US20050150642A1 - High-conductivity finstock alloy, method of manufacture and resultant product - Google Patents

High-conductivity finstock alloy, method of manufacture and resultant product Download PDF

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Publication number
US20050150642A1
US20050150642A1 US10/755,632 US75563204A US2005150642A1 US 20050150642 A1 US20050150642 A1 US 20050150642A1 US 75563204 A US75563204 A US 75563204A US 2005150642 A1 US2005150642 A1 US 2005150642A1
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finstock
strip
tolerable impurities
comprised
alloy
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US10/755,632
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English (en)
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Stephen Baumann
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Howmet Aerospace Inc
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Alcoa Inc
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Priority to US10/755,632 priority Critical patent/US20050150642A1/en
Assigned to ALCOA, INC. reassignment ALCOA, INC. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BAUMANN, STEPHEN
Priority to CNA2004800417118A priority patent/CN1918310A/zh
Priority to BRPI0418393-2A priority patent/BRPI0418393A/pt
Priority to JP2006549275A priority patent/JP2007517986A/ja
Priority to AU2004314437A priority patent/AU2004314437A1/en
Priority to EP04813718A priority patent/EP1713944A4/en
Priority to PCT/US2004/041450 priority patent/WO2005069779A2/en
Publication of US20050150642A1 publication Critical patent/US20050150642A1/en
Abandoned legal-status Critical Current

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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 FIG. 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 FIG. 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.
  • cooling fins 4 require an appropriate increase in thermal conductivity, while still maintaining an effective minimum level of post-braze strength and self-corrosion resistance.
  • U.S. Pat. No. 6,165,291 discloses a process of producing aluminum fin alloy having a tailored corrosion potential and high conductivity.
  • the fin alloy composition restricts Mn to a maximum of 0.6%.
  • U.S. Pat. No. 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.
  • casting parameters such as, for example, molten metal temperature, casting speed, cast gauge, cooling rate and position of the casting machine feeding tip
  • the present invention provides an aluminum alloy finstock having a desirable combination of, among other things, lightweight, post-braze strength, thermal conductivity and corrosion resistance.
  • the invention also provides a newly discovered method of manufacturing such finstock through continuous casting with a careful selection and control of casting parameters, such as, for example, molten metal temperature, cooling rate, casting speed, cast gauge and position of the casting machine feeding tip, and then processing the cast strip with specific combinations of cold rolling reductions and annealing steps.
  • 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 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 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 120 MPa, and more preferably greater than about 130 MPa.
  • 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 120 MPa, and more preferably greater than about 130 MPa.
  • 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 1-4 mm; 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 0.05-0.2 mm; 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 can be performed on the final gauge material.
  • a back-anneal One potential purpose for this back-anneal might be to impart more workability to the finstock.
  • This optional final back-anneal preferably involves heating the coil for about 1-12 hours at a temperature of about 150-240° C.
  • FIG. 1 is an isometric view of a portion of a brazed heat exchanger.
  • FIG. 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 FIG. 1 , are subject to increasingly stringent size and weight demands as automobile manufacturers endeavor to reduce the weight of the vehicles they produce.
  • the most common way to reduce the weight of such heat exchangers is to reduce the size of their components, including reducing the gauge and therefore the weight of the heat exchanger cooling fins 4 .
  • down-gauging the fins 4 results in reduced heat carrying capacity and therefore reduced heat exchanger efficiency. Accordingly, if the efficiency and lifetime of the heat exchanger is not to be compromised, down-gauging the fin 4 requires an appropriate increase in thermal conductivity while maintaining a sufficient level of post-braze strength and self-corrosion resistance.
  • cooling fins 4 and brazed aluminum heat exchangers 2 employing a plurality of cooling fins 4 made from such finstock, likewise exhibit the foregoing desirable characteristics.
  • 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 FIG. 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%.
  • Silicon contributes to both particle and solid solution strengthening.
  • An insufficient Si content for example, less than about 0.7%, 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.
  • 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.
  • 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. For this reason 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.
  • In can fulfill the same function as Zn. However, for cost and scrap loop reasons, In is less desirable than Zn. 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. It is envisioned that up to, for example, about 0.3% Ni might be tolerated in some specific instances, however, in general, Ni should be kept to less than about 0.05%.
  • 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.
  • 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 13 B and step 15 ), and an optional final partial anneal (see step 16 A).
  • the exemplary method of manufacture begins with a step of casting the exemplary alloy as a strip 11 with a preferable thickness of about 2-10 mm, more preferably about 5-9 mm.
  • the exemplary strip is continuously cast while carefully controlling the molten metal temperature from the furnace to the caster. For ease of illustration, 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 11 is performed in a manner that substantially avoids formation of coarse primary Fe-bearing intermetallics or heavy bands of eutectic segregation. This requires, as a minimum, control of casting conditions such as, for example, gauge, speed, and tip position, in order to solidify the alloy without deforming the semi-solid metal in a way that would result in segregation of solute-rich liquid to near the mid-plane of the strip.
  • 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 1-4 mm.
  • 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 0.05 mm to 0.2 mm, 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 16 A can be employed after the step of cold rolling to final gauge 16 .
  • This final partial anneal 16 A 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 13 A and at least one additional intermediate anneal 13 B 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 13 B 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 .
  • Three alloys were cast on a commercial twin-roll caster. Casting conditions were carefully controlled to minimize the generation of coarse intermetallics or clusters of intermetallics in the form of center-line segregation, which can be detrimental to fabrication to light gauges. Molten metal temperature at the entry to the casting tip was maintained at or above 700° C. throughout the cast. The alloys were cast as sheets with a thickness of about 7 mm, and a width of about 1070 mm. The sheets were cast at a rate of about 760 mm/min.
  • compositions of each of the three alloys are given, in weight-percent, in Table 1.
  • Table 1 Alloy Si Fe Cu Mn Mg Zn 1 0.82 2.1 0.02 0.65 0.01 0.74 2 0.96 2.2 0.02 0.65 0.01 0.77 3 0.96 2.2 0.02 0.66 0.10 0.77
  • cycle A a conventional-type brazing cycle
  • cycle B a shorter brazing cycle
  • 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 B 117 neutral salt spray cabinet. The results of each of these tests are reported in the 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 128 MPa UTS, about 52 MPa 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 ⁇ 760 mV.
  • the coarse grain size of the present invention alloys is desirable for resisting sagging of the fin during the brazing operation.
  • the experiment clearly shows that the method of manufacturing and the resultant finstock of the present invention, produces fins for brazed heat exchangers that exhibit an attractive combination of post-braze strength, thermal conductivity and corrosion resistance that compares very well relative to conventional 3003+Zn finstock.

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

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Application Number Priority Date Filing Date Title
US10/755,632 US20050150642A1 (en) 2004-01-12 2004-01-12 High-conductivity finstock alloy, method of manufacture and resultant product
CNA2004800417118A CN1918310A (zh) 2004-01-12 2004-12-09 高传导性散热片坯料合金、制造方法和得到的产品
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
AU2004314437A AU2004314437A1 (en) 2004-01-12 2004-12-09 High-conductivity finstock alloy, method of manufacture and resultant product
EP04813718A EP1713944A4 (en) 2004-01-12 2004-12-09 HIGH-GRADE RIB MATERIAL ALLOY, MANUFACTURING METHOD AND RESULTANT PRODUCT
PCT/US2004/041450 WO2005069779A2 (en) 2004-01-12 2004-12-09 High-conductivity finstock alloy, method of manufacture and resultant product

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US20160116236A1 (en) * 2013-07-05 2016-04-28 Uacj Corporation Aluminum alloy fin material for heat exchangers, and method of producing the same
US9719156B2 (en) 2011-12-16 2017-08-01 Novelis Inc. Aluminum fin alloy and method of making the same
US10473411B2 (en) 2014-12-17 2019-11-12 Carrier Corporation Aluminum alloy finned heat exchanger
US10634439B2 (en) 2016-03-29 2020-04-28 Uacj Corporation Aluminum alloy brazing sheet for a heat exchanger, and process for producing the same
US11933553B2 (en) 2014-08-06 2024-03-19 Novelis Inc. Aluminum alloy for heat exchanger fins

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US9719156B2 (en) 2011-12-16 2017-08-01 Novelis Inc. Aluminum fin alloy and method of making the same
US20160116235A1 (en) * 2013-07-05 2016-04-28 Uacj Corporation Aluminum alloy fin material for heat exchangers, and method of producing the same
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US11933553B2 (en) 2014-08-06 2024-03-19 Novelis Inc. Aluminum alloy for heat exchanger fins
US10473411B2 (en) 2014-12-17 2019-11-12 Carrier Corporation Aluminum alloy finned heat exchanger
US10634439B2 (en) 2016-03-29 2020-04-28 Uacj Corporation Aluminum alloy brazing sheet for a heat exchanger, and process for producing the same

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WO2005069779A3 (en) 2005-12-15
EP1713944A2 (en) 2006-10-25
BRPI0418393A (pt) 2007-06-05
CN1918310A (zh) 2007-02-21
EP1713944A4 (en) 2007-10-31
WO2005069779A2 (en) 2005-08-04
JP2007517986A (ja) 2007-07-05
AU2004314437A1 (en) 2005-08-04

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