WO2016013542A1 - エレクトロガスアーク溶接方法及びエレクトロガスアーク溶接装置 - Google Patents
エレクトロガスアーク溶接方法及びエレクトロガスアーク溶接装置 Download PDFInfo
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- WO2016013542A1 WO2016013542A1 PCT/JP2015/070680 JP2015070680W WO2016013542A1 WO 2016013542 A1 WO2016013542 A1 WO 2016013542A1 JP 2015070680 W JP2015070680 W JP 2015070680W WO 2016013542 A1 WO2016013542 A1 WO 2016013542A1
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Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K37/00—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups
- B23K37/02—Carriages for supporting the welding or cutting element
- B23K37/0276—Carriages for supporting the welding or cutting element for working on or in tubes
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K37/00—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups
- B23K37/02—Carriages for supporting the welding or cutting element
- B23K37/0282—Carriages forming part of a welding unit
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K37/00—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups
- B23K37/06—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups for positioning the molten material, e.g. confining it to a desired area
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/02—Seam welding; Backing means; Inserts
- B23K9/035—Seam welding; Backing means; Inserts with backing means disposed under the seam
- B23K9/0352—Seam welding; Backing means; Inserts with backing means disposed under the seam the backing means being movable during the welding operation
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/095—Monitoring or automatic control of welding parameters
Definitions
- the present invention relates to an electrogas arc welding method and an electrogas arc welding apparatus. More specifically, the present invention relates to a slag discharge technique in electrogas arc welding.
- a water-cooled sliding metal is arranged on the surface (groove surface) side of the base material, and a backing metal is arranged on the opposite surface. Then, a shield gas such as carbon dioxide gas is supplied into the space surrounded by the base material, the sliding metal and the backing metal, and the welding wire is fed out from the welding torch to perform arc welding.
- the welding posture is generally a vertical posture in which welding is performed from the bottom to the top.
- a flux-cored wire in which a steel outer sheath is filled with a flux is generally used as a welding material.
- the reason why the flux-cored wire is used is that the slag forming agent blended in the flux at the time of welding melts and functions to keep the bead appearance good.
- the slag forming agent melts during welding, and a large amount of molten slag stays immediately above the molten metal.
- the wire is buried in the slag, causing the arc to become unstable and the bead appearance to deteriorate.
- the components of the weld metal fluctuate, causing problems of excessive strength and toughness deterioration.
- Patent Documents 1 to 4 a method of forcibly discharging slag from the lower portion of the sliding metal is employed (see Patent Documents 1 to 4).
- a water-cooled sliding copper metal having a taper that becomes wider as the gap with the bead goes downward is used.
- variety which decreases gradually on the surface used as a groove side from the surface of this gold
- Patent Document 3 a surface facing the base material is formed as a curved concave portion, an opening for supplying a shielding gas is formed near the upper end of the curved concave portion, and a slide made of a flat vertical surface is formed on both the left and right sides of the curved concave portion.
- a sliding contact having a moving edge portion and a notch for forming a gap of a predetermined width between the moving edge portion and the surface of the base material.
- the molten slag staying on the molten metal in the molten pool flows downward from the gap between the curved concave portion and the molten metal, and the notch and the base material surface. Since it also flows out to the side of the track of the sliding metal from the gap formed between the two, a discharge amount of the molten slag can be increased as compared with the conventional sliding metal.
- Patent Document 4 a first groove for forming a weld bead and a second slag for discharging molten slag are formed in order from the upper side to the lower side on the surface of the welded material groove portion of the water-cooled sliding copper metal.
- a sliding allowance provided with a groove is proposed.
- the first groove is formed parallel to the surface of the welded material
- the second groove is continuous with the lower portion of the first groove and is inclined with respect to the surface of the welded material.
- the groove width is formed so as to increase from the top to the bottom and the groove depth increases from the top to the bottom.
- the sliding allowance described in Patent Document 2 sucks and discharges molten slag with a groove formed, but in the case of a slag composition having a low surface tension, a suction effect is sufficiently obtained.
- the slag that has entered the groove is solidified, and there is a problem that the discharging effect by suction cannot be obtained during welding.
- the sliding metal described in Patent Document 3 has a problem that not only the molten slag but also the molten metal flows in the notch of the water-cooled sliding copper metal and the bead shape deteriorates.
- the main object of the present invention is to provide an electrogas arc welding method and an electrogas arc welding apparatus that can efficiently discharge slag.
- the promotion of slag discharge has been devised by the structure of water-cooled sliding copper metal.
- the discharge amount of slag varies depending on the arc stability and the slag composition of the welding wire, it cannot be sufficiently controlled only by the structure of the water-cooled sliding copper alloy.
- the composition of the welding wire affects the melt physical properties of the slag, and is also related to weld metal burn-out, weld defects, and bead shape degradation. The optimal approach has not been made.
- the present inventor examines a combination of a welding material and a welding apparatus in consideration of the slag composition, can maintain efficient slag discharge even when used repeatedly for a long time, weld defects, bead shape deterioration, The present inventors have found an electrogas arc welding method capable of preventing toughness deterioration and have reached the present invention.
- the electrogas arc welding method according to the present invention is an electrogas arc welding method in which a sliding copper contact is brought into contact with a groove surface of a workpiece and arc welding is performed while raising the sliding copper contact and the welding torch.
- a flux is filled in a steel outer sheath, and C: 0.01 to 0.50 mass%, Si: 0.10 to 1.00 mass%, and Mn: 0.50 to 4.00% by mass, Mo: 0.10 to 1.00% by mass, Ti: 0.05 to 0.40% by mass, SiO 2 : 0.10 to 1.00% by mass Al: 0.30 mass% or less (including 0%), S: 0.050 mass% or less (including 0%), P: 0.050 mass% or less (including 0%), TiO 2 : 0 .30 wt% or less (including 0%), Al 2 O 3 : 0.30 quality % Or less is restricted to (including 0%), the balance being Fe and unavoidable impurities, the content of SiO 2 [SiO
- the flux-cored wire further contains Mg: 0.50 mass% or less, Ni: 2.0 mass% or less, Cr: 1.0 mass% or less, and B: 0.005 mass% or less, based on the total mass of the wire. You may do it.
- the flux-cored wire further includes at least one oxide of MgO, Li 2 O, Na 2 O, K 2 O, CaO, SrO, and BaO in total 0.80 mass per total mass of the wire. % Or less.
- the flux-cored wire having a diameter of 1.5 to 3.5 mm and a flux filling rate of 15 to 30% by mass can be used.
- the control of the rising speed of the welding torch includes a step of removing a high frequency component from the welding current detected by the low pass filter, a welding current value that has passed through the low pass filter, And a step of comparing with a preset welding current command value, and the cut-off frequency of the low-pass filter may be set to 0.98 to 2.93 Hz. It is also possible to perform welding while periodically changing the arc voltage.
- An electrogas arc welding apparatus welds a sliding copper abutting against a groove surface of a material to be welded, a welding torch for feeding a welding wire into the groove, and the welding torch.
- a torch moving mechanism that moves in the front-rear direction, the up-down direction, and the left-right direction with respect to the wire, and a control unit that controls the rising speed of the welding torch based on a welding current,
- the groove depth D is 0.5 to 5.5 mm, and the ratio (W / D) of the groove width W to the groove depth D is 5.0 to 80.0.
- the composition of the welding material is specified in addition to the structure of the sliding copper alloy, the slag can be discharged efficiently.
- FIG. 3A is a plan view schematically showing the configuration of the sliding copper alloy 2 shown in FIG. 3B is a cross-sectional view taken along the line ZZ shown in FIG. 3A. It is a block diagram which shows the method to control so that protrusion length becomes fixed. It is a figure which shows the structural example of the welding apparatus used with the electrogas arc welding method of this embodiment. It is sectional drawing which shows the welding method in the case of applying to fillet welding.
- FIG. 1 is a sectional view schematically showing an electrogas arc welding method according to an embodiment of the present invention
- FIG. 2 is a sectional view showing a groove shape
- 3A is a plan view schematically showing the configuration of the sliding copper alloy 2 shown in FIG. 1
- FIG. 3B is a cross-sectional view taken along line ZZ shown in FIG. 3A.
- a sliding copper abutment 2 is applied to one surface side of a groove formed in a material to be welded (base material 1), and the other surface. Place backing 3 on the side.
- base material 1 a material to be welded
- the groove shape for example, a V groove as shown in FIG. 2 can be applied.
- the welding wire 5 is fed from the welding torch 4 while supplying the shielding gas into the groove surrounded by the base material 1, the sliding copper metal 2 and the backing material 3, and the welding torch 4 and the sliding copper are supplied. Arc welding is performed while raising the metal 2.
- the welding wire 5 is filled with a flux in the steel outer sheath, contains a specific amount of C, Si, Mn, Mo, Ti and SiO 2 , and contains Al, S, P, TiO 2 and Al 2 O. 3 is regulated to a specific amount or less, and a flux-cored wire having a composition that satisfies the following mathematical formula (A), with the balance being Fe and inevitable impurities.
- A [SiO 2 ] is SiO 2 content
- [Si] is Si content
- [Al 2 O 3 ] is Al 2 O 3 content
- [Al] is Al content
- [TiO 2 2 ] is the TiO 2 content
- [Ti] is the Ti content.
- the Si content indicated by [Si] is the Si content excluding Si in SiO 2.
- content shown by [] is content shown by mass ratio.
- the sliding copper alloy 2 has a groove 12 having a curvature on the surface in contact with the groove, and the groove width W when the groove width is a. (1.1 ⁇ a) to (2.5 ⁇ a) mm, the groove depth D is 0.5 to 5.5 mm, and the ratio (W / D) of the groove width W to the groove depth D is 5. Use 0-80.0. Furthermore, at the time of welding, the feeding speed of the welding wire 5 is made constant, and the rising speed of the welding torch is controlled based on the welding current.
- the welding wire 5 used in the electrogas arc welding method of this embodiment is a flux-cored wire composed of a cylindrical steel outer sheath and a flux filled inside the outer sheath.
- the form of the flux-cored wire may be either a seamless type without a seam in the outer skin or a seam type with a seam in the outer skin.
- the flux-cored wire has a surface (outside of the outer skin) that is copper-plated and a surface that is not subjected to the plating, but both can be used in the electrogas arc welding method of the present embodiment. it can.
- the component amount shown below is a ratio with respect to the total mass of the wire combining the outer skin and the flux.
- C has the effect of increasing the strength of the weld metal.
- the strength of the weld metal is insufficient.
- C contains more than 0.50 mass% in the welding wire, it combines with oxygen during welding to become CO gas, and bubbles are generated on the droplet surface. And since this bubble is scattered, the arc becomes unstable and spatter occurs. Therefore, the C content of the welding wire is set to 0.01 to 0.50 mass%.
- Si is an element having a deoxidizing action and is an element necessary for ensuring the strength and toughness of the weld metal.
- the C content of the welding wire is less than 0.10% by mass, blowholes are generated in the weld metal due to insufficient deoxidation.
- the welding wire contains a large amount of Si exceeding 1.00% by mass, the molten slag 8 that accumulates on the molten metal 7 during welding becomes thick, and the welding wire 5 is buried in the molten slag 8.
- the yield of the weld metal 9 varies and the toughness deteriorates. Therefore, the Si content of the welding wire is 0.10 to 1.00% by mass.
- the Si component amount of the welding wire does not include Si in SiO 2 . This is because the SiO 2 component amount is specified separately.
- Mn acts as an oxygen scavenger or sulfur scavenger, as is the case with Si, and is an element necessary for ensuring the strength and toughness of the weld metal.
- Mn content of the welding wire is less than 0.50% by mass, welding defects (blow holes) are generated in the weld metal due to insufficient deoxidation, and the toughness of the weld metal is insufficient.
- the welding wire contains a large amount of Mn exceeding 4.00% by mass, a large amount of slag that is difficult to peel off is generated during welding, and welding defects such as slag entrainment are generated. Strength increases too much and toughness decreases significantly. Therefore, the Mn content of the welding wire is 0.50 to 4.00 mass%.
- Mo 0.10 to 1.00% by mass> Mo is an element necessary for ensuring the strength and toughness of the weld metal.
- Mo content of the welding wire is less than 0.10% by mass, the strength and toughness of the weld metal are insufficient.
- the welding wire contains more than 1.00% by mass of Mo, the weld metal has excessive strength, and weld defects such as cracks occur. Therefore, the Mo content of the welding wire is set to 0.10 to 1.00% by mass.
- Ti has the effect of refining ferrite grains in the weld metal and improving toughness.
- the toughness of the weld metal is insufficient.
- Ti is a strong deoxidizing element, if the welding wire contains Ti exceeding 0.40% by mass, the generation of TiO 2 slag with high viscosity becomes excessive. As a result, slag discharge is suppressed, the molten slag 8 that accumulates on the molten metal 7 becomes thick, the welding wire 5 is buried in the molten slag 8, the yield of the weld metal 9 varies, and the toughness deteriorates. Therefore, the Ti content of the welding wire is 0.05 to 0.40 mass%.
- SiO 2 is an oxide contained in the flux and forms a molten slag with relatively good fluidity. Moreover, when MgO and CaO which will be described later are added together with SiO 2 , the fluidity of the molten slag is further improved. Therefore, in the electro-gas arc welding, when the slag composition mainly composed of SiO 2, the discharge of the slag is promoted. Moreover, since the slag composition mainly composed of SiO 2 is vitreous and easily peeled and spreads over the entire surface of the bead, the bead appearance is also improved. Thus in order to form the SiO 2 slag composition consisting mainly of the situation, it is necessary to include SiO 2 0.10 wt% to the welding wire.
- the SiO 2 content in the welding wire is set to 0.10 to 1.00% by mass. From the viewpoint of improving the slag discharge efficiency, the SiO 2 content of the welding wire is preferably 0.20 to 0.60 mass%.
- Al like Ti described above, has the effect of refining ferrite grains in the weld metal and improving toughness, but the effect of refining ferrite grains is most effective for Ti, and Al oxide is Since the viscosity is high, the slag peelability is lowered and the bead appearance is affected. For this reason, it is preferable not to add Al to a welding wire as much as possible, and it is more preferable that it is 0 mass%.
- the welding wire since Al is a strong deoxidizing element, if the welding wire contains Al in excess of 0.30 mass%, slag is excessively generated. As a result, slag discharge is suppressed, the molten slag 8 that accumulates on the molten metal 7 becomes thick, the welding wire 5 is buried in the molten slag 8, the yield of the weld metal 9 varies, and the toughness deteriorates. Therefore, the Al content of the welding wire is regulated to 0.30% by mass or less.
- S (sulfur) and P (phosphorus) are both inevitable droplet impurities, and when the content of these elements in the welding wire exceeds 0.050% by mass, weld defects such as cracks occur in the weld metal. . Therefore, both S content and P content are regulated to 0.050 mass% or less.
- the S content and the P content of the welding wire are preferably as low as possible, and more preferably 0% by mass. However, if each is 0.050% by mass or less, the effect of the present invention is not affected.
- TiO 2 and Al 2 O 3 are oxides contained in the flux, but in order to form a highly viscous molten slag, the content of these is preferably as low as possible, more preferably 0% by mass. preferable.
- the TiO 2 content and the Al 2 O 3 content in the welding wire exceed 0.30% by mass, slag discharge is suppressed, the toughness of the weld metal deteriorates, and welding defects such as slag entrainment occur. To do. Therefore, the TiO 2 content and the Al 2 O 3 content are each regulated to 0.30% by mass or less.
- Mg is a strong deoxidizing element and has the effect of improving the toughness by reducing the oxygen content of the weld metal, so it can be added to the welding wire as needed.
- Mg is a strong deoxidizing element and has the effect of improving the toughness by reducing the oxygen content of the weld metal, so it can be added to the welding wire as needed.
- it is preferable to set it as 0.05 mass% or more.
- Mg is a strong deoxidizing element
- MgO slag becomes excessive.
- An appropriate amount of MgO is combined with SiO 2 to form molten slag with good fluidity.
- MgO is excessively increased, a large amount of slag that is difficult to peel off is generated during welding, and welding defects such as slag entrainment occur. Therefore, when adding Mg to a welding wire, it is 0.50 mass% or less.
- the flux cored wire used for the welding wire may contain Ni, Cr, and B in order to improve the strength or toughness of the weld metal. However, if these elements are added excessively, cracks are likely to occur in the weld metal. Specifically, when Ni is added to the welding wire in excess of 2.0 mass%, Cr is added in excess of 1.0 mass%, or B is added in excess of 0.005 mass%, Cracks are likely to occur in the weld metal. Therefore, when adding Ni, Cr, and B, they are made into Ni: 2.0 mass% or less, Cr: 1.0 mass% or less, and B: 0.005 mass% or less, respectively.
- MgO, Li 2 O, Na 2 O, K 2 O, CaO, SrO, BaO 0.80 mass% in total> MgO, Li 2 O, Na 2 O, K 2 O, CaO, SrO and BaO, and fused with SiO 2, to reduce the viscosity of the slag, the effect of improving the fluidity.
- MgO, Li 2 O, Na 2 O, K 2 O, CaO, SrO, and BaO exceeds 0.80% by mass, the amount of slag becomes excessive, and oxide generation occurs more than the discharge effect. Is better.
- the welding wire MgO, if Li 2 O, Na 2 O, K 2 O, CaO, adding SrO and BaO, the total content is set to be below 0.80 wt%.
- the welding wire may contain only 1 type among these oxides, and may contain 2 or more types.
- the diameter of the flux-cored wire used for the welding wire is preferably 1.5 to 3.5 mm.
- the diameter of the flux-cored wire used for the welding wire is preferably 1.5 to 3.5 mm.
- electrogas arc welding when a wire having a diameter of less than 1.5 mm is used, the amount of welding increases and the position of the molten metal increases, so that slag discharge is suppressed.
- a wire having a diameter exceeding 3.5 mm is used, the welding current becomes high and the heat input becomes large, so that the toughness of the obtained weld metal tends to deteriorate.
- the flux-cored wire used for the welding wire preferably has a flux filling rate of 15 to 30% by mass.
- a wire having a flux filling rate of less than 15% by mass the effect of improving the welding amount cannot be obtained, and the wire is easily buried in the slag bath.
- the “flux filling rate” is defined by the ratio of the mass of the flux filled in the outer skin to the mass of the entire wire (the total of the outer skin and the flux).
- the material of the outer sheath of the flux-cored wire used for the welding wire may be any of mild steel and stainless steel as long as the composition of the entire wire is within the above-described range.
- the welding wire used in the electrogas arc welding method of the present embodiment is not particularly limited, and one produced by a general production method can be used.
- mild steel or It can be manufactured by filling a U-shaped outer shell made of stainless steel with a flux, forming it into a cylindrical mold, and drawing it to a target diameter.
- the sliding copper alloy 2 used for electro arc welding according to the present embodiment is provided with a groove 12 having a curvature on the surface in contact with the groove.
- the groove shape of the sliding copper alloy 2 depends on the discharge of the molten slag. When the groove width W and the groove depth D are large, the discharge of slag is promoted, but welding defects such as bead shape failure and slag entrainment due to the molten metal being melted and the bead not being uniformly coated by the slag occur. .
- the groove width W and the groove depth D are small, the discharge of the slag is delayed, the molten slag 8 accumulated on the molten metal 7 becomes thick, the welding wire 5 is buried in the molten slag 8, and the yield of the weld metal 9 is increased. Fluctuates and deteriorates toughness. For this reason, in order to prevent the occurrence of a bead shape defect and a weld defect by uniformly covering the bead with slag, the groove should not be excessively large.
- the molten slag mainly composed of SiO 2 is formed by using the welding wire (flux-cored wire) having the above-described composition. Since molten slag mainly composed of SiO 2 has low viscosity, it has good fluidity and good wettability with copper metal, so it does not require excessive grooving. Can be coated uniformly to form a bead having a good shape.
- the groove shape suitable for the combination with the flux-cored wire having the above-described composition is such that the groove width W is (1.1 ⁇ a) to (2.5 ⁇ a) mm when the groove width is a, and the groove depth.
- the thickness D is 0.5 to 5.5 mm, and the ratio (W / D) of the groove width W to the groove depth D is 5.0 to 80.0.
- ⁇ Groove width W (1.1 ⁇ a) to (2.5 ⁇ a) mm>
- the groove width W depends on the groove width a.
- the groove width W is less than 1.1 times the groove width a, the bead shape becomes defective.
- the groove width W exceeds 2.5 times, the weld metal melts down and the bead shape defect occurs. Therefore, the groove width W is in the range of 1.1 to 2.5 times the groove width a.
- ⁇ Groove depth D 0.5 to 5.5 mm>
- the groove depth D is less than 0.5 mm, the yield of the weld metal varies and the toughness deteriorates.
- the groove depth D exceeds 5.5 mm, the slag is not evenly placed on the bead, and a weld defect such as a bead shape defect or slag entrainment occurs. Therefore, the groove depth D is in the range of 0.5 to 5.5 mm.
- ⁇ Ratio of groove width W to groove depth D (W / D): 5.0 to 80.0>
- the ratio (W / D) of the groove width W to the groove depth D is less than 5.0, even if the flux-cored wire having the above-described composition is used, the discharge of slag is delayed and the yield of the weld metal varies. , Toughness deteriorates.
- the ratio (W / D) of the groove width W to the groove depth D exceeds 80.0, welding defects such as bead shape defects and slag entrainment occur. Therefore, the ratio (W / D) of the groove width W to the groove depth D is set to 5.0 to 80.0.
- the shape of the groove 12 of the sliding copper alloy 2 is a shape having a curvature. Thereby, a favorable bead shape can be maintained.
- the radius of curvature of the groove 12 is not particularly limited, but is preferably 30 to 180 mm. Thereby, it can coat
- the protruding length of the welding wire 5 during welding is preferably 20 to 60 mm.
- the protruding length of the welding wire 5 is less than 20 mm, the welding current becomes high and the heat input becomes large, so the toughness of the weld metal deteriorates.
- the protruding length of the welding wire 5 exceeds 60 mm, the Joule heat effect becomes high and the droplet transfer becomes unstable, so that it becomes difficult to control the protruding length to be described later.
- welding is performed while controlling the rising speed of the welding torch so that the protruding length l of the welding wire 5 described above becomes constant. If the protruding length is made constant, the arc is stabilized and the peristalsis of the molten slag 8 can be reduced, so that the change in the slag discharge amount with time becomes small, and a uniform amount of slag discharge can always be made. As a result, it is possible to prevent welding defects such as defective bead shape and slag entrainment.
- FIG. 4 is a block diagram showing a control method for keeping the protruding length constant.
- the welding current is detected, and the ascending speed of the welding torch 5, that is, the welding speed is controlled based on the value. At that time, the feeding speed of the welding wire 5 is kept constant without changing.
- the method for controlling the ascending speed of the welding torch based on the welding current is not particularly limited.
- a welding current X1 obtained by removing a high frequency component by a low-pass filter F1 is used as a current detection value.
- the current value of the current detection value converter G1 is compared with a value obtained by inverting the welding current command value set by the manual operation X2 by the current setting unit G2.
- Control of the speed of the welding torch 4 is performed by, for example, calculating in the cart travel motor speed command calculator G3 and automatically controlling the cart travel motor 21 that moves the welding torch 4 through the cart travel motor drive circuit 20. be able to. By this control, the protruding length of the welding wire 5 can be made constant.
- the cut-off frequency of the low-pass filter F1 in the range of 0.98 to 2.93 Hz from the viewpoint of improving the accuracy of controlling the protruding length of the welding wire 5.
- the cut-off frequency of the low-pass filter is less than 0.98 Hz, the sensitivity of the ascending speed control of the welding torch 4 is lowered, and the change in the protruding length of the welding wire 5 may not be followed.
- the cut-off frequency exceeds 2.93 Hz, the sensitivity of the ascending speed control of the welding torch 4 becomes too high, the ascent speed is changed with a slight current change, and the protruding length of the welding wire 5 changes.
- the arc may become unstable. When the arc becomes unstable, the surrounding air is entrained and nitrogen is mixed into the weld metal, so that the toughness may deteriorate.
- FIG. 5 is a view showing a configuration example of a welding apparatus used in the electrogas arc welding method of the present embodiment.
- the electrogas arc welding method of this embodiment can be implemented by an electrogas arc welding apparatus including at least the above-described sliding copper alloy 2, the welding torch 4, the torch moving mechanism, and the control unit.
- An electrogas arc welding apparatus is generally provided with a welding power source 25, a wire feeding device 26, a shield gas supply mechanism, and the like.
- the torch moving mechanism moves the welding torch 4 in the front-rear direction, the up-down direction, and the left-right direction with respect to the weld line, and includes, for example, a carriage 22 and a traveling rail 23.
- the detachable welding carriage 22 is equipped with a welding torch 4 and a sliding copper stake 2 and can be moved up and down, back and forth, and left and right with respect to the welding line by moving with a traveling rail 23 as a guide. It is configured. Further, the welding carriage 22 is 20 kg or less, and the width between the guide rollers provided on the welding carriage 22 and the width of the traveling rail 23 are relatively changed, so that the welding carriage 22 is moved from a predetermined position on the traveling rail 23. It is preferable that it can be easily detached.
- the control unit controls the ascending speed of the welding torch 4 based on the welding current so that the protruding length of the welding wire 5 is constant, and is provided in the operation box 24, for example.
- the operation box 24 is connected to a welding power source 25 and controls switches for starting and stopping welding, welding current adjustment, welding voltage adjustment, protrusion length adjustment, travel speed adjustment, wire inching, and the like.
- board thickness of a to-be-welded material (base material 1) is not specifically limited, According to a use etc., it can select suitably and can be used.
- the welding torch 4 may be oscillated and welded. In that case, it is preferable to have a weaver angle setting mechanism, a weaver rotation transmission drive mechanism that can be maintained at the set angle, a torch rotation transmission function that always maintains a constant angle between the torch and the welding carriage, and a weaving operation transmission mechanism.
- the characteristics of the power source (welding power source) used for welding are not particularly limited, and may be a direct current welding power source or an alternating current power source. However, since the protrusion length is controlled to be constant, it is preferable to use a welding power source having a constant voltage characteristic.
- the type and material of the backing material 3 are not particularly limited, and may be, for example, a water-cooled copper alloy or a steel material having a composition close to that of the ceramic material or the base material 1.
- the arc voltage is kept high for a long time, the arc becomes unstable. Therefore, in the electrogas arc welding method of the present embodiment, it is preferable to increase the arc voltage value every arbitrary time in order to promote slag discharge.
- the timing for increasing the arc voltage may be performed at regular intervals or irregularly.
- the waveform is not particularly limited, and various pulse waveforms such as a rectangular wave, a triangular wave, and a wave shape can be adopted.
- the range of the pulse frequency is not particularly limited, but is preferably from 0.1 to 500 Hz, whereby slag discharge can be effectively obtained.
- the shielding gas in addition to 100% by volume CO 2 and 100% by volume Ar, a mixed gas of Ar and CO 2 or O 2 can be used. Among these shielding gases, 100% by volume CO 2 is particularly preferable because of its high melting effect. From the viewpoint of preventing shielding gas failure, the gas flow rate is preferably 15 to 40 L / min.
- FIG. 6 is a cross-sectional view showing a welding method when applied to fillet welding.
- a backing material is unnecessary.
- the sliding copper contact 2 is brought into contact with the surface of the base material 1 and the welding wire is fed from the welding torch while supplying the shielding gas into the groove surrounded by the base material 1 and the sliding copper contact 2.
- arc welding may be performed while raising the welding torch and sliding copper.
- Other conditions are the same as in the case of the V groove.
- a flux-cored wire that can form molten slag having the most effective physical properties for discharging molten slag and a sliding metal having a specific groove shape are used.
- efficient discharge of slag can be maintained even when used repeatedly for a long time. As a result, welding defects, bead shape deterioration, and weld metal toughness deterioration can be prevented.
- the electrogas arc welding method of this embodiment can further improve the toughness of a weld metal by using the flux-cored wire containing Mg, Ni, Cr, and B in specific amounts. Furthermore, when flux-cored wires containing at least one oxide of MgO, Li 2 O, Na 2 O, K 2 O, CaO, SrO and BaO are used, they are melted by being combined with SiO 2. Since the slag viscosity is lowered, the discharge of the molten slag that accumulates on the molten metal can be further promoted.
- the flux-cored wires W1 to W70 shown in the following Tables 1 to 4 and the sliding copper alloy shown in the following Tables 3 and 4 are used, the welding wire feeding speed is constant, and the welding current is adjusted. Based on this, electrogas arc welding was performed while adjusting the ascending speed of the welding torch so that the protruding length of the welding wire was constant.
- the remainder in the component composition of the flux-cored wire shown in Tables 1 and 2 below is Fe and inevitable impurities. Note that “ ⁇ ” in Tables 1 and 2 below indicates that they are not actively added, but these components may also be included as inevitable impurities.
- Electrogas arc welding was performed under the following conditions. Welding current: 380A Arc voltage: 35V Welding speed: 8 cm / min Heat input: 9.9 kJ / mm Base material plate thickness: 19mm Groove shape: V groove groove angle: 40 ° Gap: 5-10mm (The gap was changed to 5-10mm to adjust the groove width) Shield gas: 100% CO 2
- Bead appearance> The bead appearance was determined by visual inspection of the bead after welding. When there was a bead shape defect such as bead meandering, humping, and overlap, it was marked as x.
- the welding defect was performed by a method based on a radiation transmission test (RT: see JIS Z 3104). When the defect was confirmed, it was set as x, and when there was no defect, it was set as ⁇ .
- the toughness of the weld metal was evaluated by Charpy absorbed energy (J) of ⁇ 20 ° C. based on JIS Z 3128. Specifically, a sample was extracted from the center of the bead cross section, and an average value of three times was taken. According to the standard of flux cored wire for electrogas arc welding of JIS Z 3319, the Charpy absorbed energy (J) at ⁇ 20 ° C. is 40 J or more. In the case of exceeding 80 J, double, it was judged that it was better, and it was marked as ⁇ .
- the welding voltage and welding current running speed were set on the operation box panel, and after confirming the cooling water amount and gas flow rate, the welding start button on the operation box panel was pressed to run the carriage simultaneously with the arc start.
- the protruding length on the operation box panel it was adjusted to an arbitrary protruding length, and welding was performed while performing automatic elevation control. Welding was stopped by pressing the welding stop button on the operation box panel at the end of welding.
- Nos. 1 to 75 are examples within the scope of the present invention.
- Nos. 76 to 119 are comparative examples outside the scope of the present invention.
- Table 5 the example No. In Nos. 1 to 75, slag discharge was promoted, arc stability, bead appearance and toughness were good, and no welding defects were observed.
- No. No. 94 is an example using a welding wire having a diameter of 3.2 mm, but the arc became unstable because the welding balance was different with respect to the test current 380A.
- No. 95 is an example using a welding wire having a diameter of 1.4 mm. However, since the welding amount is larger than the optimum amount with respect to the test current 380A, the position of the molten metal rises, and it seems to be buried. As a result, the arc became unstable.
- No. 96 no. No. 97 is an example in which the flux filling rate is 12% by mass or 33% by mass, but the arc becomes unstable because the welding balance differs with respect to the test current 380A.
- No. for 98 the C content in the welding wire was too high, and the toughness deteriorated due to arc instability and excessive strength.
- No. 99 uses a welding wire with an excessive amount of Si, so the amount of molten slag increased and slag winding occurred.
- No. No. 100 uses a flux-cored wire with a small amount of Si, so that the deoxidation action is reduced and pore defects are generated.
- No. 102 uses a flux-cored wire containing an excessive amount of Mn, the weld metal has excessive strength and the toughness deteriorates.
- No. 103 uses a flux-cored wire with a large amount of Mo, the weld metal has excessive strength and the toughness deteriorates.
- No. No. 104 is a flux-cored wire to which P is added excessively, No. 104.
- No. 105 is a flux-cored wire to which B is added excessively, No. 105.
- No. 106 used a flux-cored wire to which S was added excessively, and cracks occurred in the weld metal.
- No. No. 107 used a flux-cored wire that did not contain Mo, resulting in insufficient toughness of the weld metal.
- No. 108 molten slag mainly composed of TiO 2 and Al 2 O 3 was formed, and slag discharge was suppressed, so that slag entrainment and bead shape failure occurred.
- No. 109 to 115 a flux-cored wire with an excessive amount of oxide added was used, so slag discharge was suppressed and slag entrainment occurred.
- No. No. 116 used a flux-cored wire to which Mg was excessively added, so that slag discharge was suppressed and slag entrainment occurred.
- No. 117 uses a flux-cored wire to which SiO 2 is excessively added, so that slag discharge is suppressed and slag entrainment occurs.
- No. 118 due to the use of the flux cored wire additive amount of SiO2 is insufficient, TiO 2 and Al 2 O 3 is formed molten slag of the main component, since the slag discharge is suppressed, the slag inclusion and the bead shape defect Occurred.
- Base material material to be welded
- sliding copper metal backing material
- welding power source wire feeder
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Abstract
Description
あるものとし、前記溶接ワイヤの送給速度は一定にし、前記溶接ワイヤの突出し長さが一定になるように、溶接電流に基づいて前記溶接トーチの上昇速度を制御する。
また、前記フラックス入りワイヤは、更に、ワイヤ全質量あたり、MgO、Li2O、Na2O、K2O、CaO、SrO及びBaOのうち少なくとも1種の酸化物を、合計で0.80質量%以下含有することもできる。
更に、前記フラックス入りワイヤには、直径が1.5~3.5mmであり、フラックス充填率が15~30質量%であるものを使用することができる。
一方、本発明に係るエレクトロガスアーク溶接方法では、前記溶接トーチの上昇速度の制御は、ローパスフィルターにより検出された溶接電流から高周波成分を除去する工程と、前記ローパスフィルターを通過した溶接電流値と、予め設定された溶接電流指令値とを比較する工程と、を有し、前記ローパスフィルターのカットオフ周波数を0.98~2.93Hzに設定してもよい。
また、アーク電圧を周期的に変動させながら溶接を行うこともできる。
なお本明細書において、[Si]で示すSi含有量はSiO2中のSiを除くSi含有量である。また[ ]で示される含有量は、質量比で示された含有量である。
本実施形態のエレクトロガスアーク溶接方法に用いられる溶接ワイヤ5は、筒状の鋼製外皮と、この外皮の内側に充填されたフラックスとで構成されるフラックス入りワイヤである。なお、フラックス入りワイヤの形態は、外皮に継目のないシームレスタイプ、外皮に継目のあるシームタイプのいずれでもよい。また、フラックス入りワイヤには、表面(外皮の外側)に銅めっきが施されているものと、施されていないものがあるが、本実施形態のエレクトロガスアーク溶接方法では、どちらも使用することができる。
Cは、溶接金属の強度を高める効果がある。しかしながら、溶接ワイヤのC含有量が0.01質量%未満の場合、溶接金属の強度が不足する。一方、溶接ワイヤ中にCが0.50質量%を超えて多量に含まれていると、溶接中に酸素と結合してCOガスとなり、溶滴表面に泡が発生する。そして、この泡が飛散することで、アークが不安定になり、スパッタが発生する。よって、溶接ワイヤのC含有量は0.01~0.50質量%とする。
Siは、脱酸作用のある元素であり、溶接金属の強度や靱性を確保するために必要な元素である。しかしながら、溶接ワイヤのC含有量が0.10質量%未満の場合、脱酸不足により、溶接金属にブローホールが発生する。一方、溶接ワイヤに、1.00質量%を超えて多量にSiが含まれていると、溶接中に溶融金属7上にたまる溶融スラグ8が厚くなって、溶接ワイヤ5が溶融スラグ8に埋まり、溶接金属9の歩留まりが変動して靭性が劣化する。よって、溶接ワイヤのSi含有量は0.10~1.00質量%とする。
なお、本明細書において、溶接ワイヤのSi成分量と言う場合、SiO2中のSiは含まない。SiO2成分量については別途規定しているためである。
Mnは前述したSiと同様に、脱酸素剤又は硫黄捕捉剤として作用するため、溶接金属の強度や靭性の確保に必要な元素である。しかしながら、溶接ワイヤのMn含有量が0.50質量%未満の場合、脱酸不足により溶接金属に溶接欠陥(ブローホール)が発生したり、溶接金属の靭性が不足したりする。一方、溶接ワイヤに、4.00質量%を超えて多量にMnが含まれていると、溶接中に剥離し難いスラグが大量発生し、スラグ巻き込みなどの溶接欠陥が発生すると共に、溶接金属の強度が増加しすぎて靭性が著しく低下する。よって、溶接ワイヤのMn含有量は、0.50~4.00質量%とする。
Moは、溶接金属の強度や靭性を確保するために必要な元素である。しかしながら、溶接ワイヤのMo含有量が0.10質量%未満の場合、溶接金属の強度や靭性が不足する。一方、溶接ワイヤに、1.00質量%を超えてMoが含まれていると、溶接金属が強度過多となり、割れなどの溶接欠陥が発生する。よって、溶接ワイヤのMo含有量は0.10~1.00質量%とする。
Tiは、溶接金属中のフェライト粒を微細化し、靭性を向上させる効果がある。しかしながら、溶接ワイヤのTi含有量が0.05質量%未満の場合、溶接金属の靭性が不足する。一方、Tiは強脱酸元素であるため、溶接ワイヤに0.40質量%を超えてTiが含まれていると、粘性の高いTiO2スラグの発生が過多となる。その結果、スラグ排出が抑制され、溶融金属7上にたまる溶融スラグ8が厚くなって、溶接ワイヤ5が溶融スラグ8に埋まり、溶接金属9の歩留まりが変動して靭性が劣化する。よって、溶接ワイヤのTi含有量は0.05~0.40質量%とする。
SiO2は、フラックスに含有される酸化物であり、比較的流動性の良い溶融スラグを形成する。また、SiO2と共に、後述するMgOやCaOを添加すると、溶融スラグの流動性が更に良好になる。このため、エレクトロガスアーク溶接において、SiO2を主体としたスラグ組成にすると、スラグの排出が促進される。また、SiO2を主体としたスラグ組成は、ガラス質で剥離もしやすく、ビード全面に広がるため、ビード外観も良好となる。このようなSiO2を主体としたスラグ組成を形成するためには、溶接ワイヤにSiO2を0.10質量%以上含有させる必要がある。
Alは、前述したTiと同様に、溶接金属中のフェライト粒を微細化し、靭性を向上させる効果があるが、フェライト粒の微細化効果はTiが最も効果的であり、また、Al酸化物は粘性が高いため、スラグ剥離性を低下させ、ビード外観に影響を及ぼす。このため、溶接ワイヤにAlは極力添加しないことが好ましく、0質量%であることがより好ましい。
S(硫黄)及びP(リン)は、いずれも不可避滴不純物であり、溶接ワイヤにおけるこれらの元素の含有量がそれぞれ0.050質量%を超えると、溶接金属に割れなどの溶接欠陥が発生する。よって、S含有量及びP含有量はいずれも0.050質量%以下に規制する。なお、溶接ワイヤのS含有量及びP含有量は、できるだけ少ない方が好ましく、より好ましくは0質量%であるが、それぞれ0.050質量%以下であれば、本発明の効果には影響しない。
TiO2及びAl2O3は、フラックスに含有される酸化物であるが、粘性の高い溶融スラグを形成するため、これらの含有量はできるだけ少なくすることが好ましく、0質量%であることがより好ましい。特に、溶接ワイヤにおけるTiO2含有量及びAl2O3含有量がそれぞれ0.30質量%を超えると、スラグ排出が抑制され、溶接金属の靭性が劣化したり、スラグ巻き込みなどの溶接欠陥が発生したりする。よって、TiO2含有量及びAl2O3含有量は、それぞれ0.30質量%以下に規制する。
前述したように、フラックスに由来するTiO2やAl2O3、強脱酸元素であるTi及びAlは、スラグの排出を抑制する。このため、([SiO2]+2.1×[Si])/([Al2O3]+1.9×[Al]+[TiO2]+1.7×[Ti])が1.0未満である場合、即ち、溶接ワイヤにおけるこれらの成分の含有量が上記数式(A)を満たさない場合は、TiO2やAl2O3主体のスラグ組成となり、溶接金属の靭性低下や溶接欠陥の発生を招く。
Mgは、強脱酸元素であり、溶接金属の酸素量を低減して靱性を向上させる効果があるため、必要に応じて溶接ワイヤに添加することができる。なお、溶接金属の靭性向上の観点から、溶接ワイヤにMgを添加する場合は0.05質量%以上とすることが好ましい。
溶接ワイヤに用いるフラックス入りワイヤは、溶接金属の強度又は靭性向上のため、Ni、Cr及びBを含有していてもよい。ただし、これらの元素は、過剰に添加すると、溶接金属に割れが発生しやすくなる。具体的には、溶接ワイヤに、Niを2.0質量%を超えて添加したり、Crを1.0質量%を超えて添加したり、Bを0.005質量%を超えて添加すると、溶接金属に割れが発生しやすくなる。よって、Ni、Cr及びBを添加する場合は、それぞれNi:2.0質量%以下、Cr:1.0質量%以下、B:0.005質量%以下とする。
MgO、Li2O、Na2O、K2O、CaO、SrO及びBaOは、SiO2と融合して、スラグの粘性を低下させ、流動性を向上させる効果がある。ただし、MgO、Li2O、Na2O、K2O、CaO、SrO及びBaOの総含有量が0.80質量%を超えると、スラグ量が過多になり、排出効果よりも酸化物生成の方が上回る。このため、溶融金属7上に溜まる溶融スラグ8が厚くなり、溶接ワイヤ5が溶融スラグ8に埋まり、溶接金属9の歩留まりが変動して靭性が劣化する。よって、溶接ワイヤに、MgO、Li2O、Na2O、K2O、CaO、SrO及びBaOを添加する場合は、総含有量が0.80質量%以下になるようにする。なお、溶接ワイヤは、これらの酸化物のうち1種のみを含有していてもよく、また、2種以上を含有していてもよい。
本実施形態のエレクトロガスアーク溶接方法で使用する溶接ワイヤ(フラックス入りワイヤ)の成分組成における残部は、Fe及び不可避的不純物である。
溶接ワイヤに用いるフラックス入りワイヤの直径は1.5~3.5mmであることが好ましい。エレクトロガスアーク溶接において、直径1.5mm未満のワイヤを用いると、溶着量が多くなり、溶融金属位置が高くなるため、スラグ排出が抑制される。一方、直径が3.5mmを超えるワイヤを用いると、溶接電流が高くなり、大入熱となるため、得られる溶接金属の靭性が劣化しやすくなる。
溶接ワイヤに用いるフラックス入りワイヤは、フラックス充填率が15~30質量%であることが好ましい。フラックス充填率が15質量%未満のワイヤを用いると、溶着量の向上効果が得られず、ワイヤがスラグ浴に埋もれやすくなる。一方、フラックス充填率が30質量%を超えるワイヤを用いるとジュール熱効果が高くなり、溶滴移行が不安定になるため、突出し制御が困難となる。なお、ここでいう「フラックス充填率」は、外皮内に充填されるフラックスの質量を、ワイヤ全体(外皮とフラックスの合計)の質量に対する割合で規定したものである。
溶接ワイヤに用いるフラックス入りワイヤの外皮の材質は、ワイヤ全体の組成が前述した範囲内であればよく、軟鋼及びステンレス鋼のいずれでもよい。
本実施形態のエレクトロガスアーク溶接方法で使用する溶接ワイヤ(フラックス入りワイヤの製造方法は、特に限定されるものではなく、一般的な製造方法により製造したものを使用することができる。例えば、軟鋼又はステンレスからなる外皮をU字状に成形したものにフラックスを充填した後、筒状型に成形し、目的径まで伸線することにより製造することができる。
本実施形態のエレクトロアーク溶接に用いる摺動銅当金2は、開先に接触する面に曲率をもった溝12が設けられている。この摺動銅当金2の溝形状は、溶融スラグの排出に依存する。溝幅W及び溝深さDが大きいとスラグの排出は促進されるが、溶融金属の溶け落ち、及びスラグによってビードが均一に被覆されないことによるビード形状不良やスラグ巻き込みなどの溶接欠陥が発生する。
溝幅Wは、開先幅aに依存する。溝幅Wが、開先幅aの1.1倍未満の場合、ビード形状が不良となり、また、2.5倍を超えると、溶接金属の溶け落ちやビード形状不良が発生する。よって、溝幅Wは、開先幅aの1.1~2.5倍の範囲とする。
溝深さDが0.5mm未満の場合、溶接金属の歩留まりが変動し、靭性が劣化する。また、溝深さDが5.5mmを超えると、スラグがビード上に均一に乗らず、ビード形状不良やスラグ巻き込みきなどの溶接欠陥が発生する。よって、溝深さDは、0.5~5.5mmの範囲とする。
溝幅Wと溝深さDとの比(W/D)が5.0未満の場合、前述した組成のフラックス入りワイヤを使用しても、スラグの排出が滞り、溶接金属の歩留まりが変動し、靭性が劣化する。一方、溝幅Wと溝深さDとの比(W/D)が80.0を超えると、ビード形状不良やスラグ巻き込みなどの溶接欠陥が発生する。よって、溝幅Wと溝深さDとの比(W/D)は5.0~80.0とする。
摺動銅当金2の溝12の形状は、曲率を持った形状とする。これにより、良好なビード形状を維持することができる。溝12の曲率半径は、特に限定されるものではないが、30~180mmであることが好ましい。これにより、スラグにより均一に被覆して、ビード形状を更に向上させることができる。
溶接時の溶接ワイヤ5の突出し長さは、20~60mmとすることが好ましい。エレクトロガスアーク溶接において、溶接ワイヤ5の突出し長さが20mm未満の場合、溶接電流が高くなり、大入熱となるので、溶接金属の靭性が劣化する。一方、溶接ワイヤ5の突出し長さが60mmを超えると、ジュール熱効果が高くなり、溶滴移行が不安定になるため、後述する突出し長さを一定にする制御が困難となる。
図5は本実施形態のエレクトロガスアーク溶接方法で用いる溶接装置の構成例を示す図である。本実施形態のエレクトロガスアーク溶接方法は、前述した摺動銅当金2と、溶接トーチ4と、トーチ移動機構と、制御部とを少なくとも備えるエレクトロガスアーク溶接装置により実施することができる。エレクトロガスアーク溶接装置には、一般に、溶接電源25、ワイヤ送給装置26及びシールドガス供給機構などが設けられる。
被溶接材(母材1)の板厚は、特に限定されるものではなく、用途などに応じて適宜選択して使用することができる。なお、母材1が板厚32mmを超える厚板である場合は、溶接トーチ4をオシレートして溶接してもよい。その場合、ウィーバー角度設定機構、設定角度に維持できるウィーバー回転伝達駆動機構、トーチと溶接台車の成す角度を常に一定に保持するトーチ回転伝達機能、ウィービング動作伝達機構を有していることが好ましい。
本発明のエレクトロガスアーク溶接は、母材1の形状が前述したV開先の場合以外にも、すみ肉溶接にも適用することができる。図6はすみ肉溶接に適用する場合の溶接方法を示す断面図である。図6に示すように、すみ肉溶接を行う場合は、裏当材は不要である。そして、母材1の表面に摺動銅当金2を当接し、母材1と摺動銅当金2により囲まれる開先内に、シールドガスを供給しつつ溶接トーチから溶接ワイヤを送給し、溶接トーチ及び摺動銅当金を上昇させながらアーク溶接を行えばよい。その他の条件は、V開先の場合と同様である。
溶接電流:380A
アーク電圧:35V
溶接速度:8cm/分
入熱量:9.9kJ/mm
母材板厚:19mm
開先形状:V開先
開先角度:40°
ギャップ:5~10mm(ギャップは開先幅の調整に5~10mmに変化させた)
シールドガス:100%CO2
ビード外観は、溶接終了後のビードを目視で判断した。ビード蛇行、ハンピング及びオーバーラップなどのビード形状不良があった場合は×とし、正常な場合は○とした。
アーク安定性は、溶接中のアーク電圧値をデーターロガーで測定し、判断した。具体的には、設定電圧値に対して、±5V以上に、5秒間連続で電圧が変動した場合はアーク不安定とし×とし、5秒以内に収まっていた場合は○とした。また、±5V以上の変動が無い場合はさらに良好として◎とした。
溶接欠陥は放射線透過試験(RT:JIS Z 3104参照)に準拠した方法で行った。欠陥が確認できた場合は×、無かった場合は○とした。
溶接金属の靭性は、JIS Z 3128に基づき、-20℃のシャルピー吸収エネルギー(J)で評価した。具体的には、ビード断面中央から試料を抽出し、3回の平均の値をとった。JIS Z 3319のエレクトロガスアーク溶接用フラックス入りワイヤの規格では、-20℃のシャルピー吸収エネルギー(J)が40J以上であることから、40J未満の以下の場合は×、40Jを上回っていた場合は○、倍の80Jを上回る場合はさらに良好であると判断し、◎とした。
溶接は、図5に示す装置を用いて行った。先ず、溶接台車をレールに取り付け、母材に裏当材を取り付けた。フラックス入りワイヤをワイヤ送給装置に装着し、トーチ先端まで送給した。溶接始端部に溶接台車を移動させて、摺動式銅当金を母材に接触させ、摺動式銅当金のセンタリングを行った。トーチ調整部により、ワイヤの狙い角度、狙い位置を調整した。
2 摺動銅当金
3 裏当材
4 トーチ
5 ワイヤ
6 溶接金属
7 溶融金属
8 溶融スラグ
9 固着スラグ
12 溝
20 台車走行モータ駆動回路
21 走行モータ
22 台車
23 走行用レール
24 操作箱
25 溶接電源
26 ワイヤ送給装置
27 シールドガス
Claims (7)
- 被溶接材の開先表面に摺動銅当金を当接し、前記摺動銅当金及び溶接トーチを上昇させながらアーク溶接を行うエレクトロガスアーク溶接方法であって、
前記溶接ワイヤとして、
鋼製外皮内にフラックスが充填され、
ワイヤ全質量あたり、
C:0.01~0.50質量%、
Si:0.10~1.00質量%、
Mn:0.50~4.00質量%、
Mo:0.10~1.00質量%、
Ti:0.05~0.40質量%、
SiO2:0.10~1.00質量%、
を含有すると共に、
Al:0.30質量%以下(0%を含む)、
S:0.050質量%以下(0%を含む)、
P:0.050質量%以下(0%を含む)、
TiO2:0.30質量%以下(0%を含む)、
Al2O3:0.30質量%以下(0%を含む)、
に規制され、残部がFe及び不可避的不純物からなり、
SiO2含有量を[SiO2]、Si含有量を[Si]、Al2O3含有量を[Al2O3]、Al含有量を[Al]、TiO2含有量を[TiO2]、Ti含有量を[Ti]としたとき、下記数式(A)を満たす組成を有するフラックス入りワイヤを使用し、
前記摺動銅当金は、
前記開先に接触する面に曲率をもった溝を有し、
前記開先の幅をaとしたとき、
前記溝幅Wが(1.1×a)~(2.5×a)mm、
前記溝深さDが0.5~5.5mm、
前記溝幅Wと前記溝深さDとの比(W/D)が5.0~80.0であり、
前記溶接ワイヤの送給速度は一定にし、前記溶接ワイヤの突出し長さが一定になるように、溶接電流に基づいて前記溶接トーチの上昇速度を制御するエレクトロガスアーク溶接方法。 - 前記フラックス入りワイヤは、更に、ワイヤ全質量あたり、
Mg:0.50質量%以下、
Ni:2.0質量%以下、
Cr:1.0質量%以下、
B:0.005質量%以下
を含有する請求項1に記載のエレクトロガスアーク溶接方法。 - 前記フラックス入りワイヤは、更に、ワイヤ全質量あたり、MgO、Li2O、Na2O、K2O、CaO、SrO及びBaOのうち少なくとも1種の酸化物を、合計で0.80質量%以下含有する請求項1又は2に記載のエレクトロガスアーク溶接方法。
- 前記フラックス入りワイヤは、直径が1.5~3.5mmであり、フラックス充填率が15~30質量%である請求項1又は2に記載のエレクトロガスアーク溶接方法。
- 前記溶接トーチの上昇速度の制御は、
ローパスフィルターにより検出された溶接電流から高周波成分を除去する工程と、
前記ローパスフィルターを通過した溶接電流値と、予め設定された溶接電流指令値とを比較する工程と、を有し、
前記ローパスフィルターのカットオフ周波数を0.98~2.93Hzに設定する
請求項1又は2に記載のエレクトロガスアーク溶接方法。 - アーク電圧を周期的に変動させながら溶接を行う請求項1又は2に記載のエレクトロガスアーク溶接方法。
- 被溶接材の開先表面に当接される摺動銅当金と、
前記開先内に溶接ワイヤを送給する溶接トーチと、
前記溶接トーチを、溶接線に対して、前後方向、上下方向及び左右方向に移動させるトーチ移動機構と、
溶接電流に基づいて前記溶接トーチの上昇速度を制御する制御部と、
を有し、
前記摺動銅当金は、
前記開先に接触する面に曲率をもった溝を有し、
前記開先の幅をaとしたとき、
前記溝幅Wが(1.1×a)~(2.5×a)mm、
前記溝深さDが0.5~5.5mm、
前記溝幅Wと前記溝深さDとの比(W/D)が5.0~80.0
であるエレクトロガスアーク溶接装置。
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KR20240014753A (ko) | 2022-07-26 | 2024-02-02 | 현대제철 주식회사 | 일렉트로 가스 아크 용접 장치 및 이를 이용한 용접방법 |
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- 2015-07-21 BR BR112017001213A patent/BR112017001213A2/pt not_active Application Discontinuation
- 2015-07-21 CN CN201580038994.9A patent/CN106536114B/zh active Active
- 2015-07-21 RU RU2017101994A patent/RU2669668C2/ru active
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- 2015-07-21 EP EP15825056.3A patent/EP3173176A4/en not_active Withdrawn
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Also Published As
Publication number | Publication date |
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KR101994008B1 (ko) | 2019-06-27 |
RU2017101994A3 (ja) | 2018-08-28 |
BR112017001213A2 (pt) | 2017-11-28 |
EP3173176A1 (en) | 2017-05-31 |
SA517380725B1 (ar) | 2020-11-04 |
TW201622870A (zh) | 2016-07-01 |
EP3173176A4 (en) | 2018-05-02 |
TWI590906B (zh) | 2017-07-11 |
RU2669668C2 (ru) | 2018-10-12 |
RU2017101994A (ru) | 2018-08-27 |
SG11201700409TA (en) | 2017-02-27 |
CN106536114B (zh) | 2019-06-28 |
CN106536114A (zh) | 2017-03-22 |
JP2016030262A (ja) | 2016-03-07 |
JP6190774B2 (ja) | 2017-08-30 |
KR20170015522A (ko) | 2017-02-08 |
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