ALUMINUM ALLOY CLAD MATERIAL

Abstract

An aluminum alloy clad material having four layers includes: a sacrificial material on one surface of a core material; and an AlSiMgBi-based brazing material which clads the other surface thereof on one surface of the sacrificial material on an opposite side to the core material, the brazing material containing Si: 6.0% to 14.0%, Mg: 0.05% to 1.5%, Bi: 0.05% to 0.25%, Sr: 0.0001% to 0.1%, and Al balance, and satisfying (Bi+Mg)Sr0.1, MgBi-based compounds contained in the brazing material with a diameter of 0.1-5.0 m are more than 20 in number per 10,000-m.sup.2 and the MgBi-based compounds with a diameter of 5.0 m or more are less than 2 before brazing, and the core material contains Mn: 1.0% to 1.7%, Si: 0.2% to 1.0%, Fe: 0.1% to 0.5%, Cu: 0.1% to 0.7%, and a balance consisting of Al and inevitable impurities.

Claims

1. An aluminum alloy clad material having four layers comprising: a sacrificial material disposed on one surface of a core material; and an AlSiMgBi-based brazing material which clads the other surface of the core material, and is disposed on one surface of the sacrificial material on a side opposite to the core material, wherein the brazing material contains, by mass %, Si: 6.0% to 14.0%, Mg: 0.05% to 1.5%, Bi: 0.05% to 0.25%, Sr: 0.0001% to 0.1%, and a balance consisting of Al and inevitable impurities, and satisfies a relationship of (Bi+Mg)Sr0.1 in amounts of elements by mass %, MgBi-based compounds contained in the AlSiMgBi-based brazing material and having a diameter of 0.1 m or more and less than 5.0 m in terms of equivalent circle diameter are more than 20 in number per 10,000-m.sup.2 visual field and the MgBi-based compounds having a diameter of 5.0 m or more are less than 2 in number per 10,000-m.sup.2 visual field when observed in a surface layer plane direction before brazing, and the core material contains, by mass %, Mn: 1.0% to 1.7%, Si: 0.2% to 1.0%, Fe: 0.1% to 0.5%, Cu: 0.1% to 0.7%, and a balance consisting of Al and inevitable impurities.

2. The aluminum alloy clad material according to claim 1, wherein the core material further contains, by mass %, Mg: 0.1% to 0.7%.

3. The aluminum alloy clad material according to claim 1, wherein the core material further contains, by mass %, Ti: 0.05% to 0.3%.

4. The aluminum alloy clad material according to claim 2, wherein the core material further contains, by mass %, Ti: 0.05% to 0.3%.

5. The aluminum alloy clad material according to claim 1, wherein a concentration of Mg on a surface of the brazing material at a braze melting temperature is in a range of 0.15% to 1.0%.

6. The aluminum alloy clad material according to claim 2, wherein a concentration of Mg on a surface of the brazing material at a braze melting temperature is in a range of 0.15% to 1.0%.

7. The aluminum alloy clad material according to claim 3, wherein a concentration of Mg on a surface of the brazing material at a braze inciting temperature is in a range of 0.15% to 1.0%.

8. The aluminum alloy clad material according to claim 4, wherein a concentration of Mg on a surface of the brazing material at a braze melting temperature is in a range of 0.15% to 1.0%.

9. The aluminum alloy clad material according to claim 1, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

10. The aluminum alloy clad material according to claim 2, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

11. The aluminum alloy clad material according to claim 3, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

12. The aluminum alloy clad material according to claim 4, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

13. The aluminum alloy clad material according to claim 5, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

14. The aluminum alloy clad material according to claim 6, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

15. The aluminum alloy clad material according to claim 7, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

16. The aluminum alloy clad material according to claim 8, wherein the sacrificial material contains, by mass %, one or two or more of Zn: 1.5% to 6.0%, Mn: 0.3% to 1.3%, Si: 0.2% to 0.8%, Mg: 0.1% to 0.7%, Fe: 0.2% to 0.8%, Cr: 0.05% to 0.5%, and Ti: 0.05% to 0.3%.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0103] FIG. 1 is a view illustrating a brazing sheet for flux-free brazing according to an embodiment of the present invention.

[0104] FIG. 2 is a perspective view illustrating an aluminum heat exchanger for a vehicle according to the embodiment of the present invention.

[0105] FIG. 3 is a view illustrating a brazing evaluation model in an example of the present invention.

DETAILED DESCRIPTION OF THE INVENTION

[0106] Hereinafter, an embodiment of the present invention will be described.

[0107] An aluminum alloy is melted to be adjusted to the composition of the present invention. The melting can be performed by a semi-continuous casting method.

[0108] In the present embodiment, in order to disperse a fine MgBi compound at the time before brazing, Mg and Bi are dissolved in an ingot as a solid solution by performing casing at a high cooling rate from a high molten metal temperature during casting of a brazing material while suppressing coarse crystallization of the MgBi compound.

[0109] Specifically, the solid solubility of Mg and Bi can be increased by setting the molten metal temperature to 700 C. or higher.

[0110] The obtained aluminum alloy ingot is subjected to a homogenization treatment under predetermined conditions. When the homogenization treatment temperature is low, a coarse MgBi compound is precipitated and it is difficult to obtain the distributed state of the MgBi compound of the present invention at the time before the brazing. Therefore, it is desirable to perform the treatment at a treatment temperature of 400 C. or higher for 1 to 10 hours.

[0111] Next, the brazing material is assembled with the core material and the sacrificial material and is subjected to hot clad rolling. At this time, in the present embodiment, the MgBi compound is adjusted to a predetermined size and number density by controlling a rolling time at a predetermined temperature during hot rolling, an equivalent strain from the start to the end of the hot rolling, a hot rolling finish temperature, and a cooling rate after the hot rolling.

[0112] First, by satisfying the rolling time in a predetermined temperature range during the hot rolling, precipitation of the MgBi compound having a predetermined size defined in the present invention is promoted in an environment where dynamic strain is applied. Specifically, the precipitation of the fine MgBi compound is promoted by setting the rolling time during which the material temperature during the hot rolling is between 400 C. and 500 C. to 10 minutes or more.

[0113] Furthermore, by controlling the equivalent strain from the start to the end of the hot rolling, a coarse MgBi crystallized product generated during the casting can be crushed and refined, and the number density thereof can be increased. Specifically, the MgBi crystallized product is sufficiently refined by adjusting a slab thickness and a finish thickness so that the equivalent strain represented by Formula (1) satisfies >5.0, thereby increasing the number density

=(2/3)ln(t.sub.0/t)Formula (1)

[0114] t.sub.0: Hot rolling start thickness (slab thickness)

[0115] t: Hot rolling finish thickness

[0116] Furthermore, when the hot rolling finish temperature is high and a state without dynamic strain is maintained, or when the cooling rate after the hot rolling is slow, a coarser MgBi compound than desired by the present invention is precipitated at grain boundaries and the like. Therefore, by securing a cooling rate of a certain level or more by reducing the hot rolling finish temperature to a predetermined temperature, the precipitation of a coarse MgBi compound is suppressed. Specifically, the precipitation of a coarse MgBi compound is suppressed by setting the hot rolling finish temperature to 250 C. to 350 C. and controlling the cooling rate from the finish temperature to 200 C. to be faster than 20 C./hr.

[0117] Thereafter, a brazing sheet of the present invention is obtained through cold rolling or the like.

[0118] In the cold rolling, for example, cold rolling can be performed with a total reduction rate of 75% or more, process annealing can be performed at a temperature of 200 C. to 450 C., and then final rolling with a reduction rate of 40% can be performed. In cold rolling, the MgBi compound is less likely to be crushed and does not deviate from the size and number density targeted by the present invention, so that the conditions are not particularly limited. Further, process annealing may not be performed, or H2n grade that has been finished by final annealing may be applied.

[0119] In an aluminum alloy clad material 1 made of the brazing sheet obtained in the above process, an aluminum alloy brazing material 3A is disposed on one surface of an aluminum alloy core material 2, an aluminum alloy sacrificial material 4 is disposed on the other surface of the aluminum alloy core material 2, and an aluminum alloy brazing material 3B is disposed on one surface of the aluminum alloy sacrificial material 4 on the opposite side to the core material side. The aluminum alloy clad material 1 is subjected to brazing as an assembly combined with other constituent members 10 (fin, tube, side plate, and the like) as the constituent members of the heat exchanger.

[0120] The assembly is disposed in a heating furnace having a non-oxidizing atmosphere under a normal pressure. A non-oxidizing gas can be constituted using an inert gas such as nitrogen gas, argon, a reducing gas such as hydrogen or ammonia, or a mixed gas thereof. Although the pressure of the atmosphere in a brazing furnace is basically the normal pressure, for example, in order to improve a gas replacement efficiency inside a product, a medium to low vacuum of about 100 kPa to 0.1 Pa in a temperature range before melting the brazing material may be employed, or a positive pressure of 5 to 100 Pa from the atmospheric pressure may be employed in order to suppress the infiltration of outside air (atmosphere) into the furnace.

[0121] The heating furnace does not need to have a sealed space, and may be a tunnel type having a carry-in port and a carry-out port for the brazing material. Even in such a heating furnace, non-oxidizing properties are maintained by continuously blowing the inert gas into the furnace. The non-oxidizing atmosphere desirably has an oxygen concentration of 50 ppm or less by volume ratio.

[0122] In the above atmosphere, for example, heating is performed at a temperature rising rate of 10 to 200 C./min, and braze joining is performed under heat treatment conditions in which an attainment temperature of the assembly is 559 C. to 630 C.

[0123] Under the brazing conditions, the brazing time is shortened as the temperature rising rate is increased, so that the growth of an oxide film on a material surface is suppressed and the brazability is improved. Brazing is possible when the attainment temperature is equal to or higher than at least the solidus temperature of the brazing material. However, the brazing material which flows increases in amount as the temperature approaches the liquidus temperature, and a good joined state is easily obtained at a joint having an open portion. However, when the temperature is too high, brazing erosion tends to proceed, and the structural dimensional accuracy of the assembly after brazing decreases, which is not preferable.

[0124] FIG. 2 illustrates an aluminum heat exchanger 5 in which fins 6 are formed using the aluminum alloy clad material 1 and a tube 7 made of an aluminum alloy is used as a brazing target material. The fin 6 and the tube 7 are assembled with a reinforcing member 8 and a header plate 9 to obtain the aluminum heat exchanger 5 for a vehicle or the like by flux-free brazing.

Example 1

[0125] Various brazing sheets having the compositions shown in Tables 1 and 2 and Tables 4 and 5 were produced into hot rolled sheets under the casting conditions, homogenization conditions (brazing material), and hot rolling conditions shown in Table 7. In addition, - in the component indicates that the content is 0 or the amount as an inevitable impurity.

[0126] Thereafter, cold rolled sheets having a thickness of 0.30 mm and having an H14 equivalent grade were produced by cold rolling including process annealing. The clad ratio of each layer was 7% for the brazing material on the sacrificial material side, 10% for the sacrificial material, and 7% for the brazing material on the core material side.

[0127] Moreover, as a brazing target member, a corrugated fin of an aluminum bare material (0.06 mm thickness) of A3003 alloy and H14 was prepared.

[0128] A tube having a width of 25 mm was produced using the aluminum alloy clad material, and the tube and the corrugated fin were combined so that the brazing material on the tube core material side or the brazing material on the tube sacrificial material side and the corrugated fin are in contact with each other, thereby forming a core having a 15-stage tube and a length of 300 mm as a brazing evaluation model. The core was heated to 600 C. and held for 5 minutes in a brazing furnace in a nitrogen atmosphere (oxygen content 30 ppm). The brazed state was evaluated Here, a heat input amount from room temperature to 550 C. (the integral of the product of the diffusion coefficient of Zn and time during a brazing heat treatment) was set to 610.sup.11 m.sup.2, a heat input amount until the completion of the brazing was set to 810.sup.11) m.sup.2, and cooling to room temperature was performed after the end of the brazing at a cooling rate of 100 C./min. The brazing conditions are not limited to the above.

[0129] For each specimen in examples, the following evaluation was performed, and the evaluation results are shown in Tables 3 and 6.

[0130] Brazability

[0131] Joint Ratio

[0132] A joint ratio was obtained by the following formula, and superiority and inferiority between samples were evaluated. Fin joint ratio=(total brazing length of fin and tube/total contact length of fin and tube)100

[0133] Regarding the joint ratio, 90% or more was evaluated as O, and less than 90% was evaluated as X

[0134] Fillet Length

[0135] A sample cut out from the core was embedded in a resin and mirror-polished, and a fillet length at a joint 13 between a fin 11 and a tube 12 was measured using an optical microscope as shown in FIG. 3. The number of joints to be measured was 20 and the average thereof was taken as the fillet length to evaluate superiority or inferiority.

[0136] In the fillet length, 800 m or more was evaluated as A, 700 m or more and less than 800 m as B, 600 m or more and less than 700 m as C, 500 m or more and less than 600 m as D, and less than 500 m as E.

[0137] Coarse Si Particles

[0138] A produced brazing sheet was embedded in a resin, a cross section thereof parallel to a rolling direction was mirror-polished, and the structure thereof was revealed with Barker's solution and then observed with an optical microscope to evaluate the formation state of coarse Si particles in a brazing material layer. Observation was performed on a visual field of 300 m at 10 points.

[0139] A case where coarse Si particles having an equivalent circle diameter of 30 m or more were less than 2 in number was evaluated as A, a range from 2 to 9 was evaluated as B, and a case of 10 or more particles was evaluated as C.

[0140] Strength after Brazing

[0141] The brazing sheet was placed in the furnace in a drop form, and a brazing equivalent heat treatment was performed under the brazing conditions. Thereafter, the sample was cut out, a tensile test was conducted at room temperature by a normal method based on JIS, and a tensile strength was evaluated.

[0142] Regarding the strength after brazing, 185 MPa or more was evaluated as A, 175 MPa or more and less than 185 MPa as B, 164 MPa or more and less than 175 MPa as C, and less than 164 MPa as D.

[0143] Corrosion Resistance

[0144] The brazing sheet was placed in the furnace in a drop form, and the brazing equivalent heat treatment was performed under the brazing conditions. Thereafter, the sample was cut into a size of 30 mm80 mm, masked except for a brazing material surface on the sacrificial material side, and then subjected to SWAAT for 20 days. Corrosion products were removed from the sample after the corrosion test with chromic acid phosphate, and the corrosion depth was measured by observing the cross section of a maximum corrosion portion.

[0145] Regarding the corrosion resistance, a case where the corrosion depth was in the sacrificial material layer was evaluated as A, exceeding the sacrificial material layer to half the sheet thickness as B, not penetrated although exceeding half the sheet thickness as C, and penetrated as D.

[0146] Mg Concentration of Surface of Brazing Material at Braze Melting Temperature

[0147] The brazing equivalent heat treatment was performed under the above brazing conditions, the sample was taken out from the furnace at the moment when the braze melting temperature (a solidus temperature was calculated from the components using the phase diagram calculation software JMatPro, and a temperature subtracted by 10 C. from the solidus temperature) was reached, the sample was embedded in a resin and mirror-polished, and the Mg concentration on the surface of the brazing material was measured by EPMA analysis in a cross-sectional direction. In the measured EPMA data, the average Mg concentration in a range of 5 m from the surface of the brazing material was taken as the Mg concentration on the surface of the brazing material.

[0148] Since the braze melting temperature varies depending on the components of a material, the solidus temperature was obtained using the phase diagram calculation software (JMatPro), and the temperature subtracted by 10 C. from the solidus temperature was treated as the braze melting temperature.

TABLE-US-00001 TABLE 1 MgBi Concentration of Elements added to compound Mg on surface of brazing material on [/10000 m.sup.2] brazing material core material side Manufac- Less 5 m Core material on core material [wt %] turing than or (Bi + composition [wt %] side Specimen No. Mg Si Bi Sr method 5 m more Mg) Sr Si Mg Mn Cu Fe Ti (wt %) Example 1 0.05 11.0 0.15 0.0005 E 24 0 0.0001 0.7 0.5 1.2 0.4 0.2 0.06 0.08 2 0.1 11.0 0.15 0.0005 E 39 0 0.000125 0.7 0.5 1.2 0.4 0.2 0.08 0.15 3 0.2 11.0 0.15 0.0005 E 41 0 0.000175 0.7 0.5 1.2 0.4 0.2 0.10 0.21 4 0.6 11.0 0.15 0.0005 F 35 0 0.000375 0.7 0.5 1.2 0.4 0.2 0.6 5 0.9 11.0 0.23 0.007 H 44 0 0.00791 0.7 1.2 0.4 0.2 0.84 6 0.9 11.0 0.23 0.007 H 44 0 0.00791 0.7 0.5 1.2 0.4 0.2 0.13 0.87 7 0.8 11.0 0.23 0.007 H 44 0 0.00721 0.7 0.4 1.2 0.4 0.2 0.05 0.79 8 1.0 11.0 0.23 0.06 H 46 0 0.0738 0.7 0.4 1.2 0.4 0.2 0.98 9 1.0 11.0 0.23 0.08 H 46 0 0.0984 0.7 0.4 1.2 0.4 0.2 0.12 0.99 10 1.0 11.0 0.15 0.0005 H 50 0 0.000575 0.7 0.4 1.2 0.4 0.2 0.95 11 1.2 11.0 0.15 0.0005 H 56 0 0.000675 0.7 0.4 1.2 0.4 0.2 0.15 1.2 12 1.5 11.0 0.15 0.0005 H 62 0 0.000825 0.7 0.4 1.2 0.4 0.2 0.17 1.47 13 1.2 11.0 0.15 0.0005 H 56 0 0.000675 0.7 1.2 0.4 0.2 1.2 14 1.5 11.0 0.15 0.0005 H 62 0 0.000825 0.7 1.2 0.4 0.2 0.16 1.42 15 0.5 6.5 0.23 0.008 I 54 0 0.00584 0.7 0.5 1.2 0.4 0.2 0.15 0.5 16 0.5 9.0 0.23 0.008 I 54 0 0.00584 0.7 0.5 1.2 0.4 0.2 0.18 0.5 17 0.3 10.0 0.20 0.007 B 34 0 0.0035 0.7 0.5 1.2 0.4 0.2 0.20 0.31 18 0.3 13.0 0.10 0.005 E 38 0 0.002 0.7 0.5 1.2 0.4 0.2 0.25 0.31 19 0.5 14.0 0.20 0.005 G 55 1 0.0035 0.7 0.5 1.2 0.4 0.2 0.5 20 0.3 11.5 0.05 0.005 I 32 0 0.00175 0.7 0.5 1.2 0.4 0.2 0.18 0.31 21 0.5 11.5 0.08 0.008 F 33 0 0.00464 0.7 0.5 1.2 0.4 0.2 0.5 22 0.5 11.5 0.23 0.006 A 40 0 0.00438 0.7 0.5 1.2 0.4 0.2 0.5 23 0.5 11.5 0.25 0.006 B 46 0 0.0045 0.7 0.5 1.2 0.4 0.2 0.5 24 0.5 12.5 0.15 0.0001 E 38 0 0.000065 0.7 0.5 1.2 0.4 0.2 0.5 25 0.5 11.5 0.12 0.008 F 33 0 0.00496 0.7 1.2 0.4 0.2 0.48 26 0.5 11.5 0.23 0.006 A 40 0 0.00438 0.7 1.2 0.4 0.2 0.47 27 0.5 11.5 0.25 0.006 B 46 0 0.0045 0.7 1.2 0.4 0.2 0.49 28 0.5 12.5 0.15 0.0001 E 38 0 0.000065 0.7 1.2 0.4 0.2 0.46 29 0.5 12.5 0.15 0.0005 F 31 0 0.000325 0.7 0.5 1.2 0.4 0.2 0.5 30 0.2 12.5 0.15 0.04 I 33 0 0.014 0.7 0.5 1.2 0.4 0.2 0.21 31 0.05 12.5 0.15 0.05 E 22 0 0.01 0.7 0.5 1.2 0.4 0.2 0.07 32 0.1 12.5 0.15 0.05 E 35 0 0.0125 0.7 0.5 1.2 0.4 0.2 0.15 33 0.1 12.5 0.15 0.1 E 35 0 0.025 0.7 0.5 1.2 0.4 0.2 0.15 34 0.5 11.5 0.15 0.008 E 37 0 0.0052 0.2 0.5 1.2 0.4 0.2 0.5 35 0.5 11.5 0.20 0.006 A 38 0 0.0042 0.6 0.5 1.2 0.4 0.2 0.5 36 0.5 11.5 0.20 0.007 D 43 0 0.0049 0.9 0.5 1.2 0.4 0.2 0.5 37 0.5 11.5 0.20 0.008 B 33 0 0.0056 1.0 0.5 1.2 0.4 0.2 0.5 38 0.5 11.5 0.20 0.008 B 33 0 0.0056 1.0 1.2 0.4 0.2 0.48 39 0.5 11.5 0.20 0.01 F 47 0 0.007 0.75 0.1 1.2 0.6 0.2 0.49 40 0.5 11.5 0.20 0.01 B 33 0 0.007 0.75 0.2 1.2 0.6 0.2 0.49 41 0.5 11.5 0.20 0.009 J 66 0 0.0063 0.75 0.65 1.2 0.6 0.2 0.505 42 0.3 11.5 0.20 0.01 A 41 0 0.005 0.75 0.7 1.2 0.6 0.2 0.313 43 0.3 11.5 0.20 0.01 B 36 0 0.005 0.7 0.5 1.1 0.55 0.2 0.307 44 0.3 11.5 0.20 0.004 I 55 0 0.002 0.7 0.5 1.2 0.55 0.2 0.307 45 0.3 11.5 0.15 0.007 E 41 0 0.00315 0.7 0.5 1.6 0.55 0.2 0.307 46 0.3 11.5 0.15 0.005 G 33 0 0.00225 0.7 0.5 1.7 0.55 0.2 0.307 47 0.3 11.5 0.15 0.01 J 47 0 0.0045 0.85 0.5 1.2 0.1 0.2 0.307 48 0.5 11.5 0.15 0.01 I 35 0 0.0065 0.85 0.5 1.2 0.15 0.2 0.5 49 0.5 11.5 0.20 0.01 C 38 0 0.007 0.85 0.5 1.2 0.7 0.2 0.5 50 0.5 11.5 0.20 0.008 D 44 0 0.0056 0.5 0.5 1.2 0.4 0.1 0.5 51 0.5 11.5 0.15 0.01 I 38 0 0.0065 0.5 0.5 1.2 0.4 0.12 0.5 52 0.5 11.5 0.15 0.009 J 42 0 0.00585 0.5 0.5 1.2 0.4 0.4 0.5 53 0.5 11.5 0.20 0.01 H 43 0 0.007 0.5 0.5 1.2 0.4 0.5 0.5 54 0.5 11.5 0.20 0.006 A 41 0 0.0042 0.7 0.5 1.2 0.4 0.2 0.5 55 0.5 11.5 0.20 0.0002 J 66 1 0.00014 0.7 0.5 1.2 0.4 0.2 0.5 56 0.5 11.5 0.23 0.01 B 47 0 0.0073 0.7 0.5 1.2 0.4 0.2 0.5 57 0.5 11.5 0.12 0.01 F 33 0 0.0062 0.7 0.5 1.2 0.4 0.2 0.5 58 0.5 11.5 0.2 0.008 B 34 0 0.0056 0.7 0.5 1.2 0.4 0.2 0.5 59 0.5 11.5 0.15 0.01 G 36 0 0.0065 0.7 0.5 1.2 0.4 0.2 0.5 60 0.3 10.0 0.20 0.009 B 34 0 0.0045 0.7 0.5 1.2 0.4 0.2 0.31 61 0.3 10.0 0.20 0.01 B 34 0 0.005 0.7 0.5 1.2 0.4 0.2 0.31 62 0.3 10.0 0.20 0.005 B 34 0 0.0025 0.7 0.5 1.2 0.4 0.2 0.31 63 0.3 10.0 0.20 0.009 B 34 0 0.0045 0.7 0.5 1.2 0.4 0.2 0.05 0.31 64 0.3 10.0 0.20 0.009 B 34 0 0.0045 0.7 0.5 1.2 0.4 0.2 0.15 0.31 65 0.3 10.0 0.20 0.01 B 34 0 0.005 0.7 0.5 1.2 0.4 0.2 0.31 66 0.3 10.0 0.20 0.01 B 34 0 0.005 0.7 0.5 1.2 0.4 0.2 0.31 67 0.3 10.0 0.20 0.007 B 34 0 0.0035 0.7 0.5 1.2 0.4 0.2 0.31 68 0.3 10.0 0.20 0.01 B 34 0 0.005 0.7 0.5 1.2 0.4 0.2 0.31 69 0.3 10.0 0.20 0.006 B 34 0 0.003 0.7 0.5 1.2 0.4 0.2 0.31 70 0.3 10.0 0.20 0.004 B 34 0 0.002 0.7 0.5 1.2 0.4 0.2 0.31 71 0.3 10.0 0.20 0.006 B 34 0 0.003 0.7 0.5 1.2 0.4 0.2 0.15 0.31 72 0.3 10.0 0.20 0.002 B 34 0 0.001 0.7 0.5 1.2 0.4 0.2 0.31 73 0.5 11.5 0.12 0.0008 F 33 0 0.000496 0.7 0.5 1.2 0.4 0.2 0.5 74 0.5 11.5 0.12 0.0008 F 33 0 0.000496 0.7 0.5 1.2 0.4 0.2 0.02 0.5 75 0.5 11.5 0.12 0.0008 F 33 0 0.000496 0.7 0.5 1.2 0.4 0.2 0.5 76 0.3 11.5 0.15 0.007 E 41 0 0.00315 0.7 0.5 1.6 0.55 0.2 0.307 77 0.3 11.5 0.15 0.007 E 41 0 0.00315 0.7 0.5 1.6 0.55 0.2 0.307 78 0.3 11.5 0.15 0.007 E 41 0 0.00315 0.7 0.5 1.6 0.55 0.2 0.02 0.307 79 0.3 11.0 0.20 0.02 E 35 0 0.01 0.7 0.2 1.4 0.4 0.2 0.3 80 0.5 11.5 0.15 0.008 E 37 0 0.0052 0.2 0.5 1.2 0.4 0.2 0.5 81 0.5 11.5 0.20 0.01 C 38 0 0.007 0.7 0.5 1.2 0.6 0.2 0.5 82 0.5 11.5 0.15 0.01 G 33 0 0.0065 0.4 0.5 1.2 0.2 0.2 0.5 83 0.5 11.5 0.20 0.008 C 37 0 0.0056 0.7 0.2 1 0.4 0.2 0.01 0.5

TABLE-US-00002 TABLE 2 MgBi Concentration of Elements added to brazing compound Mg on surface of material on sacrificial [/10000 m.sup.2] brazing material Sacrificial material material side Less 5 m on sacrificial composition [wt %] [wt %] than 5 or (Bi + material side Specimen No. Zn Mn Si Fe Cr Ti Mg Mg Si Bi Sr m more Mg) Sr (wt %) Example 1 5.0 0.3 0.5 0.05 11.0 0.15 0.0005 23 0 0.0001 0.09 2 5.0 0.3 0.5 0.1 11.0 0.15 0.0005 39 0 0.000125 0.11 3 3.5 0.3 0.3 0.2 11.0 0.15 0.0005 41 0 0.000175 0.2 4 3.5 0.3 0.3 0.6 11.0 0.15 0.0005 35 0 0.000375 0.6 5 5.0 0.3 0.9 11.0 0.23 0.007 44 0 0.00791 0.85 6 5.0 0.3 0.5 0.9 11.0 0.23 0.007 44 0 0.00791 0.9 7 5.0 0.3 0.5 0.8 11.0 0.23 0.007 44 0 0.00721 0.75 8 5.0 0.3 0.5 1.0 11.0 0.23 0.06 46 0 0.0738 0.99 9 5.0 0.3 0.5 1.0 11.0 0.23 0.08 46 0 0.0984 0.98 10 5.0 0.3 0.5 1.0 11.0 0.15 0.0005 50 0 0.000575 0.96 11 5.0 0.3 0.5 1.2 11.0 0.15 0.0005 56 0 0.000675 1.2 12 5.0 0.3 0.5 1.5 11.0 0.15 0.0005 62 0 0.000825 1.47 13 5.0 0.3 0.5 1.2 11.0 0.15 0.0005 56 0 0.000675 1.2 14 5.0 0.3 0.5 1.5 11.0 0.15 0.0005 62 0 0.000825 1.48 15 5.0 0.3 0.3 0.5 9.0 0.23 0.008 54 0 0.00584 0.5 16 5.0 0.3 0.3 0.5 9.0 0.23 0.008 54 0 0.00584 0.49 17 5.0 0.3 0.3 0.3 10.0 0.20 0.007 34 0 0.0035 0.3 18 4.0 0.3 0.3 0.3 13.0 0.10 0.005 38 0 0.002 0.29 19 5.0 0.5 0.3 0.5 14.0 0.20 0.005 55 1 0.0035 0.5 20 4.0 0.5 0.3 0.3 11.5 0.05 0.005 32 0 0.00175 0.3 21 2.0 0.5 0.3 0.5 11.5 0.08 0.008 33 0 0.00464 0.49 22 5.0 0.5 0.3 0.5 11.5 0.23 0.006 40 0 0.00438 0.48 23 3.0 0.5 0.3 0.5 11.5 0.25 0.006 46 0 0.0045 0.47 24 4.0 0.5 0.3 0.3 0.5 12.5 0.15 0.0001 38 0 0.000065 0.49 25 2.0 0.5 0.3 0.5 11.5 0.12 0.008 33 0 0.00496 0.48 26 5.0 0.5 0.3 0.5 11.5 0.23 0.006 40 0 0.00438 0.47 27 3.0 0.5 0.3 0.5 11.5 0.25 0.006 46 0 0.0045 0.45 28 4.0 0.5 0.3 0.3 0.5 12.5 0.15 0.0001 38 0 0.000065 0.44 29 5.0 0.5 0.3 0.3 0.5 12.5 0.15 0.0005 31 0 0.000325 0.46 30 5.0 0.8 0.3 0.3 0.2 12.5 0.15 0.04 33 0 0.014 0.2 31 5.0 0.8 0.3 0.3 0.05 12.5 0.15 0.05 22 0 0.01 0.06 32 5.0 0.8 0.3 0.3 0.1 12.5 0.15 0.05 35 0 0.0125 0.11 33 5.0 0.8 0.3 0.3 0.1 12.5 0.15 0.05 35 0 0.0125 0.1 34 1.5 0.8 0.5 0.3 0.5 11.5 0.15 0.008 37 0 0.0052 0.5 35 1.5 0.8 0.5 0.1 0.3 0.5 11.5 0.20 0.006 38 0 0.0042 0.47 36 5.0 0.8 0.5 0.1 0.3 0.5 11.5 0.20 0.007 43 0 0.0049 0.48 37 4.7 0.8 0.5 0.1 0.3 0.5 11.5 0.20 0.008 33 0 0.0056 0.42 38 4.7 0.8 0.5 0.1 0.3 0.5 11.5 0.20 0.008 33 0 0.0056 0.47 39 5.0 0.5 0.05 0.3 0.5 11.5 0.20 0.01 47 0 0.007 0.48 40 5.0 0.5 0.3 0.3 0.5 11.5 0.20 0.01 33 0 0.007 0.45 41 5.5 0.5 0.3 0.5 11.5 0.20 0.009 66 0 0.0063 0.5 42 5.0 0.5 0.3 0.3 11.5 0.20 0.01 41 0 0.005 0.3 43 5.1 0.5 0.3 0.3 11.5 0.20 0.01 36 0 0.005 0.3 44 5.0 0.5 0.05 0.3 0.3 11.5 0.20 0.004 55 0 0.002 0.29 45 5.0 0.5 0.3 0.3 11.5 0.15 0.007 41 0 0.00315 0.29 46 5.0 0.2 0.3 0.3 11.5 0.15 0.005 33 0 0.00225 0.28 47 0.2 0.3 0.3 11.5 0.15 0.01 47 0 0.0045 0.3 48 0.2 0.3 0.5 11.5 0.15 0.01 35 0 0.0065 0.5 49 0.2 0.3 0.5 11.5 0.20 0.01 38 0 0.007 0.46 50 5.0 0.8 0.2 0.3 0.5 11.5 0.20 0.008 44 0 0.0056 0.48 51 5.0 0.8 0.5 0.3 0.5 11.5 0.15 0.01 38 0 0.0065 0.5 52 5.0 0.8 0.5 0.3 0.5 11.5 0.15 0.009 42 0 0.00585 0.5 53 5.0 0.8 0.5 0.3 0.5 11.5 0.20 0.01 43 0 0.007 0.5 54 1.4 0.5 0.3 0.1 0.3 0.5 11.5 0.20 0.006 41 0 0.0042 0.5 55 6.0 0.5 0.3 0.1 0.3 0.5 11.5 0.20 0.0002 66 1 0.00014 0.5 56 5.0 0.3 0.3 0.3 0.5 11.5 0.23 0.01 47 0 0.0073 0.48 57 5.0 1.3 0.3 0.3 0.5 11.5 0.12 0.01 33 0 0.0062 0.47 58 5.0 0.5 0.2 0.3 0.3 0.5 11.5 0.20 0.008 34 0 0.0056 0.49 59 5.0 0.8 0.3 0.3 0.5 11.5 0.15 0.01 36 0 0.0065 0.5 60 0.3 10.0 0.20 0.009 34 0 0.0045 0.28 61 1.4 0.3 0.3 10.0 0.20 0.01 34 0 0.005 0.3 62 1.9 0.3 0.3 10.0 0.20 0.005 34 0 0.0025 0.29 63 0.3 10.0 0.20 0.009 34 0 0.0045 0.3 64 0.3 10.0 0.20 0.009 34 0 0.0045 0.3 65 1.4 0.5 0.3 0.3 10.0 0.20 0.01 34 0 0.005 0.3 66 1.4 0.5 0.3 0.3 10.0 0.20 0.01 34 0 0.005 0.3 67 2.0 0.2 0.3 0.3 10.0 0.20 0.007 34 0 0.0035 0.29 68 0.1 0.3 10.0 0.20 0.01 34 0 0.005 0.29 69 0.2 0.3 10.0 0.20 0.006 34 0 0.003 0.3 70 0.4 0.3 10.0 0.20 0.004 34 0 0.002 0.3 71 0.2 0.3 10.0 0.20 0.006 34 0 0.003 0.3 72 0.55 0.3 10.0 0.20 0.002 34 0 0.001 0.35 73 2.0 0.5 0.3 0.3 11.5 0.20 0.0008 40 0 0.0004 0.3 74 2.0 0.5 0.3 0.4 11.5 0.20 0.0008 41 0 0.00048 0.4 75 2.0 0.5 0.3 0.4 11.5 0.15 0.0008 38 0 0.00044 0.4 76 5.0 0.5 0.3 0.5 11.5 0.15 0.007 45 0 0.00455 0.48 77 5.0 0.5 0.3 0.2 11.5 0.15 0.007 40 0 0.00245 0.2 78 5.0 0.5 0.3 0.2 11.5 0.22 0.007 43 0 0.00294 0.2 79 5.0 0.3 0.3 11.0 0.20 0.02 35 0 0.01 0.3 80 1.5 0.8 0.5 0.3 0.5 11.5 0.15 0.008 37 0 0.0052 0.5 81 0.2 0.3 0.5 11.5 0.20 0.01 38 0 0.007 0.46 82 5.0 0.8 0.5 0.3 0.5 11.5 0.15 0.01 33 0 0.0065 0.5 83 5.0 0.5 0.3 0.5 11.5 0.20 0.008 37 0 0.0056 0.5

TABLE-US-00003 TABLE 3 Brazability of brazing Brazability of brazing material on core material on sacrificial Corrosion material side material side resistance Strength after Joint Fillet Coarse Si Joint Fillet Coarse Si Corrosion brazing Specimen No. ratio length particles ratio length particles depth [MPa] Evaluation Example 1 D A D A A 177 B 2 C A C A A 177 B 3 B A B A A 178 B 4 B A B A A 181 B 5 A A A A A 165 C 6 B A B A A 184 B 7 A A A A A 179 B 8 A A A A A 180 B 9 B B B B A 180 B 10 C A C A A 180 B 11 D A D A A 182 B 12 D A D A A 184 B 13 C A C A A 166 C 14 D A D A A 168 C 15 D A D A A 180 B 16 C A C A A 180 B 17 B A B A A 178 B 18 B A B A A 178 B 19 C B C B A 180 B 20 C A C A A 179 B 21 B A B A A 182 B 22 B A B A A 182 B 23 C A C A A 182 B 24 B B B B A 182 B 25 B A B A A 166 C 26 B A B A A 165 C 27 C A C A A 167 C 28 B B B B A 165 C 29 B A B A A 182 B 30 B A B A A 180 B 31 D B D B A 179 B 32 B A C A A 179 B 33 C A C A A 179 B 34 B A B A A 169 C 35 B A B A A 179 B 36 B A B A A 190 A 37 C A C A A 193 A 38 B A B A A 172 C 39 A A A A A 173 C 40 B A B A A 177 B 41 A A A A A 196 A 42 B A B A A 196 A 43 B A B A A 183 B 44 A A A A A 185 A 45 B A B A A 189 A 46 C A C A A 190 A 47 A A A A B 173 C 48 B A B A B 176 B 49 B A B A B 192 A 50 A A A A A 174 C 51 B A B A A 177 B 52 A A A A A 179 B 53 A A A A A 179 B 54 B A B A A 182 B 55 A A A A A 182 B 56 A A A A A 181 B 57 B A B A A 184 B 58 B A B A A 182 B 59 B A B A A 184 B 60 B A B A C 177 B 61 B A B A B 178 B 62 B A B A A 178 B 63 B A B A B 177 B 64 B A B A A 177 B 65 B A B A A 179 B 66 B A B A A 180 B 67 B A B A A 178 B 68 B A B A B 177 B 69 B A B A B 178 B 70 B A B A A 178 B 71 B A B A A 178 B 72 B A B A A 179 B 73 B A B A A 181 B 74 B A A A A 181 B 75 B A B A A 181 B 76 A A A A A 189 A 77 A A B A A 188 A 78 A A A A A 188 A 79 B A B A A 168 C 80 B A B A A 166 C 81 B A B A B 197 A 82 C A C A A 164 C 83 B A C A A 164 C

TABLE-US-00004 TABLE 4 MgBi Concentration of Elements added to compound Mg on surface of brazing material on [/10000 m.sup.2] brazing material core material side Manufac- Less 5 m Core material on core material [wt %] turing than or (Bi + composition [wt %] side Specimen No. Mg Si Bi Sr method 5 m more Mg) Sr Si Mg Mn Cu Fe Ti (wt %) Comparative 1 1.6 11.0 0.25 0.08 E 0.1408 0.7 0.2 1.4 0.4 0.2 Example 2 0.02 11.0 0.11 0.0005 B 9 0 0.000065 0.7 0.5 1.2 0.4 0.2 0.04 3 1.7 11.0 0.15 0.0005 E 32 0 0.000925 0.7 0.5 1.2 0.4 0.2 0.01 1.53 4 0.5 5.9 0.23 0.01 A 42 0 0.0073 0.7 0.5 1.2 0.4 0.2 0.15 0.5 5 0.3 14.5 0.20 0.008 I 55 1 0.004 0.7 0.5 1.2 0.4 0.2 0.10 0.307 6 0.1 11.5 0.03 0.0005 C 16 0 0.000065 0.7 0.5 1.2 0.4 0.2 0.12 0.17 7 0.5 11.5 0.28 0.01 C 45 0 0.0078 0.7 0.5 1.2 0.4 0.2 0.5 8 0.5 12.5 0.15 0.00008 C 42 0 0.000052 0.7 0.5 1.2 0.4 0.2 0.5 9 0.8 12.5 0.15 0.12 C 0.114 0.7 0.5 1.2 0.4 0.2 10 0.5 11.5 0.15 0.005 I 36 0 0.00325 1.2 0.5 1.2 0.2 0.2 0.01 0.5 11 0.5 11.5 0.20 0.01 B 0.007 0.7 0.75 1.2 0.4 0.7 0.01 12 0.5 11.5 0.20 0.006 C 0.0042 0.7 0.2 1.8 0.4 0.2 0.01 13 0.5 11.5 0.20 0.007 H 44 0 0.0049 0.7 0.3 1.2 0.08 0.2 0.01 0.5 14 0.3 11.5 0.20 0.01 A 42 0 0.005 0.1 0.3 1.4 0.9 0.2 0.01 0.3 15 0.3 11.5 0.20 0.005 D 45 0 0.0025 0.5 0.3 1.2 0.4 0.08 0.01 0.3 16 1.0 11.5 0.20 0.09 B 0.108 0.7 0.5 1.2 0.4 0.2 0.01 17 1.2 11.5 0.20 0.08 B 0.112 0.7 0.5 1.2 0.4 0.2 18 0.3 11.5 0.15 0.01 K 12 3 0.0045 0.7 0.5 1.2 0.4 0.2 0.307 19 0.3 11.5 0.15 0.007 N 18 4 0.00315 0.7 0.5 1.2 0.4 0.2 0.307 20 0.5 11.5 0.20 0.007 O 16 5 0.0049 0.7 0.5 1.2 0.4 0.2 0.5 21 0.5 11.5 0.20 0.01 L 17 3 0.007 0.7 0.5 1.2 0.4 0.2 0.5 22 0.5 11.5 0.15 0.008 M 15 6 0.0052 0.7 0.5 1.2 0.4 0.2 0.10 0.5 23 0.5 11.5 0.15 0.01 K 13 5 0.0065 0.7 0.5 1.2 0.4 0.2 0.12 0.5 24 0.5 11.5 0.12 0.006 N 18 2 0.00372 0.7 0.5 1.2 0.4 0.2 0.15 0.5 25 0.02 11.0 0.15 0.0005 E 15 0 0.000085 0.7 0.2 1.2 0.4 0.2 0.032 26 0.3 10.0 0.20 0.01 B 0.005 0.7 0.5 1.2 0.4 0.2 27 0.5 11.5 0.15 0.008 F 33 0 0.0052 0.7 0.5 1.2 0.4 0.2 0.02 0.5 28 0.5 11.5 0.20 0.008 C 37 0 0.0056 0.7 0.2 0.8 0.4 0.2 0.01 0.5 29 0.5 11.5 0.15 0.01 G 33 0 0.0065 0.1 0.5 1.2 0.4 0.2 0.5 Reference 1 0.5 11.5 0.15 0.0007 C 0.000455 0.7 0.2 1.4 0.4 0.2 Example 2 0.5 11.5 0.15 0.01 C 0.0065 0.7 0.2 1.4 0.4 0.2 3 0.5 11.5 0.15 0.008 C 0.0052 0.7 0.2 1.4 0.4 0.2 0.02 4 0.5 11.5 0.15 0.009 C 0.00585 0.7 0.2 1.4 0.4 0.2 5 0.3 10.0 0.20 0.009 B 0.0045 0.7 0.5 1.2 0.4 0.2 0.40

TABLE-US-00005 TABLE 5 MgBi Concentration of Elements added to brazing compound Mg on surface of material on sacrificial [/10000 m.sup.2] brazing material Sacrificial material material side Less 5 m on sacrificial composition [wt %] [wt %] than or (Bi + material side Specimen No. Zn Mn Si Fe Cr Ti Mg Mg Si Bi Sr 5 m more Mg) Sr (wt %) Comparative 1 2.0 0.3 1.6 11.0 0.25 0.08 0.148 Example 2 3.0 0.3 0.1 0.03 11.0 0.11 0.0005 22 0 0.00007 0.041 3 5.0 0.3 0.3 1.7 11.0 0.15 0.0005 32 0 0.000925 1.61 4 5.0 0.3 0.05 0.5 5.9 0.23 0.01 42 0 0.0073 0.5 5 5.0 0.3 0.3 0.3 14.5 0.20 0.008 55 0 0.004 0.29 6 5.0 0.5 0.3 0.2 11.5 0.03 0.0005 24 0 0.000065 0.21 7 5.0 0.5 0.08 0.5 11.5 0.28 0.01 45 0 0.0078 0.5 8 5.0 0.5 0.3 0.3 0.5 12.5 0.15 0.00008 42 0 0.000052 0.5 9 5.0 0.5 0.3 0.3 0.8 12.5 0.15 0.12 0.114 10 5.0 0.8 0.5 0.1 0.3 0.5 11.5 0.15 0.005 36 0 0.00325 0.5 11 5.0 0.5 0.2 0.3 0.5 11.5 0.20 0.01 0.007 12 5.0 0.5 0.1 0.3 0.5 11.5 0.20 0.006 0.0042 13 0.2 0.3 0.5 11.5 0.20 0.007 44 0 0.0049 0.5 14 0.2 0.3 0.3 11.5 0.20 0.01 42 0 0.005 0.3 15 5.0 0.8 0.2 0.3 0.3 11.5 0.20 0.005 45 0 0.0025 0.3 16 4.0 0.5 0.3 0.1 0.3 1 11.5 0.20 0.09 0.108 17 6.0 0.5 0.3 0.1 0.03 1.2 11.5 0.20 0.08 0.112 18 5.0 1 0.3 0.3 0.3 11.5 0.15 0.01 12 4 0.0045 0.3 19 5.0 0.5 0.2 0.3 0.3 0.3 11.5 0.15 0.007 22 4 0.00315 0.3 20 5.0 0.3 0.3 0.5 11.5 0.20 0.007 16 6 0.0049 0.5 21 4.0 0.5 0.3 0.3 0.5 11.5 0.20 0.01 21 2 0.007 0.5 22 5.0 0.4 0.3 0.3 0.5 11.5 0.15 0.008 15 6 0.0052 0.5 23 3.0 0.5 0.3 0.3 0.3 0.5 11.5 0.15 0.01 13 5 0.0065 0.5 24 3.0 0.4 0.3 0.3 0.5 11.5 0.12 0.006 18 2 0.00372 0.5 25 5.0 0.3 0.3 0.03 11.0 0.15 0.0005 39 0 0.00009 0.052 26 0.8 0.3 10.0 0.20 0.01 0.005 27 2.0 0.5 0.3 0.03 11.5 0.12 0.008 33 0 0.0012 0.063 28 5.0 0.5 0.3 0.5 11.5 0.20 0.008 37 0 0.0056 0.5 29 5.0 0.8 0.5 0.3 0.5 11.5 0.15 0.01 33 0 0.0065 0.5 Reference 1 5.0 1.8 0.4 0.4 0.02 0.5 11.5 0.15 0.0007 0.000455 Example 2 0.4 1 0.1 0.09 0.5 11.5 0.15 0.01 0.0065 3 1.0 0.5 0.4 0.3 0.6 0.1 0.2 0.5 11.5 0.15 0.008 0.0052 4 4.0 0.4 0.5 0.4 0.3 0.5 11.5 0.15 0.009 0.00585 5 0.3 10.0 0.20 0.009 0.0045

TABLE-US-00006 TABLE 6 Brazability of brazing Brazability of brazing material on core material on sacrificial Corrosion material side material side resistance Strength after Joint Fillet Coarse Si Joint Fillet Coarse Si Corrosion brazing Specimen No. ratio length particles ratio length particles depth [MPa] Evaluation Comparative 1 Evaluation material cannot be manufactured and evaluated. Example 2 X E A X E A A 176 B 3 X E A X E A A 182 B 4 E A E A A 179 B 5 X E C X E C A 178 B 6 E A E A A 177 B 7 X E A X E A A 181 B 8 X E C X E C A 182 B 9 Evaluation material cannot be manufactured and evaluated. 10 Poor brazing due to generation Poor brazing due to generation A 185 A of significant erosion of significant erosion 11 Evaluation material cannot be manufactured and evaluated. 12 Evaluation material cannot be manufactured and evaluated. 13 A A C A A 159 D 14 A A C A D 168 C 15 A A A A A 163 D 16 Evaluation material cannot be manufactured and evaluated. 17 Evaluation material cannot be manufactured and evaluated. 18 E A E A A 181 B 19 E A E A A 180 B 20 E A E A A 179 B 21 E A E A A 181 B 22 E A E A A 181 B 23 E A E A A 182 B 24 E A E A A 181 B 25 X E A X E A A 164 C 26 Evaluation material cannot be manufactured and evaluated. 27 C A X E A A 180 B 28 B A C A A 160 D 29 C A C A A 159 D Reference 1 Evaluation material cannot be manufactured and evaluated. Example 2 Evaluation material cannot be manufactured and evaluated. 3 Evaluation material cannot be manufactured and evaluated. 4 Evaluation material cannot be manufactured and evaluated. 5 Evaluation material cannot be manufactured and evaluated.

TABLE-US-00007 TABLE 7 (Brazing material) Casting Homogenization Hot rolling condition condition condition Rolling time Molten metal Temperature between 400 C. Equivalent Finish Cooling temperature and time and 500 C. strain temperature rate Specimen No. ( C.) ( C., h) (min) ( C.) ( C./h) Target A 710 450 C., 5 h 15 5.7 320 25 range B 715 450 C., 5 h 14 5.4 334 21 C 715 500 C., 2 h 10 5.5 355 35 D 725 550 C., 2 h 14 5.5 274 28 E 725 400 C., 8 h 18 5.9 290 38 F 735 400 C., 8 h 22 5.7 252 35 G 735 450 C., 8 h 15 6.1 315 42 H 720 450 C., 8 h 24 5 340 34 I 755 500 C., 5 h 14 6.4 347 52 J 745 500 C., 5 h 30 5 290 32 Outside K 695 400 C., 8 h 15 5.3 267 18 the L 680 380 C., 8 h 8 5.2 220 12 target M 715 380 C., 8 h 22 4.8 337 36 N 670 350 C., 8 h 15 4.6 395 22 O 705 350 C. 8 h 7 5.7 322 35

[0149] While preferred embodiments of the invention have been described and illustrated above, it should be understood that these are exemplary of the invention and are not to be considered as limiting. Additions, omissions, substitutions, and other modifications can be made without departing from the spirit or scope of the present invention. Accordingly, the invention is not to be considered as being limited by the foregoing description, and is only limited by the scope of the appended claims.