WO2010104088A1 - Procédé de liaison de matériaux dissemblables - Google Patents

Procédé de liaison de matériaux dissemblables Download PDF

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Publication number
WO2010104088A1
WO2010104088A1 PCT/JP2010/053924 JP2010053924W WO2010104088A1 WO 2010104088 A1 WO2010104088 A1 WO 2010104088A1 JP 2010053924 W JP2010053924 W JP 2010053924W WO 2010104088 A1 WO2010104088 A1 WO 2010104088A1
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Prior art keywords
welding
aluminum
steel material
steel
flux
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PCT/JP2010/053924
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English (en)
Japanese (ja)
Inventor
雅男 杵渕
誠二 笹部
剛 松本
康生 村井
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株式会社神戸製鋼所
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Publication of WO2010104088A1 publication Critical patent/WO2010104088A1/fr

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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
    • 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
    • B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
    • B23K35/286—Al 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
    • B23K33/00—Specially-profiled edge portions of workpieces for making soldering or welding connections; Filling the seams formed thereby
    • 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
    • B23K9/0026—Arc welding or cutting specially adapted for particular articles or work
    • 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
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • 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
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/08—Non-ferrous metals or alloys
    • B23K2103/10—Aluminium or alloys thereof
    • 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
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/18—Dissimilar materials
    • B23K2103/20—Ferrous alloys and aluminium or alloys thereof

Definitions

  • the present invention relates to a dissimilar material joining method by welding dissimilar metal members of a steel material and an aluminum material in a transport field such as an automobile and a railway vehicle, a member, a part, and a structure such as a machine and an architecture.
  • the joining is necessary to ensure the joining strength. Compared to the case of only steel materials, it can significantly contribute to weight reduction and the like.
  • the aluminum material is a general term for a pure aluminum material and an aluminum alloy material.
  • the high strength steel material and 6000 series aluminum alloy material from the low-strength dissimilar materials such as conventional mild steel and pure aluminum alloy, A5000 series aluminum alloy, etc.
  • the joining object is changing to welding joining of different materials.
  • the formation conditions of brittle Fe-Al intermetallic compounds at the joints are different from those of conventional low-strength dissimilar materials, so reliable and high joint strength is obtained. In order to do so, it is necessary to devise new joining conditions.
  • the steel material When joining dissimilar materials of steel and aluminum alloy materials, the steel material has a higher melting point, higher electrical resistance and lower thermal conductivity than the aluminum alloy material, so the heat generation on the steel side increases, and the low melting point first Aluminum melts. Next, the surface of the steel material is melted, and as a result, a Fe—Al-based brittle intermetallic compound layer is formed at the interface, so that high bonding strength cannot be obtained.
  • a method for improving the strength of the welded joint by improving the composition of the flux used for fusion welding of dissimilar joints has also been proposed.
  • a flux containing a fluoride cesium fluoride, aluminum fluoride, potassium fluoride
  • the core material is coated with aluminum or an aluminum alloy to form steel (mild steel) with a flux-cored wire.
  • arc welding an aluminum material see Patent Document 4).
  • a fluoride-based flux having an effect of reducing, dissolving and removing the oxide film from the surface of the aluminum alloy material on which a strong oxide film is formed is applied to the surface of the aluminum alloy material, and mild steel and a 6000 series aluminum alloy material are applied.
  • a method of spot welding is also proposed (see Patent Document 6).
  • these fluoride fluxes are also used for fusion welding joining between aluminum alloy materials (see Patent Documents 7 and 8).
  • FCW welding method The MIG welding method and laser brazing method (hereinafter also referred to as FCW welding method) using the above-described flux-cored wire are certainly very efficient welding methods. Further, according to this FCW welding method, in the case of overlapped fillet welding, that is, the steel material arranged on the lower side with respect to the welding direction and the aluminum material arranged on the upper side are overlapped and welded together. When doing, the bead by an aluminum welding material can be formed over the welding surface of both the said steel materials and aluminum materials. For this reason, the dissimilar material joined body (joint) of high joint strength is obtained.
  • the present invention is an improvement of the FCW welding method as a dissimilar material joining method.
  • the present invention provides a dissimilar material joining method that can ensure high joint strength even when FCW welding is performed by superimposing a steel material arranged on the upper side with respect to the welding direction and an aluminum material arranged on the lower side. The purpose is to provide.
  • the gist of the dissimilar material joining method of the present invention is that the steel material arranged on the upper side and the aluminum material arranged on the lower side are overlapped with each other along the welding line.
  • a welding method for dissimilar materials wherein at least the position of the welding surface of the aluminum material along the welding line is higher than the position of the welding surface of the steel material along the welding line.
  • a bead of aluminum welding material is formed across the welding surfaces of both the steel material and the aluminum material.
  • the welding surface of the aluminum material protrudes 0.5 to 4 mm upward with respect to the welding direction.
  • S is an interval provided so that the molten aluminum welding material wraps around between the lower surface of the steel material with respect to the welding execution direction and the surface of the aluminum material facing the lower surface of the steel material
  • the steel material G is an interval provided between the end surface of the steel material and the surface of the aluminum material facing the end surface of the steel material, the surface of the aluminum material facing the lower surface of the steel material, and the end of the steel material R, which is the radius of curvature of the curved surface to which the surface of the aluminum material facing the part surface is connected, satisfies (1) S: 1.5 mm or less, G: 1 mm or less, R: less than 3 mm, or ( 2) It is preferable to adjust so as to satisfy S: 2.5 mm or less, G: 1 mm or less, and R: 3 to 5 mm.
  • the welding is performed by MIG welding or laser welding among the FCW welding methods using the flux cored wire filled with the flux inside the aluminum outer sheath in terms of increasing welding efficiency and joint strength. preferable.
  • the present inventors investigated the reason why high joint strength could not be obtained by the FCW welding method depending on the positional relationship between the steel material and the aluminum material.
  • the aluminum material is arranged on the lower side with respect to the welding direction, it becomes clear that the molten aluminum is difficult to spread on the welding surface of the steel material arranged on the upper side, so that good bonding cannot be performed. It was. Further, in this case, since the supply of flux to the steel material surface is insufficient, the effect of improving the wettability between the molten aluminum and the steel is small, and as a result, it has become clear that good bonding cannot be performed.
  • the present inventors can solve the above problems by welding in a state where the position of the welding surface of the aluminum material protrudes upward from the position of the welding surface of the steel material with respect to the welding construction direction. It has also been found that a bead of aluminum welding material can be formed over both the steel and aluminum welding surfaces.
  • FIG. 4 (a) and 4 (b) schematically show the situation of the MIG weld bead according to the positional relationship between the steel material and the aluminum material.
  • FIG. 4A shows a case where the steel material arranged on the lower side with respect to the welding direction and the aluminum material arranged on the upper side are overlapped and welded to each other.
  • FIG.4 (b) is a case where the steel materials arrange
  • the wettability of the weld surface 2a of the steel material 2 and the molten aluminum 6 can be improved, and the removal of the oxide film on the surface of the steel material 2 (weld surface 2a) is promoted.
  • the bead 6 made of the aluminum welding material can be formed over the welding surfaces of both the steel material welding surface 2a and the aluminum material welding surface 3a, and better bonding can be realized.
  • the bead 6 on the steel material welded surface 2a side is particularly difficult to be formed.
  • the bead 6 made of the aluminum welding material over both the welding surfaces of the steel material welding surface 2a and the aluminum material welding surface 3a cannot be formed, and good bonding cannot be performed.
  • FIG. 1 shows an example of the present invention.
  • a steel material 2 arranged on the upper side with respect to the welding direction indicated by the arrow 4 and an aluminum material 3 arranged on the lower side. are superimposed on each other and fillet welded.
  • FIG. 2 shows the state after the example of this invention shown in FIG. 1 is fillet welded.
  • 1 and 2 show an example in which a steel plate automobile panel 2 such as a door is partially reinforced with an aluminum alloy extruded shape 3 or the like from the back side (inside) of the panel 2.
  • a recess 3 b is provided at the end of the aluminum material 3 disposed on the lower side on the steel material 2 side, and the recess 3 b accommodates the welding surface 2 a of the steel material 2.
  • the recess 3b has a depth greater than or equal to the thickness of the steel material 2. Therefore, when the welding surface 2a of the steel material 2 is overlapped so as to be accommodated in the concave portion 3b, the welding surface 2a of the steel material 2 with respect to the welding direction 4 is equal to the difference X (mm) between the depth of the concave portion 3b and the thickness of the steel material 2. To retreat. At the same time, the welding surface 3a of the aluminum material (welding surface along the welding line 5 with the steel material 2) is X (mm) above the welding direction 4 from the position of the welding surface 2a along the welding line 5. ) Only protrudes.
  • the molten aluminum 6 (becomes a bead) from the welding surface 3 a of the upper aluminum material 3 is formed on the surface of the lower steel material 2 ( It is easy to spread on the welding surface 2a).
  • the flux supplied to the welding surface Therefore, also in the case of the FCW welding method using the flux, the flux tends to spread on the surface of the lower steel material 2 (welded surface 2a).
  • the wettability of the weld surface 2a of the steel material 2 and the molten aluminum 6 is improved, and the removal of the oxide film on the surface of the steel material 2 (weld surface 2a) is promoted.
  • the bead 6 made of the aluminum welding material is formed over both the steel material welding surface 2a and the aluminum material welding surface 3a, and as the dissimilar material joined body 1, better bonding can be realized.
  • S indicates the clearance (interval) between the bottom surface of the recess 3 b of the aluminum material 3 and the lower surface of the steel material 2 accommodated. That is, the plate gap S is between the surface of the steel material opposite to the welding execution direction (the lower surface located below the welding execution direction) and the surface of the aluminum material facing the steel material surface. Further, the interval is provided so that the molten aluminum welding material wraps around.
  • G indicates the clearance between the end surface of the recess 3 b of the aluminum material 3 and the end surface of the steel material 2 accommodated. That is, the gap G is an interval provided between the end surface of the steel material and the surface of the aluminum material facing the end surface of the steel material.
  • These plate gaps S and G are prepared for wrapping around the steel material 2 of the molten aluminum (around).
  • the joining of the molten aluminum (molten aluminum) and the aluminum material 3 is the same as a normal welded portion, the aluminum material 3 (welded surface 3a) is melted and integrated with the molten aluminum 6, and the bead 6 is solidified after solidification. Thus, a strong joint is formed.
  • the cleaning action, wettability, and adhesiveness are improved by the flux, so that the steel weld surface 2a is widely covered with the molten aluminum 6 in a close contact state. Therefore, the steel material 2 is not directly input heat from an arc described later (arc 15 in FIG. 3 described later), but is indirectly input heat through the covered aluminum molten metal. It does not melt when heated excessively.
  • a thin intermetallic compound layer of about several ⁇ m is formed at the joining interface between the steel material 2 and the aluminum melt 6 that is in close contact. This intermetallic compound layer is brittle when it is as thick as several tens of ⁇ m or more, and weld cracking occurs and the strength deteriorates. However, a thin intermetallic compound layer of about several ⁇ m is not brittle and is strong. It becomes a state.
  • the cleaning action by the flux, the wettability, and the adhesion improving action are very good is important.
  • the cleaning action, wettability, and adhesion improving action are lowered, the molten aluminum 6 cannot sufficiently cover the steel weld surface 2a.
  • the steel material welding surface 2a is excessively heated and melted to form a thick intermetallic compound layer.
  • Aluminum material welding surface protrusion method It is possible to project the aluminum material welding surface 3 a upward from the welding surface 4 a of the steel material 2 by the shape design and processing of the aluminum material. For example, in the case of an aluminum material as shown in FIG. 1, the aluminum material welding surface 3 a is partially thickened in advance, or by joining another aluminum material to the aluminum material welding surface 3 a, the thickness is partially increased. Or just meat.
  • the simplest method is to design the shape so that the original aluminum material is provided with the support flange (arm portion) of the steel material 2 and the like.
  • the aluminum material 3 is an extruded shape
  • the thin portion (concave portion) and the joint flange (arm portion) are included in the original shape and extruded, the thin portion ( The trouble of forming the (concave portion) is unnecessary.
  • a thin portion (concave portion) can be formed by simply cutting in the middle or before and after the forming process.
  • the protrusion amount X (mm) of the aluminum material welding surface 3a is appropriately selected according to the design conditions, welding method, and welding conditions of the dissimilar material joined body. That is, the protrusion amount: X (mm) is easy to spread to the lower steel material welding surface 2a of the molten aluminum 6, and easy to spread to the lower steel material welding surface 2a of the flux (improvement of wettability, steel material welding surface). It is appropriately selected based on the degree of the promotion of removal of oxide film 2a).
  • this protrusion amount: X (mm) When this protrusion amount: X (mm) is small, the molten aluminum 6 does not sufficiently spread on the steel material welding surface 2a. On the other hand, if this protrusion amount: X (mm) is too large, it is difficult to ensure the penetration into the aluminum material 3. If the welding heat input is increased too much to ensure penetration, the intermetallic compound at the bonding interface grows thick, and in the extreme case, the steel material 3 is melted, so it is difficult to ensure the bonding strength.
  • the optimum range of the protrusion amount: X (mm) varies depending on each condition, but in the field of dissimilar material joining such as the automobile body described above, it is generally in the range of 0.5 mm to 4 mm.
  • the protrusion amount: X (mm) is appropriately determined according to the plate gap S or gap G, which is the clearance between the aluminum material 3 and the steel material 2 described above, or in consideration of the plate gap S or gap G. Designed. Further, the plate gap S and the gap G, which are the clearances between the aluminum material 3 and the steel material 2, are also appropriately designed according to the relationship with the protrusion amount: X (mm).
  • FIG. 3 the positional relationship between the steel material and the aluminum material is the same as in FIG. 1, and the steel material 2 disposed on the upper side with respect to the welding execution direction from the top to the bottom illustrated in FIG. The case is shown in which fillet welded with the aluminum material 3 arranged on the lower side being overlapped with each other.
  • FIG. 3 shows an example in which, for example, the end portion of the panel manufactured from the steel plate 2 is supported from the back side (inside) of the panel by the aluminum alloy extruded shape member 3.
  • FIG. 3 differs from FIGS. 1 and 2 particularly in the shape of the aluminum material 3. That is, in FIG. 3, the aluminum material 3 has an inverted L shape, and extends in the horizontal direction to support the end portion of the steel plate panel 2, and to extend in the vertical direction. A vertical wall 3d joined to another structural member. And the flange 3c is provided below the welding surface 3a which is the upper end part of the vertical wall 3d. That is, the welding surface 3a which is the upper end part of the vertical wall 3d protrudes upward. Thereby, the welding surface 3a of the aluminum material 3 (welding surface along the welding line 5 with the steel material 2) is protruded above the welding direction 4 from the position of the welding surface 2a of the steel material 2. .
  • a concave portion 3b is provided on the upper surface of the aluminum flange 3c in order to secure a clearance (interval) for the molten aluminum to wrap around the steel material 2 (lower part).
  • the end of the recess 3b far from the aluminum material 3 has a vertical wall shape perpendicular to the bottom surface, but the side of the recess 3b in contact with the vertical wall 3d is the same as the lower surface of the flange 3c. It is connected to the vertical wall 3d so as to have a curved surface with a radius of curvature R.
  • the curvature radius R is less than 3 mm according to the curvature radius R of the curved surface connecting the surface of the aluminum material facing the end surface of the steel material and the bottom surface of the recess 3b.
  • R 0, that is, including the case where the corners are provided at right angles
  • the radius of curvature R is 3 to 5 mm, it is recommended that the plate gap S be adjusted to 2.5 mm or less and the gap G to be adjusted to 1 mm or less.
  • Arc welding method The aspect of the welding apparatus used by this invention is demonstrated using FIG. In the present invention, it is possible to use a welding apparatus and welding method (arc welding apparatus, method and conditions) by the usual FCW welding method, and this is also an advantage of the present invention.
  • FIG. 3 although the block diagram of an arc welding apparatus (consumable electrode arc welding apparatus: MIG welding apparatus) is shown, if a laser irradiation apparatus is provided in this FIG. 3, the block diagram of a laser irradiation arc welding apparatus It becomes.
  • FCW (flux-cored wire) 10 has a specific component flux described later.
  • the FCW 10 unwound from the spool 11 is fed at a predetermined feeding speed through the welding torch 13 by the rotation of a feeding roll 12 directly connected to a wire feeding motor (not shown).
  • the shielding gas 16 is supplied into the welding torch 13.
  • a welding power source device (PS) indicated by reference numeral 14 outputs a welding voltage and a welding current for performing arc welding, and outputs a feeding control signal to the wire feeding motor.
  • the arc 15 is generated between the FCW 10 and the material to be joined, and the joining is performed.
  • at least the aluminum material welding surface 3a is protruded upward with respect to the welding direction 4 from the position of the steel material welding surface 2a.
  • the molten aluminum (not shown) from the welding surface 3a of the aluminum material 3 protruded to the upper side is easy to spread on the lower steel material welding surface 2a.
  • the flux supplied to the welding surface by the FCW 10 is likely to spread to the lower steel material welding surface 2a. For this reason, the wettability between the steel material welding surface 2a and the molten aluminum is improved, and the removal of the oxide film on the steel material 2 welding surface 2a is promoted.
  • FIG. 3 illustrates the case of MIG welding, but the arc welding method of the present invention includes DC MIG welding, DC pulse MIG welding, AC MIG welding, AC pulse MIG welding, and DC / AC TIG welding. Further, plasma arc welding, combined laser irradiation arc welding using arc welding and laser irradiation at the same time can be used. Laser welding (apparatus) can also be used instead of arc welding (apparatus).
  • FCW Flux cored wire
  • FCW The flux cored wire (FCW) for joining dissimilar materials used in the present invention uses FCW in which a fluoride-based mixed flux is covered with an aluminum alloy skin in order to improve the efficiency of fusion welding.
  • FCW a general one in which a tubular aluminum alloy outer shell (hoop) is filled with a flux can be used.
  • the FCW includes a seam type having a seam (joint: gap, opening) and a seamless type having no seam in which the seam is joined by welding or the like.
  • the aluminum alloy used for the FCW shell is not particularly limited, but 4000 series aluminum alloys such as A4043 and A4047 and 5000 series aluminum alloys such as A5356 and A5183 can be used. In addition, aluminum alloys such as 3000 series and 6000 series may be used. Among these, A4043-WY, A4047-WY, A5356-WY, A5183-WY and the like defined by JIS are preferably exemplified.
  • an optimum diameter may be selected according to the welding workability including the characteristics of the wire feeder, etc., for welding work used as high-efficiency fully automatic welding or semi-automatic welding.
  • a narrow diameter of about 0.8 to 1.6 mm ⁇ which is generally used may be used.
  • the wire having a smaller wire diameter is used in the range of the wire diameter, the heat input during welding can be reduced and the welding current can be lowered.
  • scattering of the fluoride-based mixed flux itself can be prevented, welding workability can be improved, and formation of fragile intermetallic compounds can be suppressed.
  • the wire diameter exceeds 1.6 ⁇ mm, the current for obtaining a stable arc becomes excessive, the scattering of the fluoride-based mixed flux itself increases, the melting of the base material becomes excessive, and the fragile metal It may lead to the formation of compounds.
  • the filling rate of the flux into the FCW is, of course, dependent on the flux composition, but is preferably relatively small, such as about 0.1 mass% and less than 24 mass% with respect to the total mass of the FCW.
  • a lower filling rate is preferable because it prevents scattering of the flux itself and improves welding workability. If the filling rate of the flux is too small, the effect of the flux cannot be exhibited, and a sound and highly reliable welded joint cannot be obtained.
  • FCW instead of directly applying the fluoride-based mixed flux to the weld.
  • the use of the FCW improves the welding workability by preventing the dispersion of the fluoride-based mixed flux itself, and also suppresses the generation of fragile intermetallic compounds. It is essential to do.
  • the flux composition used (filled) in the FCW is a mixed flux (Noroclock) having a specific composition in which fluorides such as aluminum fluoride and potassium fluoride are mixed among fluoride-based mixed fluxes. Flux) is preferable.
  • Noroclock a mixed flux
  • chloride acts as a corrosion promoting factor for the welded portion, and consequently, the dissimilar material joint, so the flux does not contain chloride or the amount of chloride is 1 mol% or less.
  • a regulated fluoride composition is preferred.
  • the flux filling amount in the outer skin When the flux filling amount in the outer skin is small, the flux amount is not stable, and the flux filling amount (filling rate, content rate) varies depending on the part of the FCW. On the other hand, when the flux filling amount is small, mixing the flux and the aluminum alloy powder and filling the outer skin eliminates or alleviates this problem and facilitates the manufacture of the FCW itself. Therefore, it is preferable. In addition, when aluminum alloy powder is mixed and added to this flux, there are cases where spatter during welding is reduced and effects such as suppression of excessive wetting of the molten metal may be obtained.
  • a mixed flux having such a specific composition can be joined to an aluminum material. That is, if such a mixed flux is used, the surface of the material with the galvanized steel material or the aluminum material can be cleaned, and the wettability of the weld metal is improved. As a result, the bead formation is improved. Moreover, as a result of suppressing generation of a brittle Al—Fe-based intermetallic compound layer generated in the dissimilar material joint portion and a brittle Zn—Fe-based compound layer derived from galvanization, the bonding strength is improved. Of course, this effect is also exhibited in the dissimilar material joining of a bare steel material that is not galvanized and an aluminum material.
  • the thickness of the steel materials to be joined with different materials in the present invention is preferably in the range of 0.3 to 4.0 mm. If the thickness of the steel material is less than 0.3 mm, the strength and rigidity necessary for the structural member and the structural material described above cannot be secured, which is inappropriate. If the plate thickness of the steel material is too thick, it will not be possible to reduce the weight of the structural members and structural materials described above. Further, in the present invention, the shape of the steel material to be joined with the different material is not particularly limited, and a shape generally used for a structural member such as an automobile body or a steel plate, a steel shape member, and a steel pipe selected by the structural member. The shape may be appropriate.
  • high-strength structural member such as an automobile member
  • high-tensile steel high tensile having a tensile strength of 400 MPa or more, desirably 500 MPa or more
  • Low-strength steel and mild steel having a tensile strength of less than 400 MPa are generally low alloy steels, and the oxide film is made of iron oxide. Therefore, diffusion of Fe and Al is facilitated, and brittle intermetallic compounds are easily formed.
  • the plate thickness is increased to obtain the required strength, and the weight reduction is sacrificed.
  • the surface of the steel material to be joined with the different material may or may not be subjected to surface treatment except for coating with an insulating film.
  • galvanization is previously provided on the steel material surface (at least the joint surface with the aluminum material), the wettability of the flux is improved.
  • galvanization exists in the joint surface with an aluminum material, the advantage that the corrosion resistance of a dissimilar material joining body is excellent is acquired.
  • galvanization has the effect of delaying the time for the interfacial reaction layer, which is an intermetallic compound of steel and aluminum, to be formed during welding, it also has the effect of increasing joint strength.
  • the plating means is not particularly limited, and an alloying treatment may be performed after electroplating, hot dipping, or hot dipping.
  • the thickness of the galvanizing may be in the normal film thickness (average film thickness) range of 1 to 20 ⁇ m. When the thickness of the galvanized film is too thin, the galvanized film is melted and discharged from the bonded part at the initial stage of joining at the time of welding, and the effect of suppressing the formation of the interface reaction layer cannot be exhibited. On the other hand, when the thickness of the galvanized film is too thick, a large amount of heat input is required for melting and discharging zinc from the joint.
  • the aluminum material to be bonded to the different material in the present invention is not particularly limited with respect to the alloy composition and shape, and according to the required characteristics as each structural member described above, a widely used alloy composition, plate material, shape material, A forging material, a casting material, or the like is appropriately selected. However, it is desirable that the strength of the aluminum material be higher as in the case of the steel material. Therefore, Al-Mg-Si based A6000 aluminum alloy, which has high strength among aluminum materials, has a small amount of alloy elements, is excellent in weldability and recyclability, and is widely used as a structural member of this kind, is used. It is preferable to do.
  • the plate thickness of these aluminum materials used in the present invention is preferably in the range of 0.5 to 4.0 mm.
  • the thickness of the aluminum material is less than 0.5 mm, it is inappropriate because the strength as a structural material of an automobile or the like and the energy absorption at the time of a vehicle body collision are insufficient.
  • the thickness of the aluminum material exceeds 4.0 mm, it is impossible to reduce the weight of the structural member and the structural material as in the case of the steel material.
  • the surface of the aluminum material to be joined with the different material may or may not be subjected to surface treatment except for coating with an insulating film.
  • FCW welding conditions As described above, in FCW welding, in order to suppress generation of an intermetallic compound generated at the interface between an aluminum material and a steel material, it is necessary to prevent the steel material as a base material from being excessively melted. Therefore, it is preferable to select a welding condition that allows a sound joining state to be obtained with the minimum necessary base material melting (dilution) amount.
  • the welding current is 70 A or more, preferably 80 A or more and 120 A or less, more preferably 80 A or more and 110 A or less.
  • the higher the current the more the intermetallic compound at the bonding interface that is generated can adversely affect the bonding strength. Therefore, in order to suppress such an intermetallic compound, it is recommended to join at a relatively low current condition.
  • the welding voltage is 10 V or more, preferably 15 V or more and 30 V or less, more preferably 15 V or more and 20 V or less.
  • the welding speed may be appropriately determined within a range in which the base material Fe and Al are not excessively melted according to the welding current and the welding voltage. Considering the welding efficiency and the like, the welding speed is preferably 20 CPM or more, more preferably 30 CPM or more and 100 CPM or less, and further preferably 30 CPM or more and 90 CPM or less.
  • a general-purpose gas such as Ar can be used as appropriate.
  • the gas flow rate is not particularly limited, and a general flow rate can be selected.
  • Example 1 In the joint shape shown in FIG. 1, a cold-rolled steel sheet (high-tensile, thickness 1.4 mm) subjected to alloying hot-dip galvanizing (GA) having a tensile strength of 980 MPa was used as the steel material 2. Further, as the aluminum material 3, a T6 tempered extruded material (plate thickness of 2.0 mm) of a 6000 series aluminum alloy having a 0.2% proof stress of 180 MPa class was used.
  • G hot-dip galvanizing
  • Test pieces The length of the test piece is 300 mm for both the steel material 2 and the aluminum material 3.
  • a flat concave portion 3b having a length of 100 mm is provided at the end of the extruded aluminum member 3 on the steel plate 2 side.
  • the recess 3b accommodates the welding surface 2a of the steel material 2.
  • the protrusion amount X (mm) from the steel material welding surface 2a of the aluminum material welding surface 3a was variously changed by adjusting the depth of this recessed part 3b.
  • the clearance between the bottom surface of the concave portion 3b of the aluminum material 3 and the lower surface of the steel material 2 is “plate gap S”
  • the clearance between the end portion of the steel material 2 and the end portion of the concave portion 3b is “gap G”.
  • the plate gap S and gap G are shown in Table 1. In Example 1, S and G are zero in common with each example.
  • FCW is an aluminum alloy filler with a wire diameter of 1.0 mm ⁇ and an outer skin of A4047, and fluoride flux (K3 AlF6 fluoride and aluminum alloy powder of A4047 composition) is used in all FCWs. What added 10 mass% with respect to the weight was used.
  • the shield gas 16 is Ar.
  • the weldability of the joint can be evaluated by visual observation of the bead and a peeling test using chisel.
  • ⁇ is a state in which the bead 6 is continuously and satisfactorily formed over both the weld surface 2a of the steel material 2 and the weld surface 3a of the aluminum material as shown in FIG. .
  • size of the bead by the side of the welding surface 2a of the steel material 2 was evaluated by (circle), (triangle
  • x indicates the case where the bead 6 is hardly formed on the welded surface 2a side of the steel material 2 or the case where the bead is extremely small.
  • x is a case where the bead 6 is largely peeled off and the joint can be regarded as broken.
  • the evaluation of the peel test with chisel is ⁇ , it is a guideline that the joint has a break strength of 200 N / mm or more, and if it is ⁇ , the joint has a break strength of less than about 100 N / mm. become.
  • each of the protrusion amounts X ranges from 0.5 mm to 4 mm (number 3 to number 8). It can be seen that the joint weldability evaluation is good. On the other hand, in each example of numbers 1, 2, and 10, the joint weldability evaluation is inferior.
  • the welding surface 3 a of the aluminum material 3 is below the welding surface 2 a of the steel material 2 with respect to the welding direction 4. is there.
  • the protrusion amount X of the welding surface 3a of the lower aluminum material 3 with respect to the welding execution direction 4 is too small and is zero. From these results, it is confirmed that the molten aluminum 6 does not sufficiently spread on the welding surface 2a of the steel material 2 when the projection amount X of the welding surface 3a of the aluminum material 3 with respect to the welding direction 4 is small.
  • the protrusion amount X is too large. From this result, when the protrusion amount X is too large, it is proved that it is difficult to ensure the melting of the molten aluminum 6 into the aluminum material 3. On the other hand, if the heat input of welding is increased too much to ensure penetration, the intermetallic compound at the bonding interface grows thick, and in extreme cases, the steel is melted, so it is still difficult to ensure the bonding strength. Become.
  • Example 2 In the same joint shape as in Example 1, the protrusion amount X is constant as shown in Table 2.
  • the plate gap S and the gap G were variously changed, and the same test piece as in Example 1 and a welding test were performed under welding conditions, and the effects of the plate gap S and the gap G were investigated.
  • the plate gap S was changed from 0.5 mm to 1.5 mm, and the gap G was changed from 0 mm to 1.5 mm.
  • Table 2 the weldability of the joint is good in each example (number 11 to number 13) in which the plate gap S is 0.5 mm to 1.5 mm. Further, in each example (number 11 to number 16) in which the gap G is 0 mm to 1 mm, the weldability of the joint is good. From these results, it can be seen that if the plate gap S and the gap G are made too large, good welding cannot be performed as is conventionally known.
  • Example 3 In the joint shape (groove shape) shown in FIG. 3, the protrusion amount X is constant as shown in Table 3.
  • the curvature radius R of the upper curved surface connecting the vertical wall 3d and the flange 3c is variously changed, and a welding test is performed under the same welding conditions as in the first embodiment. The effect of corner shape was investigated.
  • the steel material 2 is the same as that of each above-mentioned Example.
  • the material and strength of the aluminum extruded material 3 are the same, but only the cross-sectional shape of the aluminum extruded material 3 is changed as shown in FIG.
  • the aluminum extruded material 3 has a flange (arm portion) 3c having a length of 35 mm and a thickness of 4 mm, a vertical wall 3d having a length of 18 mm and a thickness of 3 mm. 5 mm.
  • the depth of the recessed part 3b is 1 mm
  • the protrusion amount X from the steel material welding surface 2a with respect to the welding construction direction 4 of the aluminum material welding surface 3a is constant with 3 mm in each example.
  • such a groove shape allows joint weldability even when the plate gap S and gap G are relatively large due to design convenience and assembly errors of the joint or the underlying structural member. Has improved. Therefore, it can be seen that such a groove shape allows a design convenience and assembly error, and allows the board gap S and the gap G to have a margin. Further, the groove shape having the curvature radius R as shown in FIG. 3 does not need to be produced by machining such as cutting.
  • the use of an aluminum alloy extruded shape has an advantage that such a shape can be realized without machining by only an extrusion designed to have a desired cross-sectional shape.
  • the dissimilar material joint that can stably secure a high joint strength.
  • the construction method is also easy and can provide the joining method using the arc welding which can perform efficient wire welding. Therefore, it is useful in the field of dissimilar joints between steel and aluminum, such as the manufacture of automobile bodies.

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

Abstract

La présente invention se rapporte à un procédé de liaison de matériaux dissemblables qui garantit de façon stable une résistance de liaison élevée, même lors d'un chevauchement et d'un soudage d'un élément en acier sur le dessus et d'un élément en aluminium sur le fond dans la direction de soudage. Dans ce procédé, lors du chevauchement et du soudage de l'élément en acier (2) sur le dessus et de l'élément en aluminium (3) sur le fond dans la direction de soudage (4), les matériaux sont soudés d'une façon telle que la surface soudée (3a) de l'élément en aluminium est positionnée au moins le long d'une ligne de soudage (5) faisant saillie dans la direction de soudage (4) au-dessus de la position de la surface soudée (2a) de l'élément en acier, et une perle (6) est formée à partir du matériau de soudage en aluminium sur les surfaces soudées de l'élément en acier (2) et de l'élément en aluminium (3).
PCT/JP2010/053924 2009-03-11 2010-03-09 Procédé de liaison de matériaux dissemblables WO2010104088A1 (fr)

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CN103182594A (zh) * 2011-12-31 2013-07-03 上海和达汽车配件有限公司 铝合金仪表板横梁焊接方法
CN109562490A (zh) * 2016-08-03 2019-04-02 示罗产业公司 混合焊接接头及其形成方法
CN110039209A (zh) * 2019-04-24 2019-07-23 首钢集团有限公司 一种异种金属的焊接方法

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US20120223057A1 (en) * 2011-03-02 2012-09-06 Lucian Iordache Gas tungsten arc welding using flux coated electrodes
CN105149750B (zh) * 2011-03-07 2017-05-03 株式会社神户制钢所 异种金属接合方法
EP3578290A4 (fr) * 2017-01-31 2020-02-19 Panasonic Intellectual Property Management Co., Ltd. Structure de jonction
JP7048355B2 (ja) * 2018-03-01 2022-04-05 株式会社神戸製鋼所 異材接合継手および異材接合方法
CN108581166B (zh) * 2018-04-10 2021-01-15 上海工程技术大学 铝/钢异种金属焊接中抑制Fe-Al金属间化合物层生成的方法

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JP2001047244A (ja) * 1999-08-03 2001-02-20 Laser Oyo Kogaku Kenkyusho:Kk 溶融溶接方法
JP2004223548A (ja) * 2003-01-21 2004-08-12 Daihen Corp アルミニウムと鉄鋼の接合方法
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JPS58100978A (ja) * 1981-12-09 1983-06-15 Mitsubishi Heavy Ind Ltd アルミニウム材とステンレスとの接合方法
JP2001047244A (ja) * 1999-08-03 2001-02-20 Laser Oyo Kogaku Kenkyusho:Kk 溶融溶接方法
JP2004223548A (ja) * 2003-01-21 2004-08-12 Daihen Corp アルミニウムと鉄鋼の接合方法
JP2005144500A (ja) * 2003-11-17 2005-06-09 Nissan Motor Co Ltd 異種材料の接合方法

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CN103182594A (zh) * 2011-12-31 2013-07-03 上海和达汽车配件有限公司 铝合金仪表板横梁焊接方法
CN103182594B (zh) * 2011-12-31 2015-05-27 上海和达汽车配件有限公司 铝合金仪表板横梁焊接方法
CN109562490A (zh) * 2016-08-03 2019-04-02 示罗产业公司 混合焊接接头及其形成方法
CN110039209A (zh) * 2019-04-24 2019-07-23 首钢集团有限公司 一种异种金属的焊接方法

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