JP4649326B2 - Aluminum clad material for header member and tank member of heat exchanger - Google Patents

Description

  The present invention relates to an aluminum clad material excellent in strength and corrosion resistance, and particularly to an aluminum clad material suitable for a header member and a tank member of an automotive heat exchanger such as a radiator.

  In recent years, heat exchangers for automobiles such as radiators have been made lighter and more compact, and recyclability has become important. Therefore, the header member and the tank member that have been conventionally made of resin or the like are being changed to a clad material of aluminum or aluminum alloy (hereinafter collectively referred to as “made of aluminum”).

As shown in FIGS. 3A and 3B, such a clad material is obtained by clad an aluminum alloy having a melting point lower than that of the core material 11 as a brazing material 12 on one surface side of the aluminum core material 11 , and the other surface side. The sacrificial anti-corrosion material 13 is clad with an Al—Zn alloy. 3 (a) is a fragmentary sectional view der header member 25 and tank member 27 of heat exchanger 20 which is formed by using an aluminum clad material Ri, (b) it is in (a) Ru partially enlarged view der an enlarged portion indicated by a circle. In addition, the code | symbol 21 in Fig.3 (a) is a flat tube, and the code | symbol 23 is a fin.

However, when the header member 25 and the tank member 27 are made of an aluminum clad material, a location where the brazing material 12 and the sacrificial anticorrosive material 13 are joined is generated. In such a location, as shown in the enlarged view of FIG. 3B, Zn in the sacrificial anticorrosive material 3 diffuses into the fillet 14 during brazing, and the Zn content tends to increase. When the Zn content is high, the potential of the fillet 14 becomes lower than the surface of the brazing material 12 and the sacrificial anticorrosive material 13 after brazing, and as a result, the fillet 14 is likely to be preferentially corroded. . When the fillet 14 is corroded, not only is the risk of leakage occurring, but the heat exchanger 20 may be destroyed from the corroded portion .
Note that if the header member 25 and the tank member 27 are changed to aluminum, the plate thickness becomes thinner than that of the resin header member and tank member, so it is necessary to increase the strength of the clad material.

  This invention is made | formed in view of the said subject, The objective is to provide the aluminum clad material for the header member and tank member of the heat exchanger which aimed at high corrosion resistance and high intensity | strength.

Aluminum clad material for the header member and the tank member of a heat exchanger according to the present invention which solves the previous SL problem, Cu: 0.4 to 1.0 wt%, Si: 0.3 to 1.0 wt%, Mn: 0.5 to 2.0% by mass, with the balance being aluminum and unavoidable impurities as the core material, Si: 0.6 to 1.0% by mass, Mn: 0.6 to 1.3% by mass, Zn: 2.0 % by mass or less , the balance is made of Al and inevitable impurities, and Si / Mn = 0.11 to 6.7 is added. The sacrificial anticorrosive material is clad, and a brazing material made of an aluminum alloy is clad on the other side of the core material.

As described above, the aluminum clad material for the header member and the tank member of the heat exchanger according to the present invention increases the content of Si, Cu, and Mn and performs solid solution / dispersion strengthening. It is possible to increase the strength of the clad material.
Further, by suppressing the Zn content of the sacrificial anticorrosive material to 2.0% by mass or less, the enriched amount of Zn in the fillet due to brazing can be suppressed. Thereby, it becomes possible to suppress the potential deterioration of the fillet, to suppress the potential difference between the brazing material and the sacrificial anticorrosive material, and the surface, and to suppress the preferential corrosion of the fillet.
In addition to these, by controlling the content of Si and Mn contained in the sacrificial anticorrosive material and the range of the content ratio to a specific range, the sacrificial anticorrosive material can be made high without impairing the corrosion resistance of the fillet. By increasing the strength, it is possible to further increase the strength of the aluminum clad material for the header member and the tank member of the heat exchanger of the present invention.

  In this invention, plate | board thickness is 0.7-2.5 mm, and the said core material is Ti: 0.25 mass% or less, Cr: 0.25 mass% or less, Zr: 0.25 mass% or less. It is preferable to contain at least one selected from the group consisting of

ADVANTAGE OF THE INVENTION According to this invention, the aluminum clad material for the header member and tank member of a heat exchanger excellent in intensity | strength and corrosion resistance can be provided.
Therefore, if the aluminum clad material for the header member and the tank member of the heat exchanger of the present invention is used, the heat exchanger such as a radiator (particularly the header material and the tank member) can be increased in strength and corrosion resistance. . Further, since the heat exchanger is made of aluminum or an aluminum alloy, it can greatly contribute to an improvement in the recycling rate.

  Next, an aluminum clad material (hereinafter simply referred to as “aluminum clad material”) for the header member and the tank member of the heat exchanger of the present invention will be described in detail with reference to FIG. FIG. 1 is a schematic diagram showing the configuration of the aluminum clad material of the present invention.

  As shown in FIG. 1, the aluminum clad material of the present invention has a configuration in which a core material 1, a sacrificial anticorrosive material 3 is clad on one surface side of the core material 1, and a brazing material 2 is clad on the other surface side of the core material 1. ing.

  Here, the core material 1 used in the present invention includes Cu: 0.4 to 1.0 mass%, Si: 0.3 to 1.0 mass%, Mn: 0.5 to 2.0 mass%, and the balance. Is made of an aluminum alloy composed of Al and inevitable impurities.

The sacrificial anticorrosive material 3 used in the present invention is made of an aluminum alloy containing Zn: less than 2.2% by mass, and the balance being made of Al and inevitable impurities.
The sacrificial anticorrosive material 3 contains Si: 0.15-1.0% by mass, Mn: 0.15-1.3% by mass, Zn: less than 2.2% by mass, and the balance is Al and inevitable impurities. More preferably, it is made of an aluminum alloy added in the range of Si / Mn = 0.11 to 6.7.

The brazing material 2 used in the present invention is made of an aluminum alloy having a melting point lower than that of the core material 1.
Hereinafter, the reason why the chemical composition of the core material 1 and the sacrificial anticorrosive material 3 is regulated to a specific range will be described. The brazing material 2 can be used without any particular limitation as long as it is an aluminum alloy having a melting point lower than that of the core material 1 and having a conventionally known chemical composition.

(1) Cu
Cu exists in the aluminum alloy in a solid solution state after brazing, and improves the strength. Cu is a noble element among typical aluminum-added elements. Therefore, a sufficient potential difference can be ensured between the core material 1 and the sacrificial anticorrosive material 3 by clad with a sacrificial anticorrosive material made of 1000 series or 7000 series aluminum alloy. (Corrosion resistance) can be increased.
If the Cu content is less than 0.4% by mass, no significant improvement in the strength after brazing due to solid solution strengthening is observed, and the potential difference between the core material 1 and the sacrificial anticorrosive material 3 is also small. It becomes difficult to obtain the sacrificial anticorrosive effect of the anticorrosive material 3. In particular, in the recent trend of thinning, it is difficult to obtain suitable strength and corrosion resistance after brazing, so 0.4% by mass or more is desirable.
On the other hand, when the Cu content is 1.0% by mass or more, depending on the addition amount of other elements, cracking is likely to occur during casting, and productivity is lowered. Moreover, since melting | fusing point falls by Si which diffuses from the brazing | wax material 2 at the time of brazing, the core material 1 will fuse | melt at the time of brazing, and it will become easy to generate | occur | produce erosion etc. in the core material 1 as a result. As a result, brazability is reduced.
Therefore, the Cu content is desirably 0.4 to 1.0 mass%. In particular, if the Cu content is 0.6 to 0.9% by mass, the sacrificial anticorrosive effect and high strength of the sacrificial anticorrosive material 3 can be sufficiently achieved.

(2) Si
Si has an effect of solid solution strengthening in a solid solution state, and forms an intermetallic compound with Al and Mn, and has an effect of improving strength by dispersion strengthening.
If the Si content in the core material is less than 0.3% by mass, the effect of improving the strength cannot be sufficiently obtained.
On the other hand, if the Si content in the core exceeds 1.0% by mass, the melting point decreases depending on the amount of other elements added, the core melts during brazing, and brazing becomes impossible. .
Therefore, the Si content is desirably 0.3 to 1.0 mass%. In particular, with regard to increasing the strength, an excellent effect can be exhibited by setting the Si content to 0.6% by mass or more, so it is desirable to contain 0.6% by mass or more.

On the other hand, the content of Si in the sacrificial anticorrosive material is 1.0% by mass or less, but the strength after brazing is improved by increasing the addition amount up to 1.0% by mass, but 1.0% by mass. If it is added in excess of%, the solid solution amount of Si increases, so the potential becomes noble and the corrosion resistance deteriorates. In addition, Si easily precipitates at the crystal grain boundaries, and the corrosion resistance deteriorates due to intergranular corrosion.
On the other hand, when the Si content is less than 0.15% by mass, the effect of contributing to the strength after brazing becomes small.
Therefore, the content of Si in the sacrificial anticorrosive material is preferably 0.15 to 1.0% by mass . In addition , the range recommended for achieving both the strength after brazing and the corrosion resistance suitably is 0.6 to 0.9% by mass, but is added when the core material 1 has high strength (for example, 150 MPa or more). You don't have to.

(3) Mn
Mn is an essential element for distributing fine intermetallic compounds in the alloy and improving the strength without reducing the corrosion resistance. In the chemical composition of the present invention, an intermetallic compound is formed with Al and Si, and the strength after brazing is greatly improved by the dispersion of the fine intermetallic compound. Moreover, since some Mn is dissolved in the aluminum alloy, the brazing strength can be improved by the solid solution.

When the content of Mn in the core material is less than 0.5% by mass, the effect due to the dispersion of the intermetallic compound cannot be sufficiently obtained, so that the strength after brazing is not significantly improved.
On the other hand, when the content of Mn exceeds 2.0% by mass, the strength is excessively improved, the moldability is lowered, and press molding and roll forming become difficult.
Therefore, the content of Mn in the core material is desirably 0.5 to 2.0% by mass.

On the other hand, if the content of Mn in the sacrificial anticorrosive material exceeds 1.3% by mass, the potential becomes noble due to an increase in the amount of Mn dissolved, and a sufficient sacrificial anticorrosive effect cannot be obtained. In addition, the increase in the number of intermetallic compounds that are cathode reaction sites increases the corrosion rate and degrades the corrosion resistance.
On the other hand, when the content of Mn is less than 0.15% by mass, Al and Si do not form an intermetallic compound, so that not only does not contribute to strength improvement but also does not form an intermetallic compound, The amount of grain boundary precipitation increases and corrosion resistance deteriorates.
Therefore, the content of Mn recommended for ensuring corrosion resistance and strength after brazing is preferably 0.15 to 1.3% by mass, and preferably 0.6 to 0.9% by mass. More preferably, it may not be added when the core material has high strength.

(4) Ti, Cr, Zr
Ti, Cr, and Zr are defined as 0.25% by mass or less, and if these are contained in excess of 0.25% by mass, huge crystallized products are easily formed during casting, and the corrosion resistance is greatly increased. This is because it deteriorates.
However, when Ti is contained in an amount of 0.25% by mass or less, the crystallized substance is distributed in layers at the time of rolling and can take a layered form of corrosion, so that the corrosion resistance can be improved.
Moreover, when Cr and Zr are contained at 0.25 mass% or less, the strength after brazing can be improved.

(5) Si / Mn ratio in sacrificial anticorrosive material When the sacrificial anticorrosive material contains Si in the range of 0.15 to 1.0 mass% and Mn in the range of 0.15 to 1.3 mass% ( That is, it is necessary to set Si / Mn = 0.11 to 6.7 in the case corresponding to claim 2 of the present application. When only one of the elements is added, for example, when only Si is added, Si precipitates alone at the grain boundary, and when only Mn is added, an Al-Mn intermetallic compound is crystallized. Precipitate at grain boundaries. As described above, when precipitates exist at the crystal grain boundaries, the intergranular corrosion sensitivity is remarkably increased, so that the corrosion resistance is greatly degraded.
When the same amounts of Si and Mn are added, fine Al—Mn—Si intermetallic compounds are precipitated in the crystal grain boundaries, and the strength can be improved by dispersion strengthening.

  However, when Si and Mn are present in an amount corresponding to the inevitable impurity level, they may be outside the range of the relational expression described above. The reason is that since the content is very small, the amount of simple Si and Al—Mn intermetallic compounds precipitated at the grain boundaries is extremely reduced, and the corrosion resistance is not significantly reduced. In the present invention, the amounts corresponding to the inevitable impurity levels of Si and Mn are less than 0.15% by mass of Si and less than 0.15% by mass of Mn.

(6) Zn
Zn has the effect of giving a sacrificial anticorrosive effect (corrosion resistance) to the aluminum alloy.
In general, in an aluminum clad material for a heat exchanger such as a radiator, when the Zn content of the sacrificial anticorrosive material increases, the potential difference between the core material and the sacrificial anticorrosive material after brazing increases, and the sacrificial anticorrosive effect of the sacrificial anticorrosive material 3 increases. Become.

However, for example, when the tank portion and the header portion of the radiator are brazed, there is a portion where the sacrificial anticorrosive material 3 and the brazing material 2 always come into contact with each other, so that Zn is concentrated in the fillet formed after brazing. Since the Zn content concentrated in the fillet is higher than the Zn content on the surface of the sacrificial anticorrosive material, the potential tends to be reduced, and the fillet is preferentially corroded, resulting in leakage and cracking. It will be.
Therefore, in this invention, it is necessary to make content of Zn into 2.0 mass% or less . If the Zn content is more than 2.0 % by mass, the fillet is preferentially corroded as described above. In the present invention, since the content of Cu in the core material is large, it is possible to ensure a sufficient potential difference between the core material and the sacrificial anticorrosive material without adding Zn to the sacrificial anticorrosive material 3, and the corrosion resistance is greatly deteriorated. Never do. However, considering prevention of preferential corrosion of fillets, it is more desirable to contain Zn at 1.0 mass% or less.

(7) Other elements Fe may be added to the core material and the sacrificial anticorrosive material as long as it is 0.2 mass% or less. If the Fe content exceeds 0.2% by mass, the number of crystallized products after casting is greatly increased, so that the cathode reaction is promoted and the corrosion resistance is greatly deteriorated.

(8) Plate thickness If the plate thickness of the aluminum clad material is less than 0.7 mm, the plate thickness is thin, so that the rigidity is lowered and cannot be used as a header and tank material.
On the other hand, if the thickness of the aluminum clad material exceeds 2.5 mm, molding becomes difficult.
Therefore, the plate thickness is preferably 0.7 to 2.5 mm.

Next, with respect to the aluminum clad material for the header member and tank member of the heat exchanger of the present invention (hereinafter simply referred to as “aluminum clad material”), an example that satisfies the requirements of the present invention and a reference that does not satisfy the requirements of the present invention An example and a comparative example are compared and demonstrated concretely.

≪Reference example≫
An aluminum clad material in which a sacrificial anticorrosive material was clad on one surface side of the core material and a brazing material was clad on the other surface side of the core material was manufactured by the following method.

First, test materials No. 1 having the chemical composition shown in Table 1 were used. After chamfering 1 to 12 cores to a plate thickness of 44 mm, homogenization heat treatment at 590 ° C. for 6 hours was performed. The brazing material and the sacrificial anticorrosive material are obtained by chamfering the ingot and then performing a heat treatment at 510 ° C. for 6 hours, followed by hot rolling to obtain a brazing material having a thickness of 3 mm and a sacrificial anticorrosive material having a thickness of 3 mm. did. The chemical composition of the sacrificial anticorrosive material of Reference Example includes Si and Mn. However, since the content of each test material is less than 0.15% by mass, inevitable impurities are present. It can be said that it contains a level equivalent.

  Then, the sacrificial anticorrosive material and the brazing material are superimposed on one side and the other side of the core material, respectively, to form a three-layer structure material, which is hot-rolled to obtain an aluminum clad material having a thickness of 4 mm (see FIG. 1). ).

The aluminum clad material was cold-rolled to a thickness of 1.6 mm, and then annealed at 380 ° C. for 3 hours to produce an aluminum clad material of O material. As shown in FIG. 1, a brazing material 2 is clad on one surface side of the core material 1, and a sacrificial anticorrosive material 3 is clad on the other surface side of the core material 1.
A test piece having a width of 50 mm and a length of 60 mm was cut out from the aluminum clad material produced in this manner, and after applying a predetermined amount (5 g / m ² ) of flux, as shown in FIG. The three sacrificial anticorrosive materials were overlapped so as to overlap each other by 20 mm, and brazed in a nitrogen atmosphere at 595 ° C. for 5 minutes. FIG. 2 is an enlarged view of a main part of the brazed aluminum clad material.

After brazing, a seal is applied to the sacrificial anticorrosive material 3 so that the outer surface corrosion resistance sample is the corrosion test surface, and the sacrificial anticorrosive material 3 surface is not in contact with the corrosive liquid (CASS test solution). After a part of the seal was folded back on the brazing material 2 surface, the seal end portion was coated with a bond so that the corrosive liquid did not enter the sacrificial anticorrosive material 3 surface side.
In addition, after brazing, a seal is applied to the brazing material surface so that the sacrificial anticorrosive material side becomes a corrosion test surface as a sample for evaluating the inner surface corrosion resistance, and the sacrificial anticorrosive material surface is sealed so that the brazing material 2 side does not touch the corrosive liquid. After folding a part of the seal, the seal end was coated with a bond to prevent the corrosive liquid from entering the brazing material surface.

Thereafter, a CASS test (salt spray test: JIS Z 2371) is performed for 1500 hours as an external surface corrosion resistance test, and an immersion test (Na ⁺ : 118 ppm, Cl ⁻ : 58 ppm, SO ₄ ²⁻ : 60 ppm, Cu ²⁺ ) as an internal surface corrosion resistance test. 1 ppm, Fe ³⁺ : 30 ppm), and the corrosion state was observed.

On the other hand, regarding the measurement of the strength after brazing, a test piece for strength measurement of 120 mm × 250 mm was cut out from the aluminum clad material produced by the above-described method and brazed in a nitrogen atmosphere at 595 ° C. for 5 minutes. The test pieces were brazed one by one in a state where a hole was made in the upper part of the test piece and hung on a rod.
After brazing, three JIS No. 5 test pieces were cut out from the test piece, and then a tensile test was performed to measure the strength.
Table 1 shows the components of the aluminum clad material subjected to these tests. These test results are shown in Table 2.

As shown in Table 1 and Table 2, the test material No. Nos. 1 to 6 did not satisfy the requirements of the present invention, but good results were obtained for any of the strength after brazing, the outer surface corrosion resistance, and the inner surface corrosion resistance. Therefore, it could be evaluated that it corresponds to a reference example of the present invention.

  On the other hand, test material No. Since Nos. 7 to 12 do not satisfy any of the requirements of the present invention, unfavorable results were obtained for any of the strength after brazing, the outer surface corrosion resistance, and the inner surface corrosion resistance. Therefore, it could be evaluated that it corresponds to a comparative example of the present invention.

  Specifically, the test material No. In No. 7, since the content of Cu in the core material was small, the potential difference between the brazing material and the core material was small, and the outer surface corrosion resistance could not be secured (plate penetration corrosion). Moreover, since the strength after brazing was low, the result was insufficient for use as a member of a heat exchanger such as a radiator. Moreover, the outer surface corrosion resistance was also inferior.

  Test material No. No. 8, because the content of Zn in the sacrificial anticorrosive material was large, Zn was concentrated in the fillet formed when the brazing material and the sacrificial anticorrosive material were superposed and brazed, and the potential of the fillet was reduced. The fillet corroded preferentially (fillet penetration corrosion). Moreover, the outer surface corrosion resistance was also inferior.

  Test material No. In Nos. 9 and 10, since the contents of Cu and Si in the core material were large, the melting point of the core material decreased at the time of brazing, and the brazing material eroded the core material and could not be brazed.

  Test material No. In No. 11, since the content of Mn in the core material was small, the contribution of solid solution strengthening of Mn and dispersion strengthening by intermetallic compounds was reduced. Therefore, the strength after brazing decreased. Further, due to the decrease in the number of intermetallic compounds in the core material, solid solution Si in the core material was precipitated at the grain boundaries, resulting in poor outer surface corrosion resistance and inner surface corrosion resistance, and plate penetration corrosion occurred.

  Test material No. In No. 12, since the content of Mn in the core material was large, the number and size of intermetallic compounds were significantly increased. As a result, corrosion was promoted as a cathode site in the outer surface corrosion test and the inner surface corrosion test, resulting in significantly inferior outer surface corrosion resistance and inner surface corrosion resistance and plate penetration corrosion.

<Example>
In « Examples» , Test Nos. That were able to obtain favorable results in « Reference Example» . As in 1, the core material containing Cu, Si, Mn, Ti, Fe in the contents shown in Table 3, and the sacrificial anticorrosive material containing Si, Mn, Zn, Si / Mn in the contents and ratios shown in Table 3 The aluminum clad material clad with the brazing material was hot-rolled and crimped in the same manner as in Reference Example to produce an aluminum clad material having a plate thickness of 4 mm. The test material No. The aluminum clad material of 13-22 was cold-rolled to a plate thickness of 1.6 mm and then annealed to obtain an aluminum clad material of O material. Next, a test piece having a width of 50 mm and a length of 60 mm was cut out from the aluminum clad material, and after applying a predetermined amount (5 g / m ² ) of flux, as shown in FIG. The three food materials were superposed so as to overlap each other by 20 mm, and brazed in a nitrogen atmosphere at 595 ° C. for 5 minutes.
Then, the strength after brazing, the outer surface corrosion resistance test, and the inner surface corrosion resistance test were performed in the same manner as in Reference Example .
Table 3 shows the components of the aluminum clad material subjected to these tests. These test results are shown in Table 4.

As shown in Tables 3 and 4, test material No. Since Nos. 13 to 15 satisfy the requirements of the present invention, good results could be obtained for any of the strength after brazing, the outer surface corrosion resistance, and the inner surface corrosion resistance. Therefore, it could be evaluated that it corresponds to an example of the present invention.
In particular, test material No. Nos. 13 to 15 indicate that Si and Mn in the sacrificial anticorrosive material are the test materials No. Since there were more than 1-6, these test material No. The strength after brazing was higher than those of 1 to 6, and it could be evaluated that it was a better aluminum clad material for header members and tank members of heat exchangers.

  Test material No. 16 is a test material No. As in No. 8, the content of Zn in the sacrificial anticorrosive material was large, so Zn was concentrated in the fillet formed when the brazing material and the sacrificial anticorrosive material were superposed and brazed, and the potential of the fillet was reduced. As a result, the fillet corroded preferentially (fillet penetration corrosion). Moreover, the outer surface corrosion resistance was also inferior.

  Test material No. In No. 17, since Si in the sacrificial anticorrosive material was added in a large amount and Mn was added in a small amount, Si / Mn = 42.5. As a result, single Si precipitated at the crystal grain boundaries, the inner surface corrosion resistance was inferior, and intergranular corrosion occurred, resulting in penetration corrosion.

  Test material No. In No. 18, Si in the sacrificial anticorrosive material was added in a small amount, and Mn was added in a large amount. As a result, an Al—Mn-based intermetallic compound was precipitated at the crystal grain boundaries, the inner surface corrosion resistance was inferior, and intergranular corrosion occurred, resulting in penetration corrosion.

  Test material No. No. 19, since the content of Si in the sacrificial anticorrosive material was large, the potential of the sacrificial anticorrosive material became noble, and further, the internal corrosion resistance was greatly deteriorated due to the precipitation of Si at the grain boundaries, resulting in intergranular corrosion. .

  Test material No. No. 20, since the content of Mn in the sacrificial anticorrosive material was large, the potential of the sacrificial anticorrosive material became noble, and the number and size of intermetallic compounds increased to promote the cathode reaction and deteriorate the internal corrosion resistance. Through-plate corrosion occurred.

  Test material No. In No. 21, since the content of Cu in the core material is small, the potential difference between the sacrificial anticorrosive material—the core material and the brazing material—the core material is small. In addition, since the content of Fe in the core material is large, the number of crystallized substances is large and the size is large, so that the cathode reaction is increased and corrosion is promoted. As a result, penetration corrosion occurred (plate penetration corrosion). Moreover, since the strength after brazing was low, the result was insufficient for use as a member of a heat exchanger such as a radiator. Moreover, the outer surface corrosion resistance and the inner surface corrosion resistance were also inferior.

  Test material No. In No. 22, since the amount of Ti added in the core material was large, a huge intermetallic compound was crystallized at the time of casting the core material. Therefore, it became a cathode site in the inner and outer surface corrosion resistance test, corrosion was accelerated, and the corrosion resistance was greatly deteriorated. As a result, the outer surface corrosion resistance and the inner surface corrosion resistance were inferior and plate penetration corrosion occurred.

It is a schematic diagram which shows the structure of the aluminum clad material of this invention. It is a principal part enlarged view of the brazed aluminum clad material. (A) is principal part sectional drawing of the header member and tank member of a heat exchanger formed using the clad material made from aluminum, (b) is the elements on larger scale of (a).

Explanation of symbols

1 core material 2 brazing material 3 sacrificial anticorrosive material

Claims (2)

An aluminum alloy containing Cu: 0.4 to 1.0 mass%, Si: 0.3 to 1.0 mass%, Mn: 0.5 to 2.0 mass%, with the balance being Al and inevitable impurities As heartwood,
One side of the core material contains Si: 0.6 to 1.0 mass%, Mn: 0.6 to 1.3 mass%, Zn: 2.0 mass% or less , and the balance is Al and inevitable impurities. And a sacrificial anticorrosive material added in a range of Si / Mn = 0.11 to 6.7, and a brazing material made of an aluminum alloy on the other side of the core material. Aluminum clad material for exchanger header and tank members. The plate thickness is 0.7 to 2.5 mm, and the core material is selected from Ti: 0.25% by mass or less, Cr: 0.25% by mass or less, Zr: 0.25% by mass or less. The aluminum clad material for a header member and a tank member of a heat exchanger according to claim 1, wherein at least one kind is contained.

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