CN115870620A - Single-side butt welding method and method for manufacturing welded joint - Google Patents

Single-side butt welding method and method for manufacturing welded joint Download PDF

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Publication number
CN115870620A
CN115870620A CN202211011967.0A CN202211011967A CN115870620A CN 115870620 A CN115870620 A CN 115870620A CN 202211011967 A CN202211011967 A CN 202211011967A CN 115870620 A CN115870620 A CN 115870620A
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mass
less
heat source
flux
welding method
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迎井直树
八岛圣
中村敬人
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Kobe Steel Ltd
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Kobe Steel Ltd
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    • 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
    • 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
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/20—Bonding
    • B23K26/21—Bonding by welding
    • 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
    • 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
    • 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
    • B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • 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
    • B23K9/24—Features related to electrodes
    • B23K9/28—Supporting devices for electrodes
    • B23K9/29—Supporting devices adapted for making use of shielding means
    • B23K9/291—Supporting devices adapted for making use of shielding means the shielding means being a gas
    • B23K9/295—Supporting devices adapted for making use of shielding means the shielding means being a gas using consumable electrode-wire
    • 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
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/18—Sheet panels

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Optics & Photonics (AREA)
  • Nonmetallic Welding Materials (AREA)
  • Arc Welding In General (AREA)
  • Butt Welding And Welding Of Specific Article (AREA)
  • Laser Beam Processing (AREA)

Abstract

The invention relates to a single-side butt welding method and a manufacturing method of a welded joint. Provided is a single-side butt welding method which can achieve deep penetration, can obtain a large deposition amount, can suppress thermal deformation, and can reduce the amount of spatter generated. A single-side butt welding method for welding a butt joint part (2) by butting a pair of steel plates and arranging a backing flux from the lower side of a butt joint part (2) formed between the pair of steel plates, and relatively moving a 1 st heat source and a 2 nd heat source with respect to the pair of steel plates from the upper side of the butt joint part (2) while holding a preceding arc (7 b) as a 1 st heat source and a laser (8 a) as a 2 nd heat source following the 1 st heat source so that the interval in the longitudinal direction of the butt joint part (2) is within an arbitrary range, wherein one of the 1 st heat source and the 2 nd heat source is a gas metal arc heat source using a flux cored wire (7 a) containing a slag former, and the other is a laser heat source.

Description

Single-side butt welding method and method for manufacturing welded joint
Technical Field
The present invention relates to a welding method for butt-welding steel plates from one side and a method for manufacturing a welded joint.
Background
In the field of shipbuilding and the like, a jointed plate butt joint process with a long welding line is performed, but in a welding method for welding from both sides of a steel plate, it is necessary to turn over a base material or perform overhead welding after one-side welding is completed. Therefore, this jointed board butt-joining step causes a reduction in work efficiency, and studies have been made to increase the efficiency of the jointed board butt-joining step.
For example, patent document 1 discloses a single-side submerged arc welding method using 3 or more electrodes using a copper plate and flux as a backing. Patent document 2 discloses a multi-electrode single-side submerged arc welding method in which the current value of the 1 st electrode is designed based on the filling ratio of the filler with respect to the groove cross-sectional area.
As described in patent documents 1 and 2, when submerged arc welding is performed by arranging a plurality of solid-core welding wires in parallel, a large deposition amount can be obtained, and the welding speed can be increased. Further, by lining with flux, burning through of the weld metal can be prevented, and a sound joint can be obtained.
However, since submerged arc welding with a plurality of solid wires is high heat input welding, thermal deformation after welding becomes a problem. Further, since beveling is required, the bevel cross-sectional area is increased, and a large amount of deposited metal is required.
Therefore, patent document 3 discloses a butt welding method for laser welding at least the butted portions of the metal plate materials. Patent document 3 describes that in welding using a laser beam with a groove minimized, welding with a narrow width and a deep penetration can be performed, resulting in a reduced linear energy and a welded joint with a small thermal strain can be efficiently produced.
Patent document 3 also discloses hybrid laser-arc welding using a laser and an arc together.
Documents of the prior art
Patent document
Patent document 1: japanese patent No. 2860060
Patent document 2: japanese patent laid-open No. 2007-268551
Patent document 3: international publication No. 2017/099004
Disclosure of Invention
Problems to be solved by the invention
However, according to the welding method described in patent document 3, there is a problem that a large amount of large particles are attached to the weld base material surface (welding surface) in the vicinity of the weld bead. The welded portion having large spatters adhered thereto is aesthetically unpleasing and causes defects in the painting process, and thus there is a need to remove spatters after welding. Therefore, the adhesion of a large amount of spatter leads to an increase in working costs.
The present invention has been made in view of the above problems, and an object thereof is to provide a single-side butt welding method and a method for manufacturing a welded joint, which can perform construction at a high welding speed (hereinafter, also referred to as high-speed weldability) with deep penetration, suppress thermal deformation, and reduce the amount of spatter generated.
Means for solving the problems
The present inventors have intensively studied a welding method capable of suppressing the amount of spatter generated by laser welding while ensuring deep penetration, excellent high-speed weldability, and suppression of thermal deformation, which are advantages of laser welding. As a result, it was found that the amount of spatter generated can be greatly reduced by using a gas metal arc heat source using a flux-cored wire containing a slag former as one heat source and another heat source.
The present invention has been made based on these findings.
The above object of the present invention can be achieved by the following constitution [1] of the single-side butt welding method.
[1] A one-side butt welding method, characterized by comprising a step of welding a pair of steel plates by butting the steel plates and arranging the steel plates substantially horizontally, a step of arranging a backing flux from the lower side of a butting portion formed between the steel plates, a step of holding a preceding 1 st heat source and a 2 nd heat source following the 1 st heat source so that the interval in the longitudinal direction of the butting portion is within an arbitrary range, and a step of relatively moving the 1 st heat source and the 2 nd heat source with respect to the steel plates from the upper side of the butting portion,
wherein one of the 1 st heat source and the 2 nd heat source is a gas metal arc heat source using a flux-cored wire containing a slag former,
the other of the 1 st heat source and the 2 nd heat source is a laser heat source,
the flux-cored wire contains the slag former in an amount of 2.5 mass% or more relative to the total mass of the wire.
Further, preferred embodiments of the present invention relating to the one-side butt welding method relate to the following [2] to [15].
[2] The single-side butt welding method according to item [1], wherein the content of the slag former is 18.0 mass% or less with respect to the total mass of the welding wire.
[3] The one-sided butt welding method according to [1] or [2], characterized in that the slag former contains, relative to the total mass of the welding wire:
TiO 2 :2.0 to 15.0 mass%;
SiO 2 :0.25 to 2.0 mass%;
ZrO 2 :0.15 mass% or more and 1.0 mass% or less;
Na 2 O、K 2 o and Li 2 Total amount of O: 0.02 mass% or more and 0.50 mass% or less, and
MnO: 0.50% by mass or less (including 0% by mass),
Al 2 O 3 : 0.50% by mass or less (including 0% by mass),
metal fluoride: 0.50 mass% or less (including 0 mass%).
[4] The one-sided butt welding method according to any one of [1] to [3], characterized in that,
the components of the flux-cored wire except the slag former are added into the flux-cored wire,
c:0.5 mass% or less of a surfactant,
si:2.0 mass% or less of a surfactant,
mn:3.0 mass% or less of a polymer,
ni:5.0 mass% or less of a surfactant,
mo:3.0 mass% or less of a polymer,
w:3.0 mass% or less of a nitrogen-containing gas,
nb:3.0 mass% or less of a polymer,
v:3.0 mass% or less of a polymer,
cr:5.0 mass% or less of a surfactant,
ti:3.0 mass% or less of a polymer,
al:3.0 mass% or less of a polymer,
mg:3.0 mass% or less of a polymer,
n:0.05 mass% or less of a surfactant,
s:0.05% by mass or less of a surfactant,
p:0.05 mass% or less of a surfactant,
b:0.005% by mass or less of a crystalline,
cu:2.0 mass% or less of a surfactant,
ta:3.0 mass% or less of a polymer,
REM:0.1 mass% or less, and
alkali metal: 3% by mass or less of a surfactant,
the balance being Fe and unavoidable impurities.
[5] The single-sided butt welding method according to any one of [1] to [4], wherein the flux-cored wire is formed by filling a flux into an outer sheath, and the outer sheath is formed of a cold-rolled steel strip.
[6] The method of one-sided butt welding according to any one of [1] to [5], characterized in that the backing flux contains at least one of a metal powder and a slag former, and the balance is inevitable impurities.
[7] The method of single-side butt welding according to item [6], wherein the backing flux further contains at least one of a non-metal powder and a non-metal compound powder other than a slag former.
[8] The method of one-sided butt welding according to item [6] or item [7], wherein when the backing flux contains the metal powder in an amount of 90 mass% or more based on the total mass of the backing flux, the metal powder contains at least one of Si powder and Fe-Si powder, and the Si content in the Si powder and the Fe-Si powder is 0.5 mass% or more and 50 mass% or less based on the total mass of the backing flux.
[9] The method of one-sided butt welding according to [6] or [7], wherein when the backing flux contains the slag former in an amount of more than 10% by mass relative to the total mass of the backing flux, the slag former contains a metal oxide and a metal fluoride, and the balance is unavoidable impurities.
[10] The method of one-sided butt welding according to any one of [6] to [9], wherein when the backing flux contains the slag former, the backing flux is formed by kneading a raw material with water glass, shaping the raw material into particles, and sintering the particles.
[11] The one-sided butt welding method according to any one of [1] to [10], characterized in that the 1 st heat source is a gas metal arc heat source and the 2 nd heat source is a laser heat source.
[12] The one-side butt welding method according to any one of [1] to [11], wherein a distance between a target position of the 1 st heat source and a target position of the 2 nd heat source is 0mm or more and 10.0mm or less.
[13] The one-side butt welding method according to any one of [1] to [12], wherein an energy radiation angle of the 1 st heat source is 45 ° or more and 80 ° or less with respect to a welding proceeding direction of the butted portion,
an energy radiation angle of the 2 nd heat source is 90 ° or more and 135 ° or less with respect to a welding proceeding direction of the butting portion.
[14]According to [1]～[13]The one-side butt welding method according to any one of the above methods, wherein the laser heat source is vibrated in a width direction with respect to a longitudinal direction of the butted portion, and an amplitude of the laser heat source in the width direction is defined as "a L (mm) frequency f L (Hz), and the width of the grooves of the pair of steel plates at the target position of the laser heat source is set to G L (mm) is satisfied
2a L ≤G L +1, and
f L ≤10。
[15]according to [1]～[14]The one-side butt welding method according to any one of the above methods, wherein the gas metal arc heat source is vibrated in a width direction with respect to a longitudinal direction of the butt portion, and an amplitude of the gas metal arc heat source in the width direction is defined as "a A (mm) frequency f A (Hz), and the width of the grooves of the pair of steel plates at the target position of the gas metal arc heat source is set to G A (mm) is satisfied
2a A ≤G A +1, and
f A ≤10。
the above object of the present invention is the following [16] regarding a method for manufacturing a welded joint.
[16] A method of manufacturing a welded joint, characterized in that the welded joint is manufactured by using the one-side butt welding method according to any one of [1] to [15].
Effects of the invention
According to the present invention, it is possible to provide a single-side butt welding method and a method for manufacturing a welded joint, which can perform construction at a high welding speed with deep penetration, and can suppress thermal deformation and reduce the amount of spatter generated.
Drawings
Fig. 1 is a schematic view showing an example of a single-side butt welding method according to an embodiment of the present invention.
Fig. 2 is a side view of a typical configuration of a heat source.
Fig. 3 is a schematic diagram for explaining welding conditions in the present embodiment.
FIG. 4 is a photograph showing a substitute for the drawing showing the state of welding in test No. 1.
FIG. 5 is a photograph showing the surface condition of the welded joint of test No.1 in an alternative drawing.
FIG. 6 is a photograph showing a substitute for the drawing showing the state of welding in test No. 6.
Description of the symbols
1a, 1b Steel plate
2. Butt joint part
3. Weld metal
4. 5 slag of smelting
7a flux-cored wire
7b arc
8a laser
10. Flux column
11. Gasket flux
21. Splash is generated
Detailed Description
Hereinafter, embodiments of the present invention will be described in detail. The present invention is not limited to the embodiments described below, and can be implemented by being arbitrarily changed within a range not departing from the gist of the present invention.
[1. Single-side butt welding method ]
The single-side butt welding method of the present embodiment is a method of butt-welding a pair of steel plates to be arranged substantially horizontally, A welding method for welding a butted portion formed between a pair of steel plates by closely contacting a backing flux from the lower side of the butted portion and welding the butted portion from the upper side of the butted portion. As the heat sources, the 1 st heat source that precedes and the 2 nd heat source that follows the 1 st heat source are used. Then, the 1 st heat source and the 2 nd heat source are held so that the interval in the longitudinal direction of the butting portion is within an arbitrary range, and are moved relative to the pair of steel plates, whereby welding between the steel plates is performed.
One of the 1 st heat source and the 2 nd heat source is a gas metal arc heat source using a flux-cored wire containing a slag former, and the other of the 1 st heat source and the 2 nd heat source is a laser heat source.
An example of the single-side butt welding method according to the present embodiment will be described below with reference to fig. 1 and 2. Fig. 1 is a schematic diagram showing an example of a single-side butt welding method according to an embodiment of the present invention, and fig. 2 is a side view of a typical arrangement of a heat source. As shown in fig. 1, a pair of steel plates 1a and 1b are butted and horizontally arranged at an arbitrary groove width G, and a backing flux 11 is arranged below the butted portion 2. The pad flux 11 is pressed against the butting portion 2 side by the gas pressure in the air hose 13 via the under flux 12. The pad flux 11, the primer flux 12, and the air hose 13 are contained in a コ -shaped metal case 15. Further, the metal case 15 is supported by the pressure of the gas in the air hose 14 disposed therebelow and is brought close to the butting portion, thereby ensuring the pressing of the air hose 13 against the backing flux 11. Thus, the pad flux 11 is held at a predetermined position.
Next, an arc welding torch 7 using a flux-cored wire 7a and a laser welding horn 8 are disposed at an arbitrary interval above the butting portion 2. Then, in the butting portion 2, for example, an arc 7b is generated as a 1 st heat source, and for example, a laser 8a is irradiated as a 2 nd heat source to move both in a direction indicated by an arrow. That is, the arc 7b is preceded by the laser beam 8 a.
As a result, weld metal 3 coated with dross 4 and 5 is formed on the butted portion 2 and the upper and lower surfaces thereof, respectively, whereby the steel sheet 1a and the steel sheet 1b are joined.
In the above-described embodiment shown in fig. 1 and 2, the arc 7b as the gas metal arc heat source is set as the 1 st heat source and the laser light 8a as the laser light source is set as the 2 nd heat source following the 1 st heat source, but the present invention is not limited to this. That is, the laser light 8a may be advanced to follow the arc 7 b.
Hereinafter, a flux-cored wire, a backing flux, welding conditions, and the like that can be used in the single-side butt welding method according to the present embodiment will be described in detail.
< flux cored wire >
In the present embodiment, any one of the preceding 1 st heat source and the following 2 nd heat source is a gas metal arc heat source using a flux-cored wire containing a slag former. For convenience, the slag former, the metal powder, and the like are also included in the pad FLUX described later, and therefore, if the slag former, the metal powder containing an alloy, and the other non-metal compound are included in the FLUX-cored wire, they are expressed as slag former < FCW >, metal powder < FCW >, and compound < FCW >, respectively, and if the slag former, the metal powder containing an alloy, the non-metal powder, and the non-metal compound powder other than the slag former are included in the pad FLUX, they are expressed as slag former < FLUX >, metal powder < FLUX > and the like, non-metal powder < FLUX >, and non-metal compound powder other than the slag former < FLUX >.
( Slagging agent < FCW >: 2.5 to 18.0 mass% )
In the present embodiment, the slag former < FCW > is contained in the wire, thereby preventing spattering. If the slag former < FCW > in the wire is less than 2.5 mass% with respect to the total mass of the wire, the high-melting-point oxide in the flux is insufficient, and it is difficult to reliably form a flux column, and stable droplet transfer cannot be performed. If a solid wire is used, the droplet is ejected by the metal vapor generated by the laser used as the other heat source, and a large amount of large spatters are generated.
Therefore, the content of the slag former < FCW > is 2.5 mass% or more, preferably 3.0 mass% or more, and more preferably 3.4 mass% or more, based on the total mass of the wire.
On the other hand, if the slag former < FCW > in the wire is 18.0 mass or less based on the total mass of the wire, the sheath can be prevented from being thinned due to an increase in the amount of flux relative to the sheath of the wire, and production problems such as wire breakage during wire drawing can be prevented. Further, by controlling the amount of flux, a desired deposition amount can be obtained. Therefore, the content of the slag former < FCW > is preferably 18.0 mass% or less, more preferably 15.0 mass% or less, still more preferably 13.0 mass% or less, and particularly preferably 10.5 mass% or less, with respect to the total mass of the wire.
As mentioned above, the flux-cored wire contains a slag former < FCW >. In the present specification, the term "slag former" means a metal oxide powder, a composite oxide powder, a metal fluoride powder, and a composite fluoride powder, which are positively added to a welding wire. In the present embodiment, the components and the preferable content of the slag forming agent < FCW > which are preferably contained are specifically described below.
(TiO 2 :2.0 to 15.0 mass%)
Because of TiO 2 Is a high-melting component, so that TiO is contained in the welding wire in an appropriate content as a slag former < FCW > 2 The flux column is likely to remain and functions as an arc stabilizer, so that spatter can be reduced.
Therefore, tiO in the slag former < FCW > 2 The content of (b) is preferably 2.0 mass% or more, and more preferably 2.5 mass% or more, based on the total mass of the wire.
On the other hand, tiO in the case of slag formers < FCW > 2 If the content of (B) is more than 15.0 mass%, the resultant alloy may not be sufficiently melted during welding and may be carried into a molten pool to cause slag inclusion. Therefore, the slag former is TiO in < FCW > 2 The content of (b) is preferably 15.0 mass% or less, more preferably 13.0 mass% or less, and further preferably 10.5 mass% or less, based on the total mass of the wire.
(SiO 2 :0.25 mass% or more and 2.0 mass% or less)
SiO 2 With TiO 2 Is also a high-melting component, so that, as a slag former < FCW >, if SiO is contained in the welding wire in an appropriate amount 2 The flux column is likely to remain and functions as an arc stabilizer, so that spatter can be reduced.
Thus, siO in the slag former < FCW > 2 The content of (b) is preferably 0.25% by mass or more based on the total mass of the wire, and more preferably 0.30% by mass or more, and still more preferably 0.35% by mass or more in order to function as an arc stabilizer.
On the other hand, siO in the case of slag former < FCW > 2 When the content of (b) is 2.0% by mass or less, the slag removability can be further improved. Thus, siO in the slag former < FCW > 2 The content of (b) is preferably 2.0% by mass or less, more preferably 1.60% by mass or less, and still more preferably 1.10% by mass or less, based on the total mass of the wire.
(ZrO 2 :0.15 mass% or more and 1.0 mass% or less)
ZrO 2 With TiO 2 Also a high-melting component, as slag former < FCW >, if ZrO is contained in the welding wire in the right amount 2 Flux columns are liable to remain because of ZrO 2 Since the arc stabilizer functions, spatter can be reduced. In addition, zrO 2 Is a component that affects the meltability of slag and contributes to the shape of a weld beadThe improvement of (1).
Thus, in order to further improve the effect as an arc stabilizer, zrO in the slag former < FCW > 2 The content of (b) is preferably 0.15 mass% or more, and more preferably 0.19 mass% or more, based on the total mass of the wire.
On the other hand, in the case of a liquid, zrO in case of slag formers < FCW > 2 When the content of (b) is 1.0% by mass or less, the slag can be adjusted to a favorable fusibility for improving the bead shape. Thus, zrO in slag formers < FCW > 2 The content of (b) is preferably 1.0 mass% or less, more preferably 0.95 mass% or less, and further preferably 0.90 mass% or less, based on the total mass of the wire.
(Na 2 O、K 2 O and Li 2 Total amount of O: 0.02 mass% or more and 0.50 mass% or less)
Na 2 O、K 2 O and Li 2 O is a component having an effect of improving arc stability. In addition, na 2 O、K 2 O and Li 2 O is also a component that affects the meltability of slag, and contributes to the improvement of the bead shape. In the present embodiment, it is not necessary to contain Na in the wire 2 O、K 2 O and Li 2 All the components of O, preferably containing at least one of the above-mentioned alkali metal oxides, are preferably contained in amounts specified by the total amount thereof.
Na in the slag former < FCW > 2 O、K 2 O and Li 2 When the content of O is 0.02 mass% or more in total based on the total mass of the wire, the effect of improving arc stability can be obtained. Thus, na 2 O、K 2 O and Li 2 The total amount of O is preferably 0.02 mass% or more, more preferably 0.04 mass% or more, and still more preferably 0.05 mass% or more, based on the total mass of the wire.
On the other hand, na in the slag former < FCW > 2 O、K 2 O and Li 2 When the content of O is 0.50% by mass or less in total based on the total mass of the wire, the slag can be adjusted to a favorable fusibility for improving the bead shape. Thus, na 2 O、K 2 O and Li 2 The total amount of O is preferably 0.50 mass% or less, more preferably 0.20 mass% or less, and still more preferably 0.15 mass% or less, based on the total mass of the wire.
(MnO: 0.50% by mass or less (including 0% by mass))
MnO is a component that affects the meltability of slag, and when MnO is contained in an appropriate content in the wire as a slag forming agent < FCW >, the bead shape can be improved.
In the present embodiment, the content of MnO in the slag forming agent < FCW > may be 0 mass%, but in order to adjust the slag to a preferable fusibility for improving the bead shape, it is preferably 0.01 mass% or more, more preferably 0.02 mass% or more, with respect to the total mass of the wire.
On the other hand, if the MnO content in the slag former < FCW > is 0.50 mass% or less, the slag can be adjusted to a favorable fusibility for improving the bead shape. Therefore, the content of MnO in the slag former < FCW > is preferably 0.50 mass% or less, more preferably 0.30 mass% or less, and still more preferably 0.25 mass% or less, based on the total mass of the wire.
(Al 2 O 3 : 0.50% by mass or less (including 0% by mass)
Al 2 O 3 Is a component for adjusting the fusibility of slag, and has an effect of improving the shape of a weld bead during welding.
In the present embodiment, al in the slag former < FCW > 2 O 3 The content of (b) may be 0 mass%, but in order to adjust the slag to a favorable fusibility for improving the bead shape, it is preferably 0.01 mass% or more, more preferably 0.05 mass% or more, based on the total mass of the wire.
On the other hand, al in the case of slag formers < FCW > 2 O 3 When the content of (b) is 0.50% by mass or less, the slag can be adjusted to a favorable fusibility for improving the bead shape. Therefore, al in the slag former < FCW > 2 O 3 The content of (b) is preferably 0.50% by mass or less, more preferably 0.30% by mass or less,more preferably 0.15 mass% or less.
( Metal fluoride: 0.50% by mass or less (including 0% by mass) )
Metal fluorides, act on the slag's fusibility or act as arc stabilizers.
In the present embodiment, the content of the metal fluoride in the slag former < FCW > may be 0 mass%, but in order to further improve the action as an arc stabilizer, it is preferably 0.02 mass% or more, and more preferably 0.04 mass% or more, based on the total mass of the wire.
On the other hand, if the content of the metal fluoride in the slag former < FCW > is 0.50 mass% or less, the slag can be adjusted to a favorable fusibility for improving the bead shape. Therefore, the content of the metal fluoride in the slag former < FCW > is preferably 0.50 mass% or less, more preferably 0.40 mass% or less, and still more preferably 0.30 mass% or less, based on the total mass of the wire.
Further, as the metal fluoride, K is exemplified 2 SiF 6 、NaF、KF、CeF 3 、Na 3 AlF 6 、Na 2 SiF 6 、AlF 3 、MgF 2 、K 2 ZrF 6 And the like.
The flux-cored wire used in the welding method of the present embodiment is not particularly limited in terms of components other than the slag former < FCW > and may be appropriately adjusted depending on the application. Examples of suitable applications of the present embodiment include welding of mild steel, high tensile steel, low temperature steel, and weathering steel, which require deep penetration, high speed weldability, and low spatter. Therefore, any component of the flux-cored wire other than the slag former < FCW > is preferably JISZ3313:2009, or JISZ3320 for weathering steel: the same compositional range as the chemical compositional range of the deposited metal specified in 2012. In addition, in order to meet any application, it is also possible to add JISZ3313 for mild steel, high tensile steel or low temperature steel to the flux-cored wire in the general technical knowledge: 2009, or JISZ3320 for weathering steel: the welding workability was also improved by adjusting the mechanical properties by the composition other than the elements specified in 2012.
In the flux-cored wire used for mild steel, high tensile steel, low temperature steel, weathering steel, and the like, the composition of any component other than the slag former < FCW > is, for example, preferably C:0.5 mass% or less, si:2.0 mass% or less, mn:3.0 mass% or less, ni:5.0 mass% or less, mo:3.0 mass% or less, W:3.0 mass% or less, nb:3.0 mass% or less, V:3.0 mass% or less, cr:5.0 mass% or less, ti:3.0 mass% or less, al:3.0 mass% or less, mg:3.0 mass% or less, N:0.05 mass% or less, S:0.05 mass% or less, P:0.05 mass% or less, B:0.005 mass% or less, cu:2.0 mass% or less, ta:3.0% by mass or less, REM:0.1 mass% or less, and an alkali metal: 3% by mass or less.
In addition, these elements also include 0 mass% unless otherwise specified. In general, a flux-cored wire used for mild steel, high tensile steel, low temperature steel, weathering steel, and the like has an Fe-based alloy as a sheath.
Hereinafter, any component of the flux-cored wire that can be used in the present embodiment, that is, a component other than the slag former < FCW >, and the reason for the limitation thereof will be described in more detail. Unless otherwise specified, the contents of the respective components are expressed in mass% with respect to the total mass of the flux cored wire. Further, the non-metal component and the metal component (also referred to as an alloy component) such as C, P, S defined below are based on metal powder < FCW >, compound < FCW > and the like contained in a strip (metal strip) and flux of a flux-cored wire.
(C: 0.5% by mass or less)
C is a component that affects the strength of the weld metal, and the strength increases as the content increases. The content of C in the wire is preferably 0.5 mass% or less, and more preferably 0.2 mass% or less, in order to satisfy the strength range required for common steel grades such as mild steel, high tensile steel, and low temperature steel. On the other hand, the content of C is preferably 0.001 mass% or more for adjusting the strength.
(Mn: 3.0% by mass or less)
Mn is a component that affects the strength and toughness of the weld metal. In order to satisfy the mechanical properties required for steel grades in common use such as mild steel, high tensile steel, and low temperature steel, the content of Mn in the wire is preferably 3.0 mass% or less, and more preferably 2.5 mass% or less. On the other hand, the Mn content is preferably 0.5 mass% or more.
(Si: 2.0 mass% or less)
Si functions as a deoxidizer of the weld metal, reduces the oxygen content in the weld metal, and is a component contributing to improvement of toughness. In order to satisfy the mechanical properties required for a steel grade commonly used, such as mild steel, high tensile steel, and low temperature steel, the content of Si in the wire is preferably 2.0 mass% or less, more preferably 1.2 mass% or less, and still more preferably 1.0 mass% or less. On the other hand, the content of Si is preferably 0.1 mass% or more.
(Ni: 5.0 mass% or less)
Ni is a component for stabilizing the austenite composition of the weld metal and improving the low-temperature toughness, and is a component capable of adjusting the amount of crystallization of the ferrite composition. The Ni content in the wire is preferably 5.0 mass% or less, and more preferably 3.0 mass% or less. On the other hand, when used for welding low-temperature steel or the like, the Ni content is preferably 0.20 mass% or more.
(Mo: 3.0% by mass or less)
Mo is a component for improving high-temperature strength and pitting corrosion resistance. The content of Mo in the wire is preferably 3.0 mass% or less, and more preferably 2.0 mass% or less, in order to satisfy the mechanical properties required for steel grades in general use such as mild steel, high tensile steel, and low temperature steel. On the other hand, when used for welding high tensile steel, heat resistant steel, or the like, the content of Mo is preferably 0.10 mass% or more.
(W: 3.0% by mass or less)
W is a component for improving the high-temperature strength and pitting corrosion resistance. In order to satisfy the mechanical properties required for steel grades in common use such as mild steel, high tensile steel, and low temperature steel, the W content in the wire is preferably 3.0 mass% or less, and more preferably 2.0 mass% or less.
(Nb: 3.0 mass% or less)
Nb is a component that affects mechanical properties such as strength. The content of Nb in the wire is preferably 3.0 mass% or less, and more preferably 2.0 mass% or less, in order to satisfy the mechanical properties required for steel grades in general use such as mild steel, high tensile steel, and low temperature steel.
(V: 3.0% by mass or less)
V exerts an effect of improving the strength of the weld metal, while it reduces toughness and crack resistance. Therefore, the content of V in the wire is preferably 3.0 mass% or less, and more preferably 2.0 mass% or less.
(Cr: 5.0% by mass or less)
Cr is a component that affects mechanical properties such as strength of the weld metal. The content of Cr in the wire is preferably 5.0 mass% or less, and more preferably 3.0 mass% or less, in order to satisfy the mechanical properties required for steel grades in general use, such as mild steel, high tensile steel, and low temperature steel. In addition, when used for heat-resistant steel or the like, the content of Cr is preferably 0.10 mass% or more.
(Ti: 3.0% by mass or less)
Ti is a component that contributes to grain refinement by bonding with C, N and mainly improves the toughness of the weld metal. In a steel type commonly used for mild steel, high tensile steel, low temperature steel, and the like, when Ti is contained in the wire for the purpose of improving toughness, the content of Ti in the wire is preferably 3.0 mass% or less, and more preferably 1.0 mass% or less. The content of Ti is preferably 0.01 mass% or more.
(Al: 3.0% by mass or less)
Al is a deoxidizing component, and has the effect of reducing the amount of dissolved oxygen in the weld metal and reducing the amount of occurrence of porosity defects. In a steel type commonly used for mild steel, high tensile steel, low temperature steel, and the like, when Al is contained in the wire for the purpose of improving toughness, the content of Al in the wire is preferably 3.0 mass% or less, more preferably 1.0 mass% or less, and still more preferably 0.5 mass% or less. The content of Al is preferably 0.01 mass% or more, more preferably 0.05 mass% or more, and still more preferably 0.10 mass% or more.
(Mg: 3.0% by mass or less)
Mg is a deoxidizing component as in Al, and has the effect of reducing the amount of dissolved oxygen in the weld metal and reducing the amount of porosity defects.
In the present embodiment, the content of Mg in the wire may be 0 mass%, but when Mg is contained in the wire for the purpose of improving toughness in a steel type commonly used such as mild steel, high tensile steel, low temperature steel, or the like, the content of Mg in the wire is preferably 3.0 mass% or less, more preferably 1.0 mass% or less, and still more preferably 0.5 mass% or less. The Mg content is preferably 0.01 mass% or more, and is preferably 0.10 mass% or more, and more preferably 0.20 mass% or more, based on the total mass of the wire.
(N: 0.05% by mass or less)
N is a component that increases the strength by interstitial solid solution in the crystal structure. On the other hand, N also causes a void defect such as a void or a pit in the weld metal, and is not positively added unless strength is particularly required. Therefore, the content of N in the wire is preferably 0.05 mass% or less, and more preferably 0.03 mass% or less. The content of N is preferably 0.0010 mass% or more.
(S: 0.05% by mass or less)
S reduces the viscosity and surface tension of the droplet when the wire is melted, and smoothes the droplet transition, thereby exerting the effect of reducing the spatter and improving the welding workability, and on the other hand, is an element that reduces the crack resistance. Therefore, the content of S in the wire is preferably 0.05 mass% or less, and more preferably 0.03 mass% or less. The content of S is preferably 0.0005 mass% or more.
(P: 0.05% by mass or less)
P is an element that reduces crack resistance and mechanical properties of the weld metal, and therefore the content of P in the wire is preferably suppressed to 0.05 mass% or less, more preferably 0.03 mass% or less.
(B: 0.005 mass% or less)
B is an element for preventing the toughness from being lowered by nitrogen in the weld metal and for lowering the crack resistance. Therefore, the content of B in the wire is preferably 0.005 mass% or less, and more preferably 0.003 mass% or less. When B is contained in the wire for the purpose of securing toughness, the content of B is preferably 0.0005 mass% or more.
(Cu: 2.0 mass% or less)
Cu is an element contributing to the improvement of the strength and weather resistance of the weld metal. The Cu content in the wire is preferably 2.0 mass% or less, and more preferably 1.0 mass% or less, in order to satisfy strength and weather resistance in the range required for steel grades commonly used, such as mild steel, high tensile steel, and low temperature steel. When Cu is contained in the wire for the purpose of securing the strength and weather resistance of the weld metal, the content of Cu is preferably 0.01% by mass or more.
(Ta: 3.0% by mass or less)
Ta is the force influencing strength chemical properties and (4) elements. The content of Ta in the wire is preferably 3.0 mass% or less, more preferably 2.0 mass% or less, in order to satisfy the mechanical properties required for common steel grades such as mild steel, high tensile steel, and low temperature steel.
(total amount of REM:0.1% by mass or less)
REM (Rare Earth Metals) means Rare Earth elements, and Ce and La are exemplified. REM has a high affinity for S, suppresses grain boundary segregation of S, and also exhibits an effect of suppressing thermal cracking due to S. On the other hand, as for the arc stability, the smaller the amount of REM added, the more preferable, the total content of REM in the wire is 0.1 mass% or less, and more preferably 0.05 mass% or less, in order to satisfy the required crack resistance and arc stability.
(total of alkali metals: 3% by mass or less)
The alkali metal element functions as an arc stabilizer. The alkali metal in the present embodiment is based on metal powder < FCW > and compound < FCW > containing one or more alkali metal elements. The alkali metal element includes K, li, na, and the like. The total content of alkali metals in the wire means the total content of alkali metals in the wire in terms of metal powder < FCW > and compound < FCW > consisting of alkali metal elements. From the viewpoint of easy adjustment to the fusibility preferable for improving the bead shape, the total amount of alkali metals in the wire is preferably 3 mass% or less, more preferably 2 mass% or less, based on the total mass of the wire.
(balance: fe and unavoidable impurities)
In the flux-cored wire of the present embodiment, the balance other than the slag former < FCW > and the above elements is preferably Fe and inevitable impurities.
The content of the balance Fe is preferably 80 mass% or more, and preferably 98 mass% or less. The term "impurity" means not intended to be added, and examples of elements other than those described above include Sn, co, sb, and As. When the above element is contained as an oxide, O is also included in the balance. The content of impurities in the wire is preferably 0.5 mass% or less in total, and more preferably 0.3 mass% or less.
In addition, the flux-cored wire that can be used in the present embodiment is one in which the flux is filled in the outer sheath, and from the viewpoint of practicality and economy, the outer sheath is preferably formed of a cold-rolled steel strip. As the cold-rolled steel strip, for example, JISG3141:2017, and the like under the type designations SPCC, SPCD, SPCE, SPCF, SPCG, and the like.
Therefore, as described above, at least the following is preferable as the flux-cored wire that can be used in the present embodiment.
That is, a flux-cored wire having a flux filled in the inside of a steel sheath, wherein the following flux-cored wire is preferably used:
the flux contains a slag former < FCW > 2.50% or more and 18.0% or less in mass% based on the total mass of the flux-cored wire,
chemical components except for the slag former < FCW > are calculated by mass percent relative to the total mass of the flux-cored wire as C:0.5% or less, si:2.0% or less, mn:3.0% or less, ni:5.0% or less, mo:3.0% or less, W:3.0% or less, nb:3.0% or less, V:3.0% or less, cr:5.0% or less, ti:3.0% or less, al:3.0% or less, mg:3.0% or less, N:0.05% or less, S:0.05% or less, P:0.05% or less, B:0.005% or less, cu:2.0% or less, ta:3.0% or less, REM: less than 0.1%, and alkali metal: less than 3%, and the balance Fe and inevitable impurities.
< gasket flux >
In the present embodiment, the FLUX for gasket preferably contains at least one of metal powder < FLUX > and slag former < FLUX > with the balance being unavoidable impurities. The pad FLUX may further contain at least one of non-metal powder < FLUX > and non-metal compound powder < FLUX > other than the slag former. Examples of the metal powder < FLUX > include Fe powder, si powder, fe-Mn powder, fe-Al powder, and mixtures thereof, examples of the non-metal powder < FLUX > include graphite, and examples of the non-metal compound powder < FLUX > other than the slag former include carbides, nitrides, and sulfides other than the slag former.
The FLUX for gasket may be a metallic FLUX containing metal powder < FLUX > 90 mass% or more based on the total mass of the FLUX for gasket, or an actively added FLUX containing slag former < FLUX > 10 mass% or more based on the total mass of the FLUX for gasket, and may be used in various ways according to the intended use. Further, since the metallic flux has an effect of reducing oxygen in the weld metal, the metallic flux may be selected when the mechanical properties of the weld metal are important, and the slag flux may be positively added when the back bead shape and the slag removability are important.
The following describes a metallic flux and an active slag-added flux.
< solder of metal type >
The metal type FLUX contains the rest part of less than 10 mass% except for metal powder < FLUX >, slag former < FLUX >, non-metal powder < FLUX > and non-metal compound powder < FLUX > except for slag former, and the rest is impurity. In addition, if the slag removability is improved, the slag former < FLUX > described in detail later is loweredThe amount of the non-metallic powder is adjusted within a range of 10 mass%, and if the mechanical properties are improved, the amount of the non-metallic powder < FLUX > and the amount of the non-metallic compound powder < FLUX > excluding the slag former are adjusted within a range of 5 mass% or less in total. In other words, slagging agent < FLUX ＞ Non-metal powder < FLUX > and non-metal compound powder < FLUX > except for the slag former are not necessary and can be used as metal powder and residual impurities. The main elements constituting the non-metal powder and the non-metal compound powder other than the slag former include C, N, S, and the total amount of C, N, S is preferably adjusted to be 5 mass% or less.
The element contained in the metal powder < FLUX > preferably contains Si, more preferably further contains Mn and Fe, and still more preferably consists of only Si, mn and Fe. Next, si, mn, and Fe contained in the metal powder will be described in detail.
( Si in the pad flux: 0.5 to 50 mass% )
When Si is contained in the backing flux, the shape of the back bead can be stabilized, and an effect of smoothing the appearance can be obtained. If the content of Si in the Si powder and Fe — Si powder contained as the metal powder < FLUX > in the backing FLUX is 0.5 mass% or more based on the total mass of the backing FLUX, the appearance of the back bead can be improved. Therefore, the content of Si in the backing flux is preferably 0.5 mass% or more, and more preferably 1.5 mass% or more, based on the total mass of the backing flux.
On the other hand, if the Si content of the Si powder and the Fe — Si powder contained as the metal powder < FLUX > in the backing FLUX is 50 mass% or less with respect to the total mass of the backing FLUX, surface cracks caused by the excessive Si content in the back bead can be reduced. Therefore, the content of Si in the backing flux is preferably 50 mass% or less, more preferably 25 mass% or less, and still more preferably 10 mass% or less, with respect to the total mass of the backing flux.
(Mn in the backing solder: 50% by mass or less)
Mn has an effect of improving hardenability, and is an effective component for improving mechanical properties. Therefore, the backing flux of the present embodiment may be contained for adjusting the mechanical properties as needed, and the lower limit is not critical. In consideration of adjustment of mechanical properties expected to be applied to mild steel, high tensile steel, or low temperature steel, the adjustment is preferably performed in a range of 50 mass% or less. In addition to Mn alone, mn may be added to the flux in the form of an alloy such as Fe — Mn.
(Fe in the backing flux: 99.5 mass% or less)
Since Fe can increase the apparent density of the flux, if dust resistance is required, fe may be added as needed, and the lower limit is not critical. Since Fe can also reduce the alloy cost of the weld metal, the remaining metal powder may be Fe in addition to Si and Mn described above from the viewpoint of cost. As described above, if Si is 0.5 mass% or more, the appearance of the back bead can be improved, and therefore, from the viewpoint of the appearance of the back bead, if Fe is at least 99.5 mass% or less, it is preferable.
Fe may be added to the pad flux as an alloy of Fe-Mn, fe-Si, or the like, in addition to Fe alone.
In the present embodiment, the FLUX for gasket may contain a slag former < FLUX > in addition to the above metal powder < FLUX >. When the backing FLUX contains the slag former < FLUX >, the back bead is protected by the slag, and the slag is peeled off, so that a glossy and good appearance can be obtained. Also, it is preferable that the slag former < FLUX > contain metal oxides and metal fluorides, and the balance is inevitable impurities.
Examples of the metal oxide that can be contained in the slag former < FLUX > include TiO 2 、SiO 2 、ZrO 2 、MnO、Al 2 O 3 、Na 2 O、K 2 O、Li 2 And O. Further, as the metal fluoride which can be contained in the slag former < FLUX >, K is exemplified 2 SiF 6 、NaF、KF、CeF 3 、Na 3 AlF 6 、Na 2 SiF 6 、AlF 3 、MgF 2 、K 2 ZrF 6 And the like. And alsoWhen an aggressive fluxing agent to be described later is used, tiO is preferably used in mass% based on the total mass of the backing agent 2 :2.00% to 16.00% of SiO 2 :5.00% or more and 20.00% or less, zrO 2 :3.00% to 9.00% of Al 2 O 3 :3.00% or more and 9.00% or less, na 2 O、K 2 O and Li 2 Total of O: less than 3.00%, K 2 SiF 6 、NaF、KF、CeF 3 、Na 3 AlF 6 、Na 2 SiF 6 、AlF 3 、MgF 2 And K 2 ZrF 6 The sum of (A) and (B): 35.00% or less.
< active addition of flux to slag >
Further, the higher the content of the slag former < FLUX > in the gasket FLUX, the better the slag releasability. Therefore, when the FLUX for a pad is positively added with slag, the content of the slag former < FLUX > in the FLUX for a pad is preferably more than 10 mass%, more preferably 14.0 mass% or more, based on the total mass of the FLUX for a pad. The upper limit of the content of the slag former < FLUX > is not critical, and as components other than the slag former < FLUX >, metal powder, non-metal elements, and non-metal compound powder other than the slag former may be added as necessary. For example, as described above, the content of Si contained in the metal powder is preferably 0.5 mass% or more with respect to the total mass of the backing FLUX from the viewpoint of stabilization of the back bead shape, and therefore, the content of the slag forming agent < FLUX > may be 99.5 mass% or less when both slag removability and stabilization of the back bead shape are desired. The elements, slag former, and the like contained in the metal powder have the same effects as those described in detail in the above-described metal-based flux.
In the present embodiment, when the FLUX for gasket contains the above-mentioned slag former < FLUX >, the FLUX for gasket is preferably formed by kneading raw materials with water glass, shaping the raw materials into particles, and then sintering the particles. The fine powder backing flux may scatter to deteriorate the working environment, and may segregate due to vibration to cause variations in the welding result.
On the other hand, the backing flux obtained by sintering after forming into a granular form is not easily scattered and hardly segregated, and therefore, can be suitably used.
< welding conditions >
Next, the 1 st heat source and the 2 nd heat source following the first heat source will be described in more detail, as well as the welding conditions of the heat sources.
(Heat sources 1 and 2.)
In the present embodiment, it is preferable that the 1 st heat source in the preceding is a gas metal arc heat source, and the 2 nd heat source following it is a laser heat source. By radiating a laser heat source on a molten pool obtained by a gas metal arc heat source, even if there is a gap (groove width G is higher than 0 mm), heat is not allowed to escape to a gasket flux, and heat is easily conducted to a bevel surface, so that a sound joint can be easily obtained.
( Distance between target position P1 of 1 st heat source and target position P2 of 2 nd heat source: 0mm to 10.0mm inclusive )
Fig. 3 is a schematic diagram for explaining the welding conditions in the present embodiment. In fig. 3, a steel plate 1a is disposed in abutment with a steel plate not shown, thereby constituting an abutment portion 2. In addition, the welding torch 17 is advanced and the laser welding head 18 follows the welding torch 17.
If the distance (P1-P2 pitch) between the target position P1 of the 1 st heat source generated from the welding torch 17 and the target position P2 of the 2 nd heat source generated from the laser welding head 18 is slightly separated, the droplet separated from the flux-cored wire can be dropped without being disturbed by the laser. On the other hand, the melting efficiency can be improved by making the P1-P2 pitches close.
In the present embodiment, the 1 st heat source and the 2 nd heat source are held so that the interval in the longitudinal direction of the butting portion is within an arbitrary range. The 1 st heat source and the 2 nd heat source are normally moved while keeping a constant distance, but the interval between the 1 st heat source and the 2 nd heat source may be increased or decreased within an arbitrary range in consideration of the deflection of the apparatus and the like. The arbitrary range specifically means a range in which a heat source following a molten pool melted by a preceding 1 st heat source enters during a melting period.
Specifically, the P1-P2 pitch is preferably 0mm or more, and more preferably 2mm or more. The P1-P2 pitch is preferably 10.0mm or less, more preferably 7mm or less.
(energy radiation angle θ of No.1 Heat Source 1 : more than 45 degrees and less than 80 degrees)
(energy radiation angle θ of No.2 Heat Source 2 : more than 90 degrees and less than 135 degrees)
The 1 st heat source and the 2 nd heat source can efficiently input heat in the depth direction of the butting portion 2 by disposing the welding torches 17 and 18 so as to be perpendicular to the horizontally disposed steel plate 1 a. However, in order to avoid interference between the welding torch 17 and the welding torch 18, the angle of the welding torches 17 and 18 is in an appropriate range because of the problem of interference of the apparatuses.
Angle of welding torch 17 where 1 st heat source occurs in advance, i.e., energy radiation angle θ of 1 st heat source 1 Preferably, the angle is 45 ° or more and 80 ° or less with respect to the welding traveling direction of the butting portion 2.
In addition, the angle of the welding torch 18 where the 2 nd heat source occurs following the 1 st heat source, that is, the energy radiation angle θ of the 2 nd heat source 2 Preferably, the angle is 90 ° or more and 135 ° or less with respect to the welding traveling direction of the butting portion 2.
The energy radiation angle is an angle formed by an extension line of the shaft center of the 1 st heat source and the 2 nd heat source and a weld line in the weld traveling direction.
(2a L ≤GL+1，f L ≤10)
Since laser welding using a laser heat source has high energy density and can obtain a weld portion with a narrow bead width, it is preferable to vibrate the laser heat source in the width direction (the left-right direction in fig. 1) with respect to the longitudinal direction of the butted portion in accordance with the groove width.
That is, let the amplitude of the laser heat source in the width direction be a L (mm) frequency f L (Hz) and the width of the grooves of the pair of steel plates at the target position of the laser heat source is G L (mm), it is preferable to satisfy
2a L ≤G L +1, and
f L ≤10。
(2a A ≤G A +1，f A ≤10)
in the present embodiment, only the laser heat source may be vibrated, but only the gas metal arc heat source may be vibrated without vibrating the laser heat source, or both the laser heat source and the gas metal arc heat source may be vibrated. It is preferable to prevent the gas metal arc heat source from being accelerated at a high acceleration with a low amplitude and frequency. On the other hand, by adjusting the amplitude and frequency of the vibration of the gas metal arc heat source, the range in the width direction of the heat input can be appropriately expanded, and the molten state of the bevel face can be made sound.
That is, let the amplitude of the gas metal arc heat source in the width direction be a A (mm) frequency f A (Hz) the width of the grooves of a pair of steel plates under the target position of the gas metal arc heat source is G A (mm), it is preferable to satisfy
2a A ≤G A +1, and
f A ≤10。
(protective gas)
In the present embodiment, the type of the shielding gas is not particularly limited, and the content of CO can be 100% 2 Gas, or Ar gas and CO 2 Gas mixtures of gases, and the like. It is generally known that when a mixed gas having a high Ar content is used, for example, 80% Ar-20% CO 2 The amount of spatter generated can be suppressed by using the gas of (3) as a shielding gas.
According to the welding method of the present embodiment, even if 100% CO is used at low cost 2 The amount of spatter generated can be sufficiently suppressed even with a gas, and therefore, the cost for welding can be reduced.
[2. Method for producing welded joints ]
The method for manufacturing a welded joint according to the present embodiment is a method for manufacturing a welded joint by using the welding method described in [1. Single-side butt welding method ].
The heat source used, the composition of the flux-cored wire for the gas metal arc heat source, the composition of the backing flux, the welding conditions, and the like are as described in the above [1. Single-side butt welding method ].
Examples
The present invention will be described in detail below by way of examples of the invention and comparative examples, but the present invention is not limited thereto.
[1. Single-side butt welding ]
(1-1. Preparation of welding material, welding wire and backing flux)
Two SM490A steel sheets having a thickness of 12mm were prepared as materials to be welded, and welding wires having various compositions and backing fluxes having various compositions were prepared as heat sources for gas metal arcs. Solid wire and flux-cored wire were prepared as welding wires. The kind of solid wire is shown in table 1 below, and the size and composition of the flux cored wire are shown in table 2 below. In addition, the composition of the pad flux is shown in table 3 below.
The flux for gasket, designated BF-L, is obtained by kneading raw materials of water glass, molding the mixture into granules, and sintering the granules.
In Table 3, fe was contained in the range of 99.5 mass% or less in addition to Mn and Si as components other than the slag former < FLUX >, but not described in the table. In addition, the pad flux contains inevitable impurities in addition to the components described in the table.
As the sheath of the flux-cored wire shown in table 2, JISG3141:2017 which corresponds to the designation SPCG. The SPCG steel strip contains the following components in percentage by weight: 0.02 mass% or less, mn:0.25 mass% or less, P: 0.020% by mass or less, S: 0.020% by mass or less.
Table 2 shows that the MnO content of wire No. F-B is 0.004 mass% or less.
In addition, "-" in tables 2 and 3 indicates that the component was not positively added.
(1-2. Laser arc hybrid welding)
As shown in fig. 1 and 2, a pair of steel plates 1a and 1b are butted and horizontally arranged with a bevel width G, and a backing flux 11 is arranged below the butted portion 2. Then, as the preceding 1 st heat source, an arc (gas metal arc heat source) 7b is used, and as the 2 nd heat source following the 1 st heat source, an excimer is usedLight (laser heat source) 8a as a protective gas, using 100% of CO 2 The gas moves the 1 st heat source and the 2 nd heat source in the direction indicated by the arrow in fig. 2 while maintaining a predetermined interval. Thus, the butt portion 2 is subjected to laser-arc hybrid welding. The types of wire and backing flux used, as well as the laser conditions, arc conditions, and heat source movement conditions are shown in table 4 below.
In table 4, the focal position of the laser conditions indicates the deviation between the position of the upper surface of the steel plates 1a and 1b as the base material and the focal position of the laser light, and when the focal position is positive, the focal position of the laser light is above the upper surfaces of the steel plates 1a and 1 b. The 1 st heat source and the 2 nd heat source share the same welding speed, amplitude, and frequency, respectively, and therefore common conditions are described in the column of the movement conditions. In the column of the amplitude, 0 indicates that no vibration is present, that is, that no yaw motion bar is implemented. Thus, for no vibration, the frequency column is denoted as "-".
Further, the energy radiation angle θ of the 1 st heat source (gas metal arc heat source) shown in FIG. 3 is made 1 Is 50 degrees, and the energy radiation angle theta of the No.2 heat source (laser heat source) 2 The distance (P1-P2 pitch) between the target position P1 of the 1 st heat source and the target position P2 of the 2 nd heat source was set to 100 ℃. The center of the target position of each heat source is the center of the groove width G shown in fig. 1.
[2. Evaluation ]
The surface (weld surface) and the back surface of the joint after the single-side butt welding were observed, and the appearance of the joint was evaluated according to various items shown below.
(2-1. Splash of joint surface)
The amount of spatter generated on the joint surface was visually observed.
As an evaluation criterion, the state where no large particles of 1mm or more were splashed was "A" (excellent). In addition, in the range of the length of the welding line of 100mm, the number of the large-particle spatters attached to 1mm or more is "B" (good) when the number of the large-particle spatters attached is less than 10. In addition, in the range of the length of the welding line of 100mm, 10 or more of large spatters of 1mm or more are attached as "NA" (defective).
(2-2. Bead shape of joint surface)
The shape of the weld bead on the joint surface was visually observed.
As an evaluation criterion, there was a smooth bead shape of "A" (excellent). In addition, the convex bead was "B" (good). Further, the state where undercut and under-weld occur and additional processing such as repair welding is required is "C" (acceptable).
(2-3. Melting state of coating on the joint)
The molten state of the back surface of the joint was visually observed.
As an evaluation criterion, the groove on the back surface on which no unmelted groove was observed was "a" (excellent). In addition, the back surface was found to have "NA" (defective) of the non-melted groove.
(2-4. Smoothness of joint back)
The smoothness of the back of the joint was visually observed.
As an evaluation criterion, the surface of the back bead was smooth and "a" (excellent) without slag adhesion. The area where the slag remains attached is less than 40% of the total area of the bead back surface, or the state of attachment of the metallic flux is inferior to the above "a" and the unevenness is large, that is, "B" (good). The area remaining after the adhesion of the slag was 40% or more of the total area of the back surface of the bead, but "C" (acceptable) was usable.
(2-5 bead sagging at the back of the joint)
The sagging of the weld bead on the back of the joint was visually observed.
As an evaluation criterion, the height of the back bead was uniform, and the height of the back bead was "A" (excellent) when it was less than 3mm. Further, the height of the back bead is less than 3mm, but the height thereof is not uniform, or the height of the back bead is in the range of 3mm or more and less than 6mm, which is "B" (acceptable). Further, the height of the back bead of 6mm or more is "NA" (defective).
The evaluation results are shown in table 5 below.
[ TABLE 1]
Figure BDA0003810913400000241
[ TABLE 2]
Figure BDA0003810913400000251
[ TABLE 3]
Figure BDA0003810913400000261
[ TABLE 4]
Figure BDA0003810913400000271
[ TABLE 5]
TABLE 5
Figure BDA0003810913400000281
FIG. 4 is a photograph showing a substitute for the drawing showing the state of welding in test No. 1. Fig. 5 is a photograph substitute for drawing showing the state of the joint surface after welding of test No. 1. Test No.1 as a comparative example is laser arc hybrid welding, but as in the method described in patent document 3, a solid wire 27 was used as the 1 st heat source. Therefore, as shown in fig. 4 and 5, large spatters 21 bounce off the molten pool 19, and a large amount of large spatters 21 adhere to both sides of the weld line 20 on the joint surface.
In test No.2 as a comparative example, the content of the slag former in the flux-cored wire was lower than the lower limit value of the range specified in the present invention, and therefore, large spatters were generated.
FIG. 6 is a photograph showing a substitute for the drawing showing the state of welding in test No. 6. In test No.6 as an invention example, welding was performed by the single-side butt welding method specified in the present invention, and a flux-cored wire 7a containing a slag former was used as the 1 st heat source. Therefore, as shown in fig. 6, a flux column 10 is formed at the tip of the wire, and the droplet passes along the column, so that scattering of large spatters is reduced.
As described above, according to the one-side butt welding method of the present invention and the method of manufacturing a welded joint of the present invention, a deep penetration and a large deposition amount can be obtained, and a welded joint in which a spatter generation amount is reduced and thermal deformation is suppressed can be obtained. Further, as the shielding gas, even if 100% of CO is used 2 Gas can also reduce the occurrence of spatter, and therefore the manufacturing cost of the welded joint can be reduced.

Claims (16)

1. A one-side butt welding method for welding a butt joint portion formed between a pair of steel plates by butting the steel plates and arranging a backing flux substantially horizontally, holding a preceding 1 st heat source and a 2 nd heat source following the 1 st heat source so that an interval in a longitudinal direction of the butt joint portion is within an arbitrary range, and moving the 1 st heat source and the 2 nd heat source relative to the pair of steel plates from above the butt joint portion,
either one of the 1 st heat source and the 2 nd heat source is a gas metal arc heat source using a flux-cored wire containing a slag former,
the other of the 1 st heat source and the 2 nd heat source is a laser heat source,
the flux-cored wire contains the slag former in an amount of 2.5 mass% or more relative to the total mass of the wire.
2. A single-sided butt welding method according to claim 1, wherein the content of the slag former is 18.0 mass% or less with respect to the total mass of the welding wire.
3. The single-side butt welding method according to claim 1, wherein the slag former contains a slag forming agent in an amount corresponding to a total mass of the welding wire
TiO 2 :2.0 to 15.0 mass%,
SiO 2 :0.25 to 2.0 mass% inclusive,
ZrO 2 :0.15 to 1.0 mass% inclusive,
Na 2 O、K 2 O and Li 2 Total amount of O: 0.02 mass% or more and 0.50 mass% or less, and,
MnO:0.50 mass% or less and including 0 mass%,
Al 2 O 3 :0.50 mass% or less and including 0 mass%,
metal fluoride: 0.50% by mass or less and including 0% by mass.
4. A single-sided butt welding method according to claim 1,
the components of the flux-cored wire except the slag former are C:0.5 mass% or less of a surfactant,
si:2.0 mass% or less of a surfactant,
mn:3.0 mass% or less of a polymer,
ni:5.0 mass% or less of a surfactant,
mo:3.0 mass% or less of a polymer,
w:3.0 mass% or less of a polymer,
nb:3.0 mass% or less of a polymer,
v:3.0 mass% or less of a polymer,
cr:5.0 mass% or less of a surfactant,
ti:3.0 mass% or less of a polymer,
<xnotran> Al: </xnotran> 3.0 mass% or less of a polymer,
mg:3.0 mass% or less of a polymer,
n:0.05 mass% or less of a surfactant,
s:0.05 mass% or less of a surfactant,
p:0.05 mass% or less of a surfactant,
b:0.005% by mass or less of a polymer,
cu:2.0 mass% or less of a surfactant,
ta:3.0 mass% or less of a polymer,
REM:0.1 mass% or less, and
alkali metal: 3% by mass or less of a surfactant,
the balance being Fe and unavoidable impurities.
5. The single-side butt welding method according to claim 1, wherein the flux-cored wire is formed by filling a flux in an outer sheath,
the skin is formed from a cold rolled steel strip.
6. A single-sided butt welding method according to claim 1,
the backing flux contains at least one of metal powder and slag former,
the balance being unavoidable impurities.
7. A single-sided butt welding method according to claim 6,
the backing flux further contains at least one of non-metal powder and non-metal compound powder other than a slag former.
8. A single-sided butt welding method according to claim 6,
when the pad flux contains the metal powder in an amount of 90 mass% or more based on the total mass of the pad flux,
the metal powder contains at least one of Si powder and Fe-Si powder,
the Si content in the Si powder and the Fe-Si powder is 0.5 mass% to 50 mass% of the total mass of the backing flux.
9. A single-sided butt welding method according to claim 6,
when the backing flux contains the slag former in an amount of more than 10 mass% relative to the total mass of the backing flux,
the slag former contains metal oxide and metal fluoride, and the balance is inevitable impurities.
10. A single-sided butt welding method according to claim 6,
when the backing flux contains the slag former,
the lining welding flux is formed by mixing raw materials of water glass, shaping into particles and sintering.
11. A single-sided butt welding method according to claim 1,
the 1 st heat source is a gas metal arc heat source,
and enabling the 2 nd heat source to be a laser heat source.
12. A single-sided butt welding method according to claim 1,
the distance between the target position of the 1 st heat source and the target position of the 2 nd heat source is 0mm to 10.0 mm.
13. A single-sided butt welding method according to claim 1,
an energy radiation angle of the 1 st heat source is 45 ° or more and 80 ° or less with respect to a welding proceeding direction of the butting portion,
an energy radiation angle of the 2 nd heat source is 90 ° or more and 135 ° or less with respect to a welding proceeding direction of the butting portion.
14. A single-sided butt welding method according to claim 1,
vibrating the laser heat source in a width direction with respect to a longitudinal direction of the butting portion,
the amplitude in the width direction of the laser heat source is set to a L At a frequency of f L The width of the grooves of the pair of steel plates under the target position of the laser heat source is G L When it is satisfied
2a L ≤G L +1, and
f L ≤10
wherein, the a L 、G L In mm, said f L In Hz.
15. A single-sided butt welding method according to claim 1,
vibrating the gas metal arc heat source in a width direction with respect to a longitudinal direction of the butting portion,
the amplitude of the gas metal arc heat source in the width direction is defined as A Frequency of f A The width of the grooves of the pair of steel plates at the target position of the gas metal arc heat source is G A When it is satisfied with 2a A ≤G A +1, and
f A ≤10
wherein, the a A 、G A In mm, said f A In Hz.
16. A method for manufacturing a welded joint, characterized in that the welded joint is manufactured by using the single-side butt welding method according to any one of claims 1 to 15.
CN202211011967.0A 2021-09-29 2022-08-23 Single-side butt welding method and method for manufacturing welded joint Pending CN115870620A (en)

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