WO2005069779A2 - Alliage pour materiau d'ailette haute conductivite, procede de fabrication et produit resultant - Google Patents

Alliage pour materiau d'ailette haute conductivite, procede de fabrication et produit resultant Download PDF

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Publication number
WO2005069779A2
WO2005069779A2 PCT/US2004/041450 US2004041450W WO2005069779A2 WO 2005069779 A2 WO2005069779 A2 WO 2005069779A2 US 2004041450 W US2004041450 W US 2004041450W WO 2005069779 A2 WO2005069779 A2 WO 2005069779A2
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Prior art keywords
finstock
strip
tolerable impurities
comprised
alloy
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PCT/US2004/041450
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English (en)
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WO2005069779A3 (fr
Inventor
Stephen Baumann
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Alcoa Inc.
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Publication date
Application filed by Alcoa Inc. filed Critical Alcoa Inc.
Priority to AU2004314437A priority Critical patent/AU2004314437A1/en
Priority to BRPI0418393-2A priority patent/BRPI0418393A/pt
Priority to JP2006549275A priority patent/JP2007517986A/ja
Priority to EP04813718A priority patent/EP1713944A4/fr
Publication of WO2005069779A2 publication Critical patent/WO2005069779A2/fr
Publication of WO2005069779A3 publication Critical patent/WO2005069779A3/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/003—Aluminium alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F1/00—Tubular elements; Assemblies of tubular elements
    • F28F1/10—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses
    • F28F1/12—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses the means being only outside the tubular element
    • F28F1/126—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses the means being only outside the tubular element consisting of zig-zag shaped fins
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
    • F28F21/081—Heat exchange elements made from metals or metal alloys
    • F28F21/084—Heat exchange elements made from metals or metal alloys from aluminium or aluminium alloys

Definitions

  • the present invention relates generally to aluminum alloy fin material and, more particularly, to an aluminum alloy finstock for brazed heat exchangers having a desirable combination of post-braze strength, thermal conductivity and self- corrosion resistance.
  • the invention also relates to fins made from the finstock and to brazed heat exchangers employing the finstock.
  • the invention further relates to a method of manufacturing the finstock.
  • Heat exchangers such as, for example, the brazed aluminum alloy automobile radiator 2 shown in Figure 1 , typically include a plurality of cooling fins 4 disposed between a plurality of flat fluid-carrying tubes 6.
  • the ends of the fluid- carrying tubes 6 are open to a header plate 8 and a tank 10 (one end of the tubes 6, one header plate 8 and one tank 10 are shown in Figure 1).
  • Coolant is circulated from the tank 10, through the fluid-carrying tubes 6 and into another tank (not shown).
  • the cooling fins 4 transfer heat away from the fluid-carrying tubes 6, in order to facilitate a heat exchange thereby cooling the fluid therein.
  • the cooled fluid is then recirculated through the closed loop circuit of which the radiator is one component.
  • the fin material or finstock for brazed heat exchangers is typically fabricated from 3XXX series aluminum alloys such as, for example, AA3003 or AA3003+Zn. After brazing, these alloys are characterized by a fairly low thermal conductivity (as measured by electrical conductivity) because of high levels of Mn trapped in solid solution. This has become increasingly problematic as heat exchanger fabricators continually endeavor to reduce the weight of heat exchanger components by, for example, down-gauging the fluid-carrying tubes 6 and cooling fins 4. The thermal conductivity of the cooling fins 4 directly impacts the efficiency of the heat exchanger. The cooling fins 4 need to effectively conduct heat away from the. fluid-carrying tubes 6 in order to cool the fluid therein.
  • 6,620,265 discloses a method for manufacturing an aluminum alloy fin material for brazing in which the Fe content in the alloy is limited to a maximum of 2.0%.
  • an object of the present invention to provide an aluminum alloy finstock having a desirable combination of post-braze strength, thermal conductivity and self-corrosion resistance.
  • This combination of properties is such that it will permit down-gauging of the fin for use in, for example, automotive heat exchangers, such as, for example, radiators, without negatively impacting the performance or service lifetime of the heat exchanger.
  • It is another object of the present invention to improve the thermal conductivity of finstock containing Si, Fe, Mn, and Zn, while achieving sufficient post-braze strength, self-corrosion resistance and thermal conductivity.
  • a finstock comprises: an aluminum alloy preferably comprised of about 0.7-1.2% Si, more preferably about 0.8-1.1% Si, about 1.9-2.4% Fe, more preferably about 2.0-2.2% Fe, about 0.6-1.0% Mn, more preferably about 0.6-0.8% Mn, up to about 0.5% Mg, more preferably up to about 0.2% Mg, up to about 2.5% Zn, more preferably up to about 1.5% Zn, up to about 0.10% Ti, more preferably up to about 0.05% Ti, and up to.
  • Any incidental elements or tolerable impurities are preferably comprised from the following: up to about 0.2% Cu, more preferably up to about 0.05% Cu, up to about 0.2% Zr, more preferably up to about 0.05% Zr, up to about 0.05% Cr and up to about 0.3% Ni, more preferably up to about 0.05% Ni, with the aggregate of all tolerable impurities preferably not to exceed about 0.4% and more preferably not to exceed about 0.10%.
  • the foregoing finstock preferably exhibits a post-braze electrical conductivity of greater than about 48%IACS, and more preferably greater than about 50%IACS, and a post-braze ultimate tensile strength (UTS) preferably greater than about 120MPa, and more preferably greater than about 130MPa.
  • a post-braze electrical conductivity of greater than about 48%IACS, and more preferably greater than about 50%IACS, and a post-braze ultimate tensile strength (UTS) preferably greater than about 120MPa, and more preferably greater than about 130MPa.
  • a fin for a heat exchanger such as, for example, a brazed aluminum automobile radiator is formed from an aluminum alloy finstock preferably comprised of about 0.7-1.2% Si, more preferably about 0.8-1.1% Si, about 1.9-2.4% Fe, more preferably about 2.0-2.2% Fe, about 0.6- 1.0% Mn, more preferably about 0.6-0.8% Mn, up to about 0.5% Mg, more preferably up to about 0.2% Mg, up to about 2.5% Zn, more preferably up to about 1.5% Zn, up to about 0.10% Ti, more preferably up to about 0.05% Ti, and up to about 0.05% In, more preferably up to about 0.03% In, with the remainder comprising Al and tolerable impurities.
  • Any incidental elements or tolerable impurities in the foregoing fin are preferably comprised from the following: up to about 0.2% Cu, more preferably up to about 0.05% Cu, up to about 0.2% Zr, more preferably up to about 0.05% Zr, up to about 0.05% Cr and up to about 0.3% Ni, more preferably up to about 0.05% Ni, with the aggregate of all tolerable impurities preferably not to exceed about 0.4% and more preferably not to exceed about 0.10%.
  • a brazed aluminum heat exchanger comprises: at least one tank structured to hold a coolant; a header plate coupled to the at least one tank, the header plate including a plurality of apertures for receiving a plurality of substantially parallel fluid-carrying tubes each extending substantially perpendicular from one of the plurality of apertures in the header plate and structured to receive the coolant therethrough; and a plurality of fins disposed between the plurality of fluid-carrying tubes, the fins being in thermal communication with the plurality of fluid-carrying tubes and structured to transfer heat away therefrom, in order to cool the fluid as it circulates therein.
  • the plurality of fins being formed from an aluminum alloy finstock preferably comprised of about 0.7-1.2% Si, more preferably about 0.8-1.1 % Si, about 1.9-2.4% Fe, more preferably about 2.0- 2.2% Fe, about 0.6-1.0% Mn, more preferably about 0.6-0.8% Mn, up to about 0.5% Mg, more preferably up to about 0.2% Mg, up to about 2.5% Zn, more preferably up to about 1.5% Zn, up to about 0.10% Ti, more preferably up to about 0.05% Ti, and up to about 0.05% In, more preferably up to about 0.03% In, with the remainder comprising Al and tolerable impurities.
  • a method of manufacturing aluminum alloy finstock from an alloy preferably comprised of about 0.7-1.2% Si, more preferably about 0.8-1.1 % Si, about 1.9-2.4% Fe, more preferably about 2.0-2.2% Fe, about 0.6-1.0% Mn, more preferably about 0.6-0.8% Mn, up to about 0.5% Mg, more preferably up to about 0.2% Mg, up to about 2.5% Zn, more preferably up to about 1.5% Zn, up to about 0.10% Ti, more preferably up to about 0.05% Ti, and up to about 0.05% In, more preferably up to about 0.03% In, with the remainder comprising Al and tolerable impurities, comprises the steps of: casting the alloy as a strip with a preferable thickness of about 2-10 mm, more preferably about 5-9 mm, by controlled continuous strip casting with an average cooling rate above about 300°C/sec.
  • cold rolling the strip in one or more passes to a first intermediate annealing gauge of about l-4mm; applying a first intermediate anneal to the strip for about 1-10 hours at a temperature of about 300-450°C, more preferably about 1-6 hours at a temperature of about 330-400°C; cold rolling the strip to a final intermediate anneal gauge of about 0.05-0.2mm; applying a final intermediate anneal to the strip for about 1-10 hours at a temperature of preferably about 300-450°C, more preferably about 1-6 hours at a temperature of about 330- 400°C; and cold rolling the strip to a final gauge using a preferable reduction of about 15-50%, more preferably about 15-35%.
  • the method of manufacture may further include the steps of at least one additional intermediate anneal, after the step of applying the first intermediate anneal and subsequently imparting some further cold reduction to the strip after such first intermediate anneal, but before the step of cold rolling the strip to a final intermediate anneal gauge.
  • the strip may be cold rolled to a second intermediate anneal gauge using a reduction of at least about 70% after the first intermediate anneal, annealed for 1 -10 hours at a temperature of about 300-450°C, more preferably for 1-6 hours at a temperature of about 330-400°C, then cold rolled again using a reduction of at least 70% to the final intermediate anneal gauge, followed by a final intermediate anneal for about 1 -6 hours at a temperature preferably about 300-450°C and more preferably about 330-400°C, and then cold rolled to final gauge.
  • a final partial anneal known as a back-anneal, can be performed on the final gauge material.
  • FIG. 1 is an isometric view of a portion of a brazed heat exchanger.
  • Figure 2 is a flow chart illustrating the steps of a process for manufacturing finstock in accordance with the present invention.
  • the finstock and resultant products such as, for example, heat exchanger fins and brazed heat exchangers, produced in accordance with the method of manufacture of the present invention, exhibit a desirable combination of post-braze strength, thermal conductivity and self-corrosion resistance that is unmatched by conventional finstock materials currently used in brazed aluminum heat exchangers.
  • Brazed aluminum heat exchangers such as, for example, automobile radiators 2, as shown in Figure 1, are subject to increasingly stringent size and weight demands as automobile manufacturers endeavor to reduce the weight of the vehicles they produce.
  • a brazed aluminum heat exchanger 2 in accordance with the present invention includes a plurality of fluid-carrying tubes 6.
  • the ends of the fluid-carrying tubes 6 are open to a header plate 8 and a tank 10 (one end of the fluid-carrying tubes 6, one header plate 8 and one tank 10 are shown in Figure 1). Coolant is circulated from the tank 10, through the fluid-carrying tubes 6 and into another tank (not shown).
  • a plurality of cooling fins 4, made from the following exemplary finstock, are disposed between the fluid-carrying tubes 6, in order to transfer heat away therefrom thereby facilitating a heat exchange cooling the fluid therein.
  • the composition of the exemplary finstock alloy preferably comprises between about 0.7-1.2% Si, more preferably between about 0.8-1.1 % Si, between about 1.9-2.4% Fe, more preferably between about 2.0-2.2% Fe, between about 0.6- 1.0% Mn, more preferably between about 0.6-0.8% Mn, up to about 0.5% Mg, more preferably up to about 0.2% Mg, up to about 2.5% Zn, more preferably up to about 1.5% Zn, up to about 0.10% Ti, more preferably up to about 0.05% Ti, and up to about 0.05% In, more preferably up to about 0.03% In, with the remainder comprising Al and tolerable impurities.
  • Incidental elements or tolerable impurities in the finstock are preferably comprised from the following: up to about 0.2% Cu, more preferably up to about 0.05% Cu, up to about 0.2% Zr, more preferably up to about 0.05% Zr, up to about 0.05% Cr and up to about 0.3% Ni, more preferably up to about 0.05% Ni, with the aggregate of all tolerable impurities preferably not to exceed about 0.4% and more preferably not to exceed about 0.10%.
  • the purpose for using each of the aforementioned alloying components in the exemplary finstock, and the reasons for limiting the content of each therein, will now be discussed. Silicon contributes to both particle and solid solution strengthening.
  • An insufficient Si content results in reduced strengthening while too much Si, for example, more than about 1.2%, results in decreased thermal conductivity and a reduced melting temperature undesirably effecting the heat exchanger during the brazing operations.
  • Iron in the alloy forms relatively small intermetallic particles during casting, that contribute to particle strengthening. Less than about 1.9% Fe does not take full advantage of the strengthening effect, while Fe in excess of about 2.4% results in the formation of large primary intermetallic particles which inhibit the ability to cold roll the alloy to the desired final gauge. Fe has very low solubility in aluminum, so its influence on conductivity is relatively small. Iron in the range of about 2.0 - 2.2% is a good compromise for balancing post-braze strength and ease of manufacture.
  • Mn in solid solution has a negative impact on conductivity.
  • Mn levels of about 0.6-1.0% can be beneficial for strengthening and self corrosion resistance without a significant negative impact on conductivity.
  • the preferred range of about 0.6-0.8% Mn provides the best balance of conductivity with the other product attributes.
  • Magnesium improves the post-braze strength of the cooling fin and for that reason, Mg levels of up to about 0.5% are acceptable and beneficial for strengthening.
  • the Mg level is preferably kept low, preferably less than about 0.2%.
  • Zinc affects the corrosion potential of the finstock. By reducing the corrosion potential of the finstock, Zn has the effect of causing the fins to function as sacrificial anodes, thereby providing corrosion protection for the tubes of the heat exchanger to which they are brazed. Zinc has a detectable, but relatively small effect on strength and thermal conductivity.
  • the minimum amount of Zn required for cathodic protection of the tube is added. Usually that will require at least about 0.3% Zn. More than about 1.5% Zn will have an impact on conductivity and self-corrosion rate. However, in some instances, higher Zn contents of, for example, up to about 2.5% Zn might be desirable at the expense of conductivity and self- corrosion properties.
  • Indium in the finstock functions similarly to Zn, serving to lower the corrosion potential of the finstock and thus provide a sacrificial anode effect. When used in conjunction with, or in place of Zn, In can fulfill the same function as Zn. However, for cost and scrap loop reasons, In is less desirable than Zn.
  • In When In is used it should be at levels of less than about 0.05% and most benefit will be obtained by keeping In content less than about 0.03%.
  • Titanium can be used as a grain refining additive during casting to aid the casting process and to help minimize centerline segregation.
  • Ti in solid solution has a negative impact on conductivity. Therefore, only the minimum amount needed for grain refinement is employed. This is preferably less than about 0.10% and more preferably less than about 0.05%.
  • Cu can enhance the post braze strength of the fin material, however, it can have a detrimental influence on the corrosion potential of the fin and also on fin self-corrosion characteristics. For that reason, while up to about 0.2% can be added for strength, Cu content is preferably kept at levels below about 0.05%.
  • Zirconium can be added to fin alloys to help control the post-braze grain size and shape. For that reason up to about 0.2% Zr might be incorporated in the invention finstock alloys. However, it has been discovered that control of the grain structure is relatively easy in these alloys. Accordingly, Zr is not generally needed, and levels of less than about 0.05% are preferred. Cr may perhaps add a small amount of strength. However, Cr is known to reduce conductivity. Therefore, Cr content should preferably be kept below about 0.05%. Ni has been shown to promote strength without a significant detrimental influence on conductivity. It is known, however, to have a negative impact on self-corrosion characteristics of the fin.
  • the present invention also relies on precise selection of the continuous casting parameters suitable for producing re-roll useful for fabrication of finstock from the exemplary alloy composition.
  • Such parameters include, for example, molten metal temperature, cooling rate, casting speed, casting gauge and position of the casting machine feeding tip.
  • casting needs to be performed in such a manner as to produce an alloy strip substantially without coarse intermetallics, such as, for example, primary Fe-bearing intermetallics and without heavy bands of eutectic segregation in the form of center-line segregation.
  • coarse intermetallics such as, for example, primary Fe-bearing intermetallics and without heavy bands of eutectic segregation in the form of center-line segregation.
  • Patent No. 6,620,265 it would be expected that a cast stock having the exemplary alloy composition would result in unacceptable fabrication characteristics, such as, for example, strip breaks during cold rolling, due to, for example, primary Fe-bearing particles.
  • U.S. Patent No. 6,620,265 indicates that a finstock in accordance with the present invention would exhibit excessive droop during a brazing thermal cycle, would have unacceptable self- corrosion characteristic, and would exhibit melting during brazing.
  • careful selection and control of casting conditions and employing the method of manufacture in accordance with the present invention overcomes such problems and allows for the production of finstock with highly desirable combinations of, among other things, post-braze strength, thermal conductivity and corrosion resistance.
  • the exemplary finstock is fabricated using a method of manufacture, including a first step of continuously casting the exemplary alloy into a strip 11.
  • the exemplary strip is preferably twin-roll cast using any known or suitable twin-roll casting machine which, with appropriate selection of casting conditions and caster roll release agent, will provide the requisite minimum cooling rate during freezing.
  • the preferred minimum cooling rate is about 300°C/sec.
  • the resultant finstock is fabricated from this twin-roll cast strip by multiple pass cold rolling (see, for example, step 12, optional step 13 A, step 14 and step 16) and using one or more intermediate partial anneals (see, for example, step 13, optional step 13B and step 15), and an optional final partial anneal (see step 16A).
  • the exemplary method of manufacture begins with a step of casting the exemplary alloy as a strip 1 1 with a preferable thickness of about 2-10mm, more preferably about 5-9mm.
  • the exemplary strip is continuously cast while carefully controlling the molten metal temperature from the furnace to the caster.
  • the furnace and caster have not been shown.
  • controlling the molten metal temperature from the furnace to the caster might require maintaining the minimum temperature of the molten metal to within the range of about 695°C to 750°C.
  • the exemplary strip casting step 1 1 is performed in a manner that substantially avoids formation of coarse primary Fe-bearing intermetallics or heavy bands of eutectic segregation.
  • the next step of the exemplary manufacturing process includes cold rolling the cast strip to a first intermediate annealing gauge 12, in one or more passes.
  • the thickness of this gauge is preferably between about l-4mm.
  • the next step is to apply a first intermediate anneal 13.
  • the first intermediate anneal occurs for about 1-10 hours at a temperature preferably about 300-450°C, and more preferably for about 1-6 hours at a temperature of about 330- 400°C.
  • the strip is then cold rolled to a final intermediate anneal gauge 14, preferably about 0.05mm to 0.2mm, in several passes.
  • a final intermediate anneal 15 is then applied, again for about 1-10 hours at a temperature preferably about 300-450°C, and more preferably for about 1-6 hours at a temperature of about 330-400°C.
  • the alloy strip is cold rolled to a final gauge 16.
  • the exemplary final cold rolling step uses a preferred reduction of about 15-50%, and more preferably about 15-35%.
  • an optional final partial anneal 16A can be employed after the step of cold rolling to final gauge 16. This final partial anneal 16A preferably consists of heating the product for between about 1-12 hours at a temperature of about 150-240°C.
  • alternative embodiments of the method of manufacture may optionally further include the additional steps of cold rolling to at least one additional intermediate anneal gauge 13A and at least one additional intermediate anneal 13B of the strip. If employed, these fabricating steps occur after the step of applying a first intermediate anneal 13 but before the step of cold rolling the strip to the final intermediate anneal gauge ' 14.
  • a preferred embodiment employing such additional fabricating steps will include cold rolling the strip to a second intermediate anneal gauge 13 A, using a preferred reduction of at least about 70% after the first intermediate anneal 13, and applying a second intermediate anneal 13B for preferably about 1-10 hours at a temperature preferably about 300-450°C, and more preferably for between about 1-6 hours at a temperature of about 330-400°C.
  • the second intermediate anneal is preferably followed by a cold reduction of at least about 70% to the final intermediate anneal gauge 14.
  • the alloys were cast as sheets with a thickness of about 7mm, and a width of about 1070mm. The sheets were cast at a rate of about 760mm/min.
  • the compositions of each of the three alloys are given, in weight- percent, in Table 1. Table 1
  • Each of the three cast sheets were then processed to 0.05mm gauge finstock in a commercial aluminum sheet mill by the following fabrication process: 1 ) cold rolling in several passes from about 7mm to 1.8mm; 2) annealing for about 3 hrs at about 360°C; 3) cold rolling in several passes from 1.8mm to 0.062mm; 4) annealing for about 5 hrs at about 360°C; and 5) cold rolling to 0.05mm.
  • cycle A One was a conventional-type brazing cycle (referred to as cycle A).
  • Cycle A involved a soak of about 4-1/4 minutes at a temperature above about 590°C with a peak metal temperature of about 595°C and a cooling rate of about 70°C/minute below about 500°C.
  • the second brazing thermal cycle was a shorter brazing cycle, (referred to as cycle B).
  • Cycle B had a soak of about 3 minutes at a temperature above about 590°C with a peak metal temperature of about 598°C and a cooling rate of about 190°C/minute below about 500°C.
  • the post-braze tensile strength, electrical conductivity and corrosion characteristics of the three materials were measured after both of these cycles.
  • the tensile data was measured in the longitudinal direction using ASTM E345 Specimen type B. Electrical conductivity was calculated from a measurement of electrical resistivity using a potential drop technique commonly employed in the art.
  • the corrosion potential measurements were made in accordance with ASTM G69.
  • the self-corrosion measurements were done by measuring weight loss after one week of exposure in an ASTM Bl 17 neutral salt spray cabinet. The results of each of these tests are reported in the Table 2.
  • Table 2 Table 2
  • the post-braze conductivity for these materials is seen to be dependent upon the braze cycle employed and this is understood in terms of the cooling rate from the braze temperature influencing the amount of elements retained in solid solution with higher cooling rates trapping more solute and decreasing conductivity.
  • This data substantiates the fact that the finstock and method of manufacture discovered through the present invention, provides an improvement over conventional finstock material, such as, for example, an AA3003+1.4 Zn type finstock.
  • typical AA3003+1.4 Zn type finstock after braze thermal cycle A has about 128MPa UTS, about 52MPa YS but only has a conductivity of about 40%IACS.
  • the self-corrosion rate of a typical 3003+1.4 Zn alloy is approximately the same as the alloys of the present invention, and the solution potential for a 3003+1.4 Zn fin is about -760mV.
  • the coarse grain size of the present invention alloys is desirable for resisting sagging of the fin during the brazing operation.

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Abstract

La présente invention se rapporte à un alliage de matériau d'ailette haute conductivité destiné à des échangeurs de chaleur en aluminium brasé. Le matériau d'ailette comprend un alliage d'aluminium constitué d'environ 0,7 à 1,2 % de Si; d'environ 1,9 à 2,4 % de Fe; d'environ 0,6 à 1,0 % de Mn; jusqu'à environ 0,5 % de Mg; jusqu'à environ 2,5 % de Zn; jusqu'à environ 0,10 % de Ti; et jusqu'à environ 0,05 % de In; le reste étant formé de Al et des impuretés acceptables. Un procédé de production de matériau d'ailette à partir dudit alliage d'aluminium consiste à couler en continu l'alliage sous forme d'une bande d'une épaisseur d'environ 2 à 10 mm à une vitesse de refroidissement moyenne supérieure à environ 300 °C/sec, puis à laminer à froid par passages multiples la bande au moyen d'au moins un recuit partiel intermédiaire à une température comprise entre environ 300 et 450 °C. La présente invention concerne également une ailette réalisée à partir du matériau d'ailette selon l'invention ainsi qu'un échangeur de chaleur en aluminium brasé comprenant des ailettes de refroidissement réalisées à partir du matériau d'ailette présenté.
PCT/US2004/041450 2004-01-12 2004-12-09 Alliage pour materiau d'ailette haute conductivite, procede de fabrication et produit resultant WO2005069779A2 (fr)

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AU2004314437A AU2004314437A1 (en) 2004-01-12 2004-12-09 High-conductivity finstock alloy, method of manufacture and resultant product
BRPI0418393-2A BRPI0418393A (pt) 2004-01-12 2004-12-09 liga de conjunto de aletas de alta condutividade, método de produção e produto resultante
JP2006549275A JP2007517986A (ja) 2004-01-12 2004-12-09 高伝導性フィンストック合金、製造方法及び得られた製品
EP04813718A EP1713944A4 (fr) 2004-01-12 2004-12-09 Alliage pour materiau d'ailette haute conductivite, procede de fabrication et produit resultant

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US10/755,632 2004-01-12
US10/755,632 US20050150642A1 (en) 2004-01-12 2004-01-12 High-conductivity finstock alloy, method of manufacture and resultant product

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WO2005069779A3 WO2005069779A3 (fr) 2005-12-15

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EP (1) EP1713944A4 (fr)
JP (1) JP2007517986A (fr)
CN (1) CN1918310A (fr)
AU (1) AU2004314437A1 (fr)
BR (1) BRPI0418393A (fr)
WO (1) WO2005069779A2 (fr)

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US7850796B2 (en) 2007-08-20 2010-12-14 Denso Corporation Aluminum alloy fin material for brazing

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CN1918310A (zh) 2007-02-21
BRPI0418393A (pt) 2007-06-05
US20050150642A1 (en) 2005-07-14
EP1713944A2 (fr) 2006-10-25
JP2007517986A (ja) 2007-07-05
AU2004314437A1 (en) 2005-08-04
EP1713944A4 (fr) 2007-10-31
WO2005069779A3 (fr) 2005-12-15

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