US20160237527A1 - Aluminum alloy composition, aluminum extrusion tube and fin material with improved corrosion durability comprising same, and heat exchanger constructed of same - Google Patents

Aluminum alloy composition, aluminum extrusion tube and fin material with improved corrosion durability comprising same, and heat exchanger constructed of same Download PDF

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US20160237527A1
US20160237527A1 US15/025,166 US201415025166A US2016237527A1 US 20160237527 A1 US20160237527 A1 US 20160237527A1 US 201415025166 A US201415025166 A US 201415025166A US 2016237527 A1 US2016237527 A1 US 2016237527A1
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corrosion
alloy
aluminum
heat exchanger
present disclosure
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Jung Gu Kim
In Jun Park
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Sungkyunkwan University Research and Business Foundation
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    • 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • 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
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • 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
    • F28F1/40—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses the means being only inside the tubular element
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F19/00—Preventing the formation of deposits or corrosion, e.g. by using filters or scrapers
    • 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 disclosure generally relates to an aluminum alloy with enhanced penetration resistance for a heat exchanger, an aluminum alloy extruded tube and an aluminum alloy fin for a heat exchanger, the tube and fin being made of the alloy, and a heat exchanger comprising the tube and fin. More particularly, the present disclosure relates to an aluminum alloy extruded tube and an aluminum alloy fin for a heat exchanger, and a heat exchanger comprising the tube and fin, where the tube and fin have enhanced penetration and corrosion resistances to prevent the tube and fin from penetration and damage, which otherwise occur due to corrosion caused by internal refrigerant and external condensed water in the heat exchanger, for example, in an air-conditioner, refrigerator, radiator, etc.
  • Aluminum-based materials for a heat exchanger includes pure aluminum-based formulations (A1XXX) with a high extrusion rate, high thermal conductance, and a low cost, and aluminum manganese-based formulations (A3XXX) with a lower extrusion rate compared to the pure aluminum-based formulations, a relatively high strength, and relatively high corrosion resistance.
  • a following Table 1 describes respective compositions of A1070 and A3003 alloys as the previous aluminum-based formulations for a heat exchanger.
  • the A1070 belongs to the pure aluminum-based formulations, while the A3003 belongs to the aluminum manganese-based formulations.
  • the A1070 may be employed for a tube and a fin, for example, in a condenser in home appliances such as an air-conditioner, a refrigerator, etc. where a high strength of the Al based material is not demanded but economical aspects such as a low material cost, and a low extrusion cost of the Al based material are demanded.
  • the A3003 has a higher strength and corrosion resistance, but more expensive extrusion cost compared to the A1070, and, thus may be employed for a tube and a fin of a heat exchanger in an intercooler, radiator, etc. in an automobile.
  • Aluminum may have a high chemical activation, and may form an oxidized film at a surface thereof in an air space to have high corrosion resistance.
  • a pitting corrosion where corrosion may occur only at a local area in which the oxidized film is damaged.
  • the corrosion may propagate and concentrate on a certain area due to electrochemical reaction with various impurities in the aluminum alloy. This corrosion mechanism may cause an aluminum heat exchanger to be locally penetrated, leading to a leak of internal refrigerant or hot fluids. Therefore, there is a need for an aluminum alloy with enhanced penetration resistance for the heat exchanger.
  • the home appliances have been widely used in China, India etc. suffering from heavy air pollution.
  • the aluminum heat exchanger in the home appliances may be susceptible to such a leak therefrom due to the corrosion. This may be true of a seashore area. This leak may cause economical loss such as a component replacement, and may lead to deterioration of the home appliances.
  • FIG. 1 shows a mechanism for pitting corrosion and intergranular corrosion of a previous aluminum formulation.
  • a left side drawing in FIG. 1 shows a grain-boundary distribution of a cathodic site.
  • a protective passive film is formed on an aluminum surface, and Al 2 Cu, Al 3 Fe, etc. are distributed along and in the grain boundary in an intermetallic phase.
  • pitting corrosion is initiated, such that, as shown in a middle drawing in FIG. 1 , there may be generated a potential difference between a base material and the intermetallic phase materials Al 2 Cu, and Al 3 Fe, and, thus, a local circuit may be created. This may lead to the passive film damage, which may confirm the pitting corrosion initiation.
  • the pitting corrosion propagates.
  • a propagation rate of the pitting corrosion along the grain boundary may be higher than an initiation rate of new pitting corrosion at the surface of the alloy. This causes a larger penetration depth relative to an actual corrosion amount.
  • This aluminum corrosion mechanism may cause a local penetration through the aluminum heat exchanger, and, thus, a leak of an internal refrigerant or hot fluid from the exchanger.
  • FIG. 2 illustrates corrosion propagation behavior in a previous aluminum alloy for a heat exchanger. As shown in the figure, a penetration depth becomes gradually larger due to the propagation of the pitting corrosion as time goes by.
  • the present disclosure may provide an aluminum alloy for a tube and a fin in a heat exchanger, the alloy having enhanced penetration resistance and corrosion resistance and, at the same time, a non-lowered extrusion rate, which are not the case in the previous A1070 and A3003 aluminum alloys.
  • This may be achieved by adding zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof into the alloy and adjusting composition ratios thereof to suppress corrosion concentration and thus allow uniform corrosion.
  • the present disclosure may provide an aluminum alloy extruded tube and an aluminum alloy fin for a heat exchanger, the tube and fin being made of the above-defined aluminum alloy, and, thus, having enhanced penetration resistance. Further, the present disclosure may provide a heat exchanger comprising the above-defined tube and fin.
  • an aluminum alloy comprising: copper (Cu); iron (Fe); zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof; and the remainder being aluminum (Al), and unavoidable impurities, wherein the zirconium (Zr), titanium (Ti), or hafnium (Hf), or the mixture thereof has a content from 0.05 wt % to 0.2 wt % relative to a total weight of the alloy; wherein contents of the copper and iron are adjusted such that a PHI (penetration hazard index) value defined by following equations (1) and (2) is equal to or smaller than 1.5:
  • the alloy may further comprises silicon (Si), wherein a content of the silicon may be adjusted to be equal to or smaller than 0.2 wt % relative to a total weight of the alloy.
  • the alloy may further comprises magnesium (Mg), wherein a content of the magnesium is adjusted to be equal to or smaller than 0.05 wt % relative to a total weight of the alloy.
  • Mg magnesium
  • an aluminum tube with enhanced corrosion resistance for a heat exchanger the tube being made of the above-defined aluminum alloy.
  • an aluminum fin with enhanced corrosion resistance for a heat exchanger the fin being made of the above-defined aluminum alloy.
  • a heat exchanger with enhanced corrosion resistance comprising the above-defined aluminum tube.
  • a heat exchanger with enhanced corrosion resistance comprising the above-defined aluminum fin.
  • a heat exchanger with enhanced corrosion resistance comprising an aluminum fin and an aluminum tube, wherein both the fin and tube are defined above.
  • the above-defined aluminum alloy may have superior penetration resistance and corrosion resistance, compared to the previous A1070 for a heat exchanger, and, thus, have superior corrosion and penetration resistances against external condensed water and internal refrigerant.
  • the addition of the zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof may allow uniform corrosion of the alloy, and, thus, more enhanced penetration resistance relative to the pitting corrosion.
  • control of contents of the zirconium (Zr), titanium (Ti), or hafnium (Hf) may suppress intergranular corrosion, and, thus, may spread corrosion propagation, leading to enhanced penetration resistance of the alloy.
  • the above-defined aluminum alloy may exhibit an extrusion rate (about 90 m/min) similar to that of the previous A1070, and, thus, have good productivity and economy.
  • the above-defined heat exchanger may include components (for example, the fin and tube) thereof with enhanced corrosion resistance, such that the exchanger has a prolonged life span, good performance, and more energy-saving effect due to lack of leak of the refrigerant and, thus, improved heat-exchanging efficiency.
  • FIG. 1 shows a mechanism for pitting corrosion and intergranular corrosion of a previous aluminum alloy.
  • FIG. 2 illustrates corrosion propagation behavior in a previous aluminum alloy for a heat exchanger.
  • FIG. 3A and FIG. 3B illustrate cross-sectional views of a A1070 specimen as a previous 1XXX-based aluminum alloy for a heat exchanger, after being subjected to a potentiostatic polarization test.
  • FIG. 4A and FIG. 4B illustrate cross-sectional views of a A3003 specimen as a previous 3XXX-based aluminum alloy for a heat exchanger, after being subjected to a potentiostatic polarization test.
  • FIG. 5 is a schematic view illustrating a pitting corrosion and intergranular corrosion mechanism of an aluminum alloy of the present disclosure.
  • FIG. 6A and FIG. 6B illustrate cross-sectional views of specimens made of the aluminum alloy in accordance with one embodiment of the present disclosure, after being subjected to a potentiostatic polarization test.
  • FIG. 7 illustrates an aluminum heat exchanger in accordance with one embodiment of the present disclosure.
  • FIG. 8 illustrates a graph describing varying PHIs and varying extrusion rates of the present aluminum tube relative to varying zirconium contents.
  • FIG. 9 illustrates a graph describing varying PHIs relative to varying copper and iron contents.
  • FIG. 10 illustrates a graph describing a correlation between an X factor and a PHI value.
  • a stated range of “1 to 10” should be considered to include any and all subranges between (and inclusive of) the minimum value of 1 and the maximum value of 10; that is, all subranges beginning with a minimum value of 1 or more and ending with a maximum value of 10 or less, e.g., 1 to 6.3, or 5.5 to 10, or 2.7 to 6.1.
  • the term “substantially,” “about,” and similar terms are used as terms of approximation and not as terms of degree, and are intended to account for the inherent deviations in measured or calculated values that would be recognized by those of ordinary skill in the art. Further, the use of “may” when describing embodiments of the present disclosure refers to “one or more embodiments of the present disclosure.”
  • an aluminum alloy with enhanced penetration resistance includes copper (Cu); iron (Si); zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof; the remainder being aluminum (Al), and unavoidable impurities.
  • the aluminum alloy with enhanced penetration resistance contains zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof.
  • the zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof may not only refine a grain size to improve strength of the alloy, but also suppress pitting corrosion and, thus, allow uniform corrosion.
  • the suppression of pitting corrosion, and, thus, creation of the uniform corrosion may be achieved as follows: the addition of the zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof may generate a potential difference in the alloy to finely spread precipitations serving as initiation points for corrosion, and thus, may suppress the pitting corrosion occurring locally and intensely and thus hard to predict corrosion locations.
  • Zr zirconium
  • Ti titanium
  • Hf hafnium
  • a content of each component refers to a content in % by weight.
  • experiment conditions are set such that a content of zirconium is variable, while each of contents of copper, and iron is controlled to a given content.
  • the results of the experiments indicate corrosion depth averages and corresponding corrosion depth standard deviations, and PHIs and extrusion rates, depending on the varying contents of the zirconium.
  • the PHIs and extrusion rates depending on the varying contents of the zirconium are graphically presented as shown in FIG. 8 .
  • a PHI refers to an acronym of a “penetration hazard index”.
  • the PHI may be calculated by means of a corrosion penetration depth of an aluminum tube after being subjected to electrochemical corrosion acceleration.
  • the PHI may serve as a measure of corrosion resistance of an aluminum alloy.
  • a lower PHI value may mean superior corrosion resistance of an aluminum alloy.
  • the PHI may be expressed as follows:
  • an aluminum alloy specimen is subjected to electrochemical corrosion acceleration in a synthetic acid rain, and, then, a cross-section of the resulting specimen is analyzed to measure a corrosion depth average and a corrosion depth standard deviation.
  • an optimal Zr content may be 0.05 wt % to 0.2 wt %.
  • an alloy composition of No. 1 in the Table 2 (whose Zr content is smaller than 0.05 wt %) may not suppress a crack in the alloy due to a much smaller Zr amount (this is confirmed from a remarkably high PHI value), while alloy compositions of No. 4 and No. 5 in the Table 2 (whose Zr content is larger than 0.2 wt %) may lower an extrusion rate of the alloy due to a much larger Zr amount.
  • it is desirable that the aluminum alloy should not only exhibit uniform corrosion, but also maintain an extrusion rate.
  • an intergranular corrosion mechanism of the alloy may be as follows:
  • FIG. 5 is a schematic view illustrating a pitting corrosion and intergranular corrosion mechanism of the present aluminum alloy.
  • the addition of the zirconium (Zr), titanium (Ti), or hafnium (Hf), or a mixture thereof may allow a decrease of a residence of Al 2 Cu, Al 3 Fe, etc. in the grain boundary in the intermetallic phase, and, thus, spread the residence of Al 2 Cu, Al 3 Fe, etc.
  • the Al 2 Cu, Al 3 Fe, etc. mainly reside in the grain boundary
  • FIG. 5 see a left side drawing therein
  • the residence of the Al 2 Cu, Al 3 Fe, etc. in the grain boundary may decrease.
  • an aluminum alloy specimen is subjected to electrochemical corrosion acceleration in a synthetic acid rain, and, then, a cross-section of the resulting specimen is analyzed to measure a corrosion depth average and a corrosion depth standard deviation. Details about an experimental procedure are as follows: first, a surface of the aluminum alloy specimen is polished using a #600 SiC paper, and, then, an exposure area thereof is controlled to be 1 cm ⁇ 1 cm. Then, the specimen is immersed for 4 hours in a test solution (synthetic acid rain) of pH 5 containing 4 ppm SO4 2 ⁇ , 1.5 ppm NO 2 ⁇ , and 2 ppm Cl ⁇ to stabilize a surface state of the specimen.
  • a test solution synthetic acid rain
  • the specimen has a constant potential of 0.25 V applied thereto for 6 hours, the potential being relative to SCE (saturated calomel electrode), to accelerate corrosion in a constant rate.
  • the synthetic acid rain simulates a corrosion environment to which a heat exchanger including an aluminum tube is exposed in an air space.
  • the electrochemical acceleration method simulates a corrosion mechanism identical with an actual corrosion environment purely in an electrochemical manner.
  • the electrochemical acceleration method may be more similar to the actual corrosion environment than an existing chemical acceleration method.
  • differences in corrosion resistances between the specimens may be evaluated in a more reliable manner.
  • a following Table 3 indicates chemical compositions, corrosion penetration depths after the electrochemical acceleration, and the PHI values for 11 aluminum specimens.
  • a No. 11 specimen is made in accordance with one embodiment of the present disclosure. As seen from the Table 3, when a PHI value is smaller than or equal to 1.5, corrosion resistance of the alloy is superior. From comparison of the PHI values between previous alloys (No. 1 to No. 10 specimens) and the present alloy (No. 11 specimen), it is confirmed that when the PHI value of the alloy is smaller than or equal to 1.5, the alloy exhibits a relatively low average corrosion depth and standard deviation, which means that corrosion of the alloy occurs and propagates substantially uniformly, and, thus, the alloy has sufficient corrosion resistance enhancement.
  • an alloy element when a metal has a different element injected intentionally thereto, the element is referred to as an alloy element. Meanwhile, impurities are unavoidably injected into the alloy due to a technical limitation and an economical aspect during the alloy formation.
  • the impurities may be limited in contents thereof by contents equal to or smaller than acceptable amounts, and, thus, presences thereof in the alloy may be acceptable.
  • the acceptable contents of the impurities may depend on what extent of harm the impurities give the metal.
  • the copper (Cu) may react with the aluminum and hence be precipitated into Al 2 Cu promoting the cathodic reaction of corrosion.
  • the copper may mainly reside in a continuous or networking manner along the grain boundary of the aluminum, and, thus, may be a factor for intergranular corrosion where the corrosion damage propagates along the grain boundary. This intergranular corrosion may cause the aluminum alloy for a heat exchanger to be susceptible to the penetration.
  • the copper should be controlled in a content thereof by a content smaller than a high content at a room temperature.
  • the iron (Fe) may react with the aluminum and silicon to generate precipitations acting as initiation points of cathodic reactions in corrosion environment, thereby to play a considerable role for the aluminum corrosion.
  • the iron content should be minimized.
  • the precipitations derived from the irons may reside in a non-continuous or isolated manner and, thus, be less susceptible to the interganular corrosion compared to the copper. Further, in order to reduce the content of the iron below a low concentration, a high cost may occur. Therefore, the iron (Fe) content should be controlled from considerations of the above.
  • the copper and iron may play a significant role in aluminum corrosion in a corrosion environment based on a content correlation between there.
  • the content correlation is determined to suppress intergranular corrosion.
  • FIG. 9 illustrates a graph describing varying PHIs relative to varying copper and iron contents. It is confirmed that when a content of copper is equal to or larger than 0.01 wt %, the intergranular corrosion may occur, and, thus, the PHI may increase. When a content of copper is equal to or larger than 0.01 wt %, the copper may precipitate along the grain boundary of the aluminum in a continuous or networking manner.
  • This continuous or networking manner of the precipitation may allow the corrosion of the aluminum alloy, for example, an aluminum tube to propagate along the grain boundary and, thus, be susceptible to penetration. Therefore, it is observed that when a content of copper is equal to or larger than 0.01 wt %, the content of the copper and the PHI have a linear correlation. Meanwhile, it is confirmed that when a content of iron is equal to or larger than 0.2 wt %, the PHI may increase exponentially.
  • the iron may act as a highly corrosive impurity. However, the iron may be individually spread in a form of islands in the aluminum in a low concentration thereof, and, thus, may not cause intergranular corrosion. This is not true of the copper.
  • the zirconium content may also affect the intergranular corrosion (the larger the Zr content is, the lower the PHI is; the optimal Zr content may be 0.05 to 0.2 wt %). Thus, the zirconium content should be taken into account.
  • the PHI may be expressed as follows:
  • the X factor refers to concentrations of alloy elements. That is, the PHI may be expressed as a function of the X factor.
  • FIG. 10 illustrates a graph describing a correlation between the X factor and the PHI value. It may be seen from this graph that the X factor and the PHI value have an exponential relationship, which may be expressed as follows:
  • the PHI value may be adjusted to be equal to or smaller than 1.5, the PHI value is fixed to 1.5 for the sake of an exemplary simplified calculation.
  • the PHI 1.5 may suffice to suppress the intergranular corrosion and thus obtain enhanced corrosion resistance of the aluminum alloy for a fin and a tube of a heat exchanger.
  • the PHI value smaller than 1.5 may be more preferable.
  • the PHI value 1.5 may be employed to define a maximum numerical range.
  • the Cu and Fe contents may be adjusted as in the equation (4).
  • the aluminum alloy composition of one embodiment of the present disclosure may contain silicon and magnesium impurities beside the copper and iron.
  • the silicon and magnesium impurities should be limited in contents thereof as follows.
  • the magnesium (Mg) may react with the silicon (Si) to form precipitations to improve alloy strength.
  • the magnesium (Mg) may create an oxide film to deteriorate brazing bonding ability.
  • the Mg content should be minimized.
  • the Mg content may be controlled to be as follows: 0 wt % ⁇ Mg ⁇ 0.05 wt %.
  • the brazing bonding ability may be deteriorated, leading to poor brazing process.
  • the Mg content should be adjusted to be equal to or smaller than 0.05 wt %.
  • the alloy may avoidably contain the impurity Mg, and, thus, the Mg content has no choice but to exceed zero %.
  • the silicon (Si) may react with unavoidable impurities (magnesium) to generate precipitations, which may promote cathodic reaction in corrosion environment.
  • the silicon content should be minimized.
  • the silicon (Si) content may be controlled to be greater than 0% by weight and equal to or smaller than about 0.2% by weight.
  • contents of the above-mentioned impurities namely, copper, iron, silicon and magnesium should be minimized
  • the contents thereof may be controlled to the above-defined contents due to the economical aspect.
  • the above-defined contents thereof may suffice to provide the good aluminum alloy for a heat exchanger as illustrated below.
  • FIG. 3A and FIG. 3B illustrate cross-sectional views of a A1070 specimen as a previous 1XXX-based aluminum alloy for a heat exchanger, after being subjected to a potentiostatic polarization test.
  • FIG. 4A and FIG. 4B illustrate cross-sectional views of a A3003 specimen as a previous 3XXX-based aluminum alloy for a heat exchanger, after being subjected to a potentiostatic polarization test.
  • FIG. 6A and FIG. 6B illustrate cross-sectional views of specimens made of the aluminum alloy in accordance with one embodiment of the present disclosure, after being subjected to a potentiostatic polarization test.
  • the potentiostatic polarization test a constant voltage is applied and maintained to the specimen to accelerate corrosion. This test may be useful to evaluate a corrosion resistance of the alloy.
  • the alloy specimen is subjected to the potentiostatic polarization test for 6 hours using the synthetic acid rain simulating the external condensed water, and a cross-section of the resulting specimen is measured in terms of a corrosion depth.
  • the penetration depth may be relative to the reference line (red line).
  • the reference line red line
  • corrosion is concentrated on a certain region, and propagate inwardly along the grain boundary, to form a large penetration depth.
  • corrosion is spread along the reference line, that is, a surface line of the alloy, and an intergranular corrosion may not occur and, thus, create a uniform corrosion, to form a small penetration depth.
  • the present specimen has a greater decrease in the corrosion propagation than in the A1070 and A3003 specimens.
  • Table 4 indicates corrosion depth measurements of the previous A1070 and A3003 specimens, and the present specimens made of the aluminum alloy of one embodiment of the present disclosure, after being subjected to the potentiostatic polarization test.
  • the A1070 specimens exhibit an average corrosion depth of 139.14 ⁇ m, and a standard deviation of 98.63 ⁇ m.
  • the A3003 specimens exhibit an average corrosion depth of 94.49 ⁇ m, and a standard deviation of 50.07 ⁇ m.
  • the present specimens made of the aluminum alloy of one embodiment of the present disclosure exhibit an average corrosion depth of 40.68 ⁇ m, and a standard deviation of 14.4 ⁇ m.
  • the present specimens made of the aluminum alloy of one embodiment of the present disclosure exhibit about 3.5 times corrosion resistance improvement compared to the A1070 specimens.
  • the present specimens made of the aluminum alloy of one embodiment of the present disclosure exhibit an overall lowered corrosion depth deviation which means that a uniform corrosion occurs, leading to enhanced penetration resistance.
  • the present specimens made of the aluminum alloy of one embodiment of the present disclosure exhibit a good extrusion rate of about 90 m/min. This rate may be substantially equal to an extrusion rate of the previous A1070, and may be higher than an extrusion rate of the previous A3003 which is about 60-70 m/min. That is, the present specimens made of the aluminum alloy of one embodiment of the present disclosure may have a superior extrusion rate compared to the previous A3003.
  • the aluminum alloy of one embodiment of the present disclosure may be employed for not only an extruded tube but also for a fin in a heat exchanger.
  • FIG. 7 illustrates an aluminum heat exchanger in accordance with one embodiment of the present disclosure.
  • the heat exchanger comprising those extruded tube and fin may be classified into a stack type, a tube type, draw-on cap type, etc. in terms of a structure.
  • the tube type heat exchanger may increase heat dissipation via a fin internally attached thereto or a pipe having multiple holes formed therein.
  • the heat exchanger may be manufactured by provisionally assembling the extruded tube with a fin, a plate and a side tank, etc. and fixing one another via a clamp, and applying a flux treatment to the fixed structure, and passing the structure through a brazing furnace.
  • the aluminum alloy of the present disclosure for the heat exchanger has greatly enhanced corrosion resistance, and, thus, the heat exchanger made of the alloy has enhanced penetration resistance, leading to a prolonged life span and improved performance.

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KR20240044900A (ko) 2022-09-29 2024-04-05 엘지전자 주식회사 열교환기
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US10465265B2 (en) 2019-11-05
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US20160237528A1 (en) 2016-08-18
CN105579601A (zh) 2016-05-11
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CN105637107B (zh) 2017-08-25
KR101586152B1 (ko) 2016-01-15

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