JP5629113B2 - Aluminum alloy brazing sheet excellent in brazing and corrosion resistance, and heat exchanger using the same - Google Patents

Description

  The present invention is mainly used as a header plate constituting a medium flow path of a heat exchanger for automobiles such as a condenser and an evaporator, and has a particularly excellent brazing property and corrosion resistance, and a heat exchange using this brazing sheet It is about a vessel.

  Aluminum alloy header plate materials used in conventional automotive heat exchangers include, for example, JIS3003 alloy as the core material, and a skin made of Al-Si-Zn alloy or Al-Zn alloy on the outer surface of the heat exchanger. A brazing sheet formed by cladding a material is used.

  In the manufacture of aluminum alloy automotive heat exchangers such as radiators, heaters, condensers, and evaporators, in general, aluminum plates and extrusions molded into a predetermined shape are assembled into a predetermined structure, and then a fluoride-based heat exchanger is assembled. A method of applying flux and brazing and joining in a heating furnace in an inert gas atmosphere is employed.

  In recent years, in heat exchangers for automobiles, the thickness of constituent materials has been reduced from the viewpoint of energy saving and resource saving, and header plates of constituent members have also become thinner. Therefore, corrosion resistance has been improved by adding Zn to the brazing material. However, when trying to ensure corrosion resistance by adding Zn to the brazing material, Zn concentrates in the eutectic structure at the joint between the header plate material and the tube material. The problem was that preferential corrosion became prominent and lead to early penetration.

  Patent Document 1 discloses a method for improving the corrosion resistance without adding Zn to the brazing material. In this document, a header formed by clad an aluminum alloy brazing material containing Si: 1.6 to 5.0% and Mn: 0.05 to 1.6% on the surface of the aluminum alloy core material on the refrigerant side Aluminum alloy materials for plates have been proposed. In Patent Document 1, it is described that a brazing material not containing Zn is used and exhibits good corrosion resistance in an alkaline environment on the refrigerant side. However, in the joint portion between the outer surface and the header plate material or the tube material. There is no mention of corrosion resistance.

JP 2008-303405 A

  The present invention uses a brazing material to which no Zn is added, has excellent brazing properties, and has improved brazing resistance at the outer surface when used, for example, as a header plate material and at the joint between the header plate material and the tube material. An object of the present invention is to provide an aluminum alloy brazing sheet having excellent properties and corrosion resistance.

  Another object of the present invention is to provide a heat exchanger using the brazing sheet and improving the corrosion resistance at the outer surface of the header plate material and the joint portion between the header plate material and the tube material.

In order to solve the above problems, the invention of claim 1 is an aluminum alloy brazing sheet comprising a core material and a first brazing material clad on one main surface of the core material ,
The core material is made of Si: 0.02 to 0.3% (mass%, hereinafter the same), Fe: 0.02 to 0.3%, Cu: 0.3 to 1.0%, Mn: 0.6 to 1.8, Ti: 0.05 to 0.25%, the balance is made of an aluminum alloy consisting of Al and inevitable impurities,
Wherein the first brazing material, Si: 3.0~ 5.5%, Fe : contains 0.1 to 1.5%, the aluminum alloy and the balance being Al and inevitable impurities,
In the case where the amount of Si in the first brazing material is b (%),
50 <a ≦ −34 × b + 425 (1)
0.03 × t ≦ a ≦ 0.30 × t (2)
It is related with the aluminum alloy brazing sheet excellent in brazing property and corrosion resistance characterized by satisfying these relationships.

  In order to solve the above-described problems, the present inventors have conducted various experiments and studies, and as a result, appropriately adjusted the component composition of the core material and the brazing material constituting the aluminum alloy brazing sheet, the thickness and The inventors have found that the above object can be achieved by setting the elements constituting the brazing filler metal so as to satisfy a predetermined relationship, and have achieved the present invention.

  In the present invention, the main surface of the core material clad with the brazing material described above is located outward when the aluminum alloy brazing sheet is used as a header plate material of a heat exchanger, for example. That is, the brazing filler metal exhibits high corrosion resistance by satisfying the above-described composition components and relational expressions, and therefore, when it is positioned outward as described above, its effects can be sufficiently achieved. Is. However, it is not excluded to place the brazing material inside the header plate material.

The invention according to claim 2 is the aluminum alloy brazing sheet excellent in brazing and corrosion resistance. In the other main surface of the core material, Si: 3.0 to 12.0%, Fe: 0.1 A second brazing material made of an aluminum alloy containing 0.5% and the balance being made of Al and inevitable impurities is clad. This other main surface is located inward when the aluminum alloy brazing sheet is used, for example, as a header plate material of a heat exchanger.

  According to a third aspect of the present invention, there are provided a plurality of tanks, a plurality of tubes laid between the tanks, a fin material brazed to each tube, and a header plate material sandwiching the plurality of tubes. In the automotive heat exchanger provided, the above-mentioned aluminum alloy brazing sheet is used as the header-plate material. In this case, the heat exchanger which improves the corrosion resistance in the outer surface of a header plate material and the junction part of this header plate material and a tube material can be provided.

  As described above, according to the present invention, the brazing material to which Zn is not added is used, and the brazing property is excellent. For example, the outer surface when used as a header plate material and the joint portion between the header plate material and the tube material are used. It is possible to provide an aluminum alloy brazing sheet having improved brazing resistance and excellent brazing and corrosion resistance. Moreover, the heat exchanger which uses the said brazing sheet and can improve the corrosion resistance in the outer surface of a header plate material and the junction part of this header plate material and a tube material can be provided.

It is a figure which shows schematic shape of the test piece for evaluating the corrosion resistance in the junction part of the header plate material and tube material in an Example.

  Hereinafter, details of the present invention and other features and advantages will be described based on embodiments.

[1. Heartwood]
The core material mainly contains Si, Fe, Cu, Mn, and Ti, and is composed of the balance Al and inevitable impurities. Further, the content of each element and the effects based on it are as described below.

Si:
Si forms an Al-Mn-Si-based or Al-Fe-Mn-Si-based intermetallic compound together with Mn and Fe, and acts on coarsening of grains after brazing, or is dissolved in an aluminum matrix. Thus, there is an effect of improving the strength by solid solution strengthening. The content of Si is in the range of 0.02 to 0.3% (% of the composition represents mass%, the same shall apply hereinafter), and if less than 0.02%, the effect is small, and if it exceeds 0.3% The types of intermetallic compounds produced increase, the cathode sites increase, and the corrosion resistance of the core material decreases. Preferably, it is 0.05 to 0.2%.

Fe:
Fe forms an Al—Fe—Mn—Si-based or Al—Fe—Si-based intermetallic compound together with Mn and Si, and acts on coarsening of crystal grains after brazing. The Fe content is 0.02 to 0.3%. If it exceeds 0.3%, the types of intermetallic compounds produced increase, the cathode sites increase, and the corrosion resistance of the core material decreases. If it is less than 0.02%, high-purity aluminum ingots must be used, resulting in high costs. Preferably, it is 0.05 to 0.2%. However, when the cost is not considered, the smaller the Fe content, the better.

Cu:
Cu has an effect of improving strength by solid solution strengthening and promoting age hardening. Since the Cu content can further increase the potential, it can contribute to the improvement of corrosion resistance. The Cu content is in the range of 0.3 to 1.0%. If the content is less than 0.3%, the effect is small. If the content exceeds 1.0%, the intergranular corrosion susceptibility increases and conversely the corrosion resistance decreases. I will let you. Preferably, it is 0.35 to 0.6%.

Mn:
Mn forms an Al-Mn-Si-based or Al-Fe-Mn-Si-based intermetallic compound together with Si and Fe and acts on the coarsening of crystal grains after brazing, or forms a solid solution in the aluminum matrix. And strength is improved by solid solution strengthening. In addition, it forms a dense compound with Si that diffuses from the brazing material during the heat of brazing, contributing to improved corrosion resistance. The content of Mn is 0.6 to 1.8%. If the content is less than 0.6%, the effect is small. If the content exceeds 1.8%, the use of Mn increases, and a coarse intermetallic compound is produced. As a result, workability and corrosion resistance are reduced. Preferably, it is 0.8 to 1.5%.

Ti:
Ti improves the strength by solid solution strengthening. Moreover, there exists an effect which suppresses that Ti precipitates in a layer form in a core material and a pitting corrosion advances to a depth direction. The content of Ti is 0.05 to 0.25%, and if it is less than 0.05%, the effect cannot be obtained, and if it exceeds 0.25%, it becomes easy to form a coarse intermetallic compound, workability, Corrosion resistance will decrease. More preferably, it is 0.08 to 0.2%.

  In addition to the above elements in the core material, even if 0.3% or less of Zr, V, or the like is contained, the effects of the present invention are not impaired. The balance may be Al and inevitable impurities. The contents of inevitable impurities are each 0.05% or less, and the total amount is preferably 0.15% or less.

[2. First brazing material]
The first brazing material clad on one main surface of the core material described above mainly contains Si and Fe, and consists of the balance Al and unavoidable impurities. Further, the content of each element and the effects based on it are as described below.

Si:
Si is an essential element for functioning as a brazing material in a liquid phase during brazing addition heat. For example, it is an element that enables brazing when brazing the aluminum alloy brazing sheet of the present invention to a tube material. Most of the brazing layer is in the α phase, and a small amount of the eutectic part flows out to the surface and functions as a brazing material. The corrosion resistance of the α phase remaining after the brazing heat is very good, and the brazing layer can have high corrosion resistance. The Si content is 3.0 to 9.4%. If the amount of Si is less than 3.0%, the resulting liquid phase becomes small and external brazing becomes difficult to function. On the other hand, when the amount of Si exceeds 9.4%, most of it flows as a liquid phase at the time of brazing addition heat and hardly remains on the surface, making it difficult to form the brazing layer itself, and functioning as an anticorrosion layer. Will not be fulfilled. A preferable amount of Si is 3.0 to 5.5%.

Fe:
Fe forms, for example, an Al-Fe-based or Al-Fe-Si-based compound in the eutectic portion in the joint when the aluminum alloy brazing sheet of the present invention is overlapped with a tube material to form a heat exchanger or the like. . Since these compounds serve as starting points of corrosion, the corrosion resistance is improved by the sacrificial anode effect. On the other hand, in the eutectic part in the joint, these compounds serve as a cathode and promote the occurrence of preferential corrosion. Therefore, the Fe content is set to 0.1 to 1.5% by considering the trade-off relationship between these functions and effects.

  If the Fe amount is less than 0.1%, the Al—Fe—Si-based compound present in the surface layer is reduced and the corrosion resistance is lowered. If the Fe amount exceeds 1.5%, the eutectic portion Al— Since the number of Fe-based and Al-Fe-Si-based compounds increases, the corrosion resistance of the joint portion decreases. In order to secure these effects more reliably, the Fe content is preferably 0.2 to 1.0%.

[3. (1) and (2)]
In order to improve the corrosion resistance of the aluminum alloy brazing sheet of the present invention at the outer surface when used as, for example, a header plate material and the joint between the header plate material and the tube material, the brazing sheet is excellent in brazing properties. In the case where 1 brazing material satisfies the above-mentioned requirements and the amount of Si in the brazing material is b (%),
50 <a ≦ −34 × b + 425 (1)
0.03 × t ≦ a ≦ 0.30 × t (2)
It is necessary to satisfy the relationship.

  The formula (1) particularly ensures the above corrosion resistance, and the formula (2) allows the clad rate to be sufficiently controlled when a brazing layer is formed on the main surface of the core material by brazing addition heat. It is a condition to do. In addition, these (1) Formula and (2) Formula are obtained empirically based on the vast experiment of the present inventors.

[4. Second brazing material]
As described above, when the brazing material is formed on the other main surface, i.e., the inner surface, which requires not particularly high corrosion resistance, in addition to one main surface, i.e., the outer surface, which requires particularly high corrosion resistance, it is usually used. Al-Si alloy brazing material can be used. As such a brazing material of an Al—Si based alloy, for example, JIS 4343, 4045, 4047 alloy (Al: 7 to 13%) can be used.

[5. Manufacturing method of aluminum alloy brazing sheet]
The aluminum alloy brazing sheet described above can be produced, for example, as follows.
As the core material, the aluminum alloys having the desired composition described above are melted and cast. In order to make the intermetallic compound produced during casting fine, the cooling rate during casting is preferably 0.5 ° C./s or more. It is preferable that the ingot is chamfered and the ingot is not homogenized before hot rolling or at 550 ° C. or higher. By not performing the homogenization treatment of the core material, the intermetallic compound obtained at the time of casting can be used for the subsequent steps while maintaining a fine state. Alternatively, the homogenization treatment of the core material is performed at 550 ° C. or more, so that the intermetallic compound in the core material can be re-dissolved and finely precipitated again in the subsequent steps.

  The obtained core material is combined with the first brazing material having the above-mentioned desired composition or, if necessary, the second brazing material, heated in that state, and subjected to hot clad rolling. Here, this hot clad rolling is hereinafter simply referred to as “hot rolling”. The total thickness of the laminated material before hot rolling is not particularly limited, but is usually about 250 to 800 mm (preferably about 300 to 600 mm).

  The temperature before hot rolling of this combination material is, for example, 450 ° C. or more and 550 ° C. or less and 2 hours or more and 20 hours or less, and the temperature when the plate thickness reaches 20 mm, for example, during the hot rolling process is 400 ° C. or more. The clad material is produced by controlling and controlling the temperature at the end of hot rolling to 300 ° C. or higher. By such control, precipitation of fine intermetallic compounds occurs during heating before hot rolling, during hot rolling, and after hot rolling, and an appropriate distribution of intermetallic compounds is obtained.

  The clad material obtained by hot rolling is then rolled to a predetermined plate thickness by cold rolling. During the cold rolling or after the cold rolling, an annealing process may be performed about once or twice. The annealing step is usually performed at 200 to 500 ° C. for 1 to 10 hours using a batch furnace, or at 200 to 550 ° C. using a continuous furnace.

[6. Production of heat exchanger and heat exchanger]
Next, the heat exchanger of the present invention will be described.
The heat exchanger according to the present invention includes a plurality of tanks, a plurality of tubes installed between the tanks, a fin material brazed to each tube, and a header plate material sandwiching the plurality of tubes. Do it.

  After forming and combining parts such as a tube material, a fin material, and a header plate material, it is manufactured by heating at 600 ° C. and brazing, for example. The heat exchanger is cooled by air cooling or the like after brazing.

  Hereinafter, the present invention will be described in more detail based on examples. It should be noted that this example is for explaining the effects of the present invention until it is tired, and the technical scope of the present invention is not limited by the example.

(Examples 1-15 and Comparative Examples 1-14)
The core material of the component composition shown in alloy code a1 to a13 in Table 1, the first brazing material on the outer surface side of the component composition shown in alloy code b1 to b7 in Table 2, and the component composition shown in alloy codes c1 to c4 in Table 3 The second brazing material on the inner surface side of each was DC cast to produce an ingot.

  The first brazing material on the outer surface side and the second brazing material on the inner surface side were hot-rolled at 500 ° C. to a predetermined plate thickness after chamfering. The core material was chamfered after homogenizing the ingot at 580 ° C. for 6 hours. A first brazing material on the outer surface side, a core material, and a second brazing material on the inner surface side are stacked in this order, heated to 480 ° C., and then hot-rolled to form a three-layer clad material having a thickness of 3.5 mm. Was subjected to cold rolling to 2.0 mm, and then annealed at 360 ° C. for 3 hours, and then cold rolled to a predetermined plate thickness to obtain a clad material for evaluation.

  By press molding, the three-layer clad material is pressed into a header plate shape, combined with tube material, fin material and reinforcing material, applied with Nocolok flux, dried, and then brazed at 600 ° C for 3 minutes in a high-purity nitrogen gas atmosphere The heat treatment was performed to produce a heat exchanger (size: tube width 16 mm, core size: 160 mm length × 200 mm width) having 16 stages of tubes. In addition, each component composition value shown to Table 1-Table 3 was measured with the emission-spectral-analysis apparatus.

Table 4 shows the combination of the core material and the brazing material, the final plate thickness, and the evaluation results for each of the obtained clad materials.

  An evaluation method of manufacturability, tensile strength, brazing property, and corrosion resistance will be described.

Manufacturability evaluation:
When the clad material was manufactured, a case where a sound clad material was produced was marked with ◯, and when a crack occurred during casting or when the clad rate could not be controlled, x was marked.

Tensile strength measurement:
A JIS No. 5 test piece was cut out from each aluminum alloy clad material, heated at 600 ° C. for 3 minutes in a nitrogen atmosphere as a brazing equivalent heat treatment, a tensile test was conducted, and the tensile strength was examined. And the tensile strength after brazing equivalent heat processing made 120 MPa or more (circle) and 120 MPa or less x.

Brazing evaluation:
Five heat exchangers made of the respective clad materials were submerged, sealed with nitrogen gas at a pressure of 180 KPa inside the heat exchanger, sealed, and held for 30 seconds. The core without leakage did not have a pressure drop, and the core where the pressure drop occurred confirmed the location where bubbles were generated in a submergence test. Of the five units examined, the case where there was no leakage from the fitting portion between the tube material and the header plate material was marked with ◯. The results are shown in Table 4.

Corrosion resistance evaluation:
A sample was cut out from the produced heat exchanger, and a test material for corrosion test was prepared in which the opening of the cut portion was covered with resin so that no corrosive liquid entered the hollow body. For the corrosion resistance evaluation, the SWAAT test (based on ASTM G85) was performed for 1000 hours.

(1) Header plate material flat portion The maximum corrosion depth after the SWAAT test of the header plate flat portion was measured, and the results are shown in Table 4 based on the following criteria.
Evaluation criteria: If the corrosion remained in the brazing filler metal layer on the outer surface side, it was accepted, and if the corrosion reached the core material, it was rejected.

(2) Joint portion of header plate material and tube material The corrosion state of the joint portion of the header plate and the tube after the SWAAT test was investigated and shown in Table 4 according to the following criteria.
Evaluation criteria: A case where the preferential corrosion length L of the corroded portion C is less than 0.3 mm in the joint portion 31 of the header plate material 21 and the tube material 22 shown in FIG.

  As shown in Table 4, as a result of various tests, in Examples 1 to 15 of the present invention, all of the productivity, the tensile strength, the brazing property, and the corrosion resistance are applied to the use and environment to which the clad material of the present invention is applied. It was confirmed that it was suitable. Moreover, in Comparative Examples 1-14, it turned out that it becomes an unreasonable result in the use and environment where the clad material of this invention is used, as described below.

  In the case of Comparative Example 1, a sufficient tensile strength could not be obtained because the amount of Mn in the core material was small. On the other hand, in the case of Comparative Example 2, since the amount of Mn in the core material is large, a coarse intermetallic compound is generated and the corrosion resistance is lowered.

  In the case of Comparative Example 3, since the amount of Si in the core material is large, the types of intermetallic compounds produced such as Al-Mn-Si or Al-Fe-Mn-Si are increased, and the cathode sites are increased. Corrosion resistance of the core material decreased. In the case of Comparative Example 4, since the amount of Fe in the core material is large, the types of intermetallic compounds produced such as Al—Mn—Si or Al—Fe—Mn—Si are increased, and the cathode sites are increased. Corrosion resistance of the core material decreased.

  In the case of Comparative Example 5, since the amount of Cu in the core material is small, the sacrificial anode effect of the first brazing material on the outer surface side becomes insufficient and the corrosion resistance is lowered. In the case of Comparative Example 6, intergranular corrosion occurred because the amount of Cu in the core material was large.

  In the case of Comparative Example 7, since the amount of Ti in the core material was small, Ti was not sufficiently precipitated and the corrosion resistance was lowered. In the case of Comparative Example 8, since the amount of Ti in the core material was large, a coarse intermetallic compound was generated and could not be rolled.

  In the case of Comparative Example 9, since the amount of Si and the amount of Fe in the first brazing material on the outer surface side were small, brazing joining was insufficient, so that the corrosion resistance of the joint could not be evaluated. In the case of Comparative Example 10, since the amount of Si in the first brazing filler metal on the outer surface side is large, it flows almost as a liquid phase at the time of brazing addition heat and cannot function as an anticorrosion layer, and the amount of Fe is also large. Therefore, the compound of the eutectic part in the joint portion increased, the compound worked as a cathode, and corrosion around the compound became remarkable. In the case of Comparative Example 11, since the amount of Si in the first brazing material was large, coarse Si was crystallized at the time of casting, and cracks were generated at the time of clad rolling, so that an evaluation material could not be produced.

  In the case of Comparative Examples 12 and 13, since the expression (1) was not satisfied, the corrosion resistance was lowered. Moreover, in the case of the comparative example 14, since (2) Formula was not satisfied, the clad rate could not be controlled and the predetermined brazing sheet could not be manufactured.

(Examples 16 to 30 and Comparative Examples 15 to 28)
The core material having the component composition indicated by alloy codes a1 to a13 in Table 1 and the brazing material on the outer surface side having the component composition indicated by alloy codes b1 to b7 in Table 2 were each DC casted to produce ingots.

  The brazing material on the outer surface side was hot rolled at 500 ° C. after chamfering to a predetermined thickness. The core material was chamfered after homogenizing the ingot at 580 ° C. for 6 hours. The outer surface brazing material and the core material are stacked in this order, heated to 480 ° C., and then hot-rolled to form a two-layer clad material having a thickness of 3.5 mm, which is then cold-rolled to 2.0 mm, After annealing at 360 ° C. for 3 hours, cold rolling was performed to a predetermined plate thickness to obtain a clad material for evaluation.

  By press molding, the two-layer clad material is pressed into a header plate shape, combined with tube material, fin material and reinforcing material, applied with Nocolok flux, dried, and then brazed at 600 ° C for 3 minutes in a high-purity nitrogen gas atmosphere The heat treatment was performed to produce a heat exchanger (size: tube width 16 mm, core size: 160 mm length × 200 mm width) having 16 stages of tubes. Table 5 shows the combination of the core material and the brazing material, the final plate thickness, and the evaluation results for each of the obtained clad materials. The evaluation of manufacturability, tensile strength, brazing property, and corrosion resistance was carried out in the same manner as in Example 1.

  As shown in Table 5, as a result of various tests, in Examples 16 to 30 of the present invention, all of the productivity, the tensile strength, the brazing property, and the corrosion resistance are applied to the use and environment to which the clad material of the present invention is applied. It was confirmed that it was suitable. Further, in Comparative Examples 15 to 28, as described below, it has been found that an unreasonable result is obtained in the application and environment in which the clad material of the present invention is used.

  In the case of Comparative Example 15, since the Mn content of the core material was small, sufficient tensile strength could not be obtained. In the case of Comparative Example 16, since the amount of Mn in the core material was large, a coarse intermetallic compound was generated, and the corrosion resistance was lowered.

  In the case of Comparative Example 17, since the amount of Si in the core material is large, the types of intermetallic compounds produced such as Al—Mn—Si or Al—Fe—Mn—Si are increased, and the cathode sites are increased. Corrosion resistance of the core material decreased. In the case of Comparative Example 18, since the amount of Fe in the core material is large, the types of intermetallic compounds produced such as Al-Mn-Si or Al-Fe-Mn-Si are increased, and the cathode sites are increased. Corrosion resistance of the core material decreased.

  In the case of Comparative Example 19, since the amount of Cu in the core material is small, the sacrificial anode effect of the brazing material on the outer surface side is insufficient, and the corrosion resistance is lowered. In the case of Comparative Example 20, since the amount of Cu in the core material is large, intergranular corrosion has occurred.

  In the case of Comparative Example 21, since the amount of Ti in the core material was small, Ti was not sufficiently precipitated, and the corrosion resistance was lowered. In the case of Comparative Example 22, since the amount of Ti in the core material was large, a coarse intermetallic compound was generated and could not be rolled.

  In the case of Comparative Example 23, since the amount of Si and the amount of Fe in the brazing material on the outer surface side were small, the brazing joint was insufficient, and thus the corrosion resistance of the joint could not be evaluated. In the case of Comparative Example 24, since the amount of Si in the brazing material on the outer surface side is large, it flows almost as a liquid phase at the time of brazing addition heat and cannot function as an anticorrosion layer. The compound of the eutectic part in the part increased, the compound worked as a cathode, and corrosion around the compound became remarkable. In the case of Comparative Example 25, since the amount of Si in the brazing material was large, coarse Si was crystallized at the time of casting, and cracks were generated at the time of clad rolling, so that an evaluation material could not be produced.

  In the case of Comparative Examples 26 and 27, since the expression (1) was not satisfied, the corrosion resistance was lowered. In the case of Comparative Example 28, since the formula (2) was not satisfied, the clad rate could not be controlled, and a predetermined brazing sheet could not be manufactured.

  The present invention has been described in detail based on the above specific examples. However, the present invention is not limited to the above specific examples, and various modifications and changes can be made without departing from the scope of the present invention.

Claims (3)

An aluminum alloy brazing sheet comprising a core material and a first brazing material clad on one main surface of the core material,
The core material is made of Si: 0.02 to 0.3% (mass%, hereinafter the same), Fe: 0.02 to 0.3%, Cu: 0.3 to 1.0%, Mn: 0.6 to 1.8, Ti: 0.05 to 0.25%, the balance is made of an aluminum alloy consisting of Al and inevitable impurities,
The first brazing material contains Si: 3.0 to 5.5%, Fe: 0.1 to 1.5%, and the balance is made of an aluminum alloy composed of Al and inevitable impurities,
In the case where the amount of Si in the first brazing material is b (%),
50 <a ≦ −34 × b + 425 (1)
0.03 × t ≦ a ≦ 0.30 × t (2)
An aluminum alloy brazing sheet excellent in brazing and corrosion resistance, characterized by satisfying the following relationship: An aluminum alloy brazing sheet comprising a core material, a first brazing material clad on one main surface of the core material, and a second brazing material clad on the other main surface of the core material,
The core material is made of Si: 0.02 to 0.3% (mass%, hereinafter the same), Fe: 0.02 to 0.3%, Cu: 0.3 to 1.0%, Mn: 0.6 to 1.8, Ti: 0.05 to 0.25%, the balance is made of an aluminum alloy consisting of Al and inevitable impurities,
The first brazing material contains Si: 3.0 to 5.5%, Fe: 0.1 to 1.5%, and the balance is made of an aluminum alloy composed of Al and inevitable impurities,
The second brazing material contains Si: 3.0-12.0%, Fe: 0.1-0.5%, the balance is made of an aluminum alloy consisting of Al and inevitable impurities,
In the case where the amount of Si in the first brazing material is b (%),
50 <a ≦ −34 × b + 425 (1)
0.03 × t ≦ a ≦ 0.30 × t (2)
An aluminum alloy brazing sheet excellent in brazing and corrosion resistance, characterized by satisfying the following relationship: An automotive heat exchanger comprising a plurality of tanks, a plurality of tubes installed between the tanks, a fin member brazed to each tube, and a header plate member sandwiching the plurality of tubes. Because
The heat exchanger using the aluminum alloy brazing sheet according to claim 1 or 2 as the header-plate material.

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