Method of producing aluminum alloy heat-exchanger

Abstract: A method of producing aluminum alloy heat-exchanger is disclosed, wherein, upon producing aluminum alloy heat-exchanger by soldering technique, it is retained for 10 minutes to 30 hours at 400 to 500 °C after the finish of heating for soldering. It is better to retain the heat-exchanger during cooling after the finish of heating for soldering or the heat-exchanger cooled to 150 °C or lower after the finish of heating for soldering for 10 minutes to 30 hours at 400 to 500 °C and further it is preferable to cool at a cooling velocity of not slower than 30 °C/min across a temperature range from 200 °C to 400 °C after said reteinment. Excellent thermal efficiency, high strength and excellent corrosion resistance can be achieved.

Description: BACKGROUND OF THE INVENTION The present invention relates to a method of producing aluminum alloy heat-exchanger. In more detail, it relates to a method of improving the thermal efficiency, strength and corrosion resistance of heat-exchanger produced by brazing technique. The heat-exchangers such as radiator used for cars etc. have a structure, wherein, for example, as shown in Fig. 1, thin-wall fins (2) machined into corrugated shape are formed unitedly between a plurality of flat tubes (1) and both ends of these flat tubes (1) are opened respectively toward spaces constituted with header (3) and tank (4). A high-temperature refrigerant is fed from the space on the side of one tank to the space on the side of other tank (4) through the flat tubes (1) and the refrigerant having become low temperature through the heat-exchange at the portions of tube (1) and fin (2) is circulated again to the external portion. As the materials of tube and header of such heat-exchanger, for example, a brazing sheet wherein JIS 3003 (Al-0.15 wt. % Cu-1.1 wt. % Mn) alloy is used as a core material and, on one side of said core material, JIS 7072 (Al-1 wt. % Zn) alloy is cladded as an internal lining material and, on other side, JIS 4045 (Al-10 wt. % Si) alloy or the like is cladded usually as a brazing material is used, constituting so as the side of said internal lining material to become inside, that is, the side of refrigerant contacting at all times. Moreover, for the fin material, corrugated JIS 3003 alloy or a material allowed to contain Zn etc. for the purpose of giving the sacrificial effect thereto is used. And, these are assembled unitedly by brazing. Next, in the multilayer type evaporator, as shown in Fig. 2, fins (5) and pathway-constituting sheets (6) and (6') forming path way (7) of refrigerant and comprising brazing sheet are layered alternately and these are joined by brazing. For this fin (5), around 0.1 mm thick brazing sheet is used ordinarily and, for the pathway-constituting sheet (7) or (7'), about 0.5 mm thick brazing sheet is used. For such evaporator, for preventing the pathway of refrigerant from the external corrosion, a fin material comprising JIS 3003 alloy or an alloy allowed to contain Zn etc. for the purpose of giving the sacrificial effect thereto is used and, for the material of refrigerant's pathway, such one that an alloy added with Cu, Zr, etc. to Al-1 wt. % Mn alloy, if necessary, is used as a core material and, on the surface, brazing material such as JIS 4004 (Al-9.7 wt. % Si-1.5 wt. % Mg) alloy or JIS 4343 (Al-7.5 wt. % Si) alloy is cladded is used. Moreover, the serpentine type condenser is shown in Fig. 3. In this, a tube (8) molded by extruding tubularly in hot or warm state is folded meanderingly and, in the openings of this tube (8), corrugated fins (9) comprising brazing sheet are attached. Besides, numeral (10) in the diagram shows a connector. As the materials of such condenser, for said tube, JIS 3003 alloy or the like is used and, for the corrugated fin, such one that JIS 3003 alloy or an alloy allowed to contain Zn etc. for the purpose of giving the sacrificial effect thereto is used as a core material and, on both sides, brazing material such as JIS 4004 alloy or JIS 4343 alloy is cladded is used. All of above-mentioned heat-exchanger etc. are assembled by brazing to unify by heating to a temperature near 600 °C and joining with bracing material. This brazing method includes vacuum brazing method, flux brazing method, Nocolock brazing method using noncorrosive flux, and the like. Now, the heat-exchanger is in a trend of lightening in weight and miniaturization recently and, for this reason, thinning of wall of materials is desired. However, if thinning of wall is made with conventional materials, then first there has been a problem that, as the thickness of materials decreases, the thermal conductivity ends up to decrease resulting in decreased thermal efficiency of heat-exchanger. For this problem, Al-Zr alloy material etc. have been developed as conventional fin materials, which, in turn, have a new problem of low strength. Moreover, as a second problem, short of strength by thinning of wall can be mentioned. For this problem, some high-strength alloys have been proposed, but any alloy with sufficient strength is still not obtained. This is because of that the ingredients of high-strength alloys themselves are restricted in view of the brazerability, corrosion resistance, etc. aforementioned and, in addition, due to the brazing to be heated near 600 °C in the final process of production, strength-improving mechanisms such as hardening cannot be utilized. As a result of extensive investigations in view of this situation, a production method of aluminum alloy heat-exchanger with excellent thermal efficiency, high-strength and excellent corrosion resistance has been developed by the invention. In EP-A-0 241 125 a thermal treatment of brazed products is disclosed, according to which the product after the brazing is subjected to a heat treatment at a temperature of 150°C to 425°C for at least 25 minutes. Furthermore, it is disclosed to cool the product to a temperature below the temperature ultimately selected for the post-braze heat treatment and, in any event, below about 290°C prior to the post-braze heat treatment. SUMMARY OF THE INVENTION The production method of the invention is characteized in that, upon producing aluminum alloy heat-exchanger by brazing technique, it is retained for 10 minutes to 30 hours at 400 to 500 °C after the finish of heating for brazing, and thereafter it is cooled at a cooling velocity of not slower than 30°C/min across a temperature range from 200 °C to 400 °C. According to one embodiment, the aluminum alloy heat-exchanger is retained for 10 minutes to 30 hours at 400 to 500 °C during cooling after the finish of heating for brazing, and thereafter it is cooled at a cooling velocity of not slower than 30°C/min across a temperature range from 200°C to 400°C. According to another embodiment, the aluminum alloy heat-exchanger is cooled to 150°C or lower after the finish of heating for brazing and is further retained for 10 minutes to 30 hours at 400 to 500°C, and thereafter it is cooled at a cooling velocity of not slower than 30°C/min across a temperature range from 200°C to 400°C. Moreover, as the brazing technique, said flux brazing method, Nocolock brazing method or vacuum brazing method can be used and, in the case of vacuum brazing method, Al-Si-Mg-based Al alloy is preferable as a brazing material. Furthermore, as the fin material of aluminum alloy heat-exchanger becoming a subject of the production method of the invention, it is preferable to use a bare material of Al alloy containing Si: 0.05-1.0wt. %, Fe: 0.1-1.0 wt. % and Mn: 0.05-1.5 wt. % and further containing one kind or not less than two kinds of Cu: not more than 0.5 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Zr: not more than 0.3 wt. %, Ti: not more than 0.3 wt. %, Zn: not more than 2.5 wt. %, In: not more than 0.3 wt. % and Sn: not more than 0.3 wt. % (however, in the case of vacuum brazing method, Zn is deleted), the balance comprising Al and inevitable impurities, or a bare material of Al alloy containing Si: 0.05-1.0 wt. %, Fe: 0.1-1.0 wt. % and Zr: 0.03-0.3 wt. % and further containing one kind or not less than two kinds of Cu: not more than 0.5 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Ti: not more than 0.3 wt. %, Zn: not more than 2.5 wt. %, In: not more than 0.3 wt. % and Sn: not more than 0.3 wt. % (however, in the case of vacuum brazing method, Zn is deleted), the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. Still more, as the pathway-constituting member for refrigerant of aluminum alloy heat-exchanger, it is better to use a bare material of Al alloy containing Si: 0.05-1.0 wt. % and Fe: 0.1-1.0 wt. % and further containing one kind or not less than two kinds of Mn: not more than 1.5 wt. %, Cu: not more than 1.0 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Zr: not more than 0.3 wt. % and Ti: not more than 0.3 wt. %, the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. And, in the invention, it is only necessary to use the bare material for either one of fin and pathway of refrigerant and the brazing sheet for the other. BRIEF DESCRIPTION OF THE DRAWING Fig. 1 is an oblique view shown by notching a part of radiator, Fig. 2 is an oblique view shown by notching a part of multilayer type evaporator, and Fig. 3 is an oblique view showing serpentine type condenser. DETAILED DESCRIPTION OF THE INVENTION In following,the invention will be illustrated in detail. First, the brazing technique aimed at in the invention may be any of conventional vacuum brazing method, flux brazing method, Nocolock brazing method, etc. using brazing materials described in JIS 4004, JIS 4343, JIS 4045, etc. and is not particularly restricted. This is because of that the invention provides a method of improving the characteristics of heat-exchanger by giving said treatment to the heat-exchanger having completed the heating for brazing, hence it is unrelated to the previous brazing itself. The assembling prior to brazing, washing and flux coating in the case of flux brazing method, etc. therefore may by performed as usual. Further, at this time, the brazing conditions determined based on the brazerability, collapse prevention of fin, etc. are not needed to be altered particularly. Consequently, the characteristics accompanying on brazing such as brazerability are not aggravated by the invention. And, in the invention, the heat-exchanger is retained for 10 minutes to 30 hours at 400 to 500 °C after the heating for brazing. It is also possible to cool the heat-exchanger after brazing to 150 °C or lower during a period until this retainment. The reason why the heat-exchanger is once cooled to 150 °C or lower in this way is due to that the cooling is effective for generating intermetallic compounds to become the nuclei for deposition during raising the temperature to retaining temperature thereafter. If raising the temperature from the temperature over 150 °C, the intermetallic compounds would hardly generate. Besides, the heat-exchanger may be safely cooled, of course, to room temperature, for example, if being under 150 °C. And, in the invention, the heat-exchanger after brazing is retained for 10 minutes to 30 hous at 400 to 500 °C with cooling to 150 °C or lower or without cooling in this way. Further, in a final cooling step the heat-exchanger is cooled at a cooling velocity of not slower than 30°C/min across a temperature range from 200°C to 400°C. This is one of the gists of the invention and has been obtained as a result of diligent investigations by the inventors on the change in the metal texture of materials during the heating for brazing. Namely, the heating for brazing is usually performed at a temperature near 600 °C and, at this time, the alloy elements in material come to solid solution in considerable amounts. For example, in the case of JIS 3003 alloy, the formation of solid solution progresses during temperature-raising on heating for brazing and retainment until about 1.0 wt. % of Mn, about 0.025 wt. % of Fe and all amounts of Si come to solid solution. With conventional heat-exchanger, materials, the alloy elements having come to solid solution in this way, have been used, but, in the invention, such elements having come to solid solution during brazing are deposited, thereby improving the thermal conductivity of material and improving the thermal efficiency of heat-exchanger. Namely, when retaining within said temperature range, mainly Mn, Fe and Si contained as added elements and inevitable impurities in the material deposit, hence the thermal conductivity of material improves and, as a result, the heat-exchange efficiency improves by about 3 % over the case not performing this treatment, though somewhat different depending on the material alloys to be used. Since such treatment is carried out for the overall part of heat-exchanger in the invention, the thermal conductivity of pathway of refrigerant, the thermal conductivity thereof having been not taken into account hitherto, improves, not to speak of that of fin, leading to extremely improved thermal efficiency as a heat-exchanger. Here, the reason why said retaining temperature was restricted to 400 to 500 °C is due to that, over 500 °C or under 400 °C, the progress of deposition of Mn, Fe, Si, etc. contributing significantly to the improvement in the thermal conductivity is slow and, in addition, in the case of the retaining time being under 10 minutes, sufficient amount of deposition cannot be achieved. Hence, the conditions were determined to retain at 400 to 500 °C for 10 minutes or longer. Moreover, even if making the retaining time over 30 hours, subsequent deposition is low, leading to poor economy. Hence, the retainment was made to be 30 hours or shorter. At this time, if retaining particularly under 400 °C, the deposited phase harmful for the corrosion resistance formed in the pathway of refrigerant during temperature-raising does not come gain to the solid solution by heating, ending up to decreased corrosion resistance. When performing above-mentioned treatment of the invention, the amount of solid solution decreases to 0.1 wt. % for Mn and about 0.001 wt. % for Fe, and, at that time, compounds containing Si also deposit, resulting in decreased amount of Si solid solution. Besides, said retainment defined in the invention does not mean to keep at a constant temperature, but it does not matter whatever the temperature may vary, if being within a temperature. range of 400 to 500 °C. Further, since the invention attempts to improve the characteristics by altering the metal texture of such materials, the inventive treatment during cooling after the finish of brazing may be performed either in vacuum or in atmosphere. Moreover, in the invention, the cooling within a temperature range from over 200 °C to under 400 °C is performed at a cooling velocity of not slower than 30 °C/min after the retainment of said temperature. This is for the reason of preventing the deposition of simple substance Si, Mg-based compounds and Cu-based compounds. These compounds are liable to deposit at a temperature near 300 °C, but all are harmful for the corrosion resistance of pathway of refrigerant. Hence, by suppressing the deposition, the corrosion resistance improves and further, through the solid solution effect and the cold aging effect of these elements, the strength improves. Here, in the case of the cooling velocity being under 30 °C/min, said deposition is caused during cooling to decrease the corrosion resistance and further to lose the effect on the improvement in strength. Moreover, the reason why the temperature range for performing the cooling at not slower than 30 °C/min was determined to be over 200 °C and under 400 °C is because of that, since the deposition velocity is slow at a temperature under 200 °C, the deposition is not caused so much even by gradual cooling at a cooling velocity of under 30 °C/min and, since the deposition is low at a temperature over 400 °C, the gradual cooling at under 30 °C/min is not needed. Besides, conventional average cooling velocity was 10 °C/min or so, which was a cause for decreased characteristics. Said method of cooling may be any of in-furnace air cooling, blast air cooling, water cooling, mist spraying, etc. and is not particularly regulated. The production method of the invention has been illustrated above. In following, illustration will be made about the aluminum alloys to be used as the materials of heat-exchanger concerning with the invention. In the aluminum alloys used usually in the industry, Fe and Si are surely contained as the inevitable impurities. In the invention, however, even aluminum alloys containing such elements are applicable, since Fe and Si are deposited as mentioned above. Hence, the alloys are not restricted, but, when using an alloy containing about 1 wt. % of Mn being conventional JIS 3003 alloy, the improving effect on thermal efficiency through the deposition of Mn appears conspicuously, and, also with materials aiming at the improved strength by the addition of Mg, Cu and Si, the improvement in strength can be aimed further because of the regulation of cooling velocity. Moreover, Al-Zr alloys exert more improving effect in thermal efficiency due to the deposition of Zr. Moreover, as mentioned above, the brazing material does not affect the invention, thus Al-Si-based or Al-Si-Mg-based brazing materials used hitherto may be used, and no restriction is made in the invention. Besides, such processes as the removal of flux and the painting onto heat-exchanger may be carried out as usual after the treatment of the invention. In following, the invention will be illustrated concretely based on the examples. Example 1 Fins A and B with a thickness of 0.08 mm (both are bare materials) comprising the compositions shown in Table 1 were produced by usual method. Also, 0.4 mm thick coil-shaped plate materials were produced by usual method, wherein alloys having the compositions shown in Table 2 were used as core materials and brazing materials shown in Table 2 were cladded on one side thereof in a thickness of 10 % per side, and thereafter these plate materials were converted to 35.0 mm wide strip materials with slitter, adjusting to the size of seam welded pipe. Further, these strip materials were processed to 16.0 mm wide, 2.2 mm thick seam welded pipes for fluid-passing pipe using a device for producing seam welded pipe to produce flat tubes a and b. Moreover, 1 mm thick coil-shaped plate materials wherein alloys having the same compositions as the core material alloys shown in said Table 2 were used as core materials and JIS 7072 alloy was cladded on one side of each of those core materials in a thickness of 10 % per side were slitted to produce 60 mm wide header plates a and b. Namely, the header plate consisting of the core material having the same composition as the core material of flat tube a in table 2 was made plate a and the header plate consisting of the core material having the same composition as the core material of flat tube b was made plate b. Fin symbol Composition of alloy (wt. %) Si Fe Cu Mn Zn Zr Ti Aℓ A 0.23 0.45 0.06 1.11 1.12 - 0.01 Balance B 0.18 0.62 - - 1.10 0.14 " " Flat tube symbol Composition of core material alloy (wt. %) brazing material JIS Si Fe Cu Mn Mg Cr Zr Ti Aℓ a 0.29 0.50 0.14 1.15 - - - 0.01 Balance 4343 b 0.56 0.52 0.45 1.20 0.34 0.15 0.15 " " 4045 * In the table, core material alloy of symbol a represents JIS 3003 alloy. All members of fin, flat tube and plate above were combined as in Table 4 to assemble a radiator shown in Fig. 1 and, after coated with 10 % concentration liquor of fluoride type flux thereonto, the assemble was heated in nitrogen gas under usual conditions to braze. And, after allowed to cool to each temperature shown in table 3, this was heated to each temperature shown in table 3 and retained at that temperature. Then, it was treated under the conditions of reheating and cooling to cool to the room temperature at each cooling velocity shown in table 3 to obtain a radiator. Of the radiator thus obtained, the thermal efficiency and the corrosion resistance were examined, which were shown in Table 4. Said thermal efficiency was determined according to JIS D1618 (Test method of automobile air conditioner) and the proportion of improvement to the thermal efficiency of radiator obtained by conventional method was indicated by percentage. Moreover, for the corrosion resistance, CASS test was performed for 720 hours to determine the depth of pit corrosion generated in the tube, which was indicated by the maximum depth of pit corrosion. Besides, the corrosion resistance can be said to be good, when the maximum depth of pit corrosion is less than 0.1 mm. Moreover, the same materials as fin and flat tube of radiator submitted at the time of heating for brazing of radiator and at the times of reheating and cooling under each condition shown in Table 3 were heated for brazing and reheated and cooled simultaneously to determine the strength, which are put down in Table 4 as the strength of fin material and the strength of tube material, respectively. Production method No. Cooling temperature after brazing (°C) Heating conditions Cooling Velocity (°C/min) Temperature (°C) Time Inventive method 1 20 480 2 hr 50 2 100 450 20 min 100 3 20 420 12 hr 50 4 20 450 2 hr 1000°C/Sec or faster (Water cooling) Comparative method 5 250 480 2 hr 50 6 20 300 2 hr 50 7 20 520 2 hr 100 8 20 480 2 hr 1 Conventional method 9 No treatments of reheating and cooling From Table 4, it is evident that the radiators according to the inventive production method show high improvement effect on the thermal efficiency and also excellent corrosion resistance. Further, the strength of members is equal to or more excellent than that of members by conventional method, even if the inventive treatments of reheating and cooling may be performed. It can be seen therefore that the inventive production method does not give an adverse effect on the strength of members at all. Example 2 By combining fin A or B shown in Table 1 with a pathway-constituting sheet comprising 0.6 mm thick brazing sheet cladded with JIS 4004 alloy on both sides of plate material of Al-0.31 wt. % Si-0.22 wt. % Fe-0.45 wt. % Cu-1.21 wt. % Mn-0.01 wt. % Ti alloy each in a thickness of 10 %, a core of multilayer type evaporator shown in Fig. 2 was assembled and the vacuum brazing was carried out under usual conditions to unify. Thereafter, as shown in table 5, these cores No. 1 through No. 18 were treated, respectively, under the reheating and cooling conditions shown in Table 3 for the Inventive methods No. 1 through No. 4, Comparative methods No. 5 through No. 8 or Conventional method No. 9 to obtain multilayer type evaporators. Of the evaporators thus obtained, the thermal efficiency and the corrosion resistance were examined similarly to above (Example 1), the results of which are shown in table 5. Moreover, the same materials as fin and plate of core submitted at the time of heating for brazing of said core and at the time of reheating and cooling under each condition shown in Table 3 were heated for brazing and reheated and cooled simultaneously to determine the strength, which are put down in Table 5 as the strength of fin material and the strength of plate material, respectively. Core No. Symbol of fin Production method (See Table 3) Improvement rate of thermal efficiency Max. depth of pit corrosion Strength of fin material Strength of plate material % mm kgf/mm 2 kgf/mm 2 1 A Inventive method No. 1 2.0 ≦ 0.05 12.5 13.5 2 " " No. 2 2.0 ≦ 0.05 12.5 13.5 3 " " No. 3 3.0 ≦ 0.05 12.5 13.5 4 " " No. 4 2.5 ≦ 0.05 12.5 13.5 5 " Comparative method No.5 1.0 0.10 12.5 13.5 6 " " No. 6 0.5 * 12.0 13.0 7 " " No. 7 0.5 0.10 12.5 13.5 8 " " No. 8 2.5 * 12.0 13.0 9 " Conventional method No. 9 - ≦ 0.05 12.0 13.0 10 B Inventive method No. 1 2.0 ≦ 0.05 8.0 13.5 11 " " No. 2 2.5 ≦ 0.05 8.0 13.5 12 " " No. 3 2.5 ≦ 0.05 8.0 13.5 13 " " No. 4 2.0 ≦ 0.05 8.0 13.5 14 " Comparative method No. 5 1.0 0.10 8.0 13.5 15 " " No. 6 0.5 * 7.5 13.0 16 " " No. 7 0.5 0.10 8.0 13.5 17 " " No. 8 2.5 * 7.5 13.0 18 " Conventional method No. 9 - ≦ 0.05 7.5 13.0 Besides, piercing pit corrosion generated in the case of mark *. According to Table 5, it is evident that the multilayer type evaporators by the inventive method are excellent in the thermal efficiency and the corrosion resistance and further have the strength of members also equal or higher compared with that of members by conventional production. Example 3 Fins C (thickness 0.14 mm) and D (thickness 0.16 mm) comprising brazing sheets wherein Aluminum alloys having the compositions shown in Table 6 were used as the core materials and JIS 4045 alloy or JIS 4343 alloy brazing material was cladded on both sides thereof in a thickness of 10 % as shown in table 6 were produced. And, 0.05 mm thick extruded multihole tube comprising Al-0.21 wt. % Si-0.54 wt. % Fe-0.15 wt. % Cu-1.11 wt. % Mn-0.01 wt. % Ti alloy (JIS 3003 alloy) was bent meanderingly, said fins C and D were attached in the openings of this tube, chloride type flux was coated, cores of condenser shown in Fig. 3 were assembled, and the brazing was carried out under usual conditions. Thereafter, as shown in Table 7, these cores No. 19 through No. 36 were treated, respectively, under the reheating and cooling conditions shown in Table 3 to obtain serpentine type condensers. Fin No. Composition of core material alloy (wt. %) brazing material JIS Si Fe Mn Zn Zr Ti Aℓ C 0.34 0.55 1.20 1.10 0.10 0.01 Balance 4045 D 0.46 0.45 - 1.12 0.15 0.01 " 4343 Of the condensers thus obtained, the thermal efficiency and the corrosion resistance were examined similarly to above (Example 1), the results of which are shown in Table 7. Moreover, the same materials as fin and extruded tube of core submitted at the time of heating for brazing of said core and at the times of reheating and cooling under each condition shown in Table 3 were heated for brazing and reheated and cooled simultaneously to determine the strength, which were put down in Table 7 as the strength of fin material and the strength of tube material, respectively. Core No. Symbol of fin Production method (See Table 3) Improvement rate of thermal efficiency Max depth of pit corrosion Strength of fin material Strength of plate material % mm kgf/mm 2 kgf/mm 2 19 C Inventive method No. 1 2.0 ≦ 0.05 13.0 12.5 20 " " No. 2 2.0 ≦ 0.05 13.0 12.5 21 " " No. 3 2.5 ≦ 0.05 13.0 12.5 22 " " No. 4 2.5 ≦ 0.05 13.0 12.5 23 " Comparative method No. 5 1.0 0.10 13.0 12.5 24 " " No. 6 0.5 0.2 12.5 12.0 25 " " No. 7 0.5 0.10 13.0 12.5 26 " " No. 8 2.5 0.2 12.5 12.0 27 " Conventional method No. 9 - ≦ 0.05 12.5 12.0 28 D Inventive method No. 1 2.0 ≦ 0.05 8.0 12.5 29 " " No. 2 2.0 ≦ 0.05 8.0 12.5 30 " " No. 3 2.5 ≦ 0.05 8.0 12.5 31 " " No. 4 2.0 ≦ 0.05 8.0 12.5 32 " Comparative method No. 5 0.8 0.10 8.0 12.5 33 " " No. 6 0.5 * 7.5 12.0 34 " " No.7 0.5 0.10 8.0 12.5 35 " " No. 8 2.5 * 7.5 12.0 36 " Conventional method No. 9 - ≦ 0.05 7.5 12.0 Besides, piercing pit corrosion generated in the case of mark * According to Table 7, it can be seen that the condensers produced by the inventive method are excellent in both the thermal efficiency and the corrosion resistance. Further, the strength of members was equal or higher over the members by conventional method. Example 4 Fin materials E and F with a thickness of 0.08 mm and extruded tube material G with a thickness of 0.5 mm having the compositions shown in Table 8 were produced by usual method (all are bare materials). Moreover, fin materials H and I and seam welded tube materials J and K comprising brazing sheets wherein alloys having the compositions shown in Table 9 were used as the core materials and the brazing material was cladded on both sides or one side thereof under the conditions shown in Table 10 were produced in thicknesses shown in Table 10. Symbol of material Composition of alloy (wt. %) Si Fe Cu Mn Zn Zr Ti Aℓ Fin material E 0.23 0.45 0.06 1.11 1.12 - 0.01 Balance Fin material F 0.18 0.62 - - 1.10 0.14 " " Tube material G 0.21 0.54 0.15 1.11 - - " " * In the table, composition of tube G corresponds to JIS 3003. Symbol of core material alloy Composition of core material alloy (wt. %) Si Fe Cu Mn Mg Zn Cr Zr Ti Aℓ d 0.34 0.55 - 1.20 - 1.10 - 0.10 0.01 Balance e 0.46 0.45 - - - 1.12 - 0.15 " " f 0.29 0.50 0.14 1.15 - - - - " " g 0.56 0.52 0.45 1.20 0.34 - 0.15 0.15 " " * In the table, composition of core material f corresponds to JIS 3003. Symbol of material Symbol of core material alloy Cladding rate brazing material (JIS) Thickness (mm) Fin material H d 10 % on both sides 4045 0.14 Fin material I e " 4343 0.16 Tube material J f 10 % on one side 4343 0.4 Tube material K g " 4045 0.4 Each of said fin materials and tube materials was treated in nitrogen gas under the heating conditions for brazing, raising the temperature at 50 °C/min and successively retaining for 5 minutes at 600 °C, and thereafter treatment under the conditions shown in following Table 11 was given in the cooling process. And, with each plate material obtained, corrosion resistance test, tensile test and measurement of electrical conductivity were performed, the results of which are shown in Table 12 through Table 15. Besides, for fin materials, only the tensile test and the measurement of electrical conductivity were performed. For the corrosion resistance test, after the completion of said treatment, the corrosion test was carried out under following conditions exposing only the central area of the surface of each tube material and sealing other overall face. Namely, cycle test wherein each tube material after seal treatment was dipped into an ASTM artificial water (aqueous solution containing 100 ppm of Cl - , 100 ppm of CO 3 2- and 100 ppm of SO 4 2- ) ) and then it was allowed to stand for 16 hours at room temperature was performed 90 times. And, after the finish of this cycle test, the corrosion products on each tube material were removed with a mixed solution of phosphoric acid with chromic acid. Then, the maximum depth of pit corrosion was determined by the focus depth method using optical microscope. Further, the cross section of corroded area was polished and the generating status of crystal boundary corrosion was examined to evaluate the corrosion resistance. Next, for the tensile test, after each plate material having completed said treatment was allowed to stand for 4 days at room temperature, the measurement was made. Moreover, the electrical conductivity was measured at 20 °C by double bridge method. Besides, the electrical conductivity is an index qf the thermal conductivity and, if the electrical conductivity of fin improves by 10 % IACS, then the thermal efficiency of heat-exchanger improves by about 2 %. Production method No. Cooling velocity to retaining temperature (°C/min) Retaining conditions Cooling velocity to room temperature (°C/min) Temperature (°C) Time Inventive method 10 10 480 2 hr 50 11 10 410 30 min 100 12 10 450 18 hr 100 13 10 450 2 hr 1000°C/sec or faster (water cooling) Comparative method 14 10 300 30 min 100 15 10 450 30 min 5 16 (No retainment) Cooled to room temperature at 100 °C/min. Conventional method 17 (No retainment) Cooled to room temperature at 20 °C/min. Symbol of material Production method (See Table 11) Tensile strength kgf/mm 2 Electrical conductivity % IACS Fin material E Inventive method No. 10 12.5 45.0 " No. 11 12.5 46.0 " No. 12 12.5 47.0 " No. 13 12.5 46.0 Comparative method No. 14 12.0 38.0 " No. 15 12.0 46.0 " No. 16 12.5 35.0 Conventional method No. 17 12.0 36.0 Fin material F Inventive method No. 10 8.0 58.0 " No. 11 8.0 59.0 " No. 12 8.0 59.5 " No. 13 8.0 58.0 Comparative method No. 14 7.5 53.0 " No. 15 7.5 58.0 " No. 16 8.0 50.5 Conventional method No. 17 7.5 51.0 Symbol of material Production method (See Table 11) Tensile strength kgf/mm 2 Electrical conductivity % IACS Fin material H Inventive method No. 10 13.0 45.0 " No. 11 13.0 45.5 " No. 12 13.0 46.0 " No. 13 13.0 45.0 Comparative method No. 14 12.5 37.5 " No. 15 12.5 45.5 " No. 16 13.0 33.5 Conventional method No. 17 12.5 34.0 Fin material I Inventive method No. 10 8.0 58.5 " No. 11 8.0 59.0 " No. 12 8.0 59.0 " No. 13 8.0 58.5 Comparative method No. 14 7.5 53.0 " No. 15 7.5 58.0 " No. 16 8.0 50.0 Conventional method No. 17 7.5 50.0 Symbol of material Production method (See Table 11) Max. depth of pit corrosion mm Generation of crystal boundary corrosion Tensile strength kgf/mm 2 Electrical conductivity % IACS Tube material G Inventive method No. 10 ≦ 0.05 No 12.5 46.0 " No. 11 ≦ 0.05 " 12.5 47.0 " No. 12 ≦ 0.05 " 12.5 48.0 " No. 13 ≦ 0.05 " 12.5 47.0 Comparative method No. 14 0.2 Yes 12.0 39.0 " No. 15 0.2 " 12.0 47.0 " No. 16 ≦ 0.05 No 12.5 36.0 Conventional method No. 17 ≦ 0.05 " 12.0 37.0 Tube material J Inventive method No. 10 ≦ 0.05 No 12.5 45.5 " No. 11 ≦ 0.05 " 12.5 47.0 " No. 12 ≦ 0.05 " 12.5 47.0 " No. 13 ≦ 0.05 " 12.5 46.5 Comparative method No. 14 0.2 Yes 12.0 38.0 " No. 15 0.2 " 12.0 46.5 " No. 16 ≦ 0.05 No 12.5 36.0 Conventional method No. 17 ≦ 0.05 " 12.0 36.5 Symbol of material Production method (See Table 11) Max. depth of pit corrosion mm Generation of crystal boundary corrosion Tensile strength kgt/mm 2 Electrical conductivity % IACS Tube material K Inventive method No. 10 ≦ 0.05 No 18.0 42.5 " No. 11 ≦ 0.05 " 18.0 43.0 " No. 12 ≦ 0.05 " 18.0 44.0 " No. 13 ≦ 0.05 " 18.0 43.0 Comparative method No. 14 Piercing pit corrosion Yes 17.0 34.5 " No. 15 Piercing pit corrosion " 17.0 43.0 " No. 16 ≦ 0.05 No 18.0 29.5 Conventional method No. 17 Piercing pit corrosion Yes 17.0 30.0 According to Tables 12 through 15, it can be seen that, when treating by the inventive method, the characteristics of each member of heat-exchanger all improve compared with those by conventional method. In particular, conspicuous improvement in the electrical conductivity is obvious. Whereas, the fin materials obtained by comparative method have equal tensile strength, but have electrical conductivity improved not so much, when comparing with those by conventional method. Besides, the fin material treated by Comparative method No. 16 shows equal characteristics to those by the inventive method (Table 12 and Table 13), but, when treating the tube material under same conditions (Table 14 and Table 15), the corrosion resistance decreases in all cases, hence those conditions are unsuitable for the production as a heat-exchanger with these members combined. Example 5 From the tube materials J and K shown in Table 10, coil-shaped plate materials were produced by usual method, respectively, and said plate materials were slitted adjusting to the size of seam welded pipe to obtain 35.0 mm with strip materials. These strip materials were processed to 16.0 mm wide, 2.2 mm thick flat tubes for fluid-passing pipe using a device for producing seam welded pipe. Moreover, 1 mm thick header plate materials L and M cladded with JIS 7072 alloy on one side of core material alloys f and g having the compositions shown in Table 9 at a cladding rate of 10 % were produced. Namely, plate material L was produced from core material alloy f and plate material M from core material alloy g. And, after coil-shaped plate materials were produced from these plate materials, they were slitted to a width of 60 mm to obtain the strip materials for header plate. Above-mentioned flat tubes (tube materials J and K), header plate materials (L and M) and aluminum alloy fin materials (E and F) shown in Table 8 were combined as in following Table 17 to assemble the radiators shown in Fig. 1. After coated with 10 % concentration liquor of fluoride type flux onto the radiators assembled in this way, temperature was raised at 30 °C/min in nitrogen gas, followed successively by heating under the conditions of 595 °C and 10 minutes to solder. Thereafter, cooling was made under the conditions shown in following tube 16 and, of the radiators thus obtained, the thermal efficiency and the corrosion resistance were examined as follows. The thermal efficiency was determined according to JIS D1618 (Test method of automobile air conditioner) and the proportion of improvement to the thermal efficiency of radiator produced by conventional method was indicated by percentage, the results of which are put down in Table 10. Moreover, for the corrosion resistance of these radiators, CASS test was carried out for 720 hours and the depth of pit corrosion generated in the flat tube was determined. Values of the maximum depth of pit corrosion are put down in Table 17. Besides, when the maximum depth of pit corrosion is less than 0.1 mm, the corrosion resistance can be said to be excellent. Production method No. Cooling velocity to retaining temperature (°C/min) Retaining conditions Cooling velocity to room temperature (°C/min) Temperature (°C) Time Inventive method 18 10 480 2 hr 50 19 10 450 30 min 100 20 10 440 10 hr 100 21 10 490 2 hr 1000 °C/sec or faster (water cooling) Comparative method 22 10 300 30 min 100 23 10 450 30 min 5 24 (No retainment) Cooled to room temperature at 100 °C/min. Conventional method 25 (No retainment) Cooled to room temperature at 20 °C/min. Radiator No. Symbol of member Production method Improvement rate of thermal efficiency (%) Max. depth of pit corrosion (mm) Fin material Tube material Plate material 1 E J L Inventive method No. 18 2.0 ≦ 0.05 2 " No. 19 2.5 ≦ 0.05 3 " No. 20 2.5 ≦ 0.05 4 " No. 21 2.0 ≦ 0.05 5 Comparative method No. 22 0.5 0.2 6 " No. 23 2.5 0.2 7 " No. 24 - 0.5 ≦ 0.05 8 Conventional method No. 25 - ≦ 0.05 9 F K M Inventive method No. 18 2.5 ≦ 0.05 10 " No. 19 3.0 ≦ 0.05 11 " No. 20 2.5 ≦ 0.05 12 " No. 21 2.5 ≦ 0.05 13 Comparative method No. 22 0.5 Piercing pit corrosion 14 " No. 23 2.5 Piercing pit corrosion 15 " No. 24 - 0.5 ≦ 0.05 16 Conventional method No. 25 - Piercing pit corrosion According to Table 17, it can be seen that the radiators by the inventive method are excellent in both the thermal efficiency and the corrosion resistance. Whereas, it is seen that the radiators by comparative method are poor in both or either one of thermal efficiency and corrosion resistance. Example 6 After coated with chloride type flux onto extruded multihole tube produced from tube material G shown in Table 8 and fin materials H and I shown in Table 10, they were combined as in Table 18 to assemble the cores of serpentine type condenser shown in Fig. 3. And, these cores were brazed by raising the temperature at 30 °C/min in nitrogen gas and successively by heating under the conditions of 595 °C and 10 minutes similarly to Example 5. Thereafter, they were cooled under the conditions shown in said Table 16 and, of the cores obtained, the thermal efficiency and the corrosion resistance were examined similarly to example 5. Core No. Symbol of member Production method Improvement rate of thermal efficiency (%) Max. depth of pit corrosion (mm) Fin material Tube material 1 H G Inventive method No. 18 2.0 ≦ 0.05 2 " No. 19 2.5 ≦ 0.05 3 " No. 20 2.5 ≦ 0.05 4 " No. 21 2.0 ≦ 0.05 5 Comparative method No. 22 0.5 0.2 6 " No. 23 2.5 0.2 7 " No. 24 - 0.5 ≦ 0.05 8 Conventional method No. 25 - ≦ 0.05 9 I Inventive method No. 18 1.5 ≦ 0.05 10 " No. 19 2.0 ≦ 0.05 11 " No. 20 2.0 ≦ 0.05 12 " No. 21 2.0 ≦ 0.05 13 Comparative method No. 22 0.5 0.2 14 " No. 23 2.5 0.2 15 " No. 24 - 0.5 ≦ 0.05 16 Conventional method No. 25 - ≦ 0.05 According to Table 18, it can be seen that the cores by the inventive method are excellent in both the thermal efficiency and the corrosion resistance, whereas those by comparative method are poor in both or either one of these characteristics. Example 7 Aluminum alloy fin materials (thickness 0.08 mm) P, Q and R and plate materials (thickness 0.6 mm) S, T and U having respective compositions shown in Table 19 were produced by usual production method. The plate materials were cladded with each 10 % 4004 alloy on both sides thereof. These were submitted to brazing and the same heating and cooling in vacuum under the conditions shown in Table 20 to test. The combinations are shown in Tables 21 and 22. With the specimens of plate materials obtained, corrosion resistance test, tensile test and measurement of electrical conductivity were carried out, the results of which are shown in Table 22. Also, with those of fin materials, only tensile test and measurement of electrical conductivity were carried out, the results of which are shown in Table 21. Besides, all of these test methods are same as the methods carried out in Example 4. As evident from Table 21 and Table 22, when treating by the inventive method, the characteristics of fin material and plate material to become the members of heat-exchanger improve and, in particular, the electrical conductivity improves surely. Moreover, the treatment by Comparative method No. brings about excellent characteristics for fin materials, but it decreases the corrosion resistance for plate materials in all cases, which is unsuitable for the production method of heat-exchanger compared with the inventive method. Example 8 Combining fin materials having the alloy compositions shown in Table 19 with plate materials having the alloy compositions similarly shown in Table 19, cores shown in Fig. 2 were assembled and brazed in vacuum under the conditions shown in Table 20. These combinations are shown in Table 23. Of the heat-exchangers thus obtained, the thermal efficiency and the corrosion resistance were examined, the results of which are shown in Table 23. The thermal efficiency was determined according to JIS D1618 (Test method of automobile air conditioner) and the proportions of improvement to the thermal efficiency of heat-exchanger by conventional method were listed in Table 23, respectively. Moreover, for the corrosion resistance, CASS test was performed for 720 hours to determine the depth of pit corrosion generated in the plate, and the maximum depth of pit corrosion is shown in Table 23. The depth of less than 0.1 mm shows good corrosion resistance. As evident from Table 23, the Inventive examples No. 74 through 77, 82 through 85 and 90 through 93 being the heat-exchangers produced by the inventive method are excellent in the thermal efficiency and the corrosion resistance compared with Conventional examples No. 81, 89 and 97. Whereas, with Comparative examples No. 78 through 80, 86 through 88 and 94 through 96 produced by comparative method, the improvement effect on thermal efficiency is not seen, and the corrosion resistance is seen to be rather decreased. As described, in accordance with the invention, such conspicuous effects are exerted industrially that the thermal efficiency, strength and corrosion resistance of fin material, plate material, etc. being the members of aluminum alloy heat-exchanger improve, thereby the miniaturization and the lightening in weight of heat-exchanger become possible, and the like. A method of producing aluminum alloy heat-exchanger is disclosed, wherein, upon producing aluminum alloy heat-exchanger by brazing technique, it is retained for 10 minutes to 30 hours at 400 to 500 °C after the finish of heating for brazing. It is better to retain the heat-exchanger during cooling after the finish of heating for brazing or the heat-exchanger cooled to 150 °C or lower after the finish of heating for brazing for 10 minutes to 30 hours at 400 to 500 °C and further it is preferable to cool at a cooling velocity of not slower than 30 °C/min across a temperature range from 200 °C to 400 °C after said retainment. Excellent thermal efficiency, high strength and excellent corrosion resistance can be achieved.

Claims: A method of producing an aluminum alloy heat-exchanger by brazing, wherein the heat-exchanger is retained for 10 minutes to 30 hours at 400 to 500°C during cooling after the finish of heating for brazing, and thereafter it is cooled at a cooling velocity of not slower than 30°C/min across a temperature range from 200°C to 400°C. A method of producing an aluminum alloy heat-exchanger by brazing, wherein the heat-exchanger is cooled to 150°C or lower after the finish of heating for brazing and is further retained for 10 minutes to 30 hours at 400 to 500°C, and thereafter it is cooled at a cooling velocity of not slower than 30°C/min across a temperature range from 200°C to 400°C. The method of producing aluminum alloy heat-exchanger of Claim 1 or 2, wherein the brazing technique using flux is used. The method of producing aluminum alloy heat-exchanger of Claim 1 or 2, wherein the Nocolock brazing technique is used. The method of producing aluminum alloy heat-exchanger of Claim 1 or 2, wherein the vacuum brazing technique is used. The method of producing aluminum alloy heat-exchanger of Claim 5, wherein the brazing material is Al-Si-Mg-based Al alloy. The method of producing aluminum alloy heat-exchanger of any of Claims 1 through 6, wherein the fin material of aluminum aloy heat-exchanger comprises a bare material of Al alloy containing Si: 0.05-1.0 wt. %, Fe: 0.1-1.0 wt. % and Mn: 0.05-1.5 wt. % and further containing one kind or not less than two kinds of Cu: not more than 0.5 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Zr: not more than 0.3 wt. %, Ti: not more than 0.3 wt. %, Zn: not more than 2.5 wt. %, In: not more than 0.3 wt. % and Sn: not more than 0.3 wt. %, the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. The method of producing aluminum alloy heat-exchanger of Claim 5 or 6, wherein the fin material of aluminum alloy heat-exchanger comprises a bare material of Al alloy containing Si: 0.05-1.0 wt. %, Fe: 0.1-1.0 wt. % and Mn: 0.05-1.5 wt. % and further containing one kind or not less than two kinds of Cu: not more than 0.5 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Zr: not more than 0.3 wt. %, Ti: not more than 0.3 wt. %, In: not more than 0.3 wt. %, and Sn: not more than 0.3 wt. %, the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. The method of producing aluminum alloy heat-exchanger of any of Claims 1 through 6, wherein the fin material of aluminum alloy heat-exchanger comprises a bare material of Al alloy containing Si: 0.05-1.0 wt. %, Fe: 0.1-1.0 wt. % and Zr: 0.03-0.3 wt. % and further containing Cu: not more than 0.5 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Ti: not more than 0.3 wt. %, Zn: not more than 2.5 wt. %, In: not more than 0.3 wt. % and Sn: not more than 0.3 wt. %, the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. The method of producing aluminum alloy heat-exchanger of Claim 5 or 6, wherein the fin material of aluminum alloy heat-exchanger comprises a bare material of Al alloy containing Si: 0.05-1.0 wt. %,Fe: 0.1-1.0 wt. % and Zr: 0.03-0.3 wt. % and further containing one kind or not less than two kinds of Cu: not more than 0.5 wt. %, Mg: not more than 0.5 wt. %, Cr: not more than 0.3 wt. %, Ti: not more than 0.3 wt. %, In: not more than 0.3 wt. % and Sn: not more than 0.3 wt. %, the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. The method of producing aluminum alloy heat-exchanger of any of Claims 1 through 10, wherein the pathway-constituting member for refrigerant of aluminum alloy heat-exchanger comprises a bare material of Al alloy containing Si: 0.05-1.0 wt. %, Fe: 0.1-1.0 wt. % and further containing one kind or not less than two kinds of Mn: not more than 1.5 wt. %, Cu: not more than 1.0 wt. %, Mg: not more than 0.5 wt. % Cr: not more than 0.3 wt. %, Zr: not more than 0.3 wt. % and Ti: not more than 0.3 wt. %, the balance comprising Al and inevitable impurities, or a brazing sheet used said Al alloy as a core material. The method of producing aluminum alloy heat-exchanger of any of Claims 1 through 11, wherein the fin of aluminum alloy heat-exchanger is made to be bare material and the pathway of refrigerant is made to be brazing sheet. The method of producing aluminum alloy heat exchanger of any of Claims 1 through 11, wherein the fin of aluminum alloy heat exchanger is made to be brazing sheet and the pathway of refrigerant is made to be bare material.

Inventors: DOKO TAKEYOSHI, DOKO, TAKEYOSHI
Applicants: FURUKAWA ALUMINIUM, FURUKAWA ALUMINUM CO., LTD.
Application year: 1992
Main classification: C22F1
IPC codes: C22F1