JPH05271833A - High strength aluminum alloy fin material for forming and its production - Google Patents

Abstract

PURPOSE:To produce a high strength aluminum alloy fin material for forming capable of draw forming, drawless forming, or combined forming of them in spite of its small thickness and also to produce a sheet thereof. CONSTITUTION:An ingot of an Al alloy having a composition consisting of, by weight, <=0.1% Si, 0.10-1.0% Fe, 0.10-0.50% Mn, 0.01-0.15% Ti, and the balance Al with inevitable impurities is subjected to temp. rise and to heating up to 430-580 deg.C. Hot rolling is done by starting hot rolling while the temp. drop from the temp. at the completion of temp. rise and heating stays within 50 deg.C. Then, cold rolling is done so that draft at the final cold rolling is >=80%. The resulting sheet is subjected to refining annealing at 250-320 deg.C, by which intermetallic compounds of <=0.1mum diameter are distributed into a metallic structure by >=10pieces/mum<3> of number density.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to draw molding, drawless molding or composite molding of both, that is, overhang processing,
TECHNICAL FIELD The present invention relates to a high-strength aluminum alloy fin material for forming, which is formed by performing all or a part of drawing, burring, ironing, and refiring, and is used as a fin for a room air conditioner, and a method for producing the same.

[0002]

2. Description of the Related Art Generally, an aluminum alloy fin for an air conditioner heat exchanger has a collar portion for mounting a heat exchange tube on a plate portion (1) as shown in FIGS. 1 (a) to 1 (d).
(2) is formed, and is classified into a flat type (a), a louver type (b), a slit type (c), and a corrugated type (d) according to the plate shape. Draw molding (molding mainly for overhanging) is shown in Fig. 2 (a) to (f)
As shown in, the process consists of overhanging (a), squeezing (b) to (d), punching, burring (e), and flare (f).
The overhanging process is central. Therefore, in the case of this draw forming, the fin material is required to have an excellent elongation, and normally, it is a thick material with a thickness of 0.12 mm or more and is tempered with an O material or H22. Is.
Also, when thin-walled materials with a thickness of 0.115 mm or less are draw-formed, problems such as deterioration of formability or insufficient strength occur, so it is very difficult to thin fins or form high-color height of thin-walled materials with current materials Met. In order to improve the above problems, drawless molding (molding mainly based on ironing) has been the mainstream of fin molding for several years. Drawless molding consists of punching-hole expansion (a), burring (b), ironing (c), and re-flare (d) as shown in Fig. 3 (a) to (d). Since it is used for forming thin fins, the fins can be made thinner (0.115 to 0.105) in low color height molding.
Thickness of around mm) is possible. In drawless molding, a semi-hard material of H24 to H26 is used because it has excellent ironing workability and requires some strength. However, it is still difficult to form a thin material having a thickness of 0.12 mm or less at a high color height, and the present situation is to use a thick material. Also, in the long-term press processing of drawless molding, a molding failure occurs due to die tool wear of the precoat (surface treatment) fins, which increases die / tool maintenance costs and lowers the viscosity of lubricating oil ( This is a serious problem such as frequent deterioration of moldability due to use of volatile oil). Therefore, it is strongly desired to maintain molding performance and reduce mold / tool maintenance costs compared to the current situation.

Recently, composite molding (hereinafter simply referred to as composite molding) in which the draw molding and the drawless molding are combined has been performed. As shown in Fig. 4, compound molding consists of the steps of overhanging (a), drawing (b), punching, burring (c), ironing (d) (e), and flare (f). This is a molding method in which ironing is performed after a certain color height is obtained, and the ironing rate can be made smaller than in drawless molding. However, with the aluminum alloy fin materials currently used, sufficient molding performance is not maintained and maintenance costs for molds and tools are not reduced by any of the molding methods.

[0004]

The present inventors have obtained the following findings as a result of various investigations for solving the above problems. With the soft fin material used for conventional draw molding,
When the wall thickness is reduced to 0.12 mm or less, there is a problem that due to insufficient strength, buckling occurs when inserting the copper tube into the collar, impairing the adhesion between the collar and the heat exchange tube, and lowering the heat exchange performance. Get up. Further, the hard fin material used in the conventional drawless molding can be thinned because of its high strength, but its elongation value is low, so that high color height molding by draw molding is difficult. In drawless molding, ironing is the main focus, so it is difficult to significantly reduce problems such as lowering the viscosity of lubricating oil, deterioration of moldability associated with the precoat film, and tool wear during long-term pressing. As a means to solve the above, by draw molding,
If hard pre-coated fins of 0.12 mm or less can be formed, it is possible to suppress formability deterioration due to deterioration of lubricity and reduce maintenance costs due to tool wear. However, conventional hard materials have a low elongation value, especially plate thickness. With a thin-walled material having a thickness of 0.105 mm or less, a good molded product cannot be obtained by draw molding. In addition, with the use of volatile oil to omit washing after molding, recently, draw molding and drawless molding have been combined to achieve a certain color height by overhanging and drawing, and then ironing is performed. Since composite molding with a reduced ironing rate has also appeared, if composite molding can form hard pre-coated fins of 0.12 mm or less, it is possible to reduce the above-mentioned deterioration of moldability and maintenance costs due to tool wear. Although it is possible to reduce the amount, the conventional hard material has a low elongation value, and in particular, a thin product having a plate thickness of 0.105 mm or less cannot obtain a good molded product by composite molding. If a material that has the strength and moldability required for drawless molding and the elongation value and moldability required for draw molding can be obtained, draw molding as a thin fin of 0.12 mm or less,
Molding by drawless molding or composite molding is possible. By controlling the addition amounts of Si, Fe, Mn, and Ti, and the manufacturing process / conditions, it is possible to obtain a metallographic state within the scope of the claims of the present application and to obtain a material corresponding to the above.

The present invention is obtained from the above findings,
In the invention according to claim 1, Si 0.1 wt% or less, Fe 0.1
0 to 1.0 wt%, Mn 0.10 to 0.50 wt%, Ti
0.01 to 0.15 wt%, the balance consisting of Al and unavoidable impurities, and having a diameter of 0.1 μm in the metal structure.
A high-strength aluminum alloy fin material for molding, characterized in that the following intermetallic compounds are distributed in a number density of 10 / μm ³ or more.
wt% or less, Fe 0.10 to 1.0 wt%, Mn 0.10
An Al alloy ingot containing 0.50 wt% and Ti of 0.01 to 0.15 wt% and the balance of Al and unavoidable impurities was used.
After heating by heating to a temperature of 30 to 580 ° C., hot rolling is started while the temperature decrease from the temperature at the end of heating by heating is within 50 ° C., hot rolling is performed, and then final cold rolling is performed. Cold rolling is performed so that the rolling reduction is 80% or more, and the obtained thin plate is subjected to temper annealing at a temperature of 250 to 320 ° C., and an intermetallic compound having a diameter of 0.1 μm or less is added to the metal structure. 1 in density
A method for producing a high-strength aluminum alloy fin material for forming, characterized in that 0 or more / μm ^{3 is} distributed. The invention according to claim 3 has Si of 0.1 wt% or less and Fe of 0.10 to 0.
1.0 wt%, Mn 0.01 to 0.50 wt%, Ti0.0
A casting plate having a thickness of 2 to 15 mm by continuously supplying an Al alloy molten metal containing 1 to 0.15 wt% and the remainder being Al and unavoidable impurities to the outer peripheral surfaces of a pair of opposing cooling molds, The cast plate was cold-rolled so that the final cold-rolling reduction rate was 80% or more, and the thin plate thus obtained was subjected to 250-3.
After tempering annealing at a temperature of 50 ° C., the metal structure has a diameter of 0.
A method for producing a high-strength aluminum alloy fin material for molding, characterized in that a metal compound of 1 μm or less is distributed at a density of 10 pieces / μm ³ or more.

[0006]

The function of the alloy composition and manufacturing conditions in the present invention will be described below. First, the reason why the alloy composition is limited as in the present invention will be described. The aluminum alloy fin material of the present invention contains Si 0.1 wt% (hereinafter simply referred to as%) or less, Fe 0.10 to 1.0%, and Mn 0.10 to 0.50.
%, Ti 0.01 to 0.15%, the balance consisting of Al and unavoidable impurities, and the intermetallic compound having a diameter of 0.1 μm or less in the metal structure before forming is made to have a number density of 1
It is characterized in that the number is 0 / μm ³ or more. S
Some of i, Fe, and Mn are solid-dissolved in aluminum and have the effect of increasing the strength of the fin material. In particular, Mn has the effect of improving the elongation value. Ti partially dissolves in aluminum and has a function of refining the structure. In particular, during temper annealing, it has an effect of uniformly promoting recovery and making the subgrain uniform and fine, and therefore has an effect of improving overhang and drawability. Further, Ti is said to have a function of improving local elongation of the material. In the fin forming process, particularly in the case of performing flange forming such as reflaring, the higher the local elongation, the higher the forming performance tends to be. Therefore, the Ti addition amount is specified in the present invention. Here, if the addition amount of Fe and Mn is less than 0.10%, not only the desired strength and elongation due to elemental solid solution cannot be obtained,
The amount of fine intermetallic compounds with a diameter of 0.1 μm or less is also reduced, and the function of suppressing the growth of recovery subgrains during temper annealing of the final plate is reduced, and as a result, an elongation value is secured. Inevitably, the strength is reduced, and the ironing property and the flare property in composite molding are also reduced. Furthermore, the subgrain distribution tends to be non-uniform,
Therefore, during draw forming, the overhanging property, drawability, etc. are actually deteriorated, and the strength is insufficient, resulting in a defective molded product. On the other hand, the addition amount of Si is more than 0.1%, the addition amount of Fe is more than 1.00%, and the addition amount of Mn is 0.5%.
When it is more than 0%, the intermetallic compound is coarsened to a value of 0.
The amount of fine intermetallic compounds of 1 μm or less is reduced, and the crystallized product during casting is also coarsened. Therefore, during molding, the overhanging property, the drawability, etc. are deteriorated due to uneven deformation in the vicinity of the coarse crystallized product, As a result, the molded product becomes defective. Therefore, the addition amount of Si is 0.1% or less, the addition amount of Fe is 0.10 to 1.0%,
The added amount of Mn needs to be 0.10 to 0.50%. If the addition amount of Ti is less than 0.01%, not only the effect of making the subgrain uniform and fine cannot be obtained, but also the formability, particularly the overhanging property, the drawability, and the flare property cannot be further improved. On the other hand, the Ti addition amount is 0.1
If it exceeds 5%, coarse Ti-based compounds are distributed, and it becomes difficult to form uniform and fine subgrains. Therefore, the Ti addition amount is 0.01 to 0.15.
Must be%. There is no problem in adding a small amount of other elements such as Zr, Cu, Y, and Hf for the purpose of improving the balance between strength and elongation or improving moldability.

In the present invention, the fine intermetallic compound in the metal structure before forming is defined to have a diameter of 0.1 μm or less. The reason is that if the diameter is larger than 0.1 μm, the processed structure of the final plate is recovered during temper annealing. The effect of delaying the movement of the grain boundaries of the subgrains becomes smaller, and as a result, the strength must be reduced to secure the elongation value, and the subgrain distribution tends to become non-uniform. At the time of molding, the overhanging property, drawing property, and reflaring property are deteriorated, and the strength of the product is insufficient. Further, the distribution of intermetallic compounds having a diameter of 0.1 μm or less is set to a number density of 1
The reason for defining 0 or more / μm ³ or more is that if the number is less than 10 / μm ^3, it is difficult to obtain the above-mentioned effect, and therefore there is no effect of improving the overhanging property, drawability, flare property and strength.

Next, a manufacturing method according to claim 2 of the present invention will be described. The production method of claim 2 is intended to suppress coarse precipitation during homogenization treatment and to promote precipitation of fine intermetallic compounds having a diameter of 0.1 μm or less during hot rolling or temper annealing. Therefore, for that purpose, it is necessary to first heat the ingot within a range of 430 to 580 ° C. by heating to start hot rolling in a holding time as short as possible.
If the ingot homogenization treatment temperature is lower than 430 ° C., the ingot microstructure is not sufficiently homogenized, so that the microstructure after hot rolling also becomes nonuniform, and the overhanging property and drawability during draw forming are obtained. , And the flare property, or the ironing property and the flare property during composite molding are deteriorated. On the other hand, if the temperature is higher than 580 ° C., a sufficient solid solubility can be obtained, but the crystallized material is coarsely spheroidized, which adversely affects the moldability, which is not preferable.

Further, in any temperature range, the longer the holding time is, the coarser the precipitates are and the adverse effect on the formability. Therefore, the holding time should be as short as possible, preferably within 4 hours. When performing hot rolling immediately after the above ingot temperature rising heating, it is necessary to start hot rolling at a temperature decrease of 50 ° C. or less compared to the temperature at the end of temperature rising heating of the ingot. When hot rolling is started at a temperature lower than 50 ° C. compared to the temperature at the end of temperature rising and heating of the ingot, the amount of solid solution element is already largely reduced at the start of hot rolling, and actually, It becomes a coarse compound of 0.1 μm or more and is largely precipitated in the aluminum matrix. Therefore, during hot rolling, or during finish annealing after hot rolling and cold rolling, fine metal compounds having a size of 0.1 μm or less are less likely to precipitate, and the distribution of the compounds defined in the present invention cannot be obtained. Therefore, when performing hot rolling after heating the ingot to raise the temperature,
It is necessary to start hot rolling when the temperature of the ingot is decreased by 50 ° C. or less as compared with the temperature at the end of heating by heating.

The final cold rolling is carried out at a rolling reduction of 80% or more because if it is less than 80%, when a thin plate having a thickness of 0.120 mm or less is draw-formed or compound-formed, strength is insufficient and problems such as buckling occur. Is. In addition, the obtained thin plate is 250
By performing temper annealing at a temperature within the range of up to 320 ° C, the strength required for composite forming of thin plate fins and the elongation value required for draw forming are secured, and good overhanging property, drawability, and hole expandability are ensured. The ironing property and the flare property are obtained. Moreover, the corrugated property is also improved. Here, if the tempering temperature is less than 250 ° C, sufficient moldability cannot be obtained.
When annealed at a temperature higher than 0 ° C., not only the strength is lowered, but also the elongation is lowered, and recrystallized grains are generated, which becomes a starting point and deteriorates the formability. Therefore,
It is necessary to perform final cold rolling at a rolling reduction of 80% or more, and to perform temper annealing on the obtained thin plate at a temperature in the range of 250 to 320 ° C.

Next, the manufacturing method of claim 3 will be described. The present invention continuously supplies the molten Al alloy between the outer peripheral surfaces of a pair of rotating opposing cooling molds to cast a plate having a thickness of 2 to 15 mm, and the resulting cast plate is subjected to final cold rolling at a rolling reduction of 80% or more. The purpose of the present invention is to accelerate precipitation of intermetallic compounds having a diameter of 0.1 μm or less by rolling and tempering the obtained thin plate at a temperature in the range of 250 to 350 ° C. Here, the aluminum alloy melt is continuously supplied to the outer peripheral surfaces of a pair of rotating cooling molds that face each other, and the plate thickness 2 to
It was stipulated that casting should be 15 mm. If it is less than 2 mm, the solidification state becomes unstable during casting, and defects such as cracks and pinholes are likely to occur, while if it exceeds 15 mm, the cooling rate in the casting process decreases and solid solution occurs. This is because the amount is decreased and the intermetallic compound is coarsely precipitated, and the structure defined above cannot be obtained. Therefore, it is necessary to cast to a plate thickness of 2 to 15 mm. There are various methods such as a water-cooled roll method and a caster method as the method for casting to the cast plate thickness of the present invention, but the effect of the present invention is not impaired even if any method is adopted.

The reason why the final cold rolling is performed at a rolling reduction of 80% or more is the same as that explained in the manufacturing method of claim 2. Further, by subjecting the obtained thin plate to temper annealing at a temperature in the range of 250 to 350 ° C., the strength required for composite forming of thin plate fins and the elongation value required for draw forming are secured, and good overhanging is achieved. Properties, drawability, hole expandability, ironing property, and flare property are obtained. Moreover, the corrugated property is also improved. Here, if the tempering temperature is less than 250 ° C., sufficient formability cannot be obtained, and when annealed at a temperature higher than 350 ° C., not only the strength decreases but also the elongation decreases, and recrystallized grains occur. As a starting point, the formability deteriorates. Therefore, the final cold rolling is performed at a rolling reduction of 80% or more, and the obtained thin plate is 250 to 350 ° C.
It is necessary to perform temper annealing at a temperature within the range.

Example 1 An Al alloy having an alloy composition shown in Table 1 was produced by water cooling casting or continuous casting (water cooling roll method). The ingot (thickness 400 mm) made by the water-cooled casting method is machined on both sides by 10 mm on each side, then homogenized under the conditions shown in Tables 2 and 3 (including heating and heating the ingot) and hot-rolled to obtain the thickness. A 6 mm hot rolled sheet was obtained. Further, a cast plate having a thickness of 5.0 mm and a thickness of 8.0 mm was obtained by the continuous casting method. Cold rolled hot-rolled sheet or cast sheet, thickness 0.115mm, 0.10
After making a thin plate of 0 mm, it is tempered at a temperature in the range of 250 to 320 ° C. (thin plate obtained by water cooling casting) or 250 to 350 ° C. (thin plate obtained by continuous casting) to obtain tensile strength. A molding fin material of 10.0 to 15.0 kgf / mm ² was obtained. The distribution state of the intermetallic compound of the fin material thus obtained and the formability evaluation results are shown in Tables 4 and 5.
Shown in. Here, for the distribution state of the intermetallic compound, the particle size of the compound and the number of the particles present in a given volume were measured using a transmission electron microscope. The particle diameter was the diameter of a circle having an area equal to the projected area of the particles. As for the formability test, first, the results of performing the limit value measurement of the color forming height by draw forming at plate thicknesses of 0.100 mm and 0.115 mm are shown. Next, as a result of evaluation by actual molding, using a fin material with a plate thickness of 0.105 mm, a collar height of 1.6 mm
The copper tube fixing hole of No. 2 was overhanged using a draw forming die, continuously formed by drawing, and the final processing was performed to the re-flare processing, and after obtaining 960 colors, cracks occurred at the tip of the re-flare (curling) part. Evaluation was performed by calculating the crack defect rate from the measurement of the number of holes, and comparing it with the refresh flare crack defect rate when a fin material having a thickness of 0.130 mm of the current material was similarly formed. Similarly, using a composite molding die, continuous processing of overhanging, squeezing, ironing, and flare was performed, and after obtaining 960 colors, cracks occurred at the tip of the flare (curling) part. Evaluation was performed by calculating the defective rate and comparing it with the above-mentioned current material.

[0014]

[Table 1]

[0015]

[Table 2]

[0016]

[Table 3]

[0017]

[Table 4]

[0018]

[Table 5]

As is clear from Tables 4 and 5, the present invention material sample No. Nos. 1 to 8 and 22 to 24 are conventional material sample Nos. 20, 2
Compared with No. 1, draw forming or composite forming can be performed with a thinner plate thickness, and in particular, the overhang formability and the flare formability by draw forming with a plate thickness of 0.100 mm are superior to the conventional material. Further, the material of the present invention is superior to the conventional material also in the limit value of the color forming height at the plate thickness of 0.115 mm. The material of the present invention is 0.1 compared with the conventional material.
Since many intermetallic compounds having a size of μm or less are distributed, in the material of the present invention, when the processed structure of the final plate is temper-annealed,
These fine compounds function to delay the grain boundary migration of the recovered subgrains, thereby suppressing the generation of recrystallization nuclei, thus maintaining the strength required for composite molding of thin fins, and Therefore, the overhang, drawing formability, and ironing reflaring formability required for the main forming are excellent. Therefore, even if the thickness of the material of the present invention is reduced from 0.130 mm to 0.115 mm, as shown in Tables 4 and 5, a marginal color height level equal to or higher than the current thickness (0.130 mm) is secured. can do. Further, even in composite molding, it is possible to maintain the flare moldability equal to or higher than the current material.

On the other hand, Comparative Material Sample No. outside the scope of the present invention. Nos. 9 to 19 and 25 to 27 are inferior to the material of the present invention in the overhanging property, drawability, reflaring property in draw molding, and the reflaring property in composite molding, and the limit color height is at a level lower than that of the present invention material. That is, S
i, Fe, Mn, or any of the contents exceeds the upper limit, the comparative material sample No. In Nos. 19, 12, 13, and 25, the coarsening of intermetallic compounds reduces the amount of fine intermetallic compounds having a diameter of 0.1 μm or less, and the crystallized substances at the time of casting also become coarse. In addition, the drawability and the refreshing property are deteriorated, resulting in a defective molded product. Also, comparative material sample N
o. In No. 14, since the Ti content exceeds the upper limit, a coarse Ti-based compound is distributed, and it becomes difficult to form uniform and fine subgrains, and as a result, the bulging property, the drawability, and the flare property are reduced during molding. descend.

Comparative material sample No. whose manufacturing conditions are out of the range of the present invention 9, 12, 25, 15, 16, 17, 26,
Nos. 27, 18, and 19 have poor bulging properties, drawability, or flare properties when subjected to draw molding and composite molding with a plate thickness of 0.105 mm. Comparative material sample No. 15, 18
Since the hot rolling start temperature is a temperature lower than the homogenization treatment temperature by 50 ° C. or more, the amount of the solid solution element has already dropped significantly at the start of hot rolling, and the diameter is actually 0.
It becomes a coarse compound exceeding 1 μm and is often precipitated in the aluminum matrix. Therefore, during hot rolling, or during finish annealing after hot rolling and cold rolling, a diameter of 0.1
Since a fine intermetallic compound having a size of μm or less is hard to precipitate and the distribution state of the intermetallic compound defined in the present invention cannot be obtained, the overhanging property, the drawability, and the flare property are deteriorated when the thin fin is formed. Of. Comparative material sample No. 17 is
Since the homogenization treatment temperature is less than the lower limit of the range of the present invention, homogenization of the ingot structure is not sufficiently performed, the structure after hot rolling also becomes non-uniform, and the overhanging property and the flare property deteriorate during draw forming. .. Comparative material sample No. Since the cast plate thicknesses of 25, 26, and 27 are out of the range of the cast plate thickness in the manufacturing method of claim 3, the solidification state becomes unstable, or the compound becomes coarse due to a decrease in solid solubility due to a decrease in cooling rate. Therefore, the distribution state of the fine intermetallic compound of 0.1 μm or less defined in the present invention cannot be obtained. Therefore, during molding,
The overhanging property, the drawability, and the flare property are deteriorated.

Example 2 The material of the present invention shown in Tables 4 and 5,
For some samples of comparative materials, the blank plate performance for each temper annealing,
Specifically, the tensile strength, elongation, Erichsen value, and limit hole expansion ratio were measured, and the results are shown in Table 6. As for the formability evaluation, as in the case of forming in Tables 4 and 5, using a fin material having a plate thickness of 0.105 mm, a draw forming die of an extension drawing type and a composite forming die were used to extend, draw, expand the hole, iron, The thickness of current material is 0.130mm
The evaluation was performed by comparing the defective rate of refraction cracking of the fin material.

[0023]

[Table 6]

As is clear from Table 6, the material of the present invention has higher elongation value, Erichsen value, and limit hole expansion ratio than the comparative material without lowering the strength, and therefore, the draw molding and the composite molding of the actual machine are performed. Excellent overhanging performance in molding,
The ironing performance and the refreshing performance are maintained.

[0025]

As described above, the fin material obtained by the present invention is excellent in overhanging property, drawability, ironing property, and reflaring property in draw molding and composite molding, and significantly reduces the molding crack defect rate. It has a remarkable effect of obtaining. It goes without saying that the fin material of the present invention can be applied to drawless molding. In particular, even a thin plate of 0.100 mm or the like can be color-molded to a height of 1.8 to 2.2 mm with a drawing mold, which makes it possible to significantly reduce the cost of equipment and materials.

[Brief description of drawings]

1 (a) to 1 (d) show the shapes of aluminum fins of a heat exchanger. (A) is a flat type, (B) is a louver type, (C) is a slit type,
(D) is a corrugated type.

FIGS. 2A to 2F are explanatory views showing a cross-sectional view of a fin forming method by draw forming.

3A to 3D are explanatory views showing a cross-sectional view of a fin forming method by drawless forming.

4 (a) to 4 (f) are cross-sectional explanatory views showing a fin forming method by composite forming.

[Explanation of symbols]

 1 Plate part 2 Color part

Claims (3)

[Claims] 1. Si 0.1 wt% or less, Fe 0.10 to
1.0 wt%, Mn 0.10 to 0.50 wt%, Ti0.0
1 to 0.15 wt%, the balance consisting of Al and unavoidable impurities, and 10 or more intermetallic compounds having a diameter of 0.1 μm or less are distributed in the metal structure at a number density of 10 / μm ³ or more. High strength aluminum alloy fin material for forming that is characteristic. 2. Si 0.1 wt% or less, Fe 0.10-
1.0 wt%, Mn 0.10 to 0.50 wt%, Ti0.0
An Al alloy ingot containing 1 to 0.15 wt% and the balance consisting of Al and unavoidable impurities is heated to a temperature of 430 to 580 ° C., and a temperature decrease from the temperature at the end of the heating is 50.
After the hot rolling was started while the temperature was within ℃, and the hot rolling was performed, the cold rolling was performed so that the rolling reduction of the final cold rolling was 80% or more. Manufacture of a high-strength aluminum alloy fin material for forming, characterized by performing temper annealing at a temperature of ℃ and distributing intermetallic compounds having a diameter of 0.1 μm or less in the metal structure at a density of 10 or more / μm ³ Method. 3. Si 0.1 wt% or less, Fe 0.10 ~
1.0 wt%, Mn 0.01 to 0.50 wt%, Ti0.0
A casting plate having a thickness of 2 to 15 mm by continuously supplying an Al alloy molten metal containing 1 to 0.15 wt% and the remainder being Al and unavoidable impurities to the outer peripheral surfaces of a pair of opposing cooling molds, The cast plate was cold-rolled so that the final cold-rolling reduction rate was 80% or more, and the thin plate thus obtained was subjected to 250-3.
After tempering annealing at a temperature of 50 ° C., the metal structure has a diameter of 0.
A method for producing a high-strength aluminum alloy fin material for molding, characterized in that a metal compound having a size of 1 μm or less is distributed at a density of 10 pieces / μm ³ or more.