JP6526404B2 - Aluminum alloy brazing sheet - Google Patents

Description

  The present invention relates to an aluminum alloy brazing sheet suitably used for a heat exchanger.

  From the viewpoint of fuel efficiency improvement and space saving, the heat exchanger tends to be lighter, and therefore, the members to be used are required to be thinner and stronger. Also, in recent years, the plate of the radiator is strongly required to have high durability (static strength, dynamic strength: fatigue strength). In order to meet such requirements, conventional materials lack durability. For this reason, some aluminum alloy brazing sheets in which the component addition amount is adjusted have been proposed so far (see, for example, Patent Documents 1 and 2).

JP, 2011-202285, A JP 2012-82459 A

In addition, in the simple increase of the amount of additive elements of the core material, which is a measure usually taken for the enhancement of strength, it is difficult to achieve the enhancement of strength because there is a limit to the amount of addition due to a problem in manufacturing. In addition, even if the strength can be increased to a certain extent, the strength of the material is also increased at the same time, which causes a problem that the formability is reduced.
On the other hand, when Mg is added to the core material, although it is possible to increase the strength without reducing the formability, there is a problem that the brazing property is reduced.
Therefore, in the prior art, it is difficult to obtain high durability and to obtain high formability while satisfying the brazeability.

  The present invention has been made on the background of the above-mentioned circumstances, and an object of the present invention is to provide an aluminum alloy brazing sheet which is excellent in formability and is excellent in high strength and brazing property.

Therefore, when the influence of the metal factor on the durability of the brazing sheet material was investigated, the component range of the core material was properly adjusted, and then from the surface of the material after passing through the temperature history at the time of using the product to the predetermined range. It was found that a material excellent in durability can be obtained by adjusting the hardness to be high and reducing the amount of coarse second phase particles in the sacrificial material.
In addition to having a sufficient durability, the 0.2% proof stress of the material is made equal to or less than a predetermined value, and the strength after passing a temperature history after brazing and after product use is made to be a predetermined value or more. It turned out that the outstanding material was obtained and came to the present invention.

That is, among the aluminum alloy brazing sheets of the present invention, the first present invention is used with a plate thickness of 0.7 mm or more, a sacrificial material is disposed on one side of the core material, and a brazing material is clad on the other side. Al alloy clad material
The said core material is Mn: 1.3-2.0%, Si: 0.7-1.2%, Fe: 0.1-0.5%, Cu: 0.7-1.3 by mass%. %, The balance being composed of Al and unavoidable impurities, and the above-mentioned sacrificial material is, by mass%, Zn: 3.0 to 6.0%, Mg: 0.5 to 1.8%, Si: 0.05 to 0.05%. 0.5% is contained, the remainder is made of Al and unavoidable impurities, and the cladding ratio of the sacrificial material is in the range of 6 to 20%, and the Al alloy clad material has 0.2% proof stress before brazing 80 MPa or less, tensile strength after brazing equivalent heat treatment at 600 ° C. × 3 minutes is 175 MPa or more, 2 μm or more distributed in the sacrificial material after aging treatment at 90 ° C. for 7 days after the brazing equivalent heat treatment Density of the second phase particles is 2000 pcs / mm 2 or less, and further, after the heat treatment corresponding to the brazing, the heat treatment is performed at 90.degree. C. for 7 days. Average hardness to a depth of 150μm from the surface of the material of the sacrificial material after the aging treatment is equal to or not less than 100 HV.

Aluminum alloy brazing sheet of the second invention, in the first invention, tensile strength after 90 ° C. × 7 days aging treatment after corresponding heat treatment with the filtrate cormorants is characterized in that at least 200MPa .

In the aluminum alloy brazing sheet according to a third aspect of the present invention, in the first or second aspect of the present invention, the brazing material is made of an Al—Si alloy or an Al—Si—Zn alloy, and the brazing material is It is characterized by containing Si: 7.2-10.0% by mass%.

Aluminum alloy brazing sheet of the fourth invention, in any one of the first to third invention, wherein the brazing material is made of Al-Si-Zn alloy, the brazing material in mass%, Zn: It is characterized by containing 0.5 to 3.0%.

  The reasons for limitation of the present invention will be described below. The content of each component in the composition is indicated by mass%.

(Core material)
Mn: 1.3 to 2.0%
Has the effect of improving the strength after brazing by forming intermetallic compounds (second phase particles) of Si, Fe, etc. and Al-Mn-Si, or Al- (Mn, Fe) -Si. ing. If the content is less than 1.3%, the effect is not sufficiently exhibited, and if it exceeds 2.0%, a huge intermetallic compound of Al- (Mn, Fe) -Si system is formed, and the aluminum alloy sheet The manufacturability of the Therefore, the Mn content is set to 1.3% to 2.0%. For the same reason, the lower limit is preferably 1.4% and the upper limit is 1.8%.

Si: 0.7 to 1.2%
Si is contained to precipitate Al-Mn-Si-based or Al- (Mn, Fe) -Si-based intermetallic compounds and to obtain strength after brazing by dispersion strengthening. Moreover, it is contained in order to be able to improve material strength by forming Mg and Mg-Si precipitates diffused from the sacrificial material. However, if the content is less than 0.7%, the effect of dispersion strengthening is small, and the desired post-braze strength can not be obtained. On the other hand, if the content exceeds 1.2%, the solid solution amount of Si is increased, the solidus temperature (melting point) is lowered, and significant brazing is liable to occur at the time of brazing. For the same reason, it is desirable to set the lower limit to 0.8% and the upper limit to 1.1%.

Fe: 0.10 to 0.50%
By the inclusion of Fe, dispersion strengthening by an Al- (Mn, Fe) -Si compound or an Al- (Mn, Fe) compound is obtained, and the strength after brazing is improved.
If the content of Fe is less than 0.10%, cracking is likely to occur during casting, making production difficult. In addition, when the content of Fe exceeds 0.50%, a large coarsened crystallized product (intermetallic compound) is formed during casting, which makes it difficult to produce the material. For the same reason, it is preferable to set the lower limit to 0.2% and the upper limit to 0.40%.

Cu: 0.7 to 1.3%
Cu is contained because it improves the strength after brazing by solid solution strengthening. However, if it is less than 0.7%, the effect can not be obtained sufficiently. On the other hand, if the content is more than 1.3%, the strength of the material becomes too high and the formability is reduced. The Cu content is 0.7 to 1.3%. For the same reason, it is desirable to set the lower limit to 0.70% and the upper limit to 1.2%.

(Sacrifice material)
The sacrificial material is not particularly limited in the present invention, but one having the following components is preferable.
Zn: 3.0 to 6.0%
By being exposed to room temperature after brazing heat treatment or a temperature range when using a radiator, Mg—Zn precipitates are formed to increase the hardness of the sacrificial material and to increase the material strength. This has the effect of improving the fatigue strength. However, if the Zn content is less than 3.0%, the effect is not sufficiently exhibited, and if it exceeds 6.0%, the melting point of the sacrificial material is lowered and the sacrificial material is melted at the time of brazing. For the same reason, it is desirable to set the lower limit to 3.3% and the upper limit to 6.0%.

Mg: 0.5 to 1.8%
Mg has the effect of increasing the hardness of the sacrificial material and the material strength by forming Zn and Mg-Zn precipitates or Si and Mg-Si precipitates. This has the effect of improving the fatigue strength. However, if the Mg content is less than 0.5%, the effect is not sufficiently exhibited, and if it exceeds 1.8%, rolling becomes difficult. For the same reason, it is desirable to set the lower limit to 0.7% and the upper limit to 1.8%.

Si: 0.05 to 0.5%
Si has the effect of improving the strength of the material by forming a fine Mg-Si compound with Mg. However, if the Si content is less than 0.05%, the effect is not sufficiently exhibited, and if it exceeds 0.5%, the melting point of the sacrificial material is lowered, and the sacrificial material is melted at the time of brazing. For the same reason, it is preferable to set the lower limit to 0.10% and the upper limit to 0.4%.

Unavoidable Impurities In addition to the above components, Mn can contain up to 0.5% of Mn, and up to 0.5% of unavoidable impurities such as Fe. For example, if Mn is contained in excess of the above content, coarse Al-Mn-Si-Fe-based or Al-Mn-Fe-based compounds are easily formed, and thus, second phase particles of 2 μm or more present in the sacrificial material The number density of N increases and the fatigue strength decreases.
In addition, if Fe is contained in excess of the above content, it is easy to form coarse Al-Mn-Si-Fe, Al-Mn-Fe, or Al-Fe-Si compounds, too. The number density of the 2nd phase particle | grains of 2 micrometers or more which exist in it will increase, and a fatigue strength will fall.

(Brazy material)
The brazing material is not particularly limited in the present invention, and general brazing materials used for brazing can be used. For example, JIS 4343 alloy, JIS 4045 alloy, JIS 4047 alloy, or an alloy of these metals is used as Zn. The alloy which contains, or the alloy containing Mg, Cu, Li etc. can be used.
As an aluminum alloy constituting the brazing material, for example, an aluminum alloy containing 7.2 to 10.0% of Si, and, if necessary, a component composition containing 0.5 to 3.0% of Zn can do.

Coarse second phase particles with a density of 2 2000m or more second phase particles distributed in the sacrificial material after aging for 7 days at 90 ° C after brazing heat treatment are 2000 pieces / mm ² or less more than 2 mm It tends to be the origin of cracks and also works to promote the development of fatigue cracks. When there are few coarse second phase particles, fatigue strength is improved. Therefore, the density of the second phase particles of 2 μm or more distributed in the sacrificial material after the above-mentioned aging treatment is set to 2000 / mm ² or less. For the same reason, the density is preferably 1600 pcs / mm ² or less.
The dispersion of the second phase particles can be achieved, for example, by optimizing the chemical components and optimizing the production conditions (homogenization treatment).

(Casting speed of sacrificial material)
When the cooling rate at the time of casting is slow, coarse second phase particles crystallized at the time of casting tend to be coarse. Therefore, it may not be preferable if the casting speed is slow in view of the material components and the homogenization treatment conditions. Therefore, the casting speed is preferably 0.3 ° C./s or more.
(Homogenization treatment of the sacrificial material)
When the homogenization treatment is applied at high temperature, coarse second phase particles crystallized at the time of casting tend to further grow and become large. Therefore, it is desirable that the homogenization treatment is not performed or at a low temperature of 500 ° C. or less.

The average hardness to a depth of 150 μm from the material surface of the sacrificial material after aging for 7 days at 90 ° C after brazing heat treatment is 100 HV (Vickers hardness) or more. A tensile stress acts on the sacrificial material side of the header plate of the radiator. Bending fatigue occurs and breaks. In this bending fatigue mode, particularly when the strength (hardness) of the material surface is high, the fatigue strength can be effectively improved. If the average hardness to 150 μm is less than 100 HV, the strength is insufficient and the fatigue strength is reduced. For the same reason, it is desirable to set the average hardness to 110 HV or more.
The average hardness can be achieved, for example, by optimizing the components, adjusting the homogenization treatment conditions, and the like.

0.2% proof stress before brazing 80MPa or less, tensile strength after brazing heat treatment 175MPa or more, tensile strength after aging treatment at 90 ° C for 7 days after brazing heat treatment 200MPa or more (before brazing 0.2% proof stress less than 80MPa)
The header plate is generally formed into a product shape by pressing. Therefore, when the proof stress of the material (before brazing) is high, the amount of spring back increases, and it becomes difficult to obtain a desired shape, and the formability is reduced. Therefore, it is desirable to set the proof stress before brazing to a predetermined value or less. If the 0.2% proof stress before brazing exceeds 80 MPa, the formability deteriorates.
(The tensile strength after brazing heat treatment is 175 MPa or more, and the tensile strength after aging treatment at 90 ° C x 7 days after brazing heat treatment is 200 MPa or more)
On the other hand, if the strength of the header plate is not high after brazing, the plate is broken due to stress caused by vibration or internal pressure fluctuation during product use, making it difficult to maintain product performance. Therefore, it is desirable that the strength after brazing and the strength after aging at 90 ° C. for 7 days simulating the temperature history at the time of using the product be equal to or greater than a predetermined value. If the tensile strength is less than the above, the durability of the product is reduced.
The strength can be achieved, for example, by optimizing the components, adjusting the homogenization treatment conditions, or the like.

Clad rate of sacrificial material: 6 to 20%
The inventive material achieves high strength and high fatigue strength characteristics by enhancing the strength of the sacrificial material more than the core material and the like. Therefore, these effects are more effectively exhibited as the ratio of the sacrificial material to the entire plate thickness is higher. In other words, if the proportion of the sacrificial material is small, the effect is not sufficiently exerted. Therefore, it is desirable that the cladding ratio of the sacrificial material be in the range of 6 to 20%. If the cladding ratio is less than 6%, the strength decreases after brazing and after aging at 90 ° C. for 7 days, and the fatigue strength decreases. On the other hand, if the cladding ratio exceeds 20%, cladding rolling becomes difficult.

  As described above, according to the present invention, the strength after brazing is excellent, and there is an effect that the characteristic excellent in corrosion resistance can be obtained.

  In this embodiment, an aluminum alloy for a core material, an aluminum alloy for a sacrificial material, and an aluminum alloy for a brazing material having the composition defined in the present invention are separately cast, and the obtained ingot is homogeneous as needed. A hot-rolled aluminum alloy sheet for a core material, an aluminum alloy for a sacrificial material, and an aluminum alloy for a brazing material are formed into a three-layer structure by hot rolling.

In the present embodiment, high strength, high hardness of the high sacrificial material layer, and high fatigue strength are obtained by making both the sacrificial material and the core material have predetermined chemical components and making the homogenization treatment of the core material a high temperature. Specifically, Zn and Mg, which easily generate fine precipitates, are disposed in a sacrificial material, and Si is arranged in a core material, and the ratio is such that precipitates are easily generated. Furthermore, by applying a homogenization treatment of the core material at a high temperature, it is possible to easily form finer precipitates by increasing the solid solution degree of Si in the core material. For example, the homogenization process of a core material can select the conditions heated at 550 degreeC-605 degreeC for 4 to 16 hours. When the homogenization treatment condition is less than 550 ° C. or less than 4 hours, the solid solution degree of Si in the core material is lowered, and it is difficult to form a Mg-Si based precipitate. As a result, the hardness of the core material in the vicinity of the sacrificial material decreases, and the average hardness of 150 μm from the surface tends to decrease. On the other hand, if the temperature is higher than 605 ° C. or 16 hours, a region where a low melting point layer such as a grain boundary exists may be locally melted.
The casting speed of the sacrificial material is preferably 0.3 ° C./s or more. Thereby, it is possible to prevent the crystallization of coarse second phase particles during casting.
In addition, it is preferable that the homogenization treatment of the sacrificial material is not performed or a low temperature of 500 ° C or less. Thereby, the second phase particles in the sacrificial material can be prevented from becoming coarse, and the number density of second phase particles of 2 μm or more present in the sacrificial material can be lowered.

After this, a brazing sheet is obtained by cold rolling to a target plate thickness (0.7 mm or more). The cladding ratio of the sacrificial material at this time is preferably 6 to 20%, and the cladding ratio of the brazing material is usually 10%.
In addition, this invention is not limited to the said process, For example, intermediate annealing can also be given to the middle of the cold rolling after hot rolling as needed.

The brazing sheet has a 0.2% proof stress before brazing of 80 MPa or less, a tensile strength of 175 MPa or more after brazing heat treatment, and a tensile strength of 200 MPa or more after aging treatment at 90 ° C. for 7 days after brazing heat treatment You can have
The high and low of the homogenization temperature of the core material affects the size and number density of dispersed particles dispersed in the core material before brazing. When the homogenization temperature is low, the dispersed particles are finely and densely distributed, and the yield strength of the material is increased. On the other hand, when the homogenization temperature is high, the dispersed particles are coarse and the density is roughly distributed, so that the yield strength of the material is lowered.
Therefore, in the present invention, the 0.2% proof stress before brazing can be reduced by carrying out the homogenization treatment temperature of the core material at a high temperature (for example, the homogenization treatment temperature of the core material is 550 ° C. or higher). .
In addition, the high and low of the homogenization temperature of the core material affects the solid solution degree of Si of the core material after brazing, and when the homogenization temperature is high, the solid solution degree of Si of the core material is increased. After the heat treatment, Mg-Si precipitates are likely to be formed at the time of aging treatment at 90 ° C. for 7 days, and the strength tends to be high at the time of aging treatment. Therefore, in the present invention, the core material is subjected to the homogenization treatment temperature at a high temperature (for example, the core material homogenization treatment temperature is set to 550 ° C. or higher), and tensile strength after aging treatment at 90 ° C. × 7 days after brazing heat treatment The strength can have 200 MPa or more.

<Brazing treatment and metal structure after brazing>
When brazing is performed using the brazing sheet, the brazing material can be melted by heating to a temperature of about 580 to 610 ° C., held for a predetermined time, and then cooled. As an example, after being carried into a brazing furnace, after heating to a brazing temperature of 600 ° C. at a predetermined heating rate in an atmosphere such as in a nitrogen atmosphere, the brazing temperature is maintained at about 3 minutes and then -100 ° C. / After cooling to a temperature range of about 300 ° C. at a cooling rate of about a minute, the temperature can be lowered to room temperature by performing air cooling using a fan or the like, and brazing can be performed.

In the present embodiment, the density of second-phase particles of 2 μm or more distributed in the sacrificial material after aging treatment at 90 ° C. for 7 days after brazing heat treatment is 2000 particles / mm ² or less, and further brazing heat treatment The characteristics that the average hardness up to 150 μm from the material surface of the sacrificial material after aging for 7 days at 90 ° C. later is 100 HV or more are obtained.

Hereinafter, examples of the present invention will be described in comparison with comparative examples.
An alloy for a core material, an alloy for a sacrificial material, and a brazing material alloy are prepared with the compositions shown in Tables 1 to 3 (the balance is Al and unavoidable impurities), and an ingot is produced by a conventional method. The sacrificial material and the core material are homogenized under predetermined conditions.
The above-mentioned alloys are hot-rolled in a combination shown in Tables 4 and 5, and are stacked on each other by cold-rolling. Core cladding ratio 55 to 90%, sacrificial cladding ratio 5 to 30%, brazing material cladding ratio 5 An aluminum alloy brazing sheet having a thickness of 1.0 mm was produced at an amount of 15%. The material produced above was subjected to final annealing at 350 ° C. for 5 hours to prepare a test material.

Evaluation Method of Each Evaluation Item The following items shown in Tables 4 and 5 were evaluated, and the evaluation results are shown in Tables 4 and 5.
○ Measurement method of 0.2% proof stress before brazing A sample was cut out parallel to the rolling direction from the produced plate material, a test piece of JIS No. 13 B shape was produced, a tensile test was carried out, and tensile strength was measured. The tensile speed was 3 mm / min.
The 0.2% proof stress evaluated 90 MPa or more as x, more than 80 MPa and less than 90 MPa as ○, and 80 MPa or less as ○.

○ Tensile strength after brazing, tensile strength after aging at 90 ° C × 7 days For tensile strength after brazing, the prepared plate is heat-treated equivalent to brazing, and then a sample is cut out in parallel with the rolling direction, JIS 13 A B-shaped test piece was produced and determined by conducting a tensile test. The tensile speed was 3 mm / min. The heat treatment equivalent to brazing was set to 600 ° C. × 3 min (the same applies hereinafter).
The tensile strength after brazing was evaluated as × for less than 170 MPa, ○ for less than 170-175 MPa, and ○ for 175 MPa or more.
The tensile strength after aging at 90 ° C for 7 days is obtained by heat-treating the prepared plate for equivalent heat treatment, then aging for 7 days in an electric furnace heated to 90 ° C, and then cutting out the sample parallel to the rolling direction A test piece having a shape of JIS No. 13 B was prepared, and a tensile test was performed to obtain it. The tensile speed was 3 mm / min.
The tensile strength after aging evaluated that less than 190 MPa as x, less than 190-200 MPa as ○, and 200 MPa or more as ○.

○ Fatigue strength after aging at 90 ° C for 7 days After heat treatment of the produced plate material for brazing equivalent, aging treatment is performed for 7 days in an electric furnace heated to 90 ° C, and then a sample is cut out parallel to the rolling direction , The usual plane bending fatigue test was carried out. The stress ratio was R = -1 (two-sided swing), and the frequency was 20 Hz.
A large number of tests in which the applied stress is varied under the above conditions are performed, and a stress-repetition number diagram (S-N diagram) is collected. A stress of several 10 ⁷ repetitions is calculated using the least squares method for a region of 10 ⁵ to 10 ⁷ repetitions of the S-N diagram, and this stress is defined and evaluated as fatigue strength.
The fatigue strength was evaluated as less than 90 MPa as ×, less than 90 to 100 MPa as ○, and 100 MPa or more as ○.

○ Hardness of sacrificial material after aging at 90 ° C for 7 days After heat-treating the prepared plate for brazing equivalent, it is further aged for 7 days in an electric furnace heated to 90 ° C, and then pieces for hardness measurement are taken. After cutting out and filling with resin, the parallel cross section in the rolling direction was mirror finished by emery polishing and buff polishing. The hardness distribution from the surface of the sacrificial material was measured using this sample using a micro Vickers hardness tester, and the average hardness from the surface to a depth of 150 μm was determined. The hardness was measured at room temperature under a load of 0.01 kgf for 15 seconds.
The hardness of the sacrificial material after aging was evaluated as less than 100 HV as ×, less than 100-110 HV as ○, and 110 HV or more as ○.

○ Density of second-phase particles of 2 μm or more in the sacrificial material after aging at 90 ° C for 7 days After heat treatment of the plate material prepared for brazing equivalent, aging treatment is performed for 7 days in an electric furnace heated to 90 ° C. After cutting out a small piece from the above and filling in the resin, the parallel cross section in the rolling direction was mirror-finished by emery polishing, buff polishing and chemical polishing. Further, it was etched with a 0.5% aqueous solution of hydrofluoric acid, photographed with an optical microscope, and the size and density of second phase particles were determined by image analysis. The observation field of view was about 7000 μm ^2, and the investigation was conducted for five fields of view. The density of second phase particles of 2 μm or more is shown in the table. If the observation field of view is too small, it is not possible to grasp the state of the entire material if there is a local location where there are few second phase particles, so it is necessary to carry out analysis over such a wide range as described above. Although the above measurement is performed on a sample after aging at 90 ° C. for 7 days, the distribution state of the second phase particles (2 μm or more) does not change after brazing and after aging, so the sample after brazing Similar surveys may be conducted for

Self-Corrosion Resistance After heat-treating the prepared plate for equivalent heat treatment, it is subjected to aging treatment for 7 days in an electric furnace heated to 90 ° C, then small pieces for corrosion resistance evaluation are cut out, and the sacrificial material surface and end portions are masked. And SWAAT test (according to ASTM G85-A) for 30 days.
The test body after the test was subjected to 10 minutes immersion in a mixed solution of boiled phosphoric acid and chromic acid to remove a corrosion product to evaluate a corrosion state (corrosion depth).
The samples with a maximum corrosion depth exceeding 100 μm were evaluated as ×, those with over 60 to 100 μm as ○, and those with 60 μm or less as ○.

As shown in the above Tables 4 and 5, when the number of compounds in the sacrificial material is small, the origin of cracks is reduced and the fatigue strength is improved. In addition, when the hardness of the sacrificial material is high, cracking is less likely to occur and fatigue strength is improved.
In addition, when the 0.2% proof stress of the material before brazing is low, the formability is good.
When the tensile strength after brazing and the tensile strength after aging are high, it becomes highly resistant to static load stress at the time of product specification. It was also found that the fatigue strength is high when the strength is high and the hardness is high.

Claims (4)

An Al alloy clad material which is used at a plate thickness of 0.7 mm or more, a sacrificial material is disposed on one side of a core material, and a brazing material is clad on the other side,
The said core material is Mn: 1.3-2.0%, Si: 0.7-1.2%, Fe: 0.1-0.5%, Cu: 0.7-1.3 by mass%. %, The balance being composed of Al and unavoidable impurities, and the above-mentioned sacrificial material is, by mass%, Zn: 3.0 to 6.0%, Mg: 0.5 to 1.8%, Si: 0.05 to 0.05%. 0.5% is contained, the remainder is made of Al and unavoidable impurities, and the cladding ratio of the sacrificial material is in the range of 6 to 20%, and the Al alloy clad material has 0.2% proof stress before brazing 80 MPa or less, tensile strength after brazing equivalent heat treatment at 600 ° C. × 3 minutes is 175 MPa or more, 2 μm or more distributed in the sacrificial material after aging treatment at 90 ° C. for 7 days after the brazing equivalent heat treatment the density of the two-phase particles 2,000 / mm ² or less, further, 7 days at 90 ° C. after corresponding heat treatment with the brazing Aluminum alloy brazing sheet average hardness to a depth of 150μm from the surface of the material of the sacrificial material after the aging treatment is equal to or not less than 100 HV.   The aluminum alloy brazing sheet according to claim 1, wherein the tensile strength after aging treated at 90 ° C for 7 days after the heat treatment corresponding to brazing is 200 MPa or more.   The brazing material is made of an Al-Si alloy or an Al-Si-Zn alloy, and the brazing material contains, by mass%, Si: 7.2 to 10.0%. The aluminum alloy brazing sheet as described in 2.   The said brazing material consists of an Al-Si-Zn type alloy, The said brazing material contains Zn: 0.5-3.0% in mass%, The any one of the Claims 1-3 characterized by the above-mentioned. Aluminum alloy brazing sheet as described in.