METHOD FOR PRODUCING METAL LAMINATE MATERIAL

Abstract

An object of the present invention is to provide a method for producing a metal laminate material that maintains sufficient bonding strength and has superior production efficiency. A method for producing a metal laminate material by bonding two sheets, one sheet composed of a material M1 and the other sheet composed of a material M2, wherein each of M1 and M2 is a metal or alloy comprising any one or more selected from the group consisting of Mg, Al, Ti, Cr, Mn, Fe, Co, Ni, Cu, Zn, Nb, Mo, Pd, Ag, In, Sn, Hf, Ta, W, Pb, and Bi, comprises the steps of subjecting the faces of the two sheets to be bonded to sputtering treatment with inert gas ions under vacuum such that oxide layers on surface layers remain; temporarily bonding the two sheets by roll pressure bonding; and conducting a thermal treatment to thereby bond the two sheets, and, when Tm1>Tm2 where Tm1 (K) is the melting point of M1 and Tm2(K) is the melting point of M2, the temperature of the thermal treatment is 0.45Tm2 or more and less than 0.45Tm1, provided that the temperature is not more than Tm2.

Claims

1. A method for producing a metal laminate material bonding two sheets, one sheet composed of a material M1 and the other sheet composed of a material M2, each of M1 and M2 being a metal or alloy comprising any one or more selected from the group consisting of Mg, Al, Ti, Cr, Mn, Fe, Co, Ni, Cu, Zn, Nb, Mo, Pd, Ag, In, Sn, Hf, Ta, W, Pb, and Bi, wherein the method comprises the steps of: subjecting the faces to be bonded of the two sheets to sputtering treatment with inert gas ions under vacuum such that oxide layers on surface layers remain; temporarily bonding the two sheets by roll pressure bonding; and conducting a thermal treatment to thereby bond the two sheets; and wherein, when Tm1>Tm2 where Tm1 (K) is the melting point of M1 and Tm2(K) is the melting point of M2, the temperature of the thermal treatment is 0.45Tm2 or more and less than 0.45Tm1, provided that the temperature is not more than Tm2.

2. The method for producing a metal laminate material according to claim 1, wherein M1 is a metal or alloy comprising any one or more selected from the group consisting of Fe, Ni, Cu, Ti, and Mo, and M2 is a metal or alloy comprising any one or more selected from the group consisting of Mg, Al, and Sn.

3. The method for producing a metal laminate material according to claim 1, wherein an etching amount by sputtering treatment on a face to be bonded is at least 1 nm in terms of SiO.sub.2.

4. A method for producing a metal laminate material, wherein three or more sheets are bonded by conducting the production method according to claim 1 a plurality of times.

5. The method for producing a metal laminate material according to claim 2, wherein an etching amount by sputtering treatment on a face to be bonded is at least 1 nm in terms of SiO.sub.2.

6. A method for producing a metal laminate material, wherein three or more sheets are bonded by conducting the production method according to claim 2 a plurality of times.

7. A method for producing a metal laminate material, wherein three or more sheets are bonded by conducting the production method according to claim 3 a plurality of times.

Description

BRIEF DESCRIPTION OF DRAWINGS

[0021] FIG. 1 is a schematic diagram illustrating a method for producing a metal laminate material of the present invention.

[0022] FIG. 2 is a graph showing the AES analysis results of the temporarily bonded laminates of Example 1 and Comparative Example 3.

[0023] FIG. 3 is a graph showing the peel strength of the metal laminate materials of Example 1 and Comparative Example 4 before and after thermally treated.

[0024] FIG. 4 is a graph showing the relationship between the etching amount by sputtering treatment on the stainless steel and the surface adsorbate layer.

[0025] FIG. 5 is a graph showing the relationship between the etching amount by sputtering treatment on the aluminum steel and the surface adsorbate layer.

DESCRIPTION OF EMBODIMENTS

[0026] The method for producing a metal laminate material of the present invention will be described hereinbelow with reference to FIG. 1.

[0027] When the materials of two sheets to be bonded by the method producing a metal laminate material according to the present invention (a sheet 1 and a sheet 2 in FIG. 1) are each referred to as M1 and M2, each of M1 and M2 is a metal or alloy comprising any one or more selected from the group consisting of Mg, Al, Ti, Cr, Mn, Fe, Co, Ni, Cu, Zn, Nb, Mo, Pd, Ag, In, Sn, Hf, Ta, W, Pb, and Bi. Incidentally, the following description is made on the assumption that Tm1>Tm2, where Tm1(K) is the melting point of M1 and Tm2(K) is the melting point of M2. Examples of such M1 and M2 include SUS304, SUS 316, Ti alloys, and Cu alloys in addition to single materials composed of each metal as described above. When M1 is a metal or alloy comprising any one or more selected from the group consisting of Fe, Ni, Cu, Ti, and Mo and M2 is a metal or alloy comprising any one or more selected from the group of consisting of Mg, Al, and Sn, a preferable combination can be achieved.

[0028] The thickness of the two sheet can be selected as appropriate depending on the type of M1 and M2, proccessability on roll pressure bonding, the strength and applications of a metal laminate material to be produced and the like. The thickness is, but not limited to, preferably from 10 m to 1 mm, for example.

[0029] As shown in (1) of FIG. 1, an adsorbate layer including contamination and an oil content and oxide layers 3 are generally present on the surface layers of the faces of the sheet 1 and the sheet 2 to be bonded (such an adsorbate layer and an oxide layer are present on the opposite face to the face to be bonded, but not shown). On bonding two sheets, these faces to be bonded are subjected to sputtering treatment with an inert gas under vacuum in advance.

[0030] Then, as shown in (2) of FIG. 1, the method for producing a metal laminate material of the present invention is characterized in that sputtering treatment is conducted so as to allow the oxide layers on the surface layer of the faces to be bonded to remain. Incidentally, under conditions where the oxide layer is partially etched and partially remains, the adsorbate layer on the surface layer of each face to be bonded becomes completely removed. According to the present invention in comparison with conventional methods for producing a metal laminate material, which completely remove the surface adsorbate layer and the oxide layer by etching by sputtering treatment (surface activating bonding methods), the time required for the sputtering treatment can be greatly reduced and thus the productivity of the metal laminate material can be improved. Specifically, the sputtering treatment time can be reduced by two-fold to 630-fold relative to conventional methods for producing a metal laminate material, and thus the productivity of the metal laminate material can be increased remarkably.

[0031] The sputtering treatment can be conducted specifically as follows: two sheets are provided in the form of a long coil having a width of 100 mm to 600 mm, for example. An alternating current at 1 MHz to 50 MHz is applied between one electrode including the two sheets having a face to be bonded each grounded and the other electrode insulatingly supported to generate glow discharge, provided that the area of the electrode to be exposed to plasma generated by the glow discharge is one-third or less of the area of the other electrode. During the sputtering treatment, the grounded electrode can prevent increase in the temperature of each conveyed material by taking the form of a cooling roll.

[0032] In the sputtering treatment, etching of the faces to be bonded of the two sheets with an inert gas under vacuum completely removes the adsorbate layers on the surface layers and allows oxide layers on the surface layers to partially remain. Examples of the inert gas that can be applied include argon, neon, xenon, krypton, and mixed gases containing at least one of these. Adsorbate layers on the surface layers can be completely removed with an etching amount of the order of about 1 nm.

[0033] Conditions for sputtering treatment may be conditions under which the oxide layers may partially remain and can be set as appropriate. Preferably, by setting conditions that an etching amount by sputtering treatment on a face to be bonded is preferably at least 1 nm in terms of SiO.sub.2, more preferably 1 nm to 10 nm in terms of SiO.sub.2, the adsorbate layers become completely removed and the oxide becomes partially remaining. If energy sufficient to etch at least 1 nm of SiO.sub.2 is applied, the amount of other materials etched is known. That is, when the sputtering rate value of SiO.sub.2 is set to 1, the sputtering rates of other materials will be as follows: Al: 1, Ti: 0.5, Cr: 0.5, Mn: 3, Fe: 1, Co: 2, Ni: 2, Cu: 1.5, Nb: 1, Mo: 1, Pd: 4, Ag: 4, Sn: 4, Ta: 0.5, W: 0.5, and Pb: 10. The sputtering rate of stainless steel (SUS) is 1.

[0034] Specifically, the sputtering treatment can be conducted, for example, under vacuum, for example, at a plasma output of 100 W to 10 KW and a line speed of 1 m/minute to 30 m/minute. The degree of vacuum at this time may be, for example, from 110.sup.5 Pa to 10 Pa although a higher degree is preferable in order to prevent readsorbates onto the surface. The temperature of the sheet 1 and the sheet 2 in the sputtering treatment is preferably maintained at ordinary temperature to 100 C. from the viewpoint of prevention of softening.

[0035] Subsequently, in the method for producing a metal laminate material of the present invention, the faces to be bonded of the two sheets sputtering treated are temporarily bonded by roll pressure bonding to form a laminate material 4 as shown in (3) of FIG. 1. The rolling line load for temporary bonding is, but not particularly limited to, from 0.1 to 10 tf/cm, for example. The temperature on temporary bonding by roll pressure bonding can be, but not particularly limited to, from ordinary temperature to 100 C.

[0036] The temporary bonding by roll pressure bonding is preferably conducted in a non-oxidizing atmosphere, for example, an inert gas atmosphere such as Ar in order to prevent decrease in the adhesion strength between the sheet 1 and the sheet 2 due to readsorption of oxygen onto the surfaces thereof.

[0037] Then, as shown in (4) of FIG. 1, thermally treating the laminate material 4 obtained by temporary bonding allows atoms to diffuse through the bonding interface to improve the bonding strength, producing the metal laminate material 5 intended. Here, the production method according to the present invention is characterized in that, when Tm1>Tm2 where Tm1(K) is the melting point of M1 and Tm2(K) is the melting point of M2, the temperature of the thermal treatment is set to 0.45Tm2 or more and less than 0.45Tm1, provided that the temperature is not more than Tm2. In the present invention, in order to diffuse the metal having a lower melting point by thermal treatment, it is necessary to heat the laminate material at a temperature of at least 0.45Tm2 or more. In contrast, an extremely high thermal treatment temperature results in metal recrystallization, leading to decrease in the strength of the metal laminate material. Thus, thermal treatment is conducted in the range of less than 0.45Tm1, as a temperature which is less than the recrystallization temperature and at which atom diffusion moderately occurs. However, a thermal treatment temperature more than Tm2 is not suitable because M2 dissolves at the temperature. The melting temperatures of metals which are the subject of the present invention are shown in Table 1.

TABLE-US-00001 TABLE 1 Melting point Melting point 0.45 Melting point Metal ( C.) (K) (K) Mg 650 923 415.35 (142.35 C.) Al 660 933 419.85 (146.85 C.) Ti 1666 1939 872.55 (599.55 C.) Cr 1857 2130 958.5 (685.5 C.) Mn 1246 1519 683.55 (410.55 C.) Fe 1536 1809 814.05 (541.05 C.) Co 1495 1768 795.6 (522.6 C.) Ni 1455 1728 777.6 (504.6 C.) Cu 1085 1358 611.1 (338.1 C.) Zn 420 693 311.85 (38.85 C.) Nb 2477 2750 1237.5 (964.5 C.) Mo 2623 2896 1303.2 (1030.2 C.) Pd 1552 1825 821.25 (548.25 C.) Ag 962 1235 555.75 (282.75 C.) In 157 430 193.5 (79.5 C.) Sn 232 505 227.25 (45.75 C.) Hf 2233 2506 1127.7 (854.7 C.) Ta 2985 3258 1466.1 (1193.1 C.) W 3407 3680 1656 (1383 C.) Pb 1552 1825 821.25 (548.25 C.) Bi 271 544 244.8 (28.2 C.)

[0038] For example, when a stainless steel (SUS316L) and an aluminum are bonded, the melting point of the stainless steel, Tm1, is 1793 K (1520 C.) and 0.45Tm1=806.85 K (533.85 C.) while the melting point of the aluminum, Tm2, is 933 K (660 C.) as shown in Table 1 above and 0.45Tm2=419.85 K (146.85 C.). Thus, thermal treatment is conducted at 146.85 C. to 533.85 C.

[0039] Alternatively, when a titanium and an aluminum are bonded, the melting point of titanium, Tm1, is 1939 K (1666 C.) and 0.45Tm1=872.55 K (599.55 C.), while the aluminum has 0.45Tm2=419.85 K (146.85 C.). Thus, thermal treatment is conducted at a temperature of 146.85 C. to 599.55 C.

[0040] As another example, when a molybdenum and an aluminum are bonded, the melting point of molybdenum, Tm1, is 2896 K (2623 C.) and 0.45Tm1=1303.2 K (1030.2 C.), while the aluminum has 0.45Tm2=419.85 K (146.85 C.). Thus, thermal treatment is conducted at a temperature of 146.85 C. to 660 C. so as not to exceed the melting point of the aluminum, Tm2.

[0041] Thermal treatment time depends on metals. Occurrence of thermal diffusion preferably leads to an improvement in the adhesion. However, heating is required to be stopped before softening of the metal because extremely long heating time may lead to softening of the metal.

[0042] Through the thermal treatment step described above, a metal laminate material having high bonding strength can be produced more efficiently. Additionally, if the thermal treatment is applied, the strength of the metal laminate material itself is not decreased. A metal laminate material including three or more sheets bonded can be produced by conducting the production method according to the present invention a plurality of times. Examples of this metal laminate material include metal laminate materials having a three layered structure composed of Fe/Al/Fe and metal laminate materials having a three layered structure composed of Ni/Al/Ni.

EXAMPLES

[0043] The present invention will described in further detail hereinbelow referring to Examples and Comparative Examples, but the present invention is not intended to be limited to these Examples.

Example 1

[0044] As the stainless steel, SUS304-BA (thickness 0.05 mm) was used, and as the aluminum, A1050-H18 (thickness 0.18 mm) was used. When each surface of SUS304-BA and A1050-H18 was measured with a scanning Auger Electron spectrometer (AES), the thickness of the SUS304-BA oxide layer was from 10 to 15 nm and the thickness of the A1050-H18 oxide layer was from 80 to 150 nm.

[0045] Subsequently, SUS304-BA and A1050-H18 were subjected to sputtering treatment. SUS304-BA was sputtered under vacuum of 0.1 Pa at a plasma output of 800 W and a line speed of 3.5 m/minute and A1050-H18 was sputtered under vacuum of 0.1 Pa at a plasma output of 2600 W and a line speed of 3.5 m/minute to thereby completely remove the adsorbate layer on the surface of each SUS304-BA and A1050-H118. The inert gas used was Ar. The amount of SUS304-BA etched was about 2 nm and the amount of A1050-H18 etched was about 6 nm. SUS304-BA and A1050-H18 after the sputtering treatment were temporarily bonded at ordinary temperature by roll pressure bonding at a rolling line load of 2 tf/cm (rolling load of 0.4 MN) to thereby form a laminate material.

[0046] The temporarily bonded laminate material was subjected to AES analysis. The results of the AES analysis on the temporarily bonded laminate material of Example 1 and the temporarily bonded laminate material of Comparative Example 3 described below are shown in FIG. 2. As shown in FIG. 2, peaks derived from oxygen (O) were observed in the front and back of the temporarily bonded laminate material interface, and it was confirmed that SUS304-BA and A1050-H18 were temporarily bonded with an oxide layer remaining on the surface layer of each SUS304-BA and A1050-H18.

[0047] Then, the temporarily bonded laminate material was thermally treated at 240 C. For 30 minutes. The metal laminate material obtained was measured for peel strength (90), and bonding strength was evaluated.

Comparative Example 1

[0048] Comparative Example 1 was the same as Example 1 except that no thermal treatment was conducted on the temporarily bonded laminate material.

Comparative Example 2

[0049] Comparative Example 2 was the same as Example 1 except that no sputtering treatment on SUS304-BA and A1050-H18 was conducted. At the interface of the laminate material after temporarily bonded, oxide layers and adsorbate layers remained on the respective surfaces of SUS304-BA and A1050-H18.

Comparative Example 3

[0050] As the stainless steel, SUS304-BA (thickness 0.05 mm) was used, and as the aluminum, A1050-H18 (thickness 0.17 mm) was used. SUS304-BA and A1050-H18 were subjected to sputtering treatment. SUS304-BA was sputtered under vacuum of 0.1 Pa at a plasma output of 700 W for a time for sputtering the face to be bonded of 180 minutes, and A1050-H18 was sputtered under vacuum of 0.1 Pa at a plasma output of 700 W for a time for sputtering the face to be bonded of 180 minutes (the sheet was sputtered in a stationary state without moved. The line speed can be converted to a line speed of 5.610.sup.3 minute under conditions of sputtering while the sheet passed through the line as in Example 1) to thereby completely remove adsorbate and oxide layers on the surface of SUS304-BA and A1050-H18. The amount of SUS304-BA etched was about 600 nm and the amount of A1050-H18 etched was about 460 nm. SUS304-BA and A1050-H18 after the sputtering treatment were temporarily bonded at ordinary temperature by roll pressure bonding at a rolling line load of 2 tf/cm (rolling load of 0.4 MN) to thereby form a laminate material. The temporarily bonded laminate material was measured for peel strength (90).

Comparative Example 4

[0051] The temporarily bonded laminate material obtained as in Comparative Example 3 was thermally treated at 240 C. fix 30 minutes. The metal laminate material obtained was measured for peel strength (90).

[0052] The peel strengths of the metal laminate materials produced in Example 1 and Comparative Example 1 to 4 are shown in Table 2. The peel strengths of the metal laminate materials of Example 1 and Comparative Example 4 before and after the thermal treatment are shown in FIG. 3. The laminate materials before the thermal treatment of the metal laminate materials of Example 1 and Comparative Example 4 respectively correspond to the laminate materials of Comparative Examples 1 and 3.

TABLE-US-00002 TABLE 2 Etching Interface oxide Thermal amount (nm) layer after treatment Peel Al SUS temporary temperature strength face face bonding ( C.) (N/20 mm) Example 1 6 2 Yes 240 34 Comparative 6 2 Yes No 10 Example 1 Comparative 0 0 Yes, 240 0 Example 2 including adsorbates Comparative 460 600 No No 19 Example 3 Comparative 460 500 No 240 36 Example 4

[0053] As shown in Table 2, the metal laminate material of Example 1 achieved improved peel strength by being thermally treated (Example 1 and Comparative Example 1). Additionally, the metal laminate material of Example 1, which was obtained by allowing oxide layers to remain on the surface of each SUS304-BA and A1050-H18, achieved peel strength equivalent to that of the metal laminate material of Comparative Example 4, which was obtained by completely removing oxide layers from the surface of each SUS304-BA and A1050-H18. Example 1 was also able to reduce the time required for the sputtering treatment by about 630-fold relative to Comparative Example 4 (calculated from the line speed of 3.5 m/minute Example 1 and the converted value of line speed of 5.610.sup.3 m/minute in Comparative Example 4). As seen from FIG. 3, the metal laminate material of Example 1 exhibited an improvement in the peel strength before and after the thermal treatment greater than that of the metal laminate material of Comparative Example 4.

Examples 2 to 5 and Comparative Examples 5 to 7

[0054] In Examples 2 to 5 and Comparative Examples 5 to 7, influences of the thermal treatment temperatures of the temporarily bonded laminate materials on the peel strength and hardness of the metal laminate materials to be obtained were examined.

[0055] In Examples 2 to 5 and Comparative Examples 5 to 7, temporarily bonded laminate materials were obtained in the same manner as Example 1 except that SUS304-BA having a thickness of 0.05 mm was replaced with SUS304-1/2H having a thickness of 0.1 mm and A1050-H18 having a thickness of 0.18 mm was replaced with AL1050 (H24) having a thickness of 0.4 mm, that sputtering treatment was conducted by changing the line speed of 3.5 m/minute to a line speed of 3.0 m/minute, and that temporary bonding by roll pressure bonding was conducted by changing the rolling line load of 2 tf/cm to a rolling line load of about 2.8 tf/cm. The amount of SUS304-1/2H etched was 3 nm and the amount of AL1050 (H24) etched was 5 nm. The temporarily bonded laminate materials obtained were thermally treated at a predetermined temperature for 240 minutes. The thermal treatment temperatures in Examples 2 to 5 and Comparative Examples 5 to 7 are shown in Table 3. The metal laminate materials obtained were measured for the amount of iron (Fe) at a point 5 mm in the aluminum layer from the bonding interface of the metal laminate materials, peel strength (90), and hardness on the SUS side. The results are shown in Table 3.

TABLE-US-00003 TABLE 3 Etching Interface oxide Thermal Amount of Fe at point amount (nm) layer after treatment 5 mm into the aluminum Peel Al SUS temporary temperature layer from interface strength Hardness face face bonding ( C.) (atm %) (N/20 mm) Hv Example 2 5 3 Yes 200 8.1 49 390 Example 3 5 3 Yes 300 8.8 85 392 Example 4 5 3 Yes 400 10.7 130 393 Example 5 5 3 Yes 500 15 Al breakage 369 Comparative 5 3 Yes No 0 22 393 Example 5 Comparative 5 3 Yes 100 2.6 24 393 Example 6 Comparative 5 3 Yes 600 Delamination 322 Example 7

[0056] As shown in Table 3, the metal laminate materials of Examples 2 to 5, of which thermal treatment temperatures were 0.45Tm2 or more and less than 0.45Tm1, had higher peel strength as well as higher hardness than those of metal laminates of Comparative Examples 5 to 7, of which thermal treatment temperatures were outside this temperature range. As for the amount of iron (Fe) at a point 5 mm in the aluminum layer from the bonding interface of the metal laminate materials, as the thermal treatment temperature was increased in the measurement range, diffusion of the iron, which was a component of stainless steel, into the aluminum layer was increased. This is assumed to increase the peel strength of the metal laminate material. Within the range of the thermal treatment temperature of 0.45Tm2 or more and less than 0.45Tm1, the higher the thermal treatment temperature became, the higher the peel strength became.

(Removal of Surface Adsorbate Layer)

[0057] The relationship between the etching amount by sputtering treatment and the surface adsorbate layer was examined for each of a stainless steel (SUS316) and an aluminum (A1050). The results for the stainless steel are shown in FIG. 4 and the results for the aluminum are shown in FIG. 5. As shown in FIG. 4 and FIG. 5, the surface adsorbate layer was completely removed by etching to of the order of about 1 nm both in the stainless steel and the aluminum.

REFERENCE SIGNS LIST

[0058] 1 sheet [0059] 2 sheet [0060] 3 oxide layer [0061] 4 laminate material [0062] 5 metal laminate material

[0063] All publications, patents, and patent applications cited herein are incorporated herein by reference in their entirety.