WO2011155214A1 - Elément de liaison et son procédé de fabrication - Google Patents

Elément de liaison et son procédé de fabrication Download PDF

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Publication number
WO2011155214A1
WO2011155214A1 PCT/JP2011/003298 JP2011003298W WO2011155214A1 WO 2011155214 A1 WO2011155214 A1 WO 2011155214A1 JP 2011003298 W JP2011003298 W JP 2011003298W WO 2011155214 A1 WO2011155214 A1 WO 2011155214A1
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WIPO (PCT)
Prior art keywords
magnesium
aluminum
alloy
intermediate layer
interface
Prior art date
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PCT/JP2011/003298
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English (en)
Japanese (ja)
Inventor
英樹 山岸
昭二 餅川
Original Assignee
ワシマイヤー株式会社
富山県
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Priority to JP2012519278A priority Critical patent/JP5830727B2/ja
Publication of WO2011155214A1 publication Critical patent/WO2011155214A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • 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
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/02—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by means of a press ; Diffusion bonding
    • B23K20/023—Thermo-compression bonding
    • 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
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/16—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating with interposition of special material to facilitate connection of the parts, e.g. material for absorbing or producing gas
    • 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
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
    • B23K20/233—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded without ferrous layer
    • B23K20/2333—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded without ferrous layer one layer being aluminium, magnesium or beryllium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/017—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of aluminium or an aluminium alloy, another layer being formed of an alloy based on a non ferrous metal other than aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • 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
    • B23K2101/006—Vehicles
    • 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
    • B23K2103/08—Non-ferrous metals or alloys
    • B23K2103/15—Magnesium 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

Definitions

  • the present invention relates to a coupling member and a manufacturing method thereof, and more specifically, a coupling member that is lightweight and excellent in the joining property between a magnesium member and an aluminum member, and the coupling member can be easily manufactured, and the productivity is also improved.
  • the present invention relates to a method for manufacturing an excellent coupling member.
  • an aluminum alloy has excellent mechanical strength, whereas a magnesium alloy has a characteristic of being lightweight.
  • a coupling member having both of these characteristics.
  • a magnesium-aluminum clad material in which a magnesium alloy is used as an inner core material and the surface layer of the magnesium alloy is directly coated with aluminum or an alloy thereof by extrusion is known (for example, see Patent Document 1). Also, rolling, extruding, drawing, or compression processing is performed on one or a plurality of surfaces of the magnesium material or the magnesium alloy material so that the thickness is 0.1 to 10% of the vertical thickness of the magnesium material or the magnesium alloy material.
  • An aluminum-coated magnesium alloy material coated with a pure aluminum material or an aluminum alloy material is known (see, for example, Patent Document 2).
  • the magnesium-aluminum clad material described in Patent Document 1 and the aluminum-coated magnesium alloy material described in Patent Document 2 are both in a form in which the magnesium alloy is simply coated with an aluminum alloy.
  • the tensile strength (hereinafter also referred to as “joinability”) of the joint portion with the above is not sufficient.
  • Non-Patent Document 1 Although the tensile strength of the joint portion is relatively strong (tensile strength of about 115 MPa: Non-Patent Document 1), in practice, wire bonding or point bonding is used. Therefore, the bondability is insufficient. The friction stir welding method cannot be applied to the joining interface inside the member, and is difficult to apply to a three-dimensional curved surface. For this reason, processing takes time and it is difficult to cope with mass production.
  • the present invention has been made in view of the above circumstances, and although it is lightweight, it is easy to manufacture a coupling member excellent in bondability between a magnesium member and an aluminum member, and the coupling member, and is excellent in productivity. It aims at providing the manufacturing method of a coupling member.
  • the inventors of the present invention have intensively studied to solve the above-mentioned problems.
  • the joining interface is fine under a predetermined condition. It has been found that a mechanical joint interface is formed in addition to diffusion bonding, resulting in an anchor effect and greatly improving the joint strength. Based on this knowledge, it has been found that the above problem can be solved by providing an intermediate layer made of a predetermined metal between the magnesium member and the aluminum member, and the present invention has been completed.
  • the present invention is a coupling member comprising (1) a magnesium member made of a magnesium alloy, an aluminum member made of an aluminum alloy, and an intermediate layer formed between the magnesium member and the aluminum member.
  • the layer is made of at least one insert material selected from the group consisting of Ni, Cu, and Ti, and exists in the bonding member that is joined so that the magnesium member, the aluminum member, and the intermediate layer are integrated.
  • a first diffusion layer made of a magnesium alloy and an insert material is formed at the interface between the magnesium member and the intermediate layer, and an aluminum alloy is formed at the interface between the aluminum member and the intermediate layer. It exists in the coupling member of the said (1) description in which the 2nd diffused layer which consists of insert materials is formed.
  • the present invention includes (3) an interface between the magnesium member and the first diffusion layer, an interface between the first diffusion layer and the intermediate layer, an interface between the intermediate layer and the second diffusion layer, and an aluminum member and the second diffusion layer.
  • a mechanical joint by plastic flow is formed at the interface.
  • the present invention is (4) the method of manufacturing a coupling member according to any one of (1) to (3) above, wherein a magnesium alloy, an insert material made of Ti, and an aluminum alloy are overlapped, It exists in the manufacturing method of the coupling member which joins a magnesium member, an intermediate
  • the present invention provides (5) the method for producing a coupling member according to any one of (1) to (3) above, wherein a magnesium alloy, an insert material made of Ni or Cu, and an aluminum alloy are laminated.
  • the present invention resides in a method for manufacturing a bonding member that joins a magnesium member, an intermediate layer, and an aluminum member by heating in a range of 300 ° C. to 400 ° C. and pressurizing at 700 MPa to 750 MPa.
  • the present invention provides (6) the method for producing a bonded member according to (4) or (5) above, wherein after the magnesium member, the intermediate layer, and the aluminum member are joined, solution treatment and aging treatment are further performed. Exist.
  • the brittle aluminum and magnesium described above are provided by providing an intermediate layer made of at least one insert material selected from the group consisting of Ni, Cu and Ti between the magnesium member and the aluminum member. Since no intermetallic compound phase is formed, the bondability between the magnesium member and the aluminum member is excellent over the entire surface via the intermediate layer. Moreover, the said coupling member is excellent in the lightweight property resulting from a magnesium alloy, and is excellent in mechanical strength or corrosion resistance resulting from an aluminum alloy. For this reason, for example, when used for a wheel of an automobile or the like, it is preferable to reduce the weight by using an aluminum member as the outer side and a magnesium member as the inner side that are easily damaged in a corrosive environment. Furthermore, since the coupling member is surface-bonded, it can be applied to the bonding interface inside the member and can be applied to a three-dimensional curved surface.
  • a first diffusion layer made of a magnesium alloy and an insert material is formed at an interface between the magnesium member and the intermediate layer, and an aluminum alloy and an insert material are formed at the interface between the aluminum member and the intermediate layer.
  • bondability improves more.
  • plastic flow occurs at the interface between the magnesium member and the first diffusion layer, the interface between the first diffusion layer and the intermediate layer, the interface between the intermediate layer and the second diffusion layer, and the interface between the aluminum member and the second diffusion layer.
  • the area to be diffusion-bonded increases, so that the bondability is further improved.
  • the coupling member of the present invention since the coupling member is obtained simply by superimposing a magnesium alloy, a predetermined insert material, and an aluminum alloy and heating and pressing under a predetermined condition, the manufacturing is easy. And excellent in productivity. Further, when the solution treatment and the aging treatment are performed after joining, it is possible to suppress the aluminum alloy from being annealed, so that the joining property is reliably improved.
  • FIG. 1 is a cross-sectional view schematically showing a coupling member according to this embodiment.
  • FIG. 2 is a schematic enlarged sectional view of a portion P in FIG. In the coupling member which concerns on Example 1, it is a side view which shows the state which laminated
  • FIGS. 4 (a) to 4 (c) show the bonding member according to Example 1 from the state in which the magnesium alloy billet, the insert material, and the aluminum alloy billet are stacked to heat and press until the bonding member is obtained. It is explanatory drawing for demonstrating this process.
  • FIG. 5 is a graph showing the relationship between the tensile strength of the joint surface, the applied pressure during heating, and the heating temperature in Examples 1 to 11.
  • FIG. 5 is a graph showing the relationship between the tensile strength of the joint surface, the applied pressure during heating, and the heating temperature in Examples 1 to 11.
  • FIG. 6 is a graph showing the relationship between the tensile strength of the joint surface, the applied pressure during heating, and the heating temperature in Examples 12 to 20.
  • FIG. 7 is a graph showing the relationship between the tensile strength of the joining surface and the applied pressure during joining in Examples 21 to 25.
  • FIGS. 8A to 8C are photographs of secondary electron images obtained by a scanning electron microscope (SEM) on the joint surface of the coupling member according to the second embodiment.
  • FIG. 9 is a photograph of a secondary electron image obtained by a scanning electron microscope (SEM) on the joint surface of the coupling member according to Example 22.
  • FIG. 10A to FIG. 10F show the surface analysis results of the coupling member according to Example 2 using an X-ray microanalyzer (EPMA).
  • FIG. 11B show the surface analysis results of the coupling member according to Example 22 by X-ray microanalyzer (EPMA).
  • 12 (a) to 12 (d) show the results of line analysis by EPMA of the coupling member according to the second embodiment.
  • FIG. 13A is a line analysis result by EPMA of the coupling member according to Example 22.
  • FIG. 13B is a line analysis result by EPMA of the coupling member according to Example 22.
  • FIG. 14 shows the relationship between the heating temperature during bonding in the bonding member according to Comparative Example 1, the tensile strength of the obtained bonding member, and the thickness of the intermetallic compound phase composed of aluminum and magnesium formed at the bonding interface. It is a graph to show.
  • 15A and 15B are photographs of secondary electron images obtained by SEM of the coupling member according to Comparative Example 1.
  • FIG. 1 is a cross-sectional view schematically showing a coupling member according to this embodiment.
  • a coupling member 100 according to this embodiment includes a magnesium member 1 made of a magnesium alloy, an aluminum member 2 made of an aluminum alloy, and an intermediate layer inserted between the magnesium member 1 and the aluminum member 2. 3. That is, the coupling member 100 has a structure in which the magnesium member 1, the intermediate layer 3, and the aluminum member 2 are laminated in this order and joined together.
  • the magnesium member 1 is made of an alloy containing magnesium as a main component. For this reason, the coupling member 100 is lightweight, and the magnesium member 1 side has a feature that internal friction is large and vibration and impact are easily absorbed.
  • the additive element of the magnesium alloy include aluminum, zinc, calcium, and lithium. The characteristics of the magnesium alloy can be changed by adjusting the blending of these additive metals. Among these, it is preferable that an additive metal is aluminum and zinc from a versatility viewpoint.
  • the aluminum member 2 is made of an alloy mainly composed of aluminum. For this reason, the aluminum member 2 side is characterized by excellent mechanical strength.
  • the additive element of the aluminum alloy include copper, manganese, silicon, magnesium, zinc, nickel, and the like.
  • the characteristics of the aluminum alloy can be changed by adjusting the blending of these additive metals. Specifically, Al—Cu alloy (duralumin), Al—Mn alloy, Al—Si alloy, Al—Mg alloy, Al—Mg—Si alloy, Al—Zn—Mg alloy, Al— Zn-Mg-Cu based alloys and the like can be mentioned.
  • the intermediate layer 3 functions like an adhesive for joining the magnesium member 1 and the aluminum member 2.
  • the intermediate layer 3 is made of at least one insert material selected from the group consisting of Ni, Cu and Ti.
  • the thickness of the intermediate layer 3 is preferably 10 ⁇ m to 2 mm.
  • the thickness of the intermediate layer 3 is preferably 10 ⁇ m to 2 mm.
  • the thickness is less than 10 ⁇ m, compared with the case where the thickness is within the above range, for example, when the shape of the coupling member is an arc, a curved surface, a three-dimensional surface, etc., unevenness occurs in the applied pressure, and the magnesium member 1 And the aluminum member 2 may be insufficiently joined.
  • the thickness exceeds 2 mm, the characteristics of the magnesium member 1 and the aluminum member 2 may not be sufficiently exhibited as compared with the case where the thickness is within the above range, resulting in an increase in weight and cost. There are also drawbacks.
  • the bonding member 100 is provided with the intermediate layer 3 made of an insert material between the magnesium member 1 and the aluminum member 2, thereby connecting the magnesium member 1 and the aluminum member 2 via the intermediate layer 3. Is excellent over the entire surface.
  • FIG. 2 is a schematic enlarged sectional view of a portion P in FIG.
  • a first diffusion layer 11 made of a magnesium alloy and an insert material is formed at the interface between the magnesium member 1 and the intermediate layer 3.
  • a second diffusion layer 12 made of an aluminum alloy and an insert material is formed at the interface between the member 2 and the intermediate layer 3.
  • a mechanical joint 21 by plastic flow is formed at the interface between the magnesium member 1 and the first diffusion layer 11, and a machine by plastic flow is formed at the interface between the first diffusion layer 11 and the intermediate layer 3.
  • the mechanical joint 22 is formed at the interface between the intermediate layer 3 and the second diffusion layer 12, and the mechanical joint 23 by plastic flow is formed at the interface between the aluminum member 2 and the second diffusion layer 12.
  • a mechanical joint 24 is formed by plastic flow.
  • the mechanical joint means a fine concavo-convex part formed by plastic flow on the boundary surface, thereby exhibiting an anchor effect.
  • the coupling member 100 not only the first diffusion layer 11 and the second diffusion layer 12 are provided, but also the mechanical joints 21 to 24 that are fine plastic flow interfaces exhibit an anchor effect. Therefore, high strength surface bonding is achieved. In addition, in the formation of the plastic flow interface, the bonding strength is further improved by increasing the area to be diffusion bonded.
  • the bonding member 100 is formed by laminating a magnesium alloy, an insert material, and an aluminum alloy, and heating and pressurizing the magnesium member 1, the intermediate layer 3 made of the insert material, and an aluminum member made of the aluminum alloy. 2 is obtained by joining them so as to be integrated with each other.
  • a magnesium alloy, a sheet of at least one insert material selected from the group consisting of Ni, Cu and Ti, and an aluminum alloy are laminated.
  • the surface roughness (Rz) of the surface laminated with the insert material of the magnesium alloy is 10 ⁇ m or less
  • the surface roughness (Rz) of the surface laminated with the insert material of the aluminum alloy is 10 ⁇ m or less.
  • the surface is clean and has a natural oxide film level by polishing. In this case, the bonding strength is further improved.
  • the surface roughness (Rz) means a value measured according to JIS B0601 (2001).
  • the whole member is heated and pressed to form the first diffusion layer and the second diffusion layer on the bonding surface, whereby the coupling member 100 is obtained.
  • the mechanical joint it is preferable to form the mechanical joint by the fine plastic flow described above.
  • the insert material is Ni or Cu
  • the tensile strength of the joint surface reaches at least 115 MPa to 120 MPa
  • the insert material is Ti
  • the tensile strength of the joint surface reaches at least 154 MPa.
  • the heating temperature is preferably in the range of 200 ° C. to 450 ° C., more preferably in the range of 200 ° C. to 400 ° C., and in the range of 300 ° C. to 350 ° C. More preferably it is. If the temperature is lower than 200 ° C., the plastic flow may be reduced as compared with the case where the temperature is within the above range, resulting in insufficient bonding. Further, when the temperature exceeds 450 ° C., the diffusion reaction layer may grow more than necessary and the bonding may be insufficient as compared with the case where the temperature is within the above range.
  • the pressure applied is preferably in the range of 100 MPa to 700 MPa.
  • the pressure is less than 100 MPa, bonding may be insufficient as compared with the case where the pressure is within the above range, and when the pressure exceeds 700 MPa, the pressure is within the above range.
  • the plastic flow becomes too large, the insert material is broken, a brittle intermetallic compound is generated by the direct reaction between the magnesium alloy and the aluminum alloy, and the strength may be lowered due to the generation of defects such as cracks and Kirkendall voids.
  • the heating temperature is preferably in the range of 300 ° C to 400 ° C. If the temperature is lower than 300 ° C., the plastic flow may be reduced as compared with the case where the temperature is within the above range, resulting in insufficient bonding. Further, when the temperature exceeds 400 ° C., the diffusion reaction layer may grow more than necessary and the bonding may be insufficient as compared with the case where the temperature is within the above range.
  • the pressure applied is preferably in the range of 700 MPa to 750 MPa. If the pressure is less than 700 MPa, bonding may be insufficient as compared with the case where the pressure is within the above range, and if the pressure exceeds 750 MPa, the pressure is within the above range. Further, the plastic flow becomes too large, the insert material is broken, a brittle intermetallic compound is generated by the direct reaction between the magnesium alloy and the aluminum alloy, and the strength may be lowered due to the generation of defects such as cracks and Kirkendall voids.
  • a coupling member is obtained simply by laminating a magnesium member, an intermediate layer, and an aluminum member, and heating and pressing under predetermined conditions, the production is easy. Excellent productivity. That is, in the atmosphere, for example, three-dimensional surface bonding is possible in a short time of about 20 seconds, so that it is possible to improve mass productivity and reduce costs.
  • the coupling member according to the present embodiment has a two-layer structure of a magnesium member and an aluminum member, but may have three or more layers. That is, the aluminum member may be laminated on both surfaces of the magnesium member, and the magnesium member may be laminated on both surfaces of the aluminum member.
  • the joint surfaces of the magnesium alloy billet and the aluminum alloy billet were ground, polished with a SiC # 1000 abrasive paper, and further the surface was degreased with acetone.
  • a magnesium alloy billet 31, an intermediate layer 33, and an aluminum alloy billet 32 are laminated, and in order to fix them, connecting plate members 34 are bolted to the side surfaces of the magnesium alloy billet 31 and the aluminum alloy billet 32. 35 and screwed.
  • laminated body As shown in Table 1, the weight of the laminated magnesium alloy billet 31, intermediate layer 33 and aluminum alloy billet 32 (hereinafter simply referred to as “laminated body”) was about 27 kg. In Table 1, “-” means not measured.
  • a laminated body 36 is installed between a lower die 37 for flat pressing and an upper die 38 of a press machine having a pressurizing force of 9000 tons.
  • the laminate 36 was placed on the mold 37. Thereafter, the laminate was heated under the temperature conditions shown in Table 2 and pressurized for 20 seconds under the pressure conditions shown in Table 1 as shown in FIG. In Table 2, “-” means that no measurement was performed. And after natural cooling, it formed into the solution by heat processing and age-hardened, and the coupling member 40 shown to (c) of FIG. 4 was obtained.
  • the joining member of Example 2 using Ni as the insert material and having a heating temperature of 300 ° C. and a pressing force of 750 MPa exhibits a tensile strength of about 120 MPa at the maximum.
  • the joining members of Examples 12 to 17 using Cu as the insert material had a maximum tensile strength of about 100 MPa. It was found that when the insert material is Ni or Cu, it is not joined at a low temperature (tensile strength of 0 MPa), but it suddenly joins when a certain temperature is exceeded. This is thought to be related to the formation of a plastic flow interface. Further, it was found that the tensile strength tends to decrease conversely when the temperature is increased beyond the point at which the joining becomes abrupt.
  • the tensile strength ⁇ B 120 MPa or more was recorded even when the applied pressure was 100 MPa, 300 MPa, 500 MPa, and 700 MPa. From these results, it was found that Ti was the most excellent insert material compared to Ni and Cu (not only the tensile strength but also the tolerance of the processing range).
  • FIG. 5 shows the relationship between the tensile strength of the joint surface in Examples 1 to 11 and the applied pressure and heating temperature at the time of joining, and the tensile strength of the joined surface in Examples 12 to 20, the applied pressure and heating at the time of joining.
  • FIG. 6 shows the relationship with temperature
  • FIG. 7 shows the relationship between the tensile strength of the joint surface in Examples 21 to 25 and the applied pressure during joining. In addition, in FIG. 7, the value with the higher result of the tensile strength shown in Table 3 is shown.
  • FIG. 8 is a photograph of the joining part of a magnesium member, an intermediate
  • FIG. 8B is a photograph of a joint portion between the magnesium member and the intermediate layer (Ni) having a measurement scale of 20 ⁇ m.
  • (C) of FIG. 8 is a photograph of the joint portion between the intermediate layer and the aluminum member having a measurement scale of 20 ⁇ m.
  • the description of arrows Line1 and Line2 indicates the joint surface and the measurement direction of the line analysis described later.
  • the upper part of the photograph is a magnesium alloy (AZ80), the central part is an insert material Ti, and the lower part is an aluminum alloy (A2017, duralumin).
  • the measurement scale is 100 ⁇ m.
  • FIG. 10 (a) to 10 (c), the measurement scale is 5 ⁇ m, the upper side is a magnesium member, and the lower side is an intermediate layer (Ni).
  • (a) of FIG. 10 is a secondary electron image.
  • FIG. 10B is a reflected electron image.
  • FIG. 10 is a surface analysis result of magnesium.
  • FIG. 10D shows the Ni surface analysis results.
  • E) of FIG. 10 is a surface analysis result of aluminum.
  • (F) of FIG. 10 is an oxygen surface analysis result. From FIG.
  • the measurement scale is 5 ⁇ m.
  • 11A is a surface analysis result of the joint surface between the magnesium alloy AZ80 and the insert material Ti along the Line 1 in FIG. 9, where SL is a secondary electron image, and CP is a reflected electron. It is a statue. Mg, Ti, Al, and O represent each element analyzed.
  • Mg in FIG. 11 (a) the upper part is a magnesium alloy AZ80 and the lower part is an insert material Ti. A thin diffusion layer and a fine plastic flow interface are formed at the interface (anchor effect). Looking at the phase diagram of the binary system, it is considered that these diffusion reactions are small because Ti has very little mutual dissolution with Mg.
  • the diffusion reaction in this case is considered to be mainly the Al component and Ti in the Mg alloy. That is, it is considered that the use of Ti for the insert material can suppress the growth of the fragile Mg reaction layer as much as possible, thereby obtaining a high-strength diffusion layer.
  • the upper surface portion is Ti and the lower surface portion is an aluminum alloy. A diffusion reaction is observed at the bonding interface.
  • the upper part is Ti and the lower part is an aluminum alloy.
  • formation of a good diffusion layer that is thin and free from defects was confirmed.
  • FIG. 12 is a line analysis corresponding to (c) of FIG. 10, and shows the analysis result of magnesium.
  • the scanning direction is perpendicular to the interface from the magnesium alloy side to the Ni insert material direction.
  • the vertical axis represents the intensity of the generated characteristic X-ray, and the horizontal axis represents the scanning distance (mm).
  • the horizontal axis of the graph is one scale of 0.001 mm (1 ⁇ m), and shows a boundary portion between a portion where magnesium is present and a portion where magnesium is not present. That is, it is a portion where a diffusion layer with nickel (Ni) can be read.
  • FIG. 12B shows the result of nickel line analysis. It can be seen that a magnesium member and a diffusion layer of about 1 ⁇ m are formed.
  • FIG. 12 is a line analysis result of aluminum.
  • FIG. 12 (d) shows the results of oxygen line analysis. It can be confirmed that the oxide layer Q is detected. Note that this portion corresponds to the oxide layer shown in FIG. The thickness of the oxide layer was about 10 ⁇ m.
  • FIG. 13A is performed along Line 1 in FIG. 9, and FIG. 13B is performed along Line 2 in FIG.
  • CP indicates the reflected electron intensity.
  • Mg, Ti, Al, and O represent the element symbols analyzed.
  • the horizontal axis is the scanning distance, and the unit is (mm).
  • FIG. 13A shows that the diffusion layer is about 2 ⁇ m.
  • Magnesium has low mutual solubility with Ti.
  • reaction with Mg is suppressed as much as possible, while thin and good diffusion layers can be obtained by mainly reacting with Al in the magnesium alloy.
  • a high-strength joint interface can be formed together with a fine plastic flow interface (a synergistic effect of mechanical joining (anchor effect) and metallurgical joining (diffusion reaction)). From the results of the oxygen line analysis, it can be understood that the formation of a fragile oxide layer is very small in Ti compared to Ni (FIG. 12) (contributes to high strength).
  • FIG. 13B shows that a thin and good diffusion layer is formed between Ti and Al at the bonding interface between the insert material (Ti) and A2017.
  • the thickness of the diffusion reaction layer seems to be around 1 ⁇ m (very thin with a resolution determined by the region where characteristic X-rays are generated). It can also be seen that there is almost no generation of oxide at the bonding interface.
  • Example 1 A coupling member was obtained in the same manner as in Example 1 except that the insert material serving as the intermediate layer was not used. That is, a magnesium alloy (AZ80) and an aluminum alloy (A6151) are directly brought into contact with each other to form a laminate, and the laminate temperature is set to 360 ° C., 385 ° C., 400 ° C., and 420 ° C. Went.
  • a magnesium alloy (AZ80) and an aluminum alloy (A6151) are directly brought into contact with each other to form a laminate, and the laminate temperature is set to 360 ° C., 385 ° C., 400 ° C., and 420 ° C. Went.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Laminated Bodies (AREA)

Abstract

La présente invention a pour objet de fournir un élément de liaison qui est léger et qui présente une meilleure capacité de liaison d'un élément de magnésium et d'un élément d'aluminium, et un procédé de fabrication pour l'élément de liaison permettant la fabrication simple et selon une productivité élevée dudit élément de liaison. La présente invention concerne un élément de liaison (100) présentant un élément de magnésium (1) comprenant un alliage de magnésium, un élément d'aluminium (2) comprenant un alliage d'aluminium, et une couche intermédiaire (3) formée entre l'élément de magnésium (1) et l'élément d'aluminium (2) ; la couche intermédiaire (3) comprenant un matériau d'insertion sélectionné parmi un groupe comprenant du Ni, Cu et Ti, et l'élément de magnésium (1), l'élément d'aluminium (2) et la couche intermédiaire (3) étant liés d'une seule pièce.
PCT/JP2011/003298 2010-06-10 2011-06-10 Elément de liaison et son procédé de fabrication WO2011155214A1 (fr)

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CN104780739A (zh) * 2014-01-09 2015-07-15 株式会社新王材料 机壳和便携设备
JP2015202680A (ja) * 2014-04-16 2015-11-16 株式会社Ｎｅｏｍａｘマテリアル クラッド材およびクラッド材の製造方法
JP6135835B1 (ja) * 2015-12-28 2017-05-31 日立金属株式会社 クラッド材および電子機器用筐体
WO2017110001A1 (fr) 2015-12-25 2017-06-29 技術研究組合次世代３Ｄ積層造形技術総合開発機構 Dispositif de fabrication additive tridimensionnelle, procédé de commande de dispositif de fabrication additive tridimensionnelle, et programme de commande de dispositif de fabrication additive tridimensionnelle
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CN110461529A (zh) * 2017-04-14 2019-11-15 旭化成株式会社 含有阻燃镁合金层的异种接头材料
CN111226315A (zh) * 2017-10-27 2020-06-02 三菱综合材料株式会社 接合体、自带散热器的绝缘电路基板及散热器
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CN104780739A (zh) * 2014-01-09 2015-07-15 株式会社新王材料 机壳和便携设备
JP2015128883A (ja) * 2014-01-09 2015-07-16 株式会社Ｎｅｏｍａｘマテリアル シャーシおよび携帯機器
KR101760557B1 (ko) * 2014-01-09 2017-07-31 히타치 긴조쿠 가부시키가이샤 섀시 및 휴대 기기
JP2015202680A (ja) * 2014-04-16 2015-11-16 株式会社Ｎｅｏｍａｘマテリアル クラッド材およびクラッド材の製造方法
US10239305B2 (en) 2015-12-25 2019-03-26 Technology Research Association For Future Additive Manufacturing Three-dimensional laminating and shaping apparatus, control method of three-dimensional laminating and shaping apparatus, and control program of three-dimensional laminating and shaping apparatus
WO2017110001A1 (fr) 2015-12-25 2017-06-29 技術研究組合次世代３Ｄ積層造形技術総合開発機構 Dispositif de fabrication additive tridimensionnelle, procédé de commande de dispositif de fabrication additive tridimensionnelle, et programme de commande de dispositif de fabrication additive tridimensionnelle
WO2017115661A1 (fr) * 2015-12-28 2017-07-06 日立金属株式会社 Matériau de gainage et boîtier pour dispositifs électroniques
CN107206747A (zh) * 2015-12-28 2017-09-26 日立金属株式会社 包层材料和电子设备用壳体
JP6135835B1 (ja) * 2015-12-28 2017-05-31 日立金属株式会社 クラッド材および電子機器用筐体
US10532422B2 (en) 2015-12-28 2020-01-14 Hitachi Metals, Ltd. Clad material and electronic device housing
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CN110461529B (zh) * 2017-04-14 2022-02-25 旭化成株式会社 含有阻燃镁合金层的异种接头材料
US11534871B2 (en) 2017-04-14 2022-12-27 Asahi Kasei Kabushiki Kaisha Dissimilar metal joint including flame-retardant magnesium alloy layer
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CN111226315B (zh) * 2017-10-27 2023-06-06 三菱综合材料株式会社 接合体、自带散热器的绝缘电路基板及散热器
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WO2020184489A1 (fr) * 2019-03-14 2020-09-17 日立金属株式会社 Matériau plaqué de magnésium, boîtier pour dispositifs électroniques, et composant pour objets mobiles
JPWO2020184489A1 (fr) * 2019-03-14 2020-09-17
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US11931821B2 (en) 2019-03-14 2024-03-19 Proterial, Ltd. Magnesium clad material, electronic device housing, and mobile object component

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