量添加することで耐ピット性を改善できる低水素系被覆アーク溶接棒が開示されている。特許文献４に記載された低水素系被覆アーク溶接棒によれば、通常のプライマ塗装鋼板の溶接でヒューム発生量を低減しつつ耐ピット性が改善されるが、これも特許文献１と同様にウォッシュプライマ塗装鋼板を溶接する場合には十分な耐ピット性が得られない。また、生産時に被覆割れが生じるなど良好な生産性が得られなくなるという問題点があった。 Furthermore, in Patent Document 4, metal fluoride, MgO, TiO 2 , SiO 2 , and fluorotetrasilicon mica are added to the coating agent in an appropriate amount to improve the fluidity of slag and improve the workability of welding, particularly fume generation. A low hydrogen-based coated arc welding rod that can improve the pit resistance by reducing the amount and adding an appropriate amount of one or more of metal carbonate and Ti, Al, Mg, Si, and SiC is disclosed. According to the low hydrogen-based coated arc welding rod described in Patent Document 4, pit resistance is improved while reducing the amount of generated fume by welding of a normal primer-coated steel sheet. When welding a wash primer coated steel sheet, sufficient pit resistance cannot be obtained. In addition, there was a problem that good productivity could not be obtained such as coating cracking during production.
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、低水素系すみ肉溶接用被覆アーク溶接棒によるプライマ塗装鋼板のすみ肉溶接において、優れた耐ピット性を確保しつつ、ヒューム発生量が少なく、良好なビード形状が得られるなど溶接作業性に優れるとともに、優れた溶接金属の機械的性質が得られ、かつ、生産時に被覆割れが生じることがなく生産性が良好な低水素系すみ肉溶接用被覆アーク溶接棒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 while ensuring excellent pit resistance in fillet welding of a primer coated steel sheet using a coated arc welding rod for low hydrogen fillet welding. In addition to excellent welding workability such as low fume generation and good bead shape, excellent mechanical properties of weld metal can be obtained, and good productivity without cracking during production An object of the present invention is to provide a coated arc welding rod for low-hydrogen fillet welding.
本発明の要旨は、鋼心線に被覆剤が塗布されている低水素系すみ肉溶接用被覆アーク溶接棒において、前記被覆剤は、当該被覆剤全質量に対する質量％で、金属炭酸塩の１種または２種以上の合計：５〜１５％、金属弗化物の２種以上の合計：３〜８％、前記金属弗化物中のＮａＦ：０．２〜１．５％、Ｔｉ酸化物のＴｉＯ2換算値の合計：５〜１５％、Ｓｉ酸化物のＳｉＯ2換算値の合計：１０〜２０％、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計：０．５〜３．０％、Ｆｅ酸化物のＦｅＯ換算値の合計：０．５〜１．５％、ＭｇＯ：２〜６％、Ｓｉ：０．５〜２．０％、Ｍｎ：５〜８％、Ｎｉ：０．３〜２．０％、鉄粉：２５〜４５％、Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計：１．５〜５．５％を含有し、残部は塗布剤、鉄合金からのＦｅ分及び不可避不純物からなることを特徴とする低水素系すみ肉溶接用被覆アーク溶接棒にある。 The gist of the present invention is that, in a coated arc welding rod for low hydrogen fillet welding in which a coating is applied to a steel core wire, the coating is 1% by mass of metal carbonate with respect to the total mass of the coating. Total of two or more species: 5 to 15%, Total of two or more metal fluorides: 3 to 8%, NaF in the metal fluoride: 0.2 to 1.5%, TiO of Ti oxide 2 Total of converted values: 5 to 15%, Total of SiO 2 converted values of Si oxide: 10 to 20%, Total of Al 2 O 3 converted values of Al oxide: 0.5 to 3.0%, Fe Total of FeO equivalent values of oxide: 0.5 to 1.5%, MgO: 2 to 6%, Si: 0.5 to 2.0%, Mn: 5 to 8%, Ni: 0.3 to 2 .0%, iron powder: 25% to 45%, the sum of the terms of Na 2 O values and K 2 O conversion value of Na oxide and K oxides: containing 1.5 to 5.5%, the balance being paint Agent, in Fe content and a low hydrogen type corner covered electrode for weld, characterized in that inevitable impurities from iron alloys.
本発明の低水素系すみ肉溶接用被覆アーク溶接棒によれば、プライマ塗装鋼板のすみ肉溶接において優れた耐ピット性を確保しつつ、ヒューム発生量が少なく、良好なビード形状が得られるなど溶接作業性が良好で、優れた溶接金属の機械的性質が得られ、かつ、生産性にも優れるので、溶接の高能率化及び品質向上が図れる。 According to the coated arc welding rod for low hydrogen fillet welding of the present invention, while ensuring excellent pit resistance in fillet welding of a primer coated steel sheet, the amount of fume generation is small and a good bead shape can be obtained. Since the welding workability is good, the excellent mechanical properties of the weld metal are obtained, and the productivity is excellent, the efficiency of welding can be improved and the quality can be improved.
本発明者らは、上述した課題を解決するため、プライマ塗装鋼板のすみ肉溶接で耐ピット性が不良になる原因などについて種々検討した。 In order to solve the above-described problems, the present inventors have made various studies on the cause of poor pit resistance by fillet welding of a primer-coated steel sheet.
プライマ塗装鋼板のすみ肉溶接では、鋼板表面に塗装したプライマが溶接時に蒸気化してガスを発生してピットとなるため、被覆アーク溶接棒でプライマ塗装鋼板を溶接する場合、被覆剤中に金属炭酸塩を多く含有させてアークの吹付けを強くして溶融プール内を攪拌させることにより、溶融プール内に残留するガスを強制的に放出させて耐ピット性を改善する方法が知られている。しかし、グラビティ溶接は、１パス溶接での溶着量を確保する目的から被覆アーク溶接棒の心線径及び被覆外径が大きく、アークの集中性が悪くなってアークの吹付けが弱くなるため、特にピットが発生しやすいウォッシュプライマ塗装鋼板をすみ肉溶接した場合、溶融プール内を十分に攪拌できず、良好な耐ピット性が得られないことを突き止めた。 In fillet welding of primer-coated steel sheets, the primer coated on the steel sheet surface is vaporized during welding, generating gas and forming pits. Therefore, when welding a primer-coated steel sheet with a coated arc welding rod, a metal carbonate is contained in the coating. There is known a method of improving the pit resistance by forcibly releasing the gas remaining in the molten pool by containing a large amount of salt and strengthening the arc spray to stir the molten pool. However, gravity welding has a large core wire diameter and a coating outer diameter of the coated arc welding rod for the purpose of securing the amount of welding in one-pass welding, and the arc concentration becomes worse and the arc spray becomes weaker. In particular, when fillet welding was performed on a wash primer-coated steel sheet that is prone to pits, it was found that the molten pool could not be sufficiently stirred and good pit resistance could not be obtained.
そこで、グラビティ溶接でのアークの吹付けを向上させるべく低水素系すみ肉溶接用被覆アーク溶接棒の被覆剤成分について種々試作して検討した結果、被覆剤中にＮａＦ及び金属炭酸塩を適量添加することにより、強いアークの吹き付けを確保し、ウォッシュプライマ塗装鋼板のすみ肉溶接でも良好な耐ピット性が得られることを見出した。 Therefore, as a result of various trial manufactures and examinations of the coating components of the coated arc welding rod for low hydrogen fillet welding in order to improve the arc spraying in gravity welding, appropriate amounts of NaF and metal carbonate were added to the coating. By doing so, it was found that strong arc spraying was ensured and good pit resistance was obtained even in fillet welding of wash primer-coated steel sheets.
次に、その他溶接作業性を改善するべく検討した結果、アークの安定化及びスパッタ発生量の低減に関しては、被覆剤中にＮａ酸化物及びＫ酸化物、Ｔｉ酸化物、Ａｌ酸化物、及び鉄粉を適量添加することでアークを安定化させてスパッタ発生量を低減できるとともに、Ｎａ酸化物及びＫ酸化物の含有量の合計及び金属弗化物の合計量をさらに規定することで、ヒューム発生量を低減できることを見出した。 Next, as a result of studies to improve other welding workability, Na oxide and K oxide, Ti oxide, Al oxide, and iron are included in the coating agent with regard to arc stabilization and reduction in spatter generation. By adding an appropriate amount of powder, the arc can be stabilized and the amount of spatter generated can be reduced, and the total amount of Na oxide and K oxide and the total amount of metal fluoride can be further specified to generate fume generation. It was found that can be reduced.
また、スラグ被包性に関しては、被覆剤中にＴｉ酸化物、Ｓｉ酸化物を適量添加することで溶融プールを完全に被包できるスラグ量を生成するとともに、金属弗化物及びＦｅ酸化物を適量添加することで溶融スラグの流動性を適正にしてビード表面にスラグを均一に被包させてスラグ被包性を改善してビード形状を改善できることを見出した。 In addition, regarding slag encapsulating properties, adding appropriate amounts of Ti oxide and Si oxide to the coating agent produces slag amount that can completely encapsulate the molten pool, and appropriate amounts of metal fluoride and Fe oxide. It was found that the bead shape can be improved by adding the slag to the bead surface uniformly by improving the flowability of the molten slag and improving the slag encapsulation.
さらに、Ｓｉ酸化物、ＭｇＯを適量添加することで、スラグ剥離性を改善するとともに優れたビード形状が得られることを見出した。 Furthermore, it has been found that by adding appropriate amounts of Si oxide and MgO, the slag peelability can be improved and an excellent bead shape can be obtained.
また、溶接金属の機械的性質に関しては、被覆剤中に金属炭酸塩を適量添加することで溶接時にＣＯ2ガスを発生させて溶融プールをシールドして溶接金属の靭性を向上すること、脱酸効果のあるＳｉ及びＭｎを適量添加するとともに、Ｎｉを適量添加することにより溶接金属の強度及び靭性を向上することができることを見出した。 In addition, regarding the mechanical properties of the weld metal, it is possible to improve the toughness of the weld metal by generating a CO 2 gas during welding by shielding the molten pool by adding an appropriate amount of metal carbonate in the coating, It has been found that the strength and toughness of the weld metal can be improved by adding appropriate amounts of effective Si and Mn and adding appropriate amounts of Ni.
生産性に関しては、被覆アーク溶接棒は原材料に水ガラスを添加して混練した塗布剤を心線の周囲に塗布した後に乾燥させて製品とするが、グラビティ溶接に用いる低水素系すみ肉溶接用被覆アーク溶接棒は通常のものに比べて心線が太径であるため、塗布する被覆剤の肉厚が大きくなり、乾燥時に被覆割れなどの欠陥が発生しやすい。そこで本発明では、被覆剤中の水ガラスのＮａ酸化物及びＫ酸化物の添加量を限定することにより、乾燥時の被覆割れなどの欠陥を防止して生産性を改善できることを見出した。 In terms of productivity, coated arc welding rods are made by adding water glass to the raw material and kneading the coating agent around the core wire and then drying to make the product, but for low hydrogen fillet welding used in gravity welding Since the coated arc welding rod has a thicker core wire than a normal one, the thickness of the coating material to be applied increases, and defects such as coating cracks are likely to occur during drying. Therefore, in the present invention, it has been found that by limiting the amount of Na oxide and K oxide added to the water glass in the coating agent, defects such as coating cracks during drying can be prevented and productivity can be improved.
以下、本発明の低水素系すみ肉溶接用被覆アーク溶接棒の被覆剤の成分組成及び成分組成の限定理由について詳細に説明する。なお、各成分組成の含有量は、被覆剤全質量に対する質量％で表すこととし、その質量％を表すときには単に％と記載することとする。 Hereinafter, the component composition of the coating agent of the coated arc welding rod for low hydrogen fillet welding of the present invention and the reason for limitation of the component composition will be described in detail. The content of each component composition is expressed as mass% with respect to the total mass of the coating agent, and when expressing the mass%, it is simply described as%.
［金属炭酸塩の１種または２種以上の合計：５〜１５％］
金属炭酸塩は、ＭｇＣＯ3、ＣａＣＯ3、ＢａＣＯ3、ＭｎＣＯ3などから添加され、アーク中で分解してＣＯ2ガスを発生して溶融プール及び溶融スラグを大気から保護して溶接金属の靭性を確保するとともに、アークの吹き付けを強くしてピットの発生を防止する効果がある。金属炭酸塩の１種または２種以上の合計が５％未満であると、シールド効果が不足して溶接金属の靭性が低下するとともに、アークの吹付けが弱くなってピットが発生しやすくなる。一方、金属炭酸塩の１種または２種以上の合計が１５％を超えると、アークの吹付けが強くなりすぎてスパッタ発生量が多くなる。したがって、金属炭酸塩の１種または２種以上の合計は５〜１５％とする。
[Total of one or more metal carbonates: 5 to 15%]
Metal carbonate is added from MgCO 3 , CaCO 3 , BaCO 3 , MnCO 3, etc., and decomposes in the arc to generate CO 2 gas to protect the molten pool and molten slag from the atmosphere, thereby improving the toughness of the weld metal. In addition to ensuring, it has the effect of preventing the generation of pits by strengthening the arc spray. If the total of one or more of the metal carbonates is less than 5%, the shielding effect is insufficient and the toughness of the weld metal is lowered, and arc spraying is weakened and pits are likely to occur. On the other hand, if the total of one or more of the metal carbonates exceeds 15%, the arc spray becomes too strong and the amount of spatter generated increases. Therefore, the total of one or more metal carbonates is 5 to 15%.
［金属弗化物の２種以上の合計：３〜８％］
金属弗化物は、ＣａＦ2、ＭｇＦ2、ＢａＦ2、ＡｌＦ3、Ｎａ3ＡｌＦ6、ＮａＦ、ＬｉＦなどから２種以上にわたり添加され、溶融スラグの流動性を調整してビード形状を良好にする効果がある。金属弗化物の２種以上の合計が３％未満では、溶融スラグの流動性が悪くビード形状が凸状となる。一方、金属弗化物の２種以上の合計が８％を超えると、溶融スラグの流動性が著しく高くなりビードの下脚側が膨らんだ形状となり、またヒューム発生量も多くなる。したがって、金属弗化物の２種以上の合計は３〜８％とする。
[Total of two or more metal fluorides: 3 to 8%]
Metal fluoride is added over two or more of CaF 2 , MgF 2 , BaF 2 , AlF 3 , Na 3 AlF 6 , NaF, LiF, etc., and the effect of adjusting the fluidity of the molten slag to improve the bead shape There is. When the total of two or more kinds of metal fluorides is less than 3%, the fluidity of the molten slag is poor and the bead shape becomes convex. On the other hand, when the total of two or more kinds of metal fluorides exceeds 8%, the fluidity of the molten slag becomes extremely high, and the lower leg side of the bead swells, and the amount of fumes generated increases. Therefore, the total of two or more kinds of metal fluorides is 3 to 8%.
［金属弗化物中のＮａＦ：０．２〜１．５％］
金属弗化物中のＮａＦは、アークの吹付けを強くする効果が高く、ウォッシュプライマ塗装鋼板のすみ肉溶接であってもピットの発生を防ぐことができる。金属弗化物中のＮａＦが０．２％未満であると、十分なアークの吹付けが得られず、ウォッシュプライマ塗装鋼板のすみ肉溶接ではピットの発生を防止することができない。一方、金属弗化物中のＮａＦが１．５％を超えると、アークの吹付けが強くなりすぎてスパッタ発生量が多くなる。したがって、金属弗化物中のＮａＦは０．２〜１．５％とする。
[NaF in metal fluoride: 0.2 to 1.5%]
NaF in the metal fluoride has a high effect of strengthening the spray of the arc, and can prevent the occurrence of pits even in the fillet welding of the wash primer coated steel sheet. When NaF in the metal fluoride is less than 0.2%, sufficient arc spraying cannot be obtained, and pit formation cannot be prevented by fillet welding of a wash primer-coated steel sheet. On the other hand, if NaF in the metal fluoride exceeds 1.5%, the arc spray becomes too strong and the amount of spatter generated increases. Therefore, NaF in the metal fluoride is 0.2 to 1.5%.
［Ｔｉ酸化物のＴｉＯ2換算値の合計：５〜１５％］
Ｔｉ酸化物は、ルチール、酸化チタン、チタン酸ソーダ、チタンスラグ、イルミナイトなどから添加され、アーク安定剤及びスラグ生成剤として作用し、アークを安定にしてスパッタ発生量を少なくし、スラグ被包性及びビード形状を良好にする効果がある。Ｔｉ酸化物のＴｉＯ2換算値の合計が５％未満では、アークが不安定となってスパッタ発生量が多くなる。またＴｉ酸化物のＴｉＯ2換算値の合計が５％未満では、スラグ量が不足し、スラグ被包性が悪くなってビード形状が不良になる。一方、Ｔｉ酸化物のＴｉＯ2換算値の合計が１５％を超えると、スラグ量が過多となってスラグの被包状態にムラができてビード形状が不良になる。したがって、Ｔｉ酸化物のＴｉＯ2換算値の合計は５〜１５％とする。
[Total of TiO 2 converted values of Ti oxide: 5 to 15%]
Ti oxide is added from rutile, titanium oxide, sodium titanate, titanium slag, illuminite, etc., and acts as an arc stabilizer and slag generator, stabilizes the arc, reduces spatter generation, and slag encapsulation. There is an effect of improving the properties and bead shape. If the total TiO 2 conversion value of Ti oxide is less than 5%, the arc becomes unstable and the amount of spatter generated increases. On the other hand, if the total TiO 2 conversion value of the Ti oxide is less than 5%, the amount of slag is insufficient, the slag encapsulation is deteriorated, and the bead shape becomes poor. On the other hand, if the total TiO 2 converted value of the Ti oxide exceeds 15%, the amount of slag becomes excessive, the slag is encapsulated, and the bead shape becomes poor. Therefore, the total of the TiO 2 converted values of the Ti oxide is 5 to 15%.
［Ｓｉ酸化物のＳｉＯ2換算値の合計：１０〜２０％］
Ｓｉ酸化物は、珪砂、長石、水ガラスなどから添加され、スラグ剥離性の改善とビード形状を良好にする効果がある。Ｓｉ酸化物のＳｉＯ2換算値の合計が１０％未満では、スラグ剥離性及びビード形状が不良になる。一方、Ｓｉ酸化物のＳｉＯ2換算値の合計が２０％を超えると、スラグの粘性が高くなってビード表面をスラグが均一に被包できずビード形状が不良になる。また、溶融プール中のガスが放出されにくくなり、ピットが発生しやすくなる。したがって、Ｓｉ酸化物のＳｉＯ2換算値の合計は１０〜２０％とする。
[Total of SiO 2 conversion value of Si oxide: 10 to 20%]
Si oxide is added from silica sand, feldspar, water glass, etc., and has the effect of improving the slag peelability and improving the bead shape. When the total of SiO 2 conversion values of the Si oxide is less than 10%, the slag peelability and the bead shape are poor. On the other hand, when the total of SiO 2 conversion values of Si oxides exceeds 20%, the slag becomes so viscous that the slag cannot be uniformly encapsulated on the bead surface and the bead shape becomes poor. Moreover, it becomes difficult to release the gas in the molten pool, and pits are likely to be generated. Therefore, the total of SiO 2 conversion values of Si oxide is 10 to 20%.
［Ａｌ酸化物のＡｌ2Ｏ3換算値の合計：０．５〜３．０％］
Ａｌ酸化物は、アルミナ、長石、マイカなどから添加され、溶融スラグの粘度を調整するとともに、スラグ剥離性を改善する効果がある。Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が０．５％未満では、スラグ剥離性が悪く、溶融スラグの粘度が低くなってビード形状が不良になる。一方、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が３．０％を超えると、スラグがガラス状となりスラグ剥離性が悪く、溶融スラグの粘度が高くなってビード形状が不良になる。したがって、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計は０．５〜３．０％とする。
[Total Al 2 O 3 conversion value of Al oxide: 0.5 to 3.0%]
Al oxide is added from alumina, feldspar, mica, etc., and has the effect of adjusting the viscosity of the molten slag and improving the slag peelability. When the total of Al 2 O 3 converted values of Al oxides is less than 0.5%, the slag removability is poor, the viscosity of the molten slag is lowered, and the bead shape becomes poor. On the other hand, if the total Al 2 O 3 conversion value of the Al oxide exceeds 3.0%, the slag becomes glassy and the slag peelability is poor, the viscosity of the molten slag becomes high, and the bead shape becomes poor. Therefore, the total of Al 2 O 3 conversion values of Al oxide is 0.5 to 3.0%.
［Ｆｅ酸化物のＦｅＯ換算値の合計：０．５〜１．５％］
Ｆｅ酸化物は、ＦｅＯ、Ｆｅ2Ｏ3などから添加され、溶融スラグの流動性を調整してスラグ被包性を良好にしてビード形状を改善する効果がある。Ｆｅ酸化物のＦｅＯ換算値の合計が０．５％未満では、溶融スラグの流動性が悪くなってスラグ被包性が悪くビード形状が不良になる。一方、Ｆｅ酸化物のＦｅＯ換算値の合計が１．５％を超えると、スラグ量が過多となりスラグの被包状態にムラができてビード形状が不良になる。したがって、Ｆｅ酸化物のＦｅＯ換算値の合計は０．５〜１．５％とする。
[Total FeO equivalent value of Fe oxide: 0.5 to 1.5%]
Fe oxide is added from FeO, Fe 2 O 3 and the like, and has an effect of improving the bead shape by adjusting the fluidity of the molten slag to improve the slag encapsulation. When the total FeO equivalent value of the Fe oxide is less than 0.5%, the fluidity of the molten slag is deteriorated and the slag encapsulation is deteriorated and the bead shape is deteriorated. On the other hand, if the total FeO equivalent value of the Fe oxide exceeds 1.5%, the amount of slag becomes excessive, the slag is encapsulated, and the bead shape becomes poor. Therefore, the total FeO equivalent value of the Fe oxide is 0.5 to 1.5%.
［ＭｇＯ：２〜６％］
ＭｇＯは、マグネシアクリンカーなどから添加され、スラグ剥離性及びビード形状を良好にする効果がある。ＭｇＯが２％未満では、その効果が得られず、スラグ剥離性及びビード形状が不良になる。一方、ＭｇＯが６％を超えると、スラグ量が過多となってスラグの被包状態にムラができてビード形状が不良になる。したがって、ＭｇＯは２〜６％とする。
[MgO: 2 to 6%]
MgO is added from magnesia clinker or the like, and has an effect of improving the slag peelability and bead shape. If MgO is less than 2%, the effect cannot be obtained, and the slag removability and the bead shape become poor. On the other hand, if MgO exceeds 6%, the amount of slag becomes excessive, and the slag is encapsulated in a non-uniform state, resulting in a poor bead shape. Therefore, MgO is 2 to 6%.
［Ｓｉ：０．５〜２．０％］
Ｓｉは、金属Ｓｉ、Ｆｅ−Ｓｉ、Ｆｅ−Ｓｉ−Ｍｎなどの合金粉などから添加され、脱酸剤として作用し、溶接金属の靭性を向上させるとともに、ピットの発生を防止する効果がある。Ｓｉが０．５％未満では、脱酸不足となって溶接金属の靭性が低下するとともに、ピットが発生しやすくなる。一方、Ｓｉが２．０％を超えると、溶接金属の粒界に低融点酸化物が析出して靭性が低下する。したがって、Ｓｉは０．５〜２．０％とする。
[Si: 0.5 to 2.0%]
Si is added from an alloy powder such as metal Si, Fe-Si, Fe-Si-Mn, and the like, and acts as a deoxidizer to improve the toughness of the weld metal and to prevent the occurrence of pits. If Si is less than 0.5%, deoxidation is insufficient, and the toughness of the weld metal is lowered, and pits are easily generated. On the other hand, when Si exceeds 2.0%, a low melting point oxide precipitates at the grain boundary of the weld metal and the toughness decreases. Therefore, Si is 0.5 to 2.0%.
［Ｍｎ：５〜８％］
Ｍｎは、金属Ｍｎ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎなどの合金粉などから添加され、脱酸剤として作用し、溶接金属の強度及び靭性を向上させるとともに、ピットの発生を防止する効果がある。Ｍｎが５％未満では、脱酸不足となって溶接金属の強度及び靭性が低下するとともに、ピットが発生しやすくなる。一方、Ｍｎが８％を超えると、溶接金属の強度が高くなって靭性が低下する。したがって、Ｍｎは５〜８％とする。
[Mn: 5 to 8%]
Mn is added from metal powder such as metal Mn, Fe-Mn, Fe-Si-Mn, etc., and acts as a deoxidizer to improve the strength and toughness of the weld metal and to prevent the occurrence of pits. is there. If Mn is less than 5%, deoxidation is insufficient, and the strength and toughness of the weld metal are lowered, and pits are easily generated. On the other hand, if Mn exceeds 8%, the strength of the weld metal increases and the toughness decreases. Therefore, Mn is 5 to 8%.
［Ｎｉ：０．３〜２．０％］
Ｎｉは、金属Ｎｉ、Ｆｅ−Ｎｉなどの合金粉などから添加され、溶接金属の強度及び靭性を向上させる効果がある。Ｎｉが０．３％未満では、必要な溶接金属の強度及び靭性が得られない。一方、Ｎｉが２．０％を超えると、溶接金属の強度が高くなって靭性が低下する。したがって、Ｎｉは０．３〜２．０％とする。
[Ni: 0.3-2.0%]
Ni is added from an alloy powder such as metal Ni or Fe—Ni, and has an effect of improving the strength and toughness of the weld metal. If Ni is less than 0.3%, the required strength and toughness of the weld metal cannot be obtained. On the other hand, if Ni exceeds 2.0%, the strength of the weld metal increases and the toughness decreases. Therefore, Ni is 0.3 to 2.0%.
［鉄粉：２５〜４５％］
鉄粉は、アーク状態をソフトにする効果を有する。鉄粉が２５％未満では、アークが不安定になってスパッタ発生量が多くなる。一方、鉄粉が４５％を超えると、アークの吹付けが弱くなり、ピットが発生しやすくなる。したがって、鉄粉は２５〜４５％とする。
[Iron powder: 25-45%]
Iron powder has the effect of softening the arc state. If the iron powder is less than 25%, the arc becomes unstable and the amount of spatter generated increases. On the other hand, if the iron powder exceeds 45%, arc spraying becomes weak and pits are likely to occur. Therefore, iron powder shall be 25 to 45%.
［Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計：１．５〜５．５％］
Ｎａ酸化物及びＫ酸化物は、水ガラス中の珪酸ソーダ及び珪酸カリウム、カリ長石、カリガラス及びソーダ長石などから添加され、特にアークを安定にしてスパッタ発生量を少なくする効果がある。またＮａ酸化物及びＫ酸化物は、被覆アーク溶接棒を生産する際、塗布剤の粘度を調整して乾燥時の被覆割れを防止して生産性を向上する効果もある。Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計が１．５％未満では、生産時に被覆割れが生じやすくなる。また、アークが不安定となってスパッタ発生量が多くなる。一方、Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計が５．５％を超えると、アークの吹付けが強くなりすぎてスパッタ発生量が多くなるとともに、ヒューム発生量も多くなる。したがって、Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計は１．５〜５．５％とする。
[Total of Na oxide and K oxide Na 2 O equivalent and K 2 O equivalent: 1.5 to 5.5%]
Na oxide and K oxide are added from sodium silicate and potassium silicate, potash feldspar, potash glass and soda feldspar in water glass, and are particularly effective in stabilizing the arc and reducing the amount of spatter generated. Na oxide and K oxide also have an effect of improving productivity by adjusting the viscosity of the coating agent to prevent coating cracks during drying when producing a coated arc welding rod. If the total of Na 2 O converted values and K 2 O converted values of Na oxide and K oxide is less than 1.5%, coating cracks are likely to occur during production. Also, the arc becomes unstable and the amount of spatter generated increases. On the other hand, when the total of Na 2 O converted value and K 2 O converted value of Na oxide and K oxide exceeds 5.5%, the spraying of the arc becomes too strong and the amount of spatter generated increases. The amount generated is also increased. Therefore, the total of Na 2 O equivalent value and K 2 O equivalent value of Na oxide and K oxide is 1.5 to 5.5%.
なお、本発明の低水素系すみ肉溶接用被覆アーク溶接棒の被覆剤中の残部は、上記の成分のほか、生産性の観点からアルギン酸ソーダ、セルロースなどの塗布剤が０．１〜３％、Ｆｅ−Ｓｉ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎなどの鉄合金からのＦｅ分及び不可避不純物である。また、使用する鋼心線は、ＪＩＳ Ｇ ３５２３ ＳＷＹ１１を用いることが好ましい。さらに、鋼心線への被覆剤の被覆率は４０〜５５％であることが好ましい。 In addition to the above components, the remainder in the coating of the low hydrogen fillet welding coated arc welding rod of the present invention is 0.1 to 3% of coating agents such as sodium alginate and cellulose from the viewpoint of productivity. , Fe-Si, Fe-Mn, Fe-Si-Mn and other iron alloys and inevitable impurities. Moreover, it is preferable to use JIS G 3523 SWY11 for the steel core wire to be used. Furthermore, it is preferable that the coating rate of the coating agent to the steel core wire is 40 to 55%.
以下、本発明の効果を実施例により更に詳細に説明する。 Hereinafter, the effect of the present invention will be described in more detail with reference to examples.
表１に示す各種被覆剤を直径８．０ｍｍ、長さ７００ｍｍのＪＩＳ Ｇ ３５２３ ＳＷＹ１１の鋼心線に被覆率４７〜５３％で塗布した後に４００℃で焼成して溶接棒を各種試作し、生産性、溶接作業性及び機械的性質について調査した。 Various coating materials shown in Table 1 were applied to a steel core wire of JIS G 3523 SWY11 having a diameter of 8.0 mm and a length of 700 mm at a covering ratio of 47 to 53%, and then fired at 400 ° C. to produce various types of welding rods. , Welding workability and mechanical properties were investigated.
生産性の評価は、各種試作溶接棒を５００ｋｇ生産し、被覆割れなどの欠陥の有無を目視で確認し、被覆外観が良好で欠陥がないものを良好とした。 For the evaluation of productivity, 500 kg of various types of test welding rods were produced, the presence or absence of defects such as coating cracks was visually confirmed, and those with good coating appearance and no defects were evaluated as good.
溶接作業性の評価は、各種試作溶接棒を用い、ＪＩＳ Ｇ ３１０６ ＳＭ４９０Ａ、板厚１２ｍｍ×幅１００ｍｍ×長さ１０００ｍｍの鋼板表面に膜厚２５〜３５μｍのウォッシュプライマを塗装したプライマ塗装鋼板をＴ字型に組んだＴ字試験体にて、交流溶接機を用いてグラビティ溶接で溶接電流３５０Ａで水平すみ肉溶接を行い、アーク状態の良否、スパッタ発生量及びヒューム発生量、スラグ被包性、スラグ剥離性及びビード形状の良否を目視で調査した。なお、耐ピット性は、溶接ビード全長にピットが全く発生しなかったものを良好とした。 Welding workability was evaluated by using various prototype welding rods, JIS G 3106 SM490A, a primer-coated steel plate with a wash primer with a film thickness of 25-35 μm coated on a steel plate surface of 12 mm thick x 100 mm wide x 1000 mm long. Using a T-shaped test body assembled in a mold, horizontal fillet welding is performed with a welding current of 350 A by gravity welding using an AC welding machine, the quality of the arc state, spatter generation and fume generation, slag encapsulation, slag The peelability and bead shape were visually inspected. Note that the pit resistance was good when no pit was generated in the entire length of the weld bead.
機械的性質の評価は、ＪＩＳ Ｇ ３１０６ ＳＭ４９０Ａの板厚２０ｍｍの鋼板を用い、ＪＩＳ Ｚ ３１１１に準じて交流溶接機で溶着金属試験を行い、引張試験片（Ａ１号）と衝撃試験片（Ｖノッチ試験片）を採取して引張試験及び衝撃試験を行った。引張試験は引張強さが４９０〜５９０ＭＰａ、衝撃試験は試験温度−２０℃で各々繰り返し３回の吸収エネルギーの平均値が４７Ｊ以上を良好とした。これらの調査結果を表２にまとめて示す。 The mechanical properties were evaluated by using a JIS G 3106 SM490A steel plate with a thickness of 20 mm and conducting a weld metal test with an AC welding machine in accordance with JIS Z 3111. Specimens) were collected and subjected to a tensile test and an impact test. In the tensile test, the tensile strength was 490 to 590 MPa, and in the impact test, the average value of the absorbed energy three times at a test temperature of −20 ° C. was 47 J or more. These survey results are summarized in Table 2.
表１及び表２中Ｎｏ．１〜Ｎｏ．１０が本発明例、Ｎｏ．１１〜Ｎｏ．２３は比較例である。本発明であるＮｏ．１〜Ｎｏ．１０は、被覆剤中の金属炭酸塩の合計、金属弗化物の２種以上の合計、金属弗化物中のＮａＦ、Ｔｉ酸化物のＴｉＯ2換算値の合計、Ｓｉ酸化物のＳｉＯ2換算値の合計、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計、Ｆｅ酸化物のＦｅＯ換算値の合計、ＭｇＯ、Ｓｉ、Ｍｎ、Ｎｉ、鉄粉、Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計が適正であるので、被覆アーク溶接棒の生産時に被覆割れなどの欠陥がなく生産性が良好であった。また、ウォッシュプライマ塗装鋼板での水平すみ肉溶接でのアーク状態が良好で、スパッタ発生量、ヒューム発生量が少なく、スラグ被包性、スラグ剥離性及びビード形状が良好で、ピットは発生しなかった。さらに、溶着金属の引張強さ及び吸収エネルギーも適正であり、極めて満足な結果であった。 No. in Table 1 and Table 2. 1-No. 10 is an example of the present invention, No. 10; 11-No. 23 is a comparative example. No. which is the present invention. 1-No. 10, the total of the metal carbonate in the coating, the total of two or more metal fluorides, in metal fluorides NaF, the sum of TiO 2 converted value of Ti oxides, the SiO 2 converted value of Si oxide total, sum of terms of Al 2 O 3 value of Al oxide, the sum of the FeO converted value of Fe oxides, MgO, Si, Mn, Ni, iron powder, Na 2 O conversion value of Na oxide and K oxides and Since the sum of K 2 O conversion values is appropriate, there was no defect such as a coating crack during the production of the coated arc welding rod, and the productivity was good. In addition, the arc state in horizontal fillet welding with wash primer coated steel plate is good, spatter generation and fume generation are small, slag encapsulation, slag peelability and bead shape are good, and no pits are generated. It was. Furthermore, the tensile strength and absorbed energy of the weld metal were also appropriate, which was a very satisfactory result.
比較例中のＮｏ．１１は、金属炭酸塩の合計が少ないので、アークの吹付けが弱く、ピットが発生した。また、溶接金属の吸収エネルギーが低かった。さらに、Ｔｉ酸化物のＴｉＯ2換算値の合計が多いので、スラグ量が過多となってスラグの被包性及びビード形状が不良であった。 No. in the comparative example. No. 11 had a small total of metal carbonates, so the arc spray was weak and pits were generated. Moreover, the absorbed energy of the weld metal was low. Furthermore, since the total of TiO 2 converted values of the Ti oxide is large, the amount of slag was excessive, and the slag encapsulation and bead shape were poor.
Ｎｏ．１２は、金属炭酸塩の合計が多いので、アークの吹き付けが強すぎてスパッタ発生量が多かった。また、Ｎｉが少ないので、溶着金属の引張強さ及び吸収エネルギーが低かった。 No. In No. 12, since the total amount of metal carbonate was large, the spraying of the arc was too strong and the amount of spatter generated was large. Moreover, since there was little Ni, the tensile strength and absorbed energy of the deposit metal were low.
Ｎｏ．１３は、金属弗化物の２種以上の合計が少ないので、ビード形状が凸状となった。また、Ｎｉが多いので、溶着金属の引張強さが高く、吸収エネルギーが低かった。 No. No. 13 had a total of two or more kinds of metal fluorides, so the bead shape became convex. Moreover, since there was much Ni, the tensile strength of the weld metal was high and the absorbed energy was low.
Ｎｏ．１４は、金属弗化物の２種以上の合計が多いので、ビード形状が不良でヒューム発生量も多かった。また、Ｓｉが多いので、溶着金属の吸収エネルギーが低かった。 No. No. 14 had a total of two or more kinds of metal fluorides, so the bead shape was poor and the amount of fume generation was large. Moreover, since there is much Si, the absorbed energy of the weld metal was low.
Ｎｏ．１５は、金属弗化物中のＮａＦが少ないので、アークの吹付けが弱くピットが発生した。また、Ｓｉ酸化物のＳｉＯ2換算値の合計が少ないので、スラグ剥離性が悪くビード形状も不良であった。 No. No. 15 had little NaF in the metal fluoride, so the arc was weakly blown and pits were generated. Further, since the total of SiO 2 conversion values of the Si oxide was small, the slag peelability was poor and the bead shape was also poor.
Ｎｏ．１６は、金属弗化物中のＮａＦが多いので、アークの吹付けが強すぎてスパッタ発生量が多かった。また、Ｓｉ酸化物のＳｉＯ2換算値の合計が多いので、スラグ被包性が悪くビード形状が不良でピットも発生した。 No. No. 16 had a large amount of NaF in the metal fluoride, so the arc spray was too strong and the amount of spatter generated was large. In addition, since the total of SiO 2 converted values of Si oxide was large, the slag encapsulation was poor and the bead shape was poor and pits were generated.
Ｎｏ．１７は、Ｔｉ酸化物のＴｉＯ2換算値の合計が少ないので、アークが不安定でスパッタ発生量が多かった。また、スラグ被包性が悪くビード形状が不良であった。さらに、Ｓｉが少ないので、ピットが発生し、溶着金属の吸収エネルギーが低かった。 No. No. 17 had a small total of TiO 2 conversion values of Ti oxides, so the arc was unstable and the amount of spatter generated was large. Moreover, the slag encapsulation was poor and the bead shape was poor. Further, since there was little Si, pits were generated and the absorbed energy of the deposited metal was low.
Ｎｏ．１８は、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が少ないので、スラグ剥離性が悪くビード形状も不良であった。また、Ｍｎが少ないので、ピットが発生し、溶着金属の引張強さ及び吸収エネルギーが低かった。 No. No. 18 had a poor total slag removability and a poor bead shape because the total of Al 2 O 3 converted values of Al oxides was small. Moreover, since Mn was small, pits were generated, and the tensile strength and absorbed energy of the deposited metal were low.
Ｎｏ．１９は、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が多いので、スラグ剥離性が悪くビード形状も不良であった。また、Ｍｎが多いので、溶着金属の引張強さが高く、吸収エネルギーが低かった。 No. In No. 19, since the total of Al 2 O 3 converted values of Al oxide was large, the slag peelability was poor and the bead shape was also poor. Moreover, since there was much Mn, the tensile strength of the weld metal was high and the absorbed energy was low.
Ｎｏ．２０は、Ｆｅ酸化物のＦｅＯ換算値の合計が少ないので、スラグ被包性が悪くビード形状が不良であった。また、鉄粉が少ないので、アークが不安定でスパッタ発生量が多かった。 No. No. 20 had a poor total bead shape due to poor slag encapsulation because the total FeO equivalent value of Fe oxide was small. Moreover, since there was little iron powder, the arc was unstable and the amount of spatter was large.
Ｎｏ．２１は、Ｆｅ酸化物のＦｅＯ換算値が多いので、スラグ被包性が悪くビード形状が不良であった。また、鉄粉が多いので、アークの吹付けが弱く、ピットが発生した。 No. Since No. 21 had many Fe oxide conversion values of Fe oxide, the slag encapsulation was poor and the bead shape was poor. In addition, since there was a lot of iron powder, arc spray was weak and pits were generated.
Ｎｏ．２２は、ＭｇＯが少ないので、スラグ剥離性が悪くビード形状も不良であった。また、Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計が少ないので、生産時に被覆表面に被覆割れが発生した。また、アークが不安定でスパッタ発生量が多かった。 No. Since No. 22 had little MgO, slag peelability was bad and the bead shape was also bad. Further, since the sum is small in terms of Na 2 O values and K 2 O conversion value of Na oxide and K oxides, coated cracking occurs in the coated surface during production. Also, the arc was unstable and the amount of spatter was large.
Ｎｏ．２３は、ＭｇＯが多いので、スラグ被包性が悪くビード形状が不良であった。また、Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計が多いので、アークの吹付けが強くなりすぎてスパッタ発生量が多く、ヒューム発生量も多かった。 No. Since No. 23 had a lot of MgO, the slag encapsulation was poor and the bead shape was poor. Moreover, since the total of Na 2 O conversion value and K 2 O conversion value of Na oxide and K oxide was large, the spraying of the arc became too strong and the amount of spatter generation was large and the amount of fume generation was also large.
Claims (1)
前記被覆剤は、当該被覆剤全質量に対する質量％で、
金属炭酸塩の１種または２種以上の合計：５〜１５％、
金属弗化物の２種以上の合計：３〜８％、
前記金属弗化物中のＮａＦ：０．２〜１．５％、
Ｔｉ酸化物のＴｉＯ2換算値の合計：５〜１５％、
Ｓｉ酸化物のＳｉＯ2換算値の合計：１０〜２０％、
Ａｌ酸化物のＡｌ2Ｏ3換算値の合計：０．５〜３．０％、
Ｆｅ酸化物のＦｅＯ換算値の合計：０．５〜１．５％、
ＭｇＯ：２〜６％、
Ｓｉ：０．５〜２．０％、
Ｍｎ：５〜８％、
Ｎｉ：０．３〜２．０％、
鉄粉：２５〜４５％、
Ｎａ酸化物及びＫ酸化物のＮａ2Ｏ換算値及びＫ2Ｏ換算値の合計：１．５〜５．５％を含有し、
残部は、塗布剤、鉄合金からのＦｅ分及び不可避不純物からなることを特徴とする低水素系すみ肉溶接用被覆アーク溶接棒。 In the coated arc welding rod for low hydrogen fillet welding where the coating is applied to the steel core wire,
The coating agent is in mass% with respect to the total mass of the coating agent,
Total of one or more metal carbonates: 5 to 15%,
Total of two or more metal fluorides: 3-8%,
NaF in the metal fluoride: 0.2 to 1.5%,
Total of TiO 2 conversion value of Ti oxide: 5 to 15%,
Total SiO 2 converted value of Si oxide: 10-20%,
Total terms of Al 2 O 3 value of Al oxide 0.5 to 3.0%
Total of Fe oxide equivalent value of Fe oxide: 0.5 to 1.5%,
MgO: 2 to 6%,
Si: 0.5 to 2.0%,
Mn: 5-8%
Ni: 0.3 to 2.0%,
Iron powder: 25-45%,
Total Na oxide and terms of Na 2 O values and K 2 O conversion value of K oxide: containing 1.5 to 5.5%,
The balance is a coated arc welding rod for low hydrogen fillet welding characterized by comprising a coating agent, an Fe component from an iron alloy, and inevitable impurities.
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| JP2019181524A (en) * | 2018-04-11 | 2019-10-24 | 日鉄溶接工業株式会社 | Covered electrode for low hydrogen type fillet welding |
| JP7346328B2 (en) | 2020-02-28 | 2023-09-19 | 日鉄溶接工業株式会社 | Low hydrogen coated arc welding rod for horizontal fillet welding |
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| JP7039374B2 (en) | 2018-04-11 | 2022-03-22 | 日鉄溶接工業株式会社 | Shielded metal arc welding rod for low hydrogen fillet welding |
| JP7346328B2 (en) | 2020-02-28 | 2023-09-19 | 日鉄溶接工業株式会社 | Low hydrogen coated arc welding rod for horizontal fillet welding |
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