JP6364910B2 - Clad material and method for producing the clad material - Google Patents

Description

  The present invention relates to a clad material and a method for producing the clad material, and in particular, a clad material in which a layer composed of an Mg-based alloy and a layer composed of an Al-based alloy are joined via an intermediate layer, and the clad material It relates to a manufacturing method.

  When a clad material is produced by joining an Mg layer composed of an Mg-based alloy and an Al layer composed of an Al-based alloy, the Mg layer and the Al layer are interposed via an intermediate layer because of low adhesion. It is known to join (for example, refer to Patent Document 1).

  In Patent Document 1, an Mg layer made of an Mg-based alloy, an Al layer made of an Al-based alloy, and an intermediate layer made of an Ag-based alloy or a Cu-based alloy are arranged between the Mg layer and the Al layer. A cladding material is disclosed. Further, in Patent Document 1, as another example, as the intermediate layer, a two-layer intermediate layer in which a layer made of Au, Pt, or Pd is formed on the Mg layer side of a layer made of an Ag-based alloy or a Cu-based alloy. A clad material using is disclosed. Further, in Patent Document 1, as another example, a layer made of Cd, Zn, Sn, or Pb having a low melting point is formed on at least one surface of a layer made of an Ag-based alloy or a Cu-based alloy as the intermediate layer. A clad material using an intermediate layer composed of two or three layers is disclosed.

JP-A-6-328617

  However, among the clad materials described in Patent Document 1, a clad material using an Ag-based alloy as an intermediate layer is considered to be impractical because the raw material cost of the clad material increases because the Ag-based alloy is expensive. .

  In addition, in a clad material using only a Cu-based alloy layer as an intermediate layer, the bonding strength between the Cu-based alloy intermediate layer and the Mg layer is small, and as a result, the intermediate layer made of the Cu-based alloy is bonded via the intermediate layer. The inventor of the present application has found that there is a problem that peeling is likely to occur between the Mg layer and the Al layer.

  Furthermore, a clad material using a two-layer intermediate layer composed of a Cu-based alloy layer and a layer composed of Au, Pt or Pd as an intermediate layer can be industrially put into practical use for any of Au, Pt and Pd. It is considered impractical because it is more expensive than possible.

  In addition, Cd and Pb are restricted in terms of environmental use in a clad material using an intermediate layer composed of two or three layers of a Cu-based alloy layer and a Cd or Pb layer as the intermediate layer. It is considered impractical.

  In addition, in a clad material using an intermediate layer composed of two or three layers of a Cu-based alloy layer and a Zn or Sn layer as the intermediate layer, the melting points of Zn and Sn were 420 ° C. and 232 ° C., respectively. Since the melting point is low, for example, when a clad material is produced by hot rolling, there is a problem that it is easily melted during hot rolling, and during the hot rolling, steam of Zn or Sn is generated and the heating furnace There is also a problem of contamination. For this reason, it is considered that a clad material using Zn and Sn is not practical.

  Therefore, the present invention has been made to solve the above-described problems, and an object of the present invention is to provide an Mg layer (a layer composed of an Mg-based alloy) and an Al layer (constructed from an Al-based alloy). To suppress peeling by increasing the bonding strength with the layer), to be industrially practical and low cost, to be environmentally friendly, and to be easy to manufacture, It is providing the clad material which satisfy | fills all these requirements, and the manufacturing method of the clad material.

As a result of intensive studies to solve the above problems, the present inventor has found that the above problems can be solved by the following configuration. That is, the clad material according to the first aspect of the present invention is disposed between the first layer made of an Mg-based alloy, the second layer made of an Al-based alloy, and the first layer and the second layer. And at least a third layer composed of a Ni-based alloy or a Fe-based alloy for joining the first layer and the second layer, and the third layer is composed of a Ni-based alloy having a thickness of 8 μm or less. dolphins, or that is composed of Fe-based alloy.

  The “Mg-based alloy” of the present invention includes pure Mg, and includes Mg alloys such as Mg—Al alloy, Mg—Al—Zn alloy, and Mg—Li alloy. Further, the “Al-based alloy” of the present invention includes A1000 series pure Al, for example, Al alloys such as A4000 series Al—Si alloys and A5000 series Al—Mg alloys. The “Ni-based alloy” of the present invention includes pure Ni such as NW2200 and NW2201, and includes Ni alloys such as Ni—Cu alloy and Ni—Cr alloy, for example. The “Fe-based alloy” of the present invention includes pure Fe such as low carbon steel, and includes, for example, Fe—Ni alloy and Fe alloy such as stainless steel.

  In the cladding material according to the first aspect of the present invention, as described above, the first layer and the second layer are provided between the first layer composed of the Mg-based alloy and the second layer composed of the Al-based alloy. By providing a third layer composed of a Ni-base alloy or a Fe-base alloy that joins to each other, the Ni-base alloy or the Fe-base alloy can exhibit high joint strength with respect to both the Mg-base alloy and Al-base alloy In addition, an Mg—Al clad material having a higher bonding strength than a clad material using a conventional Cu-based alloy as an intermediate layer (third layer) can be obtained. As a result, it is possible to suppress the occurrence of peeling in the Mg—Al clad material. This effect has been confirmed by experiments to be described later. Further, since the Ni-based alloy or the Fe-based alloy has a higher melting point than Zn and Sn, there is no melting in the heating furnace or contamination of the heating furnace, and as a result, a clad material can be easily produced. Further, unlike Au, Pt, and Pd, Ni-based alloys or Fe-based alloys are inexpensive at a level that can be put into practical use industrially. Furthermore, unlike Cd and Pb, Ni-based alloys or Fe-based alloys have no environmental restrictions. As a result, the third layer joining the first layer and the second layer is made of a Ni-based alloy or a Fe-based alloy, so that an Mg layer (a first layer made of an Mg-based alloy) and an Al layer ( Increase the bonding strength with the second layer made of an Al-based alloy to suppress delamination, be inexpensive enough to be industrially practical, and have no environmental restrictions It is possible to provide a clad material that satisfies all the requirements of being easy to manufacture.

  In the cladding material according to the first aspect, the third layer is preferably made of a Ni-based alloy. Here, when the third layer is made of a material with low ductility, it is caused by the rolling at the time of producing the clad material and simultaneously with the second layer made of an Al-based alloy having high ductility. And it becomes easy to generate | occur | produce a wave | undulation (a thick part and a thin part) in a 3rd layer, and it becomes easy to fracture | rupture. Therefore, if configured as described above, the Ni-based alloy is generally more likely to be plastically deformed and has higher ductility than the Fe-based alloy, and therefore, undulation is generated in the third layer during rolling when producing the clad material. Can be suppressed. Thereby, even when the thickness of the third layer is small, breakage of the third layer can be suppressed.

  In the clad material according to the first aspect, preferably, the thickness of the first layer is larger than the thickness of the second layer and larger than the thickness of the third layer. If comprised in this way, since the ratio for which the 1st layer comprised from a lightweight Mg-based alloy accounts can be enlarged, a cladding material can be reduced more in weight.

  In this case, the thickness of the first layer is preferably 50% or more of the thickness of the clad material. If comprised in this way, since the ratio for which the 1st layer comprised from a lightweight Mg-based alloy accounts can be enlarged reliably, a cladding material can be further reduced in weight.

  In a configuration in which the thickness of the first layer is greater than the thickness of the second layer and greater than the thickness of the third layer, the thickness of the third layer is preferably equal to or less than the thickness of the second layer. If configured in this way, the proportion of the third layer composed of the Ni-based alloy or Fe-based alloy having a specific gravity greater than that of the Mg-based alloy and Al-based alloy can be reduced, so the weight of the clad material can be reduced. can do.

  In the cladding material according to the first aspect, preferably, the thickness of the third layer is 4% or less of the thickness of the cladding material. If comprised in this way, since the ratio for which a 3rd layer accounts can be made small reliably, a clad material can be further reduced in weight.

In the cladding material according to the first aspect, preferably, the fourth layer made of an Al-based alloy is disposed between the first layer and the fourth layer, and joins the first layer and the fourth layer. fifth layer and further comprising a that, the fifth layer, or and a Ni-base alloy having a thickness of less than 8 [mu] m, or, that is composed of Fe-based alloy. If comprised in this way, it can suppress that peeling arises in the Mg-Al clad material which has a layer structure of five layers or more. Further, since the first layer can be sandwiched between the second layer and the fourth layer, both of which are made of an Al-based alloy, the clad material is warped due to the difference in ductility between the Mg-based alloy and the Al-based alloy. It can be suppressed from occurring.

  In the clad material including the fourth layer and the fifth layer, preferably, the third layer and the fifth layer are made of a Ni-based alloy. With this configuration, since the variation in the thickness of the third layer and the thickness of the fifth layer can be reduced, the third layer and the fifth layer can be obtained even when the thickness of the third layer and the fifth layer is small. Can be prevented from breaking.

  In the cladding material according to the first aspect, preferably, the specific gravity of the cladding material is 2.43 or less, and more preferably, the specific gravity of the cladding material is 2.16 or less. If comprised in this way, the specific gravity of a clad material can be made small enough and reduced in weight rather than using the Al base alloy whose specific gravity is about 2.7 alone.

Method for producing a clad material according to the second aspect of the present invention includes a first 1Al plate composed of Al-based alloy, a Ni-based alloy or Fe-based alloy gold that consists first bonding sheet, Mg based alloys And a first Al plate made of an Mg-based alloy by rolling the first Al plate, the first bonding plate, and the Mg plate at a rolling reduction of 45% or more. a layer, a second layer composed of Al-based alloy, is disposed between the first and second layers, a clad material and a third layer you join the first and second layers look including a step of preparing, the third layer, or and a Ni-base alloy having a thickness of less than 8 [mu] m, or, and a Fe-based alloy.

In the method for producing a clad material according to the second aspect of the present invention, as described above, the clad material is disposed between the first layer composed of the Mg-based alloy and the second layer composed of the Al-based alloy. by making clad material and a layer of Ni-based alloy or Fe-based alloy gold that consists third layer for bonding the second layer, Ni-based alloy or Fe-based alloy gold Mg based alloys and Al Since a high bonding strength can be exhibited with respect to both of the base alloys, an Mg—Al cladding material having a higher bonding strength than a cladding material using a conventional Cu-based alloy as an intermediate layer (third layer) can be obtained. . As a result, it is possible to suppress the occurrence of peeling in the Mg—Al clad material. Further, Ni-based alloy or Fe-based alloy gold, because both a higher melting point as compared with Zn and Sn, there is no contamination of the melting and heating furnace in the heating furnace, as a result, it is possible to easily produce a clad material . Further, Ni-based alloy or Fe-based alloy gold, Au, is a low cost levels that can be industrially practical unlike Pt and Pd. Further, Ni-based alloy or Fe-based alloy gold, there is no use restrictions in environmental Unlike Cd and Pb. These results, by a third layer for joining the first and second layers constituting the Ni-based alloy or Fe-based alloy gold or al, Mg layer (first layer comprised of Mg based alloy) and Al Increased bonding strength with the layer (second layer made of Al-based alloy) to suppress delamination, low price at a level that can be commercialized industrially, and environmental restrictions It is possible to provide a clad material that satisfies all the requirements of absence, easy manufacture. Furthermore, by rolling at a rolling reduction of 45% or more, the adhesion between the first layer and the third layer and the adhesion between the second layer and the third layer can be reliably increased. Moreover, it can suppress that peeling arises. This effect has been confirmed by experiments to be described later.

In the method for manufacturing a clad material according to the second aspect, preferably, the step of laminating a plate member, a first 1Al plate composed of Al-based alloy, Ni-based alloy or Fe-based alloy gold that consists first and bonding the plate material, and Mg plate composed of Mg-based alloy, a Ni-based alloy or Fe-based alloy gold that consists second bonding sheet and a second 2Al plate composed of Al-based alloy in this order The step of producing a clad material by rolling, including a step of laminating, is performed by rolling the first Al plate, the first bonding plate, the Mg plate, the second bonding plate, and the second Al plate at a rolling reduction of 45% or more. By doing so, the first layer composed of the Mg-based alloy, the second layer composed of the Al-based alloy, the first layer and the second layer are disposed between the first layer and the second layer, a third layer you joining, is composed of Al-based alloy That a fourth layer is disposed between the first layer and the fourth layer, it viewed including the steps of producing a clad material and a fifth layer you join the first layer and the fourth layer, the fifth The layer is made of a Ni-based alloy having a thickness of 8 μm or less, or made of a Fe-based alloy . If comprised in this way, it can suppress that peeling arises in the clad material which has a layer structure of five layers or more. Further, since the first layer can be sandwiched between the second layer and the fourth layer, both of which are made of an Al-based alloy, the clad material is warped due to the difference in ductility between the Mg-based alloy and the Al-based alloy. It can be suppressed from occurring.

  In the method for producing a clad material according to the second aspect, preferably, the step of producing the clad material by rolling is performed by subjecting the Al plate material, the joining plate material, and the Mg plate material to a temperature condition of 250 ° C. or higher and 450 ° C. or lower. And a step of hot rolling at a rolling reduction of 45% or more. If constituted in this way, the ductility of the Mg-based alloy is low under a temperature condition of less than 250 ° C., so that when the rolling is performed at a rolling reduction of 45% or more, it is possible to prevent the first layer from being cracked. it can. In addition, the Mg-based alloy can be prevented from being chemically unstable due to the temperature condition higher than 450 ° C.

  According to the present invention, as described above, the bonding strength between the Mg layer (first layer composed of Mg-based alloy) and the Al layer (second layer composed of the Al-based alloy) is increased to cause peeling. Clad material that satisfies all the requirements of suppression, low price that can be industrially put into practical use, no environmental restrictions, and easy manufacture A manufacturing method can be provided.

It is sectional drawing which showed the clad material by one Embodiment of this invention. It is a schematic diagram for demonstrating the manufacturing method of the clad material by one Embodiment of this invention. It is a figure for demonstrating the peeling test of the clad material by 1st Embodiment of this invention. It is a figure for demonstrating the peeling test of the clad material by 1st Embodiment of this invention. It is the table | surface which showed the result of the experiment 1 performed in order to confirm the effect of this invention. It is a cross-sectional photograph of the comparative example 1 of the experiment 1 performed in order to confirm the effect of this invention. It is a cross-sectional photograph of Example 1 of Experiment 1 performed in order to confirm the effect of this invention. It is a cross-sectional photograph of Example 2 of Experiment 1 performed in order to confirm the effect of this invention. It is a cross-sectional photograph of Example 3 of Experiment 1 conducted to confirm the effect of the present invention. It is a cross-sectional photograph of the comparative example 2 of the experiment 1 performed in order to confirm the effect of this invention. It is the table | surface which showed the result of the experiment 2 performed in order to confirm the effect of this invention. It is a cross-sectional photograph of Example 11 of Experiment 2 performed to confirm the effect of the present invention. It is a cross-sectional photograph of Example 12 of Experiment 2 conducted to confirm the effect of the present invention. It is a cross-sectional photograph of Example 13 of Experiment 2 conducted to confirm the effect of the present invention. It is the table | surface which showed the result of the experiment 3 performed in order to confirm the effect of this invention. It is sectional drawing which showed the clad material by the modification of one Embodiment of this invention.

  DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiments embodying the present invention will be described below with reference to the drawings.

  First, with reference to FIG. 1, the structure of the clad material 1 by one Embodiment of this invention is demonstrated.

  The clad material 1 according to an embodiment of the present invention is a metal material used as a structural member of a transport device such as an automobile or a mobile device such as a mobile phone. As shown in FIG. 1, the clad material 1 includes an Mg core material layer 10, an Al layer disposed on a surface layer on one side (Z1 side) and a surface layer on the other side (Z2 side) in the thickness direction (Z direction). Layers 11 and 12, an intermediate layer 13 disposed between the Mg core layer 10 and the Al layer 11 on the Z1 side, and an intermediate layer disposed between the Mg core layer 10 and the Al layer 12 on the Z2 side Layer 14. The Mg core material layer 10, the Al layer 11, the intermediate layer 13, the Al layer 12 and the intermediate layer 14 are respectively “first layer”, “second layer”, “third layer”, “first layer” of the present invention. It is an example of “fourth layer” and “fifth layer”.

  The clad material 1 has a five-layer structure in which an Al layer 11, an intermediate layer 13, an Mg core material layer 10, an intermediate layer 14 and an Al layer 12 are laminated in this order from the Z1 side toward the Z2 side. have. Further, in the clad material 1, the layers in contact with each other are firmly bonded by atomic diffusion or compound formation. That is, the Al layer 11 and the intermediate layer 13 are firmly bonded at the bonding interface 1a, and the intermediate layer 13 and the Mg core material layer 10 are firmly bonded at the bonding interface 1b. The layer 11 and the Mg core material layer 10 are firmly bonded. Similarly, the Al layer 12 and the intermediate layer 14 are firmly bonded at the bonding interface 1c, and the intermediate layer 14, the Mg core material layer 10 and the bonding interface 1d are firmly bonded to each other through the intermediate layer 14. The Al layer 12 and the Mg core material layer 10 are firmly joined.

  The clad material 1 is formed in a flat plate shape by hot rolling.

  Moreover, the specific gravity of the clad material 1 is smaller than the specific gravity (about 2.7) of the plate material of A1050 which is generally used Al. The specific gravity of the clad material 1 is preferably about 2.61 or less, more preferably about 2.43 (about 90% of the specific gravity of A1050) or less. The specific gravity of the clad material 1 is more preferably about 2.3 or less, and still more preferably about 2.16 (about 80% of the specific gravity of A1050) or less.

  The Mg core material layer 10 is composed of an Mg-based alloy. As the Mg-based alloy, pure Mg or Mg alloy can be used. Examples of the Mg alloy include AZ31 (Mg—Al—Zn alloy composed of 3% by mass of Al, 1% Zn, the balance Mg and inevitable impurity elements) and AZ61 (6% by mass of Al and 1% of Zn). Mg—Al—Zn alloy such as Mg—Al—Zn alloy consisting of Mg and the balance Mg and unavoidable impurity elements, AZ80 (8% by mass of Al, less than 1% Zn, the balance Mg and unavoidable impurity elements) Mg-Al alloy, Mg-Li alloy, and the like can be used. Further, the Mg-based alloy constituting the Mg core material layer 10 preferably has a smaller specific gravity. Here, the specific gravity of AZ31 as an example of the Mg-based alloy is about 1.8.

  Both the Al layers 11 and 12 located on the surface layer of the clad material 1 are made of an Al-based alloy that is superior in corrosion resistance to an Mg-based alloy and that can be easily surface processed by anodizing. As the Al-based alloy, pure Al such as A1050 composed of 99.5% by mass or more of Al and other elements, or Al-2Si (from 2% by mass of Si, the remaining Al and inevitable impurity elements). Al-Si alloys such as A4000 series such as Al-Si alloys, and Al-Mg alloys such as A5000 series can be used. Further, as the Al-based alloy constituting the Al layers 11 and 12, it is preferable to use pure Al having high ductility. Further, the specific gravity of the Al-based alloy constituting the Al layers 11 and 12 is larger than the specific gravity of the Mg-based alloy constituting the Mg core material layer 10. Here, the specific gravity of A1050 as an example of the Al-based alloy is about 2.7.

  In addition, the Al layers 11 and 12 are preferably made of an Al-based alloy having substantially the same composition. This eliminates the need to strictly distinguish the front and back of the clad material 1.

  The intermediate layers 13 and 14 are made of a Ni-base alloy, a Fe-base alloy, or a Ti-base alloy joining metal that is less expensive than Ag-base alloys and Au-base alloys. The intermediate layers 13 and 14 are preferably made of a Ni-base alloy or Fe-base alloy that is less expensive than the Ti-base alloy, and more preferably made of a Ni-base alloy that easily undergoes plastic deformation.

  As the Ni-based alloy, pure Ni such as NW2200 and NW2201, or Ni alloy such as Ni—Cu alloy and Ni—Cr alloy can be used. As the Fe-based alloy, pure Fe such as low carbon steel, Fe-Ni alloy, or Fe alloy such as stainless steel can be used. In addition, as the Ti-based alloy, pure Ti such as TP270 or Ti alloy such as Ti—Al alloy can be used.

  The specific gravity of the joining metal (Ni-based alloy, Fe-based alloy or Ti-based alloy) constituting the intermediate layers 13 and 14 is the same as that of the Mg-based alloy constituting the Mg core material layer 10 and the Al layers 11 and 12. It is larger than the specific gravity of the Al-based alloy to be constructed. The specific gravity of NW2201 as an example of a Ni-based alloy is about 8.9, the specific gravity of a low carbon steel as an example of an Fe-based alloy is about 7.9, and TP270 as an example of a Ti-based alloy. The specific gravity is about 4.5.

  Further, the melting point of the joining metal (Ni-base alloy, Fe-base alloy or Ti-base alloy) constituting the intermediate layers 13 and 14 is higher than about 450 ° C. which is the upper limit of the temperature condition T during hot rolling described later. . Specifically, the melting point of NW2201 as an example of a Ni-based alloy is about 1450 ° C., and the melting point of low-carbon steel as an example of an Fe-based alloy is about 1540 ° C. The melting point of TP270 is about 1670 ° C.

  The intermediate layers 13 and 14 are preferably made of the same type of metal (for example, Ni-based alloy) among Ni-based alloys, Fe-based alloys, and Ti-based alloys. Furthermore, it is more preferable that the intermediate layers 13 and 14 are made of a metal (for example, NW2201) having substantially the same composition.

  In the present embodiment, the thickness t2 of the Mg core material layer 10 having a small specific gravity in the thickness direction (Z direction) of the cladding material 1 is the thickness t3 of the Al layer 11, the thickness t4 of the Al layer 12, and the intermediate layer 13. It is formed to be larger than any of the thickness t5 and the thickness t6 of the intermediate layer 14. The thickness t2 is about 50% or more of the thickness t1 (= t2 + t3 + t4 + t5 + t6) of the clad material 1 having a five-layer structure. The thickness t2 is preferably about 75% or more of the thickness t1, and more preferably about 90% or more.

  Further, the thickness t5 of the intermediate layer 13 and the thickness t6 of the intermediate layer 14 having large specific gravity are both less than the thickness t2 of the Mg core material layer 10, the thickness t3 or less of the Al layer 11, and the thickness t4 or less of the Al layer 12. It is formed to become. In order to reduce the specific gravity of the entire cladding material 1, the thicknesses t5 and t6 are preferably less than t2, less than t3, and less than t4. The thicknesses t5 and t6 are both preferably about 4% or less of the thickness t1 of the clad material 1. The thicknesses t5 and t6 are both preferably about 3% or less of the thickness t1 and more preferably about 1.5% or less.

  The thickness t3 of the Al layer 11 and the thickness t4 of the Al layer 12 are both about 25% or less of the thickness t1 of the clad material 1.

  The thickness t3 of the Al layer 11 and the thickness t4 of the Al layer 12 are preferably substantially the same, and the thickness t5 of the intermediate layer 13 and the thickness t6 of the intermediate layer 14 are preferably substantially the same.

  In the present embodiment, the following effects can be obtained.

  In the present embodiment, as described above, by providing the intermediate layer 13 made of a Ni-based alloy, a Fe-based alloy, or a Ti-based alloy between the Mg core material layer 10 and the Al layer 11 on the Z1 side, Ni Since the base alloy, Fe base alloy or Ti base alloy can exhibit high joint strength to both Mg base alloy and Al base alloy, it has higher joint strength than clad materials using conventional Cu base alloy as an intermediate layer. It is possible to obtain the Mg—Al clad material 1 having the same. As a result, it is possible to suppress the occurrence of peeling in the Mg—Al clad material 1. In addition, the effect that this peeling can be suppressed is very important in the clad material 1 used as a structural member. In addition, since Ni-based alloys, Fe-based alloys or Ti-based alloys have higher melting points than Zn and Sn, there is no melting in the heating furnace or contamination of the heating furnace, and as a result, the clad material 1 is easily produced. can do. Further, unlike Au, Pt, and Pd, Ni-based alloys, Fe-based alloys, and Ti-based alloys are low in price that can be put into practical use industrially. Furthermore, unlike Cd and Pb, Ni-based alloys, Fe-based alloys or Ti-based alloys have no environmental restrictions. As a result, the intermediate layer 13 for joining the Mg core material layer 10 and the Al layer 11 is made of a Ni-based alloy, a Fe-based alloy or a Ti-based alloy, so that the Mg layer (Mg core material layer 10) and the Al layer are formed. Increased bonding strength with (Al layer 11) to suppress delamination, low price at a level that can be commercialized industrially, no environmental use restrictions, and easy manufacture The clad material 1 that satisfies all the requirements can be provided.

  In the present embodiment, if the clad material 1 is configured to have a five-layer structure in which the Al layer 11, the intermediate layer 13, the Mg core material layer 10, the intermediate layer 14, and the Al layer 12 are laminated in this order, 5 It is possible to suppress the occurrence of peeling in the Mg—Al clad material 1 having a layer structure. Further, since the Mg core material layer 10 can be sandwiched between the Al layer 11 and the Al layer 12, it is possible to prevent the clad material 1 from being warped due to a difference in ductility between the Mg-based alloy and the Al-based alloy. be able to. In addition, since Al layers 11 and 12 made of a chemically stable Al-based alloy are located on both surface layers of the clad material 1, they are chemically more unstable than the Al-based alloy and ignite when heated. It is possible to prevent the Mg core material layer 10 made of an Mg-based alloy having a concern or the like from being located on the surface layer of the clad material 1. Thereby, the chemical stability of the clad material 1 can be improved and corrosion resistance can be improved.

  In this embodiment, if the intermediate layers 13 and 14 are made of a Ni-based alloy, the Ni-based alloy is generally more easily plastically deformed and has a higher ductility than the Fe-based alloy. It is possible to suppress the occurrence of waviness (a thick part and a thin part) in the intermediate layers 13 and 14 in the rolling. Thereby, even when the thickness t5 of the intermediate layer 13 and the thickness t6 of the intermediate layer 14 are small, breakage of the intermediate layers 13 and 14 can be suppressed.

  In the present embodiment, the thickness t2 of the Mg core material layer 10 is set to be greater than any of the thickness t3 of the Al layer 11, the thickness t4 of the Al layer 12, the thickness t5 of the intermediate layer 13, and the thickness t6 of the intermediate layer 14. If the size is increased, the proportion of the Mg core material layer 10 made of a lightweight Mg-based alloy can be increased, so that the cladding material 1 can be further reduced in weight. Furthermore, when the thickness t2 of the Mg core material layer 10 is about 50% or more of the thickness of the clad material 1, the proportion of the Mg core material layer 10 made of a lightweight Mg-based alloy is surely increased. Therefore, the cladding material 1 can be further reduced in weight.

  In this embodiment, the thickness t5 of the intermediate layer 13 and the thickness t6 of the intermediate layer 14 are both less than the thickness t2 of the Mg core material layer 10, the thickness t3 of the Al layer 11, and the thickness t4 of the Al layer 12. Since the proportion of the intermediate layers 13 and 14 made of Ni-base alloy, Fe-base alloy or Ti-base alloy having a specific gravity greater than that of the Mg-base alloy and Al-base alloy can be reduced, the clad material 1 can be further reduced in weight. Furthermore, if the thickness t5 of the intermediate layer 13 and the thickness t6 of the intermediate layer 14 are both about 4% or less of the thickness of the cladding material 1, the proportion of the intermediate layers 13 and 14 can be reliably reduced. Further, the cladding material 1 can be further reduced in weight.

  Further, in this embodiment, when the specific gravity of the clad material 1 is about 2.43 or less, the specific gravity of the clad material 1 is sufficiently higher than that of using an Al-based alloy having a specific gravity of about 2.7 alone. It can be made smaller and lighter. Furthermore, when the specific gravity of the clad material 1 is about 2.16 or less, the specific gravity of the clad material 1 can be further reduced to reduce the weight.

  Next, with reference to FIG. 1 and FIG. 2, the manufacturing method of the clad material 1 by one Embodiment of this invention is demonstrated.

  First, as shown in FIG. 2, a Mg plate material 110 made of an Mg-based alloy, a pair of Al plate materials 111 and 112 made of an Al-based alloy, and a Ni-based alloy, an Fe-based alloy, or a Ti-based alloy. A pair of joining plate materials 113 and 114 are prepared. The Mg plate material 110, the Al plate materials 111 and 112, and the bonding plate materials 113 and 114 are annealed materials formed by annealing for a predetermined time under a predetermined temperature condition.

  At this time, the thickness of the Mg plate 110 is about 50% or more of the total thickness of the Mg plate 110, the pair of Al plates 111 and 112, and the pair of bonding plates 113 and 114. It may be. Further, the thicknesses of the pair of bonding plate materials 113 and 114 are both set to be less than the thickness of the Mg plate material 110 and to the thickness of the pair of Al plate materials 111 and 112 or less.

  In the manufacturing method of the present embodiment, the Al plate material 111, the bonding plate material 113, the Mg plate material 110, the bonding plate material 114, and the Al plate material 112 are successively laminated in this order from the Z1 side toward the Z2 side. Then, the five stacked metal plates are continuously rolled using a rolling roll 101. In this rolling, the rolling reduction ratio R ((1-thickness after rolling / thickness before rolling) × 100) of the rolling roll 101 is set to 45% or more. In addition, it is preferable that this rolling is a hot rolling which set temperature condition T to about 250 degreeC or more and about 450 degrees C or less. In addition, it is more preferable that the temperature condition T of the hot rolling is a value of about 350 ° C. or higher and about 450 ° C. or lower. Further, the rolling reduction R of the rolling roll 101 is preferably about 50% or more. Note that, under the environment of the temperature condition T of hot rolling, the bonding metal (Ni-based alloy, Fe-based alloy or Ti-based alloy) having a high melting point constituting the bonding plate materials 113 and 114 does not melt and is used as steam. It is rarely released.

  Thus, as shown in FIG. 1, a clad material having a five-layer structure in which an Al layer 11, an intermediate layer 13, an Mg core layer 10, an intermediate layer 14, and an Al layer 12 are joined in this order. 1 is produced. At this time, since the hot rolling is performed, the Mg core material layer 10 is plastically deformed, so that a new surface (surface newly exposed at the interface) appears and contacts the new surfaces of the intermediate layers 13 and 14. It becomes possible. As a result, adhesion is obtained at the bonding interface 1 b between the intermediate layer 13 and the Mg core material layer 10 and at the bonding interface 1 d between the Mg core material layer 10 and the intermediate layer 14.

  Then, the clad material 1 is subjected to diffusion annealing by performing heat treatment on the clad material 1 after hot rolling for about 60 minutes under a temperature condition of about 250 ° C. or higher and about 350 ° C. or lower. As a result, the atomic diffusion further occurs at the bonding interfaces 1a to 1d of the cladding material 1, thereby improving the bonding strength at the bonding interfaces 1a to 1d and the metal layers (Al layer 11, intermediate layer 13, Mg core). By annealing the material layer 10, the intermediate layer 14, and the Al layer 12), the brittleness of the metal layer of each layer is improved. Thereby, the clad material 1 used for the structural member is produced.

  In the manufacturing method of the present embodiment, the following effects can be obtained.

  In the manufacturing method of this embodiment, as described above, by rolling the Al plate material 111, the bonding plate material 113, the Mg plate material 110, the bonding plate material 114, and the Al plate material 112 at a rolling reduction R of 45% or more, the Mg core The adhesion between the material layer 10 and the intermediate layer 13 and the adhesion between the intermediate layer 13 and the Al layer 11 can be reliably increased. Similarly, the adhesion between the Mg core material layer 10 and the intermediate layer 14 and the adhesion between the intermediate layer 14 and the Al layer 12 can be reliably improved. By these, it can suppress that peeling arises in the Mg-Al clad material 1. FIG.

  Further, in the manufacturing method of the present embodiment, the Al plate material 111, the bonding plate material 113, the Mg plate material 110, the bonding plate material 114, and the Al plate material 112 are sequentially laminated in this order, and are about 250 ° C. or higher and about 450 ° C. In the case of hot rolling under a temperature condition (T) of less than or equal to 50 ° C. and with a reduction ratio R of 45% or more, the ductility of the Mg-based alloy is low at a temperature condition of less than about 250 ° C. When rolling at the rolling reduction, it is possible to suppress the occurrence of cracks or the like in the Mg core material layer 10 composed of the Mg-based alloy. Further, it is possible to suppress the Mg-based alloy from being chemically unstable due to the temperature condition higher than about 450 ° C.

(Experiment 1)
Next, with reference to FIGS. 1-10, Experiment 1 conducted in order to confirm the effect of this invention is demonstrated.

  In Experiment 1, a clad material 1 having a five-layer structure of an Al layer 11, an intermediate layer 13, an Mg core material layer 10, an intermediate layer 14, and an Al layer 12 was used to confirm a metal material suitable as an intermediate layer (see FIG. 1). ), Clad material 1 having different types of bonding metals for intermediate layers 13 and 14 was prepared, and the bonding strength was measured.

  Specifically, as shown in FIG. 2, a pair of Al plates 111 composed of an Mg plate 110 made of Mg alloy (AZ31) as an Mg-based alloy and pure Al (A1050) as an Al-based alloy. And 112, and a pair of bonding plates 113 and 114 made of pure Ni (NW2201) as a Ni-based alloy were prepared. The Mg plate 110, the Al plates 111 and 112, and the bonding plates 113 and 114 were annealed for a predetermined time under a predetermined temperature condition. Here, the thickness of the Mg plate 110 was 640 μm, the thickness of the pair of Al plates 111 and 112 was 160 μm, and the thickness of the pair of bonding plates 113 and 114 was 40 μm. The Al plate materials 111 and 112 and the bonding plate materials 113 and 114 are examples of the “first Al plate material”, “second Al plate material”, “first bonding plate material”, and “second bonding plate material” of the present invention, respectively. It is.

  Then, the Al plate material 111, the bonding plate material 113, the Mg plate material 110, the bonding plate material 114, and the Al plate material 112 were successively laminated in this order and hot-rolled. At that time, the temperature condition T was set to 400 ° C., and the rolling reduction R was set to 50%. Thereby, the Al layer 11 composed of A1050, the intermediate layer 13 composed of NW2201, the Mg core material layer 10 composed of AZ31, the intermediate layer 14 composed of NW2201, and the Al layer composed of A1050 A clad material 1 having a five-layer structure in which 12 were laminated in this order was produced. In the clad material 1 of Example 1, the thicknesses of the Al layer 11, the intermediate layer 13, the Mg core layer 10, the intermediate layer 14, and the Al layer 12 are 80 μm, 20 μm, 320 μm, 20 μm, respectively. And it became 80 micrometers. In addition, the thickness of each layer was calculated | required by each measuring the thickness of several points from the cross-sectional photograph which showed the layer state in the cross section of the clad material mentioned later, and averaging several measured thickness. At this time, the thickness ratio of the Mg core material layer 10 was 61.5%, and the thickness ratios of the intermediate layers 13 and 14 were both 3.8%.

  The clad material 1 after the hot rolling was subjected to diffusion annealing on the clad material 1 by performing a heat treatment for 60 minutes under a temperature condition of 300 ° C. Thereby, the clad material 1 of Example 1 was produced.

  Further, in the same manner as the clad material 1 of Example 1, except that the joining plate materials 113 and 114 are made of SPCC, and the intermediate layers 13 and 14 are made of pure Fe (low carbon steel), Example 2 is obtained. A clad material 1 was prepared. Further, the clad material 1 of Example 3 was produced in the same manner as the clad material 1 of Example 1 except that the intermediate layers 13 and 14 (bonding plate materials 113 and 114) were made of pure Ti (TP270).

  On the other hand, except that the intermediate layers 13 and 14 are not provided as the clad material of Comparative Example 1, the Al layer composed of A1050 and the Mg core material composed of AZ31 are the same as the clad material 1 of Example 1. A clad material having a three-layer structure in which an Al layer composed of layers and A1050 was laminated in this order was produced. At this time, the thickness ratio of the Mg core material layer 10 was set to 66.7%. Further, as the clad material of Comparative Example 2, Comparative Example 2 was performed in the same manner as the clad material 1 of Example 1 except that the intermediate layers 13 and 14 (bonding plate materials 113 and 114) were made of pure Cu (C1020). A clad material was prepared.

  And while taking a cross-sectional photograph about each clad material, the peeling test was done. In this peeling test, as shown in FIG. 3, the joining interface at the end of the clad material was forcibly peeled using a jig (not shown) such as pliers. In addition, about the clad material whose joining strength is high and forcible peeling is difficult, the clad material was joined so that the end part may be easily peeled in advance during hot rolling. Then, a peeling test shown in FIG. 4 was performed on the clad material. Specifically, the layer (for example, Mg core layer 10, Al layer 12, and intermediate layer 14 shown in FIG. 4) on one side (Z2 side) of the peeled interface (eg, bonding interface 1d shown in FIG. 4) is fixed member. In addition to fixing to 102, the other side (Z1 side) of the peeled interface (for example, the Al layer 11 and the intermediate layer 13 shown in FIG. 4) was pulled in the Z1 direction to further peel the interface. Then, by dividing the load required at that time by the width of the clad material (the width of the clad material in the direction perpendicular to the paper surface), the bonding strength as a load per unit width was obtained. The specific gravity of the clad material was calculated from the thickness ratio of each layer obtained from the cross-sectional photograph and the specific gravity of the metal material constituting each layer. Although the measured value of the specific gravity of the clad material was also measured using the water immersion method, the measured value of the specific gravity of the clad material was also almost the same as the calculated value of the specific gravity of the clad material calculated from the thickness ratio and the specific gravity of the metal material. Became. Furthermore, the layer state in the cross section of a clad material was observed using the cross-sectional photograph of each clad material.

  As a result of Experiment 1 shown in FIG. 5, in the clad materials of Examples 1 to 3 using pure Ni, pure Fe, and pure Ti as the intermediate layer, the bonding strength was 50 N / mm or more. That is, the interlayer of the clad material (the bonding interface 1a between the Al layer 11 and the intermediate layer 13, the bonding interface 1b between the intermediate layer 13 and the Mg core material layer 10, the bonding interface 1d between the Mg core material layer 10 and the intermediate layer 14, Further, it was confirmed that the adhesiveness of the bonding interface 1c) between the Al layer 12 and the intermediate layer 14 was high and difficult to peel off. On the other hand, in the clad material of Comparative Example 1 in which no intermediate layer is provided and in Comparative Example 2 using pure Cu as the intermediate layer, the bonding strength is 16 N / mm and 15 N / mm, respectively, and the adhesion between the clad material layers Was low and easy to peel.

  From this result, an intermediate layer made of Ni-base alloy, Fe-base alloy or Ti-base alloy is arranged between the Al layer made of Al-base alloy and the Mg core material layer made of Mg-base alloy. As a result, it was confirmed that the clad material can be less likely to be peeled off than when the Al layer and the Mg core material layer are directly joined. On the other hand, when an intermediate layer made of a Cu-based alloy was disposed between the Al layer and the Mg core material layer, it was confirmed that peeling was likely to occur in the clad material.

  Further, from the cross-sectional photographs shown in FIGS. 6 to 10, in Example 1 in which the intermediate layer is made of pure Ni and Comparative Example 2 in which the intermediate layer is made of pure Cu, undulation is generated in the intermediate layer. However, in Example 2 in which the intermediate layer was made of pure Fe and Example 3 in which the intermediate layer was made of pure Ti, waviness was generated in the intermediate layer. The variation in the thickness of the intermediate layer was somewhat larger. This is presumably because pure Ni and pure Cu are more easily plastically deformed by rolling than ductile Fe and pure Ti and have higher ductility. As a result, it has been found that the intermediate layer of the clad material is preferably made of pure Ni from the viewpoint of workability such as rolling or press working after rolling.

  Here, when Examples 1 to 3 are compared, it is determined that the intermediate layer is made of a Ni-based alloy (pure Ni) based on the bonding strength and the observation result (workability) of the cross-sectional photograph. It is thought that this is the most suitable because of the small variation of. On the other hand, since pure Ni has a larger specific gravity than pure Fe and pure Ti, it is considered that it is not very suitable from the viewpoint of reducing the specific gravity of the clad material. Therefore, Experiment 2 shown below was performed.

(Experiment 2)
Next, with reference to FIG. 1 and FIGS. 11-14, the experiment 2 conducted in order to confirm the effect of this invention is demonstrated.

  In Experiment 2, even when the specific gravity is reduced by reducing the thickness of the intermediate layer composed of the Ni-based alloy, the intermediate layer is hardly broken and the bonding strength can be increased. In order to confirm this, in the clad material 1 (see FIG. 1) having a five-layer structure of the Al layer 11, the intermediate layer 13, the Mg core material layer 10, the intermediate layer 14, and the Al layer 12, the intermediate layers 13 and 14 are pure. A clad material 1 made of Ni and having a different thickness ratio of each layer was prepared, and the bonding strength was measured.

  Specifically, in the clad material of Example 11, the Mg plate 110 has a thickness of 760 μm, the pair of Al plates 111 and 112 has a thickness of 400 μm, and a pair of bonding plates 113 and 114 made of pure Ni (NW2201). The thickness of was 20 μm. And by carrying out hot rolling on the same conditions as Example 1 of the above-mentioned experiment 1 (reduction ratio R: 50%), Al layer 11, intermediate layer 13, Mg core material layer 10, intermediate layer 14, and Al The thickness of each layer 12 was 200 μm, 10 μm, 380 μm, 10 μm, and 200 μm, respectively. Otherwise, the clad material of Example 11 was produced in the same manner as the clad material 1 of Example 1 above. At this time, the thickness ratio of the Mg core material layer 10 was 47.5%, and the thickness ratios of the intermediate layers 13 and 14 were both 1.3%.

  In the clad material of Example 12, the thickness of the Mg plate 110 was 760 μm, the thickness of the pair of Al plates 111 and 112 was 20 μm, and the thickness of the pair of bonding plates 113 and 114 was 20 μm. And by carrying out hot rolling on the same conditions as the said Example 1, each thickness of the Al layer 11, the intermediate | middle layer 13, the Mg core material layer 10, the intermediate | middle layer 14, and the Al layer 12 is each 10 micrometers. 10 μm, 380 μm, 10 μm, and 10 μm. Otherwise, the clad material of Example 12 was produced in the same manner as the clad material 1 of Example 1 above. At this time, the thickness ratio of the Mg core material layer 10 was 90.5%, and the thickness ratios of the intermediate layers 13 and 14 were both 2.4%.

  In the clad material of Example 13, the thickness of the Mg plate 110 was 760 μm, the thickness of the pair of Al plates 111 and 112 was 20 μm, and the thickness of the pair of bonding plates 113 and 114 was 10 μm. And by carrying out hot rolling on the same conditions as the said Example 1, each thickness of the Al layer 11, the intermediate | middle layer 13, the Mg core material layer 10, the intermediate | middle layer 14, and the Al layer 12 is each 10 micrometers. 5 μm, 380 μm, 5 μm, and 10 μm. Otherwise, the clad material of Example 13 was produced in the same manner as the clad material 1 of Example 1 above. At this time, the thickness ratio of the Mg core material layer 10 was 92.7%, and the thickness ratios of the intermediate layers 13 and 14 were both 1.2%.

  Each of the clad materials was subjected to the same peel test as in Experiment 1, and the layer state in the cross section of the clad material was observed using a cross-sectional photograph of each clad material.

  As a result of Experiment 2 shown in FIG. 11, from the results of Examples 11 to 13, the ratio of the thickness of the intermediate layer made of pure Ni is reduced, and the specific gravity of the clad material is set to the specific gravity of Al (A1050) (2 7) 90% (2.43 (= 2.7 × 0.9)) or less, it was found that a sufficient bonding strength of 50 N / mm or more can be obtained. Further, from the results of Examples 12 and 13, even when the specific gravity of the clad material is 80% (2.16 (= 2.7 × 0.8)) or less of the specific gravity of Al, it is 50 N / mm or more. It has been found that sufficient bonding strength can be obtained. Furthermore, from the results of Example 13, even a clad material having a specific gravity smaller than the specific gravity of Comparative Example 1 without an intermediate layer (2.09, see FIG. 5), sufficient bonding of 50 N / mm or more. It was found that strength was obtained.

  From this result, even when pure Ni having a relatively large specific gravity is used, the specific gravity of the clad material can be made sufficiently small by reducing the thickness ratio in the entire clad material of the intermediate layer (less than 4%). Even if it did, it turned out that a fracture | rupture of an intermediate | middle layer does not arise easily and joining strength can be made high.

  Also, from the cross-sectional photographs shown in FIGS. 12 to 14, the intermediate layer made of pure Ni (the white stripe-like part on the Al layer side of the black stripe-like part in the cross-sectional photograph) clearly exists in any layer form. Even in Example 13 where the thickness of the intermediate layer was the smallest (intermediate layer thickness: 5 μm), there were few breaks in the intermediate layer, and the formation of intermetallic compounds of Mg and Al was suppressed. . From this, it has been found that even if the thickness of the intermediate layer is reduced to 5 μm, sufficient bonding strength can be obtained in the entire cladding material. Further, from the cross-sectional photograph of Example 12 shown in FIG. 13 and the cross-sectional photograph of Example 13 shown in FIG. 14, even if the thickness of the Al layer is reduced to 10 μm, the Al layer is located in the surface layer of the clad material in the entire clad material. In addition, no breakage of the Al layer could be confirmed. Accordingly, it has been found that even if the thickness of the Al layer is reduced to 10 μm, it is possible to ensure the corrosion resistance of the cladding material.

(Experiment 3)
Next, with reference to FIG. 1 and FIG. 15, the experiment 3 performed in order to confirm the effect of this invention is demonstrated.

  In Experiment 3, in order to confirm the difference in bonding strength due to the rolling reduction R, the rolling reduction R during hot rolling was changed to change the Al layer 11, the intermediate layer 13, the Mg core material layer 10, the intermediate layer 14, and the Al A clad material 1 (see FIG. 1) having a five-layer structure of layer 12 was produced and the bonding strength was measured.

  Specifically, in Example 21, as in Example 1 of Experiment 1 above, a Mg plate 110 made of AZ31 (Mg alloy), a pair of Al plates 111 made of pure Al (A1050), and 112 and a pair of bonding plates 113 and 114 made of pure Ni (NW2201) were prepared. The thickness of the Mg plate 110 was set to 800 μm, the thickness of the pair of Al plates 111 and 112 was set to 40 μm, and the thickness of the pair of bonding plates 113 and 114 was set to 20 μm.

  Here, in Example 21, except that the rolling reduction R is set to 45%, the hot rolling is performed in the same manner as in Example 1 of Experiment 1 above, so that the structure is composed of the Al layer 11 composed of A1050 and NW2201. The intermediate layer 13, the Mg core material layer 10 composed of AZ31, the intermediate layer 14 composed of NW2201, and the Al layer 12 composed of A1050 are joined together in this state. A clad material 1 having a structure was produced. In the clad material 1 of Example 21, the thicknesses of the Al layer 11, the intermediate layer 13, the Mg core material layer 10, the intermediate layer 14, and the Al layer 12 were 22 μm, 11 μm, 440 μm, 11 μm, respectively. And it was 22 micrometers. At this time, the thickness ratio of the Mg core material layer 10 was 87.0%, and the thickness ratios of the intermediate layers 13 and 14 were both 2.2%.

  Further, in the clad material of Example 22, the clad material 1 was produced in the same manner as in Example 21 except that the rolling reduction R was set to 50%. In the clad material 1 of Example 22, the thicknesses of the Al layer 11, the intermediate layer 13, the Mg core layer 10, the intermediate layer 14, and the Al layer 12 are 20 μm, 10 μm, 400 μm, 10 μm, respectively. And it was 20 micrometers.

  Further, in the clad material of Example 23, the clad material 1 was produced in the same manner as in Example 21 except that the rolling reduction R was set to 60%. In the clad material 1 of Example 23, the thicknesses of the Al layer 11, the intermediate layer 13, the Mg core material layer 10, the intermediate layer 14, and the Al layer 12 are 16 μm, 8 μm, 320 μm, 8 μm, respectively. And it was 16 micrometers.

  On the other hand, for the clad material of Comparative Example 21, a clad material was produced in the same manner as in Example 21 except that the rolling reduction R was set to 30%. In the clad material of Comparative Example 21, the thicknesses of the Al layer, the intermediate layer, the Mg core material layer, the intermediate layer, and the Al layer were 28 μm, 14 μm, 560 μm, 14 μm, and 28 μm, respectively. .

  Moreover, in the clad material of Comparative Example 22, a clad material was produced in the same manner as in Example 21 except that the rolling reduction R was set to 40%. In the clad material of Comparative Example 22, the thicknesses of the Al layer, the intermediate layer, the Mg core material layer, the intermediate layer, and the Al layer were 24 μm, 12 μm, 480 μm, 12 μm, and 24 μm, respectively. .

  In the clad materials of Examples 21 to 23 and Comparative Examples 21 and 22, the thickness ratio and specific gravity (2.08) of each layer are the same.

  Then, the same peel test as in Experiment 1 was performed on each clad material.

  As a result of the experiment 3 shown in FIG. 15, from the results of Examples 21 to 23, a sufficient bonding strength of 40 N / mm or more that is assumed to be capable of being pressed by setting the rolling reduction to 45% or more. It was confirmed that Furthermore, it was confirmed that a sufficient bonding strength of 50 N / mm or more can be obtained by setting the rolling reduction to 50% or more. On the other hand, from the results of Comparative Examples 21 and 22, by making the rolling reduction less than 45% (40% or less), only insufficient joint strength of less than 40 N / mm (34 N / mm or less) can be obtained, and the clad material It was confirmed that the adhesion between the two layers was low and easy to peel. Furthermore, from the result of Comparative Example 21, it was confirmed that the joining itself was not possible by setting the rolling reduction to 30%.

  The embodiments and examples disclosed this time should be considered as illustrative in all points and not restrictive. The scope of the present invention is shown not by the above description of the embodiments and examples but by the scope of claims for patent, and includes all modifications within the meaning and scope equivalent to the scope of claims for patent.

  For example, in the above-described embodiment and examples, the cladding material 1 includes the Al layer 11 (second layer), the intermediate layer 13 (third layer), the Mg core material layer 10 (first layer), and the intermediate layer 14 (fifth layer). Layer) and the Al layer 12 (fourth layer) are joined in the state of being laminated in this order. However, the present invention is not limited to this. In the present invention, the cladding material has a structure in which at least an Al layer (second layer), an intermediate layer (third layer), and an Mg core material layer (first layer) are joined in this order. It only has to be. For example, as in the modification of the embodiment shown in FIG. 16, the clad material 201 is an Al layer 211 made of an Al-based alloy, an intermediate layer 213 made of a Ni-based alloy, a Fe-based alloy, or a Ti-based alloy. And, the Mg core material layer 210 composed of an Mg-based alloy may have a three-layer structure joined in a state of being laminated in this order. The Mg core material layer 210, the Al layer 211, and the intermediate layer 213 are examples of the “first layer”, “second layer”, and “third layer” of the present invention, respectively. The clad material is a four-layer structure in which an Al layer (second layer), an arbitrary metal layer, an intermediate layer (third layer), and an Mg core material layer (first layer) are joined in this order. You may have. Further, if the clad material has a structure in which an Al layer (second layer), an intermediate layer (third layer), and an Mg core material layer (first layer) are laminated in this order, six or more layers are formed. You may have a structure.

  Moreover, in the said embodiment and Example, thickness t2 of Mg core material layer 10 with small specific gravity is made into thickness t3 of Al layer 11, thickness t4 of Al layer 12, thickness t5 of intermediate layer 13, and thickness t6 of intermediate layer 14. Although the example formed so that it became larger than any of these was shown, this invention is not limited to this. In the present invention, the thickness of the Mg core material layer (first layer) is at least one of the thickness of the Al layer (second layer or fourth layer) and the thickness of the intermediate layer (third layer or fifth layer). It may be one thickness or less. In this case, from the viewpoint of reducing the specific gravity of the clad material, the thickness of the Mg core material layer (first layer) is preferably larger than the thickness of the intermediate layer (third layer or fifth layer) having a large specific gravity.

  In the above embodiment, the example in which the thickness t2 of the Mg core material layer 10 having a small specific gravity is set to about 50% or more of the thickness t1 of the clad material 1 having a five-layer structure is shown, but the present invention is not limited to this. Absent. In the present invention, the thickness of the Mg core material layer (first layer) may be less than about 50% of the thickness of the clad material.

  Moreover, in the said embodiment and Example, thickness t5 of the intermediate | middle layer 13 with large specific gravity and thickness t6 of the intermediate | middle layer 14 are both less than thickness t2 of the Mg core material layer 10, thickness t3 or less of the Al layer 11, Al layer Although the example formed so that it may become 12 or less thickness t4 was shown, this invention is not limited to this. In the present invention, the thickness of the intermediate layer (the third layer or the fifth layer) may be equal to or greater than the thickness of the Mg core material layer (the first layer), or the Al layer (the second layer or the fourth layer). It may be larger than the thickness.

  Further, in the above-described embodiments and examples, the example in which the thickness t5 of the intermediate layer 13 and the thickness t6 of the intermediate layer 14 having a large specific gravity are both about 4% or less of the thickness t1 of the clad material 1 is shown. The invention is not limited to this. In the present invention, the thickness of the intermediate layer (the third layer or the fifth layer) may be greater than about 4% of the thickness of the cladding material.

  In the above-described embodiment and examples, the thickness t3 of the Al layer 11 and the thickness t4 of the Al layer 12 are both set to about 25% or less of the thickness t1 of the clad material 1. Not limited to. In the present invention, the thickness of the Al layer (second layer or fourth layer) may be larger than about 25% of the thickness of the clad material.

1,201 Cladding material 10,210 Mg core material layer (first layer)
11, 211 Al layer (second layer)
12 Al layer (fourth layer)
13, 213 Intermediate layer (third layer)
14 Middle layer (5th layer)
110 Mg plate material 111 Al plate material (first Al plate material)
112 Al plate (2nd Al plate)
113 Bonding plate (first bonding plate)
114 Bonding plate (second bonding plate)

Claims (13)

A first layer composed of an Mg-based alloy; a second layer composed of an Al-based alloy; and the first layer and the second layer disposed between the first layer and the second layer, comprising at least a third layer you joining,
The third layer, or and a Ni-base alloy having a thickness of less than 8 [mu] m, or, that is composed of Fe-based alloy, a clad material.   The clad material according to claim 1, wherein the third layer is made of a Ni-based alloy.   3. The clad material according to claim 1, wherein a thickness of the first layer is larger than a thickness of the second layer and larger than a thickness of the third layer.   The clad material according to claim 3, wherein the thickness of the first layer is 50% or more of the thickness of the clad material.   The clad material according to claim 3 or 4, wherein a thickness of the third layer is equal to or less than a thickness of the second layer.   The thickness of the said 3rd layer is a clad material of any one of Claims 1-5 which is 4% or less of the thickness of the said clad material. A fourth layer composed of an Al-based alloy; and a fifth layer disposed between the first layer and the fourth layer and joining the first layer and the fourth layer ;
Wherein the fifth layer, or and a Ni-base alloy having a thickness of less than 8 [mu] m, or, that is composed of Fe-based alloy, a clad material according to any one of claims 1-6. Said third layer and said fifth layer, and a Ni-based alloy, a clad material of claim 7.   The clad material according to any one of claims 1 to 8, wherein a specific gravity of the clad material is 2.43 or less.   The clad material according to claim 9, wherein a specific gravity of the clad material is 2.16 or less. A first 1Al plate composed of Al-based alloy, a Ni-based alloy or Fe-based alloy gold that consists first bonding sheet, a step of laminating the Mg plate composed of Mg-based alloy in this order,
By rolling the first Al plate, the first bonding plate, and the Mg plate at a rolling reduction of 45% or more, a first layer made of an Mg-based alloy and a second layer made of an Al-based alloy a layer, disposed between the first layer and the second layer, viewed including the step of producing a clad material and a third layer you bonding the said first layer a second layer,
The method for producing a clad material, wherein the third layer is made of a Ni-based alloy having a thickness of 8 μm or less or made of a Fe-based alloy . Step includes a first 1Al plate composed of Al-based alloy, a Ni-based alloy or Fe-based alloy gold that consists first bonding sheet, and Mg plate composed of Mg-based alloy to stack plate, wherein the Ni-based alloy or Fe-based alloy gold that consists second bonding sheet, a step of laminating the first 2Al plate composed of Al-based alloy in this order,
The step of producing the clad material by rolling includes rolling the first Al plate material, the first bonding plate material, the Mg plate material, the second bonding plate material, and the second Al plate material at a rolling reduction of 45% or more. The first layer made of Mg-based alloy, the second layer made of Al-based alloy, and the first layer and the second layer are disposed between the first layer and the second layer. a third layer you join the second layer, a fourth layer composed of Al-based alloy, disposed between said first layer and said fourth layer, said fourth layer and said first layer look including the step of producing a clad material and a fifth layer you joined bets,
12. The method for manufacturing a clad material according to claim 11, wherein the fifth layer is made of a Ni-based alloy having a thickness of 8 [mu] m or less, or made of an Fe-based alloy .   The step of producing the clad material by rolling includes a step of hot rolling under a temperature condition of 250 ° C or higher and 450 ° C or lower and a rolling reduction of 45% or higher. Clad material manufacturing method.

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