JP2001105173A - Aluminum alloy compound material for heat exchanger and its manufacturing method - Google Patents

Abstract

PROBLEM TO BE SOLVED: To suppress a minute damage near a weld zone when producing a electroresistance welded tube of thin/high strength in an aluminum alloy clad material. SOLUTION: A core material has an alloy composition consisting of 0.5-2.0 wt.% Mn, 0.25-0.75 wt.% Cu, 0.3-1.3 wt.% Si, 0.01-0.5 wt.% Mg, the balance Al with an addition of an essential component of Ti, Zr, Cr, V in a range of <=0.02% in order to increase strength, a sacrifice anodizing skin material has an alloy composition consisting of 0.0001-0.15 wt.% In, 0.3-1.7 wt.% Mg, 2.0 wt.% Mn, the balance Al, with an addition of an essential component of 0.01-0.5 wt.% Si and 0.001-0.05 wt.% Ti. Further, a heat treatment condition immediately before final cold rolling after clad rolling is restricted to an annealing temperature of 360-550 deg.C, a temperature rise rate of >=55 deg.C/h between 100 deg.C and the annealing temperature and a cooling rate of >=75 deg.C/h between the annealing temperature and 150 deg.C.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy composite material for a heat exchanger, and more particularly to a tube material mainly used for a heat exchanger for a vehicle such as a radiator or a heater core. TECHNICAL FIELD The present invention relates to an aluminum alloy composite material in which generation of minute scratches near a part is suppressed and a method for manufacturing the same.

[0002]

2. Description of the Related Art Conventionally, aluminum tubing used for, for example, heat exchangers for automobiles has been made of Al-Cu-Mn JIS3.
003 alloy as a core material, for example, J
A brazing sheet is used in which an Al-Si brazing material such as an IS4343 alloy is clad and a sacrificial anode skin material of an Al-Mg system such as JIS7072 alloy is clad on the other surface of the core material. Further, as a method of manufacturing the pipe, a method of manufacturing from the brazing sheet by roll forming and high frequency welding is adopted.
The properties required for such a composite material are that it exhibits high strength when thinned, has good brazing properties, and has high strength and high corrosion resistance even after brazing.

As a material satisfying such requirements, for example, in Japanese Patent Application Laid-Open No. 5-230576, Mg is used for a sacrificial anode skin material.
Any one of Si, In, Sn, and Ga is 0.2
% Of composite materials are proposed. Examples of the composition are as follows: (a) Core material Mn: 0.3 to 2.0% (% by weight, the same applies hereinafter) Cu: 0.05 to 1.0% Si: 0.05 to 1.0% Mg: 0.1 to 1.0% 5% or less Remainder: Al (b) Sacrificial anode skin material Mg: 1.0 to 2.5% Si: 0.05% or more and less than 0.20% In: 0.2% or less, Sn: 0. 2% or less, Ga: 0.
One or two of 2% or less, the balance: Al (c) brazing material Al-Si alloy. By using such an alloy, high strength is obtained after brazing without impairing brazing properties, and the thickness of the sacrificial anode layer is not excessively increased.

In Japanese Patent Application Laid-Open No. 6-128675, a transition metal such as Cr, Ti, Zr, or Ni is added in a trace amount to a 3003 series alloy as a core material, and Mg: 0.5 to 4.0 is added to a sacrificial anode skin material.
%, In: Al-Mg-I containing 0.005 to 1.0%
A composite material using an n alloy has been proposed. Examples of the composition are as follows: (a) Core material Mn: 0.1 to 2.0% Cu: 0.1 to 1.0% Si: 0.2 to 1.5% Mg: 0.2% or less Cr: 0.1 to 2.0% 01 to 0.5% Ti: 0.01 to 0.5% Zr: 0.01 to 0.5% Ni: 0.01 to 2.0% Remainder: substantially Al (b) Sacrificial anode skin Mg : 0.5 to 4.0% In: 0.005 to 1.0% Remainder: Al (c) brazing material Al-Si alloy. It is stated that by adopting such a composition, the strength of the core material is increased and the corrosion resistance of the sacrificial anode skin material is increased, whereby high strength and high corrosion resistance are obtained.

Japanese Patent Application Laid-Open No. Hei 6-136476 discloses that a core material contains Al, Mn, Cu, Zr alloy, Mg, Si, Ti,
A composite material is proposed in which Cr and V are added to increase the strength, and an Al-Mg-Ti-In alloy having a high sacrificial anode effect is used as a sacrificial anode material. Examples of the composition are: (a) core material Mn: 0.7 to 1.5% Cu: 0.2 to 0.7% Si: 0.3 to 1.3% Mg: 0.05 to 0.5% Cr : 0.05-0.25% Ti: 0.05-0.25% Zr: 0.05-0.25% V: 0.05-0.25% Remainder: Substantially Al (b) sacrificial anode Skin material Mg: 0.35 to 3.5% In: 0.005 to 0.05% Ti: 0.001 to 0.05% Remainder: Al (c) brazing material Al-Si based alloy . With such a composition, the potential of the skin material does not increase at the time of heating by brazing, and no pitting corrosion occurs in the structural member after brazing.

The cladding material is processed by hot rolling at about 500 ° C. with the both sides of the core material sandwiched between a sacrificial anode skin material and a brazing material, and then cold rolling with appropriate intermediate annealing. The clad material having a predetermined thickness is obtained by repeating the necessary number of times. The intermediate annealing at this time is usually 300 ° C to 5 ° C.
It is carried out at a temperature of 00 ° C. for about 1 to 2 hours, but no consideration is given to the heating rate for heating to the intermediate annealing temperature or the cooling rate for cooling from the intermediate annealing temperature to room temperature.
In particular, the cooling rate was close to natural cooling.

[0007] By the way, the material used for forming the pipe is
Usually, a material having a tempering degree of about H14 is used. This is because in addition to the need for a certain strength at the time of pipe molding, it is also to prevent erosion (erosion) by the brazing material at the time of brazing after the heat exchanger is installed. For this reason, the tube before brazing is used at a final rolling reduction of 10 to 50%.

[0008]

However, with the recent demand for high strength and thinning, the formation of ERW pipes has become even more difficult. In such a situation, particularly problematic in the case of an electric resistance welded tube is a minute flaw generated in a welded portion and its vicinity. In the case of an electric resistance welded tube, the more the minute scratches, the more the defect as a tube immediately. as a result,
The product yield at the time of forming the pipe is reduced, and the acceptance rate of the heat exchanger as a final product is significantly reduced. Therefore, even if the thinness and high strength can be achieved, the life of the heat exchanger will be shortened if the tube formability is not considered. There is a demand for a material which has a high strength even if it is made thinner, does not cause micro scratches on the welded portion, and is sufficiently resistant to corrosion by a refrigerant, and a satisfactory material cannot be obtained with conventional materials.

[0009]

DISCLOSURE OF THE INVENTION The present invention has been made in view of the above-mentioned problems, and has been made to achieve a thin and high-strength flat tube material manufactured by high-frequency welding, and has excellent tube-forming properties. In order to obtain a material, we tried to make the anisotropy in the material smaller. That is, the present inventors have sought to reduce the occurrence of minute scratches in the welded portion and its vicinity during the manufacture of the ERW pipe. As a result of various studies on the composition of the core material and the sacrificial anode skin material, Al-Mn-Cu-Si-M
The strength is increased by adding Ti, Zr, Cr, and V to the g alloy as essential components in a range of 0.02% or less, respectively, and the sacrificial anode skin material is made of Al-In-Mg alloy with Si and Ti as essential components. The added alloy composition was adopted. Further, means for limiting the heat treatment conditions immediately before the final cold rolling after the clad rolling was adopted.

That is, the invention described in claim 1 is:
A sacrificial anode skin is clad on one side of the aluminum alloy core, and an Al-Si or Al-S
An aluminum alloy composite material for a heat exchanger clad with a brazing filler metal made of an i-Zn-based alloy, wherein the core material has a composition of Mn: 0.5 to 2.0% and Cu: 0.25 to 0.75.
%, Si: 0.3 to 1.3%, Mg: 0.01 to 0.5
%, Ti: ≤ 0.02%, Zr: ≤ 0.02%, Cr:
≦ 0.02%, V: ≦ 0.02%, with the balance being Al
And unavoidable impurities, and the composition of the sacrificial anode skin material is I
n: 0.0001-0.15%, Si: 0.05-0.
5%, Mg: 0.3-1.7%, Ti: 0.001
An aluminum alloy composite material for a heat exchanger, characterized by containing 0.05% and the balance consisting of Al and inevitable impurities.

The invention described in claim 2 is the first invention.
In the core material of the invention described in the section, Fe-0.5 to 1.2% is further added. That is, an aluminum alloy for a heat exchanger in which a sacrificial anode skin material is clad on one surface of an aluminum alloy core material and a brazing material made of an Al-Si or Al-Si-Zn alloy is clad on the other surface of the core material. A composite material, wherein the composition of the core material is Mn: 0.5 to 2.0.
%, Cu: 0.25 to 0.75%, Si: 0.3 to 1.%.
3%, Mg: 0.01-0.5%, Fe: 0.5-1.
2%, Ti: 0.02%, Zr: 0.02%, C
r: ≦ 0.02%, V: ≦ 0.02%, the balance consists of Al and unavoidable impurities, and the composition of the sacrificial anode skin material is In: 0.0001 to 0.15%, Si : 0.0
5 to 0.5%, Mg: 0.3 to 1.7%, Ti: 0.0
It is an aluminum alloy composite material for heat exchangers, containing from 0.01 to 0.05%, with the balance being Al and unavoidable impurities.

The invention described in claim 3 is the first invention.
In addition to the Zn, Sn, F
One or more of e and Ni are added. That is, an aluminum alloy for a heat exchanger in which a sacrificial anode skin material is clad on one surface of an aluminum alloy core material and a brazing material made of an Al-Si or Al-Si-Zn alloy is clad on the other surface of the core material. A composite material,
The composition of the core material is Mn: 0.5 to 2.0%, Cu: 0.2
5 to 0.75%, Si: 0.3 to 1.3%, Mg: 0.
01-0.5%, Ti: ≦ 0.02%, Zr: ≦ 0.0
2%, Cr: ≦ 0.02%, V: ≦ 0.02%, the balance being Al and unavoidable impurities, and the composition of the sacrificial anode skin material is In: 0.0001 to 0.15. %, S
i: 0.05 to 0.5%, Mg: 0.3 to 1.7%, T
i: 0.001 to 0.05%, and Zn: 0.5 to
5.0%, Sn: 0.001 to 0.2%, Fe: 0.5
Aluminum alloy composite material for heat exchangers, characterized in that it contains one or more of Ni: 0.1 to 0.6% and the balance of Al and unavoidable impurities. is there.

The invention described in claim 4 is the first invention.
In addition, 0.5 to 1.2% of Fe is further added to the core material of the invention described in the above section, and Zn, Sn, Fe, Ni are further added to the sacrificial anode skin material.
One or two or more of these are added. That is, a sacrificial anode skin material is clad on one surface of an aluminum alloy core material, and an Al-Si or A
An aluminum alloy composite material for a heat exchanger clad with a brazing material made of an l-Si-Zn-based alloy, wherein the composition of the core material is Mn: 0.5 to 2.0%, Cu: 0.25 to 0.5%.
75%, Si: 0.3 to 1.3%, Mg: 0.01 to
0.5%, Fe: 0.5 to 1.2%, Ti: ≦ 0.02
%, Zr: ≦ 0.02%, Cr: ≦ 0.02%, V: ≦
0.02%, the balance being Al and unavoidable impurities, and the composition of the sacrificial anode skin material is In: 0.0001.
0.15%, Si: 0.05-0.5%, Mg: 0.
3 to 1.7%, Ti: 0.001 to 0.05%, Zn: 0.5 to 5.0%, Sn: 0.001 to 0.2
%, Fe: 0.5 to 1.2%, Ni: 0.1 to 0.6%
And aluminum alloy composite materials for heat exchangers, characterized in that at least one of them is contained, and the balance consists of Al and inevitable impurities.

The invention according to claim 5 relates to a method for producing an aluminum alloy composite material for a heat exchanger according to the present invention, wherein when the composite material is produced by clad rolling, heat treatment is performed immediately before final rolling. It defines the process conditions. That is, in the heat treatment process immediately before the final rolling, the annealing temperature is set to 360 ° C. to 550 ° C., the average temperature rising rate from 100 ° C. to the annealing temperature is 55 ° C./h or more, and the annealing temperature is set to 150 ° C.
The average cooling rate up to 75 ° C. and the final rolling reduction are 20 to 40%.

The invention described in claim 6 is the first invention.
A method for producing an aluminum alloy composite material for a heat exchanger, wherein the aluminum alloy composite material for a heat exchanger according to any one of claims to 4 is produced by the method according to claim 5.

[0016]

First, the reasons for limiting the composition of the aluminum alloy constituting the core material and the sacrificial anode skin material in the aluminum alloy composite material for a heat exchanger of the present invention will be described. A: Core material (a) Mn Crystallizes or precipitates as an Al-Mn intermetallic compound, and has an effect of improving strength, particularly strength after brazing.
It functions to make the potential of the core material noble and improve not only the sacrificial anode skin material but also the corrosion resistance of the brazing material side. The content is 0.
If it is less than 5%, a sufficient effect cannot be obtained. On the other hand, if it exceeds 2.0%, workability such as rolling is reduced, and further improvement of the effect cannot be obtained. Therefore, the content of Mn is 0.5% to 2.0%.
It was decided. (B) Cu has a function to improve the strength after brazing by forming a solid solution, and to make the potential of the core material noble to improve not only the sacrificial anode skin material but also the corrosion resistance of the brazing material side. Its content is 0.25%
If it is less than 0.75%, a sufficient effect cannot be obtained, while if it exceeds 0.75%, the corrosion rate becomes too high. In particular, the corrosion rate at the joint is too high. Therefore, the content of Cu is 0.25
% To 0.75%.

(C) Si is dispersed as an Al-Mn-Si intermetallic compound or solid-dissolved in a matrix to have the effect of improving strength. If the content is less than 0.3%, a sufficient effect cannot be obtained, while if it exceeds 1.3%, the melting point is lowered and the material is melted during brazing. Therefore, the content of Si is 0.3%
％ 1.3%. (D) Improve the strength by forming a solid solution in the Mg matrix and improve the strength by forming Si diffused from the brazing material and Si and Mg ₂ Si intermetallic compound in the core material. Further, it has a function of forming an intermetallic compound of Zn and MgZn ₂ diffused from the sacrificial anode skin material to improve the strength. The content is 0.0
If it is less than 1%, a sufficient effect cannot be obtained, while if it exceeds 0.5%, it diffuses into the brazing material and impairs the brazing properties. Therefore, the content of Mg is 0.01% to 0.5%. %.

(E) Zr, Ti, Cr, V Zr, Ti, Cr, V have the same function, and have the effect of increasing the strength by refining the crystal of the Al alloy. However, if the content exceeds 0.02%, recrystallization during intermediate annealing before final rolling is hindered, so anisotropy before tube forming becomes large, which significantly impairs pipe formability and reduces workability. I do. Therefore, the contents of Zr, Ti, Cr, and V are all kept to a very small amount of 0.02% or less. (F) Fe is crystallized or precipitated as an Al-Fe-based intermetallic compound, and has an effect of improving the strength, particularly the strength after brazing.
If the addition amount is 0.5% or less, a sufficient effect cannot be obtained.
If it exceeds 2%, the corrosion rate becomes too high. Therefore, F
The content of e was determined to be 0.5% to 1.2%.

B: Sacrificial anode skin material (a) Solid solution in Mg matrix to improve strength and diffusion from core material or Si and Mg ₂ Si intermetallic compound in core material
To improve the strength. Further, it has a function of forming an intermetallic compound of Zn and MgZn ₂ in the sacrificial anode skin material to improve the strength. By forming an Mg-In-Cu intermetallic compound and suppressing the solid solubility of Cu diffused from the core material, the solid solubility of Cu in the sacrificial anode skin material can be suppressed, and the sacrificial anode effect is sufficiently exhibited. be able to. Further, intergranular corrosion generated in the sacrificial anode skin material due to generation of these intermetallic compounds can be suppressed. If the content is less than 0.3%, a sufficient effect cannot be obtained, while if it exceeds 1.7%, it diffuses into the brazing material and impairs the brazing properties. Therefore, the content of Mg is determined to be 0.3% to 1.7%. (B) In It has the effect of making the potential of the sacrificial anode skin material base and improving the sacrificial anode effect. An Mg-In-Cu intermetallic compound is formed to prevent intergranular corrosion of the sacrificial anode skin material. If the addition amount is less than 0.0001%, the effect is not exhibited, and 0.15%
Exceeding the above increases the raw material cost, and no improvement in the effect is recognized for that. Therefore, the content of In is 0.000.
1% to 0.15%.

(C) Mg in the sacrificial anode skin material and Mg diffused from the core material and Mg ₂ S
It has the effect of improving the strength by forming i intermetallic compound. If the content is less than 0.05%, a sufficient effect cannot be obtained, while if it exceeds 0.5%, the melting point decreases. Further, intergranular corrosion occurs in the sacrificial anode skin material. Therefore, the content of Si is determined to be 0.05% to 0.5%. (D) Ti is dispersed as a fine intermetallic compound after brazing to improve the strength. It has the function of promoting the formation of an Mg-In-Cu-based intermetallic compound. The formation of these intermetallic compounds can prevent intergranular corrosion of the sacrificial anode skin material. If the content is less than 0.001%, a sufficient effect cannot be obtained, while if it exceeds 0.05%, the workability decreases. Therefore,
The content of Ti was determined to be 0.001% to 0.05%.

(E) Zn The potential of the sacrificial anode skin material is made low to form a potential distribution effective for corrosion protection from the surface of the sacrificial anode skin material to the core, thereby improving pitting corrosion resistance. If the content is less than 0.5%, a sufficient effect cannot be obtained, while if it exceeds 5%, the workability decreases. Therefore, the content of Zn is determined to be 0.5% to 5%. (F) Sn has the effect of lowering the potential of the sacrificial anode skin material to improve the sacrificial anode effect. If the content is less than 0.001%, a sufficient effect cannot be obtained. On the other hand, if the content exceeds 0.2%, only a cost is required and no special effect can be expected. Therefore, the Sn content was determined to be 0.001% to 0.2%.

Next, a method for producing the aluminum alloy composite material for a heat exchanger of the present invention will be described. The outline of the method for producing an aluminum alloy composite material for a heat exchanger of the present invention is as follows.
First, an aluminum alloy for a core material, an aluminum alloy for a sacrificial anode skin material, and an aluminum alloy for a brazing material having a predetermined composition are melted and cast by a usual method, and the obtained ingots are heat-treated and homogenized. Rolling is performed to a predetermined thickness by using cold rolling or hot rolling together with cold rolling. Next, a sacrificial anode skin material and a brazing material are superimposed on both sides of the core material centering on the core material, and hot-rolled to form a clad material. Then, cold rolling is repeated with appropriate necessary intermediate annealing, and rolled to a predetermined thickness in a range where the final rolling reduction is 20 to 40%,
Obtain an aluminum alloy composite. In the present invention, the final aluminum alloy composite material has a thickness of 0.15 to 0.30.
mm.

The heat treatment and the rolling in the above-described manufacturing process are adjusted to an appropriate crystal orientation (texture) to reduce the anisotropy. At that time, it was found that by setting the annealing conditions before final rolling and the final rolling reduction under certain conditions, the anisotropy was further reduced and the pipe formability was improved.
That is, the annealing condition before the final rolling is that the annealing temperature is 360 ° C.
550 ° C., the average rate of temperature rise from 100 ° C. to the annealing temperature is 55 ° C./h or more,
The average cooling rate is 75 ° C./h or more. In the present invention, the temperature is rapidly raised to a predetermined annealing temperature, and is rapidly cooled even after the completion of the heat treatment. This is to prevent crystal grains from abnormally growing during temperature change.

The reason why the intermediate annealing conditions and the final rolling reduction are set under certain conditions in order to reduce the anisotropy in the material is as follows. In the intermediate annealing before the final rolling, the material has a recrystallized texture, and the strength is 45 to the rolling direction.
The intensity in the degree direction (including 135 degrees, 225 degrees, and 315 degrees) is relatively large. The rolling develops a rolling texture in the material by rolling, but the material strength becomes 0 with respect to the rolling direction.
The intensity at (zero) degrees and 90 degrees (including 180 degrees and 270 ° C.) increases. Since the final rolling ratio after annealing was about 30% in the conventional materials, these balanced,
Due to the large thickness, pipe making was possible, and no particular problems occurred. However, in recent years, as materials become thinner and higher in strength, the balance between them has been broken. In other words, from the viewpoint of material formability, weldability and erosion prevention, the final rolling ratio is set to about 30%.
Even at the same rolling reduction, the added strain increases and the anisotropy also increases. It is the actual condition that the formability of the tube is reduced by this. Although the anisotropy can be improved by lowering the final rolling reduction, the final rolling reduction is still 20%.
Can not be less than%.

[0025] Even for thin-walled and high-strength materials, the final rolling reduction is 20 to
It has been found that in order to secure 40% and to reduce the anisotropy, the conditions of the intermediate annealing may be set as described above. By doing so, the anisotropy is small even after the intermediate annealing, and there is no significant change even if rolling is repeated thereafter. That is, under such annealing conditions, the strength in a specific direction is not particularly increased, and the orientation tends to be random. Also,
Even if the final rolling reduction is set to 20 to 40%, the strength in a specific direction does not increase. Therefore, there is no occurrence of minute defects concentrated in the vicinity of the welded portion when manufacturing the electric resistance welded tube.

[0026]

Next, the present invention will be described in detail with reference to examples of the present invention. Aluminum alloys for the core material, the sacrificial anode skin material and the brazing material having the compositions shown in Tables 1 to 3 are melted and cast by a usual method, and are homogenized under normal conditions after being subjected to face milling. Subsequently, hot rolling was performed to obtain a hot rolled sheet having a thickness of 400 mm for the core material, a thickness of 50 mm for the sacrificial anode skin material, and a thickness of 50 mm for the brazing material. Next, a core material, a sacrificial anode skin material, and a brazing material were overlapped in a combination shown in Table 4, clad by hot rolling, and then cold-rolled while appropriately performing intermediate annealing. At this time, the annealing temperature, heating rate, and cooling rate shown in Table 4 were adopted as the intermediate annealing conditions immediately before the final cold rolling. 0.25m thickness as a result of final cold rolling
m, a final rolling reduction of 10 to 52%, and a tempered H14 aluminum alloy composite material for the present invention and for comparison.

[0027]

[Table 1]

[0028]

[Table 2]

[0029]

[Table 3]

[0030]

[Table 4]

Next, this composite material was processed into an electric resistance welded tube having an inner diameter of 10 mm by a usual method with the sacrificial anode skin material inside. With respect to the obtained electric resistance welded tube, tube formability, tensile strength, and erosion resistance were evaluated. The pipe forming property was measured by an eddy current flaw detector incorporated in a pipe forming apparatus. The output of the eddy current flaw detector is represented by the amplitude of the voltage, and it can be seen that the larger the amplitude of the voltage, the more minute flaws are formed in the welded portion and its vicinity. The more microscopic flaws, the more incomplete the welding, the poorer the pipe-forming property. In the tensile test, each electric resistance welded tube was subjected to a heat treatment at 610 ° C. for 5 minutes in a nitrogen atmosphere corresponding to brazing conditions, and then a tensile test was performed. The erosion resistance is
The degree of erosion of the wax in the cross section of the electric resistance welded tube after the heat treatment was determined by cross section observation with an optical microscope. When no erosion was visually observed, a mark was given, and when erosion was observed in some places, a mark was given. When erosion was clearly observed along the sheet thickness direction, an X was given. Table 5 shows the results.

[0032]

[Table 5]

As is clear from Table 5, when the composite material according to the present invention was used, there was little micro scratches on the welded portion at the time of pipe production, and it had sufficiently high strength even after brazing despite its thinness. It can also be seen that the erosion resistance was excellent.

Next, for comparison, the sample No. In Nos. 19 to 21, a core material and a sacrificial anode skin material whose composition range was out of the range of the present invention were processed under the same conditions as in the present invention, and evaluated similarly. Table 5 also shows these results. In addition, the sample No. The composite material is produced by changing the heating rate and the cooling rate during the intermediate annealing immediately before the final cold rolling for 1, 9 and 17,
It was processed into an electric resistance welded tube in the same manner as in the present invention, and the same evaluation was performed. These results are also shown in Table 5. Further, except that a core material and a sacrificial anode skin material having the same composition as that of the present invention were used and the final rolling ratio was set to less than 20% or more than 40%, processing was performed under the same conditions as in the present invention. Was evaluated. These results are also shown in Table 5.

As apparent from Table 5, the sample No. 19
-Sample No. No. 21 shows that the alloy composition of the core material and the sacrificial anode skin material is out of the range of the present invention, and that a composite material having high tensile strength cannot be obtained. In addition, the sample No. 22 to sample no. 24 shows that although the alloy composition of the core material and the sacrificial anode skin material is within the range of the present invention, the voltage amplitude in eddy current flaw detection is large due to improper heat treatment conditions, and the tube formability is poor. . Sample No. Sample No. 25 has good tube formability since the final rolling reduction is small, but has insufficient strength and poor erosion resistance. Sample No. No. 26 has poor tube formability because the final rolling reduction is too large. Sample No. 27 and sample no. No. 29 has low erosion resistance because the final rolling reduction is small. Conversely, for sample no. 28
And sample No. In No. 30, the final rolling reduction is too large and the erosion resistance is poor. As described above, even when the alloy composition of the core material and the sacrificial anode skin material and the heat treatment conditions are selected within the scope of the present invention, when the final rolling reduction is out of the range of 20 to 40%, the pipe forming property, tensile strength, and erosion resistance are reduced. It turns out that a composite material satisfying all the properties cannot be obtained. Thus, it can be seen that the erosion resistance largely depends on the final rolling reduction.

[0036]

According to the present invention, the core material contains Ti, Z
The addition of r, Cr, and V aims to refine the structure and improve the strength, and adds In, Ti, and Si as essential components to the sacrificial anode skin material to increase the strength and enhance the sacrificial anode effect. . In addition, by limiting the heat treatment conditions, the development of texture by rolling is suppressed, and the anisotropy of the material is reduced, thereby suppressing the occurrence of minute flaws in the welded portion generated during ERW processing.

[0037]

According to the present invention, since the minute scratches on the welded portion generated during the processing of the ERW pipe are suppressed, the production yield of the ERW pipe is improved, and the production yield of the heat exchanger is improved. This has the effect of extending the life of the heat exchanger.

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Claims (6)

[Claims] 1. A heat exchange in which a sacrificial anode skin material is clad on one surface of an aluminum alloy core material and a brazing material made of an Al-Si or Al-Si-Zn alloy is clad on the other surface of the core material. A dexterous aluminum alloy composite material,
When the composition of the core material is% by weight (hereinafter the same), Mn: 0.5 to
2.0%, Cu: 0.25 to 0.75%, Si: 0.3
To 1.3%, Mg: 0.01 to 0.5%, Ti: ≦ 0.
02%, Zr: ≦ 0.02%, Cr: ≦ 0.02%,
V: ≦ 0.02%, the balance consists of Al and inevitable impurities, and the composition of the sacrificial anode skin material is In: 0.0
001 to 0.15%, Si: 0.05 to 0.5%, M
g: 0.3-1.7%, Ti: 0.001-0.05%
An aluminum alloy composite material for a heat exchanger, comprising: Al and the balance consisting of Al and inevitable impurities. 2. A heat exchange in which a sacrificial anode skin material is clad on one surface of an aluminum alloy core material and a brazing material made of an Al-Si or Al-Si-Zn alloy is clad on the other surface of the core material. A dexterous aluminum alloy composite material,
The composition of the core material is Mn: 0.5 to 2.0% by weight, C
u: 0.25 to 0.75%, Si: 0.3 to 1.3%,
Mg: 0.01-0.5%, Fe: 0.5-1.2%,
Ti: ≦ 0.02%, Zr: ≦ 0.02%, Cr: ≦
0.02%, V: ≦ 0.02%, the balance consists of Al and inevitable impurities, and the composition of the sacrificial anode skin material is In: 0.0001 to 0.15%, Si: 0. 05-
0.5%, Mg: 0.3 to 1.7%, Ti: 0.001
An aluminum alloy composite material for a heat exchanger, characterized by containing about 0.05% and the balance consisting of Al and inevitable impurities. 3. A heat exchange in which a sacrificial anode skin is clad on one surface of an aluminum alloy core material and a brazing material made of an Al-Si or Al-Si-Zn alloy is clad on the other surface of the core material. A dexterous aluminum alloy composite material,
The composition of the core material is Mn: 0.5 to 2.0% by weight, C
u: 0.25 to 0.75%, Si: 0.3 to 1.3%,
Mg: 0.01-0.5%, Ti: ≤0.02%, Z
r: ≦ 0.02%, Cr: ≦ 0.02%, V: ≦ 0.0
2%, the balance consisting of Al and unavoidable impurities,
In addition, the composition of the sacrificial anode skin material is In: 0.0001-0.
15%, Si: 0.05-0.5%, Mg: 0.3-
1.7%, Ti: 0.001 to 0.05%, and Z
n: 0.5 to 5.0%, Sn: 0.001 to 0.2%,
Fe: 0.5 to 1.2%, Ni: 0.1 to 0.6%, containing one or more of them, the balance being Al and unavoidable impurities, for heat exchangers Aluminum alloy composite material. 4. A heat exchange in which a sacrificial anode skin material is clad on one surface of an aluminum alloy core material and a brazing material made of an Al-Si or Al-Si-Zn alloy is clad on the other surface of the core material. A dexterous aluminum alloy composite material,
The composition of the core material is Mn: 0.5 to 2.0% by weight, C
u: 0.25 to 0.75%, Si: 0.3 to 1.3%,
Mg: 0.01-0.5%, Fe: 0.5-1.2%,
Ti: ≦ 0.02%, Zr: ≦ 0.02%, Cr: ≦
0.02%, V: ≦ 0.02%, the balance consists of Al and inevitable impurities, and the composition of the sacrificial anode skin material is In: 0.0001 to 0.15%, Si: 0. 05-
0.5%, Mg: 0.3 to 1.7%, Ti: 0.001
-0.05%, Zn: 0.5-5.0%, S
n: 0.001 to 0.2%, Fe: 0.5 to 1.2%,
Ni: an aluminum alloy composite material for a heat exchanger, comprising one or more of 0.1 to 0.6%, and the balance consisting of Al and inevitable impurities. 5. A clad material is hot-rolled by sandwiching both sides of the core material with a sacrificial anode skin material and a brazing material, and then the clad material is cold-rolled at least twice with intermediate annealing therebetween. In a method of manufacturing an aluminum alloy composite material for a heat exchanger, intermediate annealing immediately before final cold rolling is performed.
Annealing temperature is 360 ° C to 550 ° C, average temperature increase rate from 100 ° C to annealing temperature is 55 ° C / h or more,
A method for producing an aluminum alloy composite material for a heat exchanger, wherein the average cooling rate to 50 ° C is 75 ° C / h or more, and the final rolling reduction is 20 to 40%. 6. The method for producing an aluminum alloy composite material for a heat exchanger according to claim 5, wherein the aluminum alloy composite material for a heat exchanger is one according to any one of claims 1 to 4. .