WO2012098991A1 - 押出性と耐粒界腐食性に優れた微細孔中空形材用アルミニウム合金とその製造方法 - Google Patents

押出性と耐粒界腐食性に優れた微細孔中空形材用アルミニウム合金とその製造方法 Download PDF

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WO2012098991A1
WO2012098991A1 PCT/JP2012/050504 JP2012050504W WO2012098991A1 WO 2012098991 A1 WO2012098991 A1 WO 2012098991A1 JP 2012050504 W JP2012050504 W JP 2012050504W WO 2012098991 A1 WO2012098991 A1 WO 2012098991A1
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Prior art keywords
mass
billet
aluminum alloy
corrosion resistance
intergranular corrosion
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PCT/JP2012/050504
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English (en)
French (fr)
Japanese (ja)
Inventor
茂 岡庭
小笠原　明徳
崇雄 大瀧
加藤　裕
Original Assignee
日本軽金属株式会社
オー・ケー・ビー株式会社
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Application filed by 日本軽金属株式会社, オー・ケー・ビー株式会社 filed Critical 日本軽金属株式会社
Priority to US13/980,078 priority Critical patent/US20130292012A1/en
Priority to KR1020157025606A priority patent/KR20150119400A/ko
Priority to KR1020137018055A priority patent/KR20130109198A/ko
Priority to KR1020177013823A priority patent/KR101850665B1/ko
Publication of WO2012098991A1 publication Critical patent/WO2012098991A1/ja

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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/01—Extruding metal; Impact extrusion starting from material of particular form or shape, e.g. mechanically pre-treated
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/02—Making uncoated products
    • B21C23/04—Making uncoated products by direct extrusion
    • B21C23/08—Making wire, bars, tubes
    • B21C23/085—Making tubes
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C29/00—Cooling or heating work or parts of the extrusion press; Gas treatment of work
    • B21C29/003—Cooling or heating of work
    • 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
    • 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
    • F28F1/02—Tubular elements of cross-section which is non-circular
    • F28F1/022—Tubular elements of cross-section which is non-circular with multiple channels
    • 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
    • F28F19/02—Preventing the formation of deposits or corrosion, e.g. by using filters or scrapers by using coatings, e.g. vitreous or enamel coatings
    • F28F19/06—Preventing the formation of deposits or corrosion, e.g. by using filters or scrapers by using coatings, e.g. vitreous or enamel coatings of metal
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28D—HEAT-EXCHANGE APPARATUS, NOT PROVIDED FOR IN ANOTHER SUBCLASS, IN WHICH THE HEAT-EXCHANGE MEDIA DO NOT COME INTO DIRECT CONTACT
    • F28D1/00—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators
    • F28D1/02—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid
    • F28D1/04—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid with tubular conduits
    • F28D1/053—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid with tubular conduits the conduits being straight
    • F28D1/0535—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid with tubular conduits the conduits being straight the conduits having a non-circular cross-section
    • F28D1/05366—Assemblies of conduits connected to common headers, e.g. core type radiators
    • F28D1/05383—Assemblies of conduits connected to common headers, e.g. core type radiators with multiple rows of conduits or with multi-channel conduits
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F2255/00—Heat exchanger elements made of materials having special features or resulting from particular manufacturing processes
    • F28F2255/16—Heat exchanger elements made of materials having special features or resulting from particular manufacturing processes extruded

Definitions

  • the present invention provides an aluminum alloy having excellent extrudability and intergranular corrosion resistance, and the effects of its alloy components, which are used for extruded microporous hollow flat tubes constituting aluminum heat exchangers such as condensers, evaporators, intercoolers and the like. It is related with the manufacturing method for taking out.
  • an aluminum heat exchanger is, for example, in a car air conditioner condenser as shown in FIG. 1, a conduit (flat tube) through which a refrigerant flows (see FIG. 2A), a corrugated fin that exchanges heat with air, and a tank It is composed of a header pipe and an entrance / exit member, which are parts, and has means for brazing to any of the members that are in contact with each other, and is brazed using a non-corrosive flux (see FIG. 2B).
  • the sacrificial anticorrosive effect combined with Zn metal also causes a problem that the Zn diffusion layer portion including the joint portion with the fins is consumed at an early stage and the heat exchanger performance is deteriorated.
  • Patent Documents 1 and 2 propose aluminum alloys with improved extrudability and corrosion resistance. It is based on pure aluminum, and positively added Cu and Fe elements to improve extrudability.
  • Patent Documents 1 and 2 have certainly improved extrudability, they are insufficient from the viewpoint of corrosion resistance.
  • a sacrificial anticorrosion method is generally employed as a means for preventing corrosion of the flat tube of the heat exchanger.
  • the aluminum alloys proposed in Patent Documents 1 and 2 can be said to be a noble alloy with a natural potential of about ⁇ 0.7 V vs. SCE in terms of potential. Therefore, there is no problem in use at a site where a sacrificial anticorrosion method is adopted. .
  • the alloy may promote corrosion of the crystal grain boundary. That is, the flat tube itself may be corroded at a portion of the heat exchanger where the Zn diffusion layer mitigation measures and the sacrificial corrosion prevention method are not formed.
  • the present invention has been devised in order to solve such a problem, and as an aluminum alloy for a microporous hollow material, suppresses the content of Cu having a problem of intergranular corrosion resistance, and provides a natural potential. It is an object of the present invention to provide an aluminum alloy that is capable of maintaining a high preciousness and is excellent in extrudability.
  • the aluminum alloy for microporous hollow parts having excellent extrudability and intergranular corrosion resistance is provided with Fe: 0.05 to 0.15% by mass, Si: 0.10% by mass or less, Cu: 0.03 -0.07% by mass, Mn: 0.30-0.55% by mass, Cr: 0.03-0.06% by mass, Ti: 0.08-0.12% by mass, with the remainder having a chemical composition consisting of Al and inevitable impurities And
  • V 0.08% by mass or less may be contained in a relationship of Ti + V: 0.08 to 0.2% by mass.
  • the aluminum alloy for hollow fine hollow shape materials was heated to 550 to 590 ° C. at a rate of 80 ° C./hour or less and held for 0.5 to 6 hours with the DC casting billet of the aluminum alloy having the above chemical composition. Thereafter, it is maintained in the range of 450 to 350 ° C. for 0.5 to 1 hour, or it is obtained by applying a soaking treatment that cools to 200 ° C. or less at a cooling rate of 50 ° C./hour.
  • the billet that has been subjected to the above homogenization treatment is reheated to 450 to 550 ° C and then extruded into a desired shape with a processing ratio of 30 to 1000 in an extrusion ratio, thereby producing an aluminum alloy having excellent intergranular corrosion resistance.
  • a microporous hollow material is obtained.
  • the aluminum alloy for fine-hole hollow materials with excellent extrudability and intergranular corrosion resistance of the present invention is basically based on pure aluminum, and the content of Fe, Cu, Mn, and Cr is kept low. Therefore, the extrudability is good. Although it is suppressed to a low level, it contains the required amounts of Fe, Cu, Mn, Cr, etc., and therefore has strength and corrosion resistance for the microporous hollow material constituting the heat exchanger.
  • the Cu content of the alloy of the present invention is suppressed to 0.07 mass% or less, the formation of Al—Cu intermetallic compounds is suppressed, and the possibility of intergranular corrosion is extremely reduced.
  • the dispersion of Ti element at the grain boundaries or matrix (matrix) suppresses the progress of intergranular corrosion and improves the corrosion resistance.
  • FIG. 1 illustrates a schematic structure of a general condenser for a car air conditioner.
  • FIG. 2 illustrates a schematic structure of a flat tube and a heat exchanger incorporating the flat tube.
  • FIG. 3 illustrates the sacrificial anticorrosive action of the Zn diffusion layer.
  • FIG. 4 shows a cross-sectional shape of a hollow flat tube for a heat exchanger produced in the example.
  • FIG. 5 compares the pressure-time curves during extrusion of the homogenized billet in the example.
  • the aluminum alloy for extrusion proposed in Patent Document 2 is excellent in extrusion moldability, but the contained Cu forms an Al—Cu-based intermetallic compound at the grain boundary. It is an alloy that easily causes intergranular corrosion.
  • the present inventors have found that the above problem can be solved if the Cu content is suppressed to 0.07% by mass or less, the content of other Fe, Si, Mn, Cr, etc. is appropriately adjusted and an appropriate amount of Ti is added. . Details will be described below.
  • the aluminum alloy for a microporous hollow member having excellent extrudability and intergranular corrosion resistance according to the present invention has Fe: 0.05 to 0.15 mass%, Si: 0.10 mass% or less, Cu: 0.03 to 0.07 mass%, Mn: 0.30. Contains 0.5% by mass, Cr: 0.03 to 0.06% by mass, Ti: 0.08 to 0.12% by mass, and if necessary, V: 0.08% by mass or less in the relationship of Ti + V: 0.08 to 0.2% by mass, and the balance Has a chemical composition comprising Al and inevitable impurities.
  • Fe 0.05-0.15% Fe has the effect
  • Si 0.10% or less Si is an unavoidable impurity mixed from the Al base material, but its upper limit is set to 0.10% in order to suppress the formation of Al—Fe—Si compounds that adversely affect workability.
  • Cu 0.03-0.07%
  • Cu is an element effective for suppressing deep pitting corrosion of Al ground. The effect is recognized when the content is 0.03% or more. However, when the content is increased, an Al—Cu compound is formed at the grain boundary to promote corrosion from the grain boundary. Therefore, the Cu content is set to 0.03 to 0.07%.
  • Mn 0.30 to 0.55% Mn has the effect of improving corrosion resistance and strength, particularly high temperature strength. These actions are effectively expressed by the inclusion of 0.30% or more. Since Mn increases strength at high temperatures, it does not cause significant softening during brazing and has a great role in maintaining the rigidity of the structure. On the other hand, since the high temperature strength is high, the processing pressure at the time of extrusion becomes large and the extrudability is lowered. Further, Al—Mn intermetallic compounds are formed along the grain boundaries, which may adversely affect the intergranular corrosion resistance. Therefore, the upper limit of the Mn content is 0.55%.
  • Cr 0.03-0.06% Cr has an action of suppressing the coarsening of the extruded structure. This effect is effectively manifested when the content is 0.03% or more. However, since the extrudability deteriorates if contained in a large amount, the upper limit was made 0.06%.
  • Ti 0.08 to 0.12%, Ti refines the cast structure, and the distribution state of the Ti element has the effect of suppressing intergranular corrosion of the extruded material. This effect is effectively exhibited when the content is 0.08% or more. However, if the content is increased, a coarse intermetallic compound is produced and the extrudability is deteriorated, so the upper limit was made 0.12%.
  • V 0.08% or less
  • V compounds crystallized at the time of casting have a function of dispersing in a layer form by extrusion and preventing the progress of intergranular corrosion.
  • the upper limit was made 0.08%.
  • the aluminum alloy for fine-hole hollow shapes with excellent extrudability and intergranular corrosion resistance according to the present invention is melted by ordinary means and provided as a billet of a desired shape by a semi-continuous casting method which is a general casting method. Is done.
  • the elements constituting the intermetallic compound crystallized during casting by heating the billet after casting at a high temperature are re-dissolved in the matrix. It is necessary to perform a homogenization treatment that eliminates the concentration distribution of the additive element. As the homogenization treatment, it is preferable to perform a heat treatment at 550 to 590 ° C. for 0.5 to 6 hours.
  • the aluminum alloy of the present invention is an alloy that regulates Fe and Si on a pure Al base and adds Cu, Mn, Cr, and Ti.
  • the billet obtained by casting is not held at 550 ° C. or more for 0.5 hour or more, the Al—Fe—Si compound cannot be finely dispersed, and defects are caused when it is extruded at a high workability. Also, in order to dissolve other elements such as Cu, Cr, Mn, etc. into the Al ground or to exist as fine compounds, it is necessary to hold at 550 ° C. or higher for 0.5 hour or longer.
  • the appropriate temperature for the homogenization treatment is 570 ° C ⁇ 10 ° C. Economically, it is better to raise the temperature quickly and cool it down quickly. When the temperature rise exceeds 80 ° C / h, a large amount of Mn and Cr is dissolved, and the cast state (the presence of coarse compounds and a large amount of penetration) is kept at the proper temperature rise rate until the homogenization temperature. Coarse compounds such as Al—Fe and Al—Fe—Si are dissolved in solid solution for a sufficient diffusion time. On the other hand, the solid solution of Cr and Mn is precipitated as an Al— (Fe, Mn, Cr) —Si compound and Al—Mn compound to improve the billet structure.
  • Mn and Cr compounds are dissolved by holding at a high temperature, and it is necessary to deposit them as an appropriate compound. For that purpose, hold at a temperature of 450 to 350 ° C. for 0.5 to 1 hour. Alternatively, it is necessary to cool to 200 ° C. or less at a moderate cooling rate of 50 ° C./hour. If this condition is not met, Mn and Cr remain in solid solution in the matrix (matrix), and only a small amount precipitates during heating before extrusion in the subsequent process, resulting in high extrusion pressure and reduced workability.
  • the material obtained by extruding the billet obtained by such a homogenization process has a uniform surface and internal structure of the extruded material, and can suppress the coarsening of crystal grains due to hot working.
  • the billet obtained by casting the alloy composition of the present invention is subjected to a predetermined homogenization treatment, and the billet is heated at 450 ° C. or higher and 550 ° C. or lower in order to obtain a desired fine hollow extruded shape. It is necessary to extrude at a working degree of an extrusion ratio of 30 to 1000.
  • the extrusion ratio of the fine hollow shape material is high, so that the limit of the extrusion pressure of the extruder (usually 210 kg / cm 2 ) is exceeded, and extrusion becomes impossible. Even if extrusion is possible, defects such as peeling occur on the inner surface of the fine hollow material, and the shape and dimensions are out of tolerance.
  • extrusion can be easily performed, but the extrusion ratio and extrusion speed are high, so the shape temperature during extrusion becomes high, and mussels frequently occur on the surface and inside of the fine hollow material. Local melting occurs and the required shape cannot be maintained.
  • the extrusion ratio is so small that it is less than 30, it is difficult to obtain the Ti effect (a state in which Ti exists in a layered manner in the extrusion direction inside the profile), which is a feature of the present invention. Conversely, if the extrusion ratio exceeds 1000, it is difficult to design the mold and select the extrusion conditions, and the extrusion process itself becomes impossible.
  • Fluorocarbon refrigerant is used as the heat exchange fluid.
  • the materials used in heat exchangers are excellent in corrosion resistance, strength and brazing, and are extruded into microporous hollow materials (flat tubes) of about 0.5 to 2 mm, which are the main components of heat exchanger assemblies.
  • An alloy that can be processed is required.
  • FIG. 1 A hollow flat tube for heat exchanger having 12 holes with a width of 16.2 mm, a thickness of 1.93 mm, and a wall thickness of 0.35 mm was extruded.
  • the strength was judged from the room temperature strength of the annealed material, and based on 65 MPa of pure Al, ⁇ was over 90 MPa, ⁇ was about 60 to 90 MPa, and ⁇ was less than 60 MPa.
  • Corrosion resistance is evaluated by evaluating the presence and progress of intergranular corrosion based on microstructural observation after the corrosion test. ⁇ indicates that there is almost no intergranular corrosion, ⁇ indicates that layered corrosion is 100 ⁇ m or less, and indicates layered corrosion is 500 ⁇ m or more. Was marked with x.
  • the acceptable product that can be used as a hollow flat tube for a heat exchanger is indicated by ⁇
  • the rejected product that cannot be used is indicated by ⁇ .
  • the casting billet was heated at a homogenization temperature of 590 ° C. (heating process) at a heating rate of 80 ° C./hour or less, and further cooled at a homogenization temperature for 4 hours.
  • the range of ⁇ 350 ° C. was cooled at a cooling rate of 50 ° C./hour, and then cooled outside the furnace.
  • This billet will be referred to as a billet according to the present invention.
  • the presently treated billet shows no significant compounds other than the crystallized material of the billet before the treatment, whereas the structure of the billet of the present invention method In addition to the crystallized product, it was confirmed that precipitates (Al—Mn system) were finely dispersed.
  • FIG. 5 shows a comparison of pressure-time curves during extrusion.
  • the method of the present invention has a lower maximum pressure and a faster pressure drop than the current method. And it turns out that the area in a curve is small and the energy required at the time of extrusion is small.
  • the billet of the present invention used for verification of the homogenization conditions was heated to 480 ° C., and a flat tube having an extrusion ratio of 150 and a flat bar material having an extrusion ratio of 20 were extruded at a speed of 20 m / min. The microstructure of these two types of extruded materials was observed, and the dispersion state of the Ti compound was compared. The results are shown in Table 4.
  • the present invention it is possible to suppress the content of Cu having a problem of intergranular corrosion resistance as an aluminum alloy for a microporous hollow shape material, and to maintain a natural potential preciously and to be excellent in extrudability.
  • An aluminum alloy is provided.

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  • Chemical & Material Sciences (AREA)
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PCT/JP2012/050504 2011-01-20 2012-01-12 押出性と耐粒界腐食性に優れた微細孔中空形材用アルミニウム合金とその製造方法 WO2012098991A1 (ja)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US13/980,078 US20130292012A1 (en) 2011-01-20 2012-01-12 Aluminum alloy for small-bore hollow shape use excellent in extrudability and intergranular corrosion resistance and method of production of same
KR1020157025606A KR20150119400A (ko) 2011-01-20 2012-01-12 압출성과 내입계 부식성이 우수한 미세 구멍 중공형재용 알루미늄 합금과 그 제조 방법
KR1020137018055A KR20130109198A (ko) 2011-01-20 2012-01-12 압출성과 내입계 부식성이 우수한 미세 구멍 중공형재용 알루미늄 합금과 그 제조 방법
KR1020177013823A KR101850665B1 (ko) 2011-01-20 2012-01-12 압출성과 내입계 부식성이 우수한 미세 구멍 중공형재용 알루미늄 합금과 그 제조 방법

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JP2011-009706 2011-01-20
JP2011009706A JP5653233B2 (ja) 2011-01-20 2011-01-20 押出性と耐粒界腐食性に優れた微細孔中空形材用アルミニウム合金とその製造方法

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013150957A1 (ja) * 2012-04-05 2013-10-10 日本軽金属株式会社 押出性と耐粒界腐食性に優れた微細孔中空形材用アルミニウム合金およびその製造方法
US10557188B2 (en) 2014-03-19 2020-02-11 Rio Tinto Alcan International Limited Aluminum alloy composition and method

Families Citing this family (4)

* Cited by examiner, † Cited by third party
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JP5906113B2 (ja) 2012-03-27 2016-04-20 三菱アルミニウム株式会社 熱交換器用押出伝熱管と熱交換器および熱交換器用押出伝熱管の製造方法
ES2870139T3 (es) * 2016-04-29 2021-10-26 Rio Tinto Alcan Int Ltd Aleación resistente a la corrosión para productos extruidos y soldados con soldadura fuerte
CN114182120A (zh) * 2021-12-13 2022-03-15 桂林理工大学 一种变形铝铁合金及其制备方法
KR20240044900A (ko) * 2022-09-29 2024-04-05 엘지전자 주식회사 열교환기

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006316294A (ja) * 2005-05-10 2006-11-24 Furukawa Sky Kk 自然冷媒用熱交換器のアルミニウム合金押出しチューブ材
JP2008050657A (ja) * 2006-08-24 2008-03-06 Furukawa Sky Kk 自動車熱交換器用アルミニウム配管材
JP2008208416A (ja) * 2007-02-26 2008-09-11 Furukawa Sky Kk 自然冷媒用熱交換器に用いられるアルミニウム合金押出材
JP2008255457A (ja) * 2007-04-09 2008-10-23 Furukawa Sky Kk 熱交換器用アルミニウム合金配管材及びその製造方法

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6023A (en) * 1849-01-09 Body-brace
EP1158063A1 (en) * 2000-05-22 2001-11-28 Norsk Hydro A/S Corrosion resistant aluminium alloy
JP4837188B2 (ja) * 2000-10-02 2011-12-14 株式会社デンソー 耐食性および加工性に優れた配管用アルミニウム合金材

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006316294A (ja) * 2005-05-10 2006-11-24 Furukawa Sky Kk 自然冷媒用熱交換器のアルミニウム合金押出しチューブ材
JP2008050657A (ja) * 2006-08-24 2008-03-06 Furukawa Sky Kk 自動車熱交換器用アルミニウム配管材
JP2008208416A (ja) * 2007-02-26 2008-09-11 Furukawa Sky Kk 自然冷媒用熱交換器に用いられるアルミニウム合金押出材
JP2008255457A (ja) * 2007-04-09 2008-10-23 Furukawa Sky Kk 熱交換器用アルミニウム合金配管材及びその製造方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013150957A1 (ja) * 2012-04-05 2013-10-10 日本軽金属株式会社 押出性と耐粒界腐食性に優れた微細孔中空形材用アルミニウム合金およびその製造方法
US10309001B2 (en) 2012-04-05 2019-06-04 Nippon Light Metal Company, Ltd. Aluminum alloy for microporous hollow material which has excellent extrudability and grain boundary corrosion resistance, and method for producing same
US10557188B2 (en) 2014-03-19 2020-02-11 Rio Tinto Alcan International Limited Aluminum alloy composition and method

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