EP1730320B1 - Herstellungsverfahren eines aluminiumlegierungsbandes oder -bleches für wärmetauscher - Google Patents

Herstellungsverfahren eines aluminiumlegierungsbandes oder -bleches für wärmetauscher Download PDF

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Publication number
EP1730320B1
EP1730320B1 EP05716483A EP05716483A EP1730320B1 EP 1730320 B1 EP1730320 B1 EP 1730320B1 EP 05716483 A EP05716483 A EP 05716483A EP 05716483 A EP05716483 A EP 05716483A EP 1730320 B1 EP1730320 B1 EP 1730320B1
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EP
European Patent Office
Prior art keywords
aluminium
strip
alloy
heat exchangers
producing
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EP05716483A
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German (de)
English (en)
French (fr)
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EP1730320A1 (de
Inventor
Raimund Sicking
Pascal Wagner
Manfred Mrotzek
Thomas Husse
Gerhard Berming
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Hydro Aluminium Deutschland GmbH
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Hydro Aluminium Deutschland GmbH
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Application filed by Hydro Aluminium Deutschland GmbH filed Critical Hydro Aluminium Deutschland GmbH
Priority to PL05716483T priority Critical patent/PL1730320T3/pl
Publication of EP1730320A1 publication Critical patent/EP1730320A1/de
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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
    • 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
    • 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 invention relates to a method for producing an aluminum strip or sheet for heat exchangers.
  • heat exchangers consisting of aluminum or aluminum alloys are increasingly used.
  • the heat exchangers made of aluminum or an aluminum alloy are nowadays usually used in the motor vehicle for cooling the cooling water, oil, as a charge air cooler and in air conditioning systems.
  • Automotive heat exchangers are commonly made from aluminum strips or sheets in which the individual prefabricated components of the heat exchanger, such as fins, pipes and manifolds, are joined together by brazing.
  • the cold-hardenable aluminum alloys hitherto used in the vacuum brazing of heat exchangers for example the aluminum alloy AA6063 (AlMgO, 7Si), AA6061 (AlMg1SiCu) or AA6951 (AlMg0, 6SiCu) have relatively high magnesium contents and are generally treated with high Mg-containing solders, such as AA4004, for example.
  • inert gas soldering allows up to 20% shorter soldering cycles, but the use of high magnesium content aluminum alloy, known as vacuum brazing, is not possible because magnesium reacts with the non-corrosive flux during brazing. The processability can be extended by using expensive cesium-containing fluxes up to higher Mg contents.
  • Protective gas soldering also known as CAB brazing, is the most important process for the production of heat exchangers for the automotive industry.
  • the salt bath soldering is still available, in which the components are preheated and then immersed in a salt bath. The salt bath is at the same time flux and transport medium for the heat. The liquid salt reacts with the oxide skin and allows the wetting reaction of the solder protected by the flux.
  • the heat exchangers After the holding time to soldering temperature, the heat exchangers are moved out of the salt bath, whereby the flow of the liquid salt must be ensured. Since the fluxes are generally hygroscopic in salt bath soldering and contain chlorides, all heat exchangers must be cleaned after salt bath soldering in a multi-stage process in order to avoid corrosion problems. To a melting of the aluminum core alloy, the aluminum alloy should have a solidus temperature of at least 620 ° C.
  • Aluminum alloy sheets for heat exchangers or for highly corrosive environments and their production processes are known from JP 07286250 , of the JP 02129333 , of the JP 04263033 and from the EP 0 718 072 A1 known.
  • the object of the present invention is to provide a method for producing an aluminum alloy strip or sheet which, with good recyclability, has a solidus temperature of at least 620 ° C. and at the same time an improved heat resistance after soldering.
  • the above-derived object is achieved by a method having the features of claim 1.
  • the aluminum alloy used has the following alloy constituents in% by weight: 0, 3% ⁇ Si ⁇ 1%, Fe ⁇ 0.5%, 0.3% ⁇ Cu ⁇ 0.7%, 1.1% Mn ⁇ 1, 8%, 0.15% ⁇ Mg ⁇ 0.6%, 0.01% ⁇ Cr ⁇ 0.3%, To ⁇ 0, 1%, Ti ⁇ 0.3%, unavoidable accompanying elements individually max. 0.1%, in total max. 0.15% and the balance aluminum.
  • the aluminum alloy is characterized not only by having a solidus temperature of more than 620 ° C, it also has a particularly high heat resistance after soldering.
  • the yield strength Rp0.2 after soldering the heat exchanger both at room temperature and at a test temperature of 250 ° C is more than 65 MPa.
  • heat exchanger elements produced from the aluminum alloy thus have a more than 20% higher heat resistance, in particular even at temperatures up to 265 ° C.
  • the achievable heat resistance is attributed to the fact that with the aluminum alloy a high secondary phase density is achieved by combining an increased Si-Mn and Cr content.
  • the aluminum alloy has a more positive corrosion potential of -750 mV.
  • Made of aluminum alloy elements such as pipes, tube sheets, side panels or discs of a heat exchanger allow a design of the corrosion design of the heat exchanger, so that said elements of the heat exchanger have a high corrosion resistance.
  • the aluminum alloy shows only a little cold-curing, so that the aluminum alloy tapes or sheets are not subject to storage time limitation before processing or deformation before soldering.
  • the limitation of the Fe content of the aluminum alloy to a maximum of 0.5% by weight in combination with the Cu content improves the corrosion resistance of the aluminum alloy after Soldering.
  • the near-surface layers of the core material of the aluminum alloy deplete of copper, so that a protective potential gradient is formed to the nobler core material with a higher Cu content.
  • This behavior of the aluminum alloy during soldering is promoted by the low iron content.
  • the heat resistance of the aluminum alloy decreases significantly at a Cu content of less than 0.3 wt .-%, on exceeding the upper limit of the Cu content, however, the aluminum alloy tends to cracking hot during casting.
  • corrosion and soldering problems also arise at higher Cu contents, because the near-surface layers of the core material, despite depletion, have a relatively high Cu content.
  • the Mn content of the aluminum alloy determines the size of the precipitates.
  • the Mn content also has an influence on the heat resistance. If the lower limit of 1.1 wt .-% of manganese in the aluminum alloy is exceeded, the heat resistance of the aluminum alloy is reduced. An increase in the manganese content above the upper limit of 1.8 wt .-%, however, leads to coarse precipitates in the structure, which adversely affect the overall forming capacity of the aluminum alloy.
  • the strength of the aluminum alloy after brazing is additionally influenced by the Mg content. A reduction of the Mg content below 0.15% results in a lack of strength of the aluminum alloy.
  • the upper limit of the Mg content to 0.6 wt .-% ensures that the aluminum alloy with all three common soldering processes, the vacuum, CAB and Salzbadlötvon, is solderable.
  • the Cr content of the aluminum alloy of at least 0.01% by weight ensures that the aluminum alloy has sufficient heat resistance.
  • the formability of the aluminum alloy is ensured by restricting the Cr content to a maximum of 0.3 wt%, because in case of exceeding, coarse precipitates are found in the crystal structure of the aluminum alloy.
  • the Zn content of the aluminum alloy is limited to a maximum of 0.1 wt .-%.
  • a higher Zn content lowers the corrosion potential of the aluminum alloy, so that the aluminum alloy is, for example, too baseless with respect to Zn-free lamellae.
  • Ti content at most 0.3% by weight, it is ensured that no coarse precipitates are formed in the aluminum alloy, which in turn adversely affect the forming capability of the aluminum alloy.
  • the aluminum alloy according to a next further developed embodiment has the following proportions by weight of alloying constituents: 0.15% ⁇ Mg ⁇ 0.3% To ⁇ 0.05% 0.01% ⁇ Ti ⁇ 0.3%, Can the aluminum alloy without expensive cesium-containing flux after the CAB soldering process can be processed, at the same time by the Ti content reduces the risk of cracks during solidification of the rolling ingot and the reduced Zn content, the corrosion potential is increased.
  • the inventive method for producing an aluminum strip or sheet for heat exchangers is characterized in that a roll ingot is cast from a heat-resistant aluminum alloy described above in a continuous casting process, the ingot is preheated before hot rolling at 400 to 500 ° C, the ingot to a hot strip rolling, wherein the hot strip temperature is 250 to 380 ° C, the hot strip is rolled to a hot strip thickness of 3 to 10 mm at the end of the hot rolling and the hot strip is cold rolled to final thickness.
  • a roll ingot is cast from a heat-resistant aluminum alloy described above in a continuous casting process, the ingot is preheated before hot rolling at 400 to 500 ° C, the ingot to a hot strip rolling, wherein the hot strip temperature is 250 to 380 ° C, the hot strip is rolled to a hot strip thickness of 3 to 10 mm at the end of the hot rolling and the hot strip is cold rolled to final thickness.
  • the rolling bar can be homogenized before preheating. Due to the transformations that are necessary for the production of a tube plate, side part or a disc of a heat exchanger, the aluminum strip should have a maximum forming capacity before processing to one of the latter elements of a heat exchanger. This is ensured by the homogenization before the preheating of the rolling ingot. If the aluminum strip does not have to be subjected to strong forming prior to brazing, as for example in the production of tubes, homogenization prior to preheating can be dispensed with.
  • the yield strength Rp0.2 of the aluminum strip decreases.
  • the yield strength Rp0.2 is still more than 50 MPa, especially at test temperatures of 250 ° C, so that yield points are achieved, which are far higher than those of the standard alloy AA 3003.
  • the Umformites the aluminum strip can be further increased by the hot strip is annealed at a temperature of 300 to 450 ° C.
  • the hot strip is annealed at a temperature of 300 to 450 ° C.
  • solidifications which have arisen in the aluminum strip due to deformation are largely broken down again.
  • the aforementioned process steps ensure maximum formability during cold rolling of the aluminum strip or sheet.
  • the final state of the aluminum strip is, according to a further developed embodiment of the method, adjusted by the fact that after the cold rolling, a state annealing to the final state at a temperature of 250 to 400 ° C. If the aluminum strip is used for the production of tubesheets, side panels or discs of a heat exchanger, soft annealing takes place after cold rolling. If pipes are produced from the aluminum strip, which does not require strong transformations, the aluminum strip is merely back-annealed after cold rolling.
  • the method according to the invention is after the preheating of the rolling bars on one or two sides provided with boards made of another alloy.
  • other non-solder alloy circuit boards may be mounted on the aluminum cored bars, such as anticorrosion plating.
  • an aluminum soldering board is used, during hot rolling, the aluminum brazing layer is cold-welded to the core ingot so that the aluminum strip has a uniform cladding layer of an aluminum braze.
  • the inventive method for producing an aluminum strip be improved in that as aluminum solder an aluminum alloy with 6 to 13% Si, in particular an AlSi7.5 or AlSi10 alloy is used. Due to the high Si content of the solder, the silicon diffuses from the solder into the core of the aluminum strip and leads there to form a precipitation seam of AlMnSi phases, which have a negative corrosion potential compared to the core alloy. In a corrosive attack on an aluminum strip produced by the process according to the invention, the corrosion therefore develops along the length of the aluminum strip or along the Ausscheidungssaumes.
  • the core of the aluminum strip remains corrosion-free and a perforation, for example of a tube made of a corresponding aluminum alloy, can thus be avoided.
  • heat exchangers can be produced with reduced wall thickness, which nevertheless meet the increased future operating requirements.
  • the aluminum strip or sheet is a pipe band, a tube bottom band, a side band or a belt band for producing a heat exchanger.
  • a pipe tape according to the invention tube bottom band, side band or disc band corresponding elements of the heat exchanger, tubes, tubesheets, side panels or slices can be made, which despite the smaller wall thickness meet all other requirements, in particular with respect to the formability before soldering and the yield strength at room and operating temperature.
  • the weight of the heat exchanger can, according to an advantageous embodiment of the aluminum strip according to the invention, be reduced in that the pipe strip has a final thickness of 0.15 to 0.6 mm, preferably 0.15 to 0.4 mm, the tube bottom strip a final thickness of 0 , 8 to 2.5 mm, preferably 0.8 to 1.5 mm, the side panel tape has a final thickness of 0.8 to 1.8 mm, preferably 0.8 to 1.2 mm, or the disk tape has a final thickness of 0.3 to 1.0 mm, preferably 0.3 to 0.5 mm.
  • Fig. 1 is schematically illustrated a first embodiment of a method according to the invention for producing an aluminum strip or sheet for heat exchangers.
  • a first step shows the Fig. 1 ingot casting 1.
  • both the aluminum alloy for the core and the alloy for plating for example, an aluminum solder are cast as ingots.
  • the plating bar is usually preheated, hot rolled to the desired thickness and split lengthwise to the board.
  • the board may also be made using alternative methods, such as by separating from a rolling billet.
  • the aluminum alloy core ingot may optionally be homogenized prior to preheating, depending on the rolled product to be produced.
  • a tubular strip for heat exchangers is produced by the method according to the invention, however, it is also possible to dispense with homogenization prior to hot rolling, since the pipe strip is not subjected to any great deformation until the production of a tube for heat exchangers.
  • the boards needed for plating are placed on one or both sides of the core bar.
  • the resulting package of a core ingot, consisting of an aluminum alloy, which is provided with one or two sides with sinkers, is preheated at 400 to 500 ° C before hot rolling.
  • the package 4 is hot rolled in a reversing stand 5 or alternatively on a tandem stand 5a to a hot strip thickness of 3 to 10 mm.
  • the hot strip temperature during hot rolling is 250 to 380 ° C.
  • the strip After hot rolling, the strip is cold rolled on a cold roll 6.
  • the tape for example to achieve the forming properties, after hot rolling at a temperature of 300 ° C to 450 ° C are annealed.
  • This also applies to cold rolling, in which the intermediate annealing can also take place at a temperature of 300 ° C to 450 ° C before reaching the final thickness.
  • the finished cold-rolled aluminum strip or sheet can be subjected to a state annealing to the final state in a chamber furnace 7, depending on the required properties. A state annealing could also be done in a continuous furnace.
  • Fig. 2 shows a heat exchanger 8 in the tube-fin design in a perspective view.
  • the heat exchanger is constructed from a tube 9, a tube plate 10, side parts 11 and fins 12.
  • the side parts 11 and the tubesheet 10 are subjected to strong transformations before soldering, so that the aluminum strip provided for the side parts 11 and the tubesheet 10 should have correspondingly good forming properties.
  • the tubes 10 of a heat exchanger are usually produced by longitudinal seam welding.
  • the thickness of the processed during this process tube tape is between 0.15 mm and 0.6 mm, preferably 0.15 to 0.4 mm, depending on the design of the heat exchanger, the tube tape is soldered outside or on both sides.
  • An aluminum strip produced according to the invention for the tubesheet 10 typically has a thickness of 0.8 to 2.5 mm, preferably 0.8 to 1.5 mm, and is preferably in the Condition "soft" produced and processed.
  • the aluminum alloy is annealed after cold rolling to the final state "soft".
  • the requirements on the formability before soldering are high in the tube bottom strip, since usually a high degree of deformation is performed, which serves for sealing and fixing, for example, a water box, collector, air connection or similar components.
  • the tube bottom band is usually plated on one side, but can also be plated on both sides.
  • the tube sheet 10, as well as the tube 9, may have a different aluminum alloy than protective plating in order to be even more corrosion-resistant.
  • the side parts 11 are made and processed from an aluminum strip consisting of an aluminum alloy according to the invention having a wall thickness of 0.8 to 1.8 mm, preferably 0.8 to 1.2 mm, preferably in the "soft" state. As with the tube sheet 10, the demands on the formability of the side parts are high. This also applies to one in the FIG. 2 not shown disks of a heat exchanger, which are used in heat exchangers in sliced disk type or heat exchanger in stacking disk design.
  • the reduced iron content and increased copper content enable an "in situ formation" of a cathodic corrosion protection during the soldering process.
  • copper diffuses from the core material into the aluminum solder layer during soldering from the areas near the plating layer, so that a protective potential gradient is created towards the more noble core material.
  • silicon diffuses out of the strongly silicon-containing aluminum solder into the Core material of the aluminum strip according to the invention and leads there to a formation of a precipitation seam of AlMnSi phases.
  • the AlMnSi phases have a more negative corrosion potential compared to the core alloy.
  • the hot strength was determined by measuring the yield strength.
  • the yield strength Rp0.2 was 72 MPa at a test temperature of 250 ° C.
  • Conventional aluminum alloys have significantly lower yield strengths, especially at test temperatures of 250 ° C on.
  • the yield strengths of the typically used aluminum alloys for tubes of a heat exchanger are below 65 MPa at room temperature.
  • a conventional alloy AA3003 after brazing at a temperature of 250 ° C has only a yield strength Rp0.2 of less than 40 MPa.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • General Engineering & Computer Science (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Details Of Heat-Exchange And Heat-Transfer (AREA)
  • Laminated Bodies (AREA)
  • Coating With Molten Metal (AREA)
  • Separation By Low-Temperature Treatments (AREA)
  • Continuous Casting (AREA)
EP05716483A 2004-03-31 2005-03-31 Herstellungsverfahren eines aluminiumlegierungsbandes oder -bleches für wärmetauscher Active EP1730320B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL05716483T PL1730320T3 (pl) 2004-03-31 2005-03-31 Sposób wytwarzania taśmy lub blachy ze stopu aluminium na wymienniki ciepła

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102004016482 2004-03-31
PCT/EP2005/003398 WO2005095660A1 (de) 2004-03-31 2005-03-31 Warmfeste aluminiumlegierung für wärmetauscher

Publications (2)

Publication Number Publication Date
EP1730320A1 EP1730320A1 (de) 2006-12-13
EP1730320B1 true EP1730320B1 (de) 2011-05-11

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Country Status (13)

Country Link
US (1) US20070286763A1 (pt)
EP (1) EP1730320B1 (pt)
JP (1) JP2007530794A (pt)
KR (1) KR20060134189A (pt)
CN (1) CN100519796C (pt)
AT (1) ATE509127T1 (pt)
BR (1) BRPI0509358B1 (pt)
CA (1) CA2558108C (pt)
ES (1) ES2366442T3 (pt)
PL (1) PL1730320T3 (pt)
PT (1) PT1730320E (pt)
WO (1) WO2005095660A1 (pt)
ZA (1) ZA200607545B (pt)

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JP6481052B2 (ja) 2015-06-25 2019-03-13 ハイドロ アルミニウム ロールド プロダクツ ゲゼルシャフト ミット ベシュレンクテル ハフツングＨｙｄｒｏ Ａｌｕｍｉｎｉｕｍ Ｒｏｌｌｅｄ Ｐｒｏｄｕｃｔｓ ＧｍｂＨ 高強度かつ容易に成形可能なＡｌＭｇストリップおよび同を製造するための方法
CN105112739A (zh) * 2015-09-28 2015-12-02 亚太轻合金(南通)科技有限公司 耐腐蚀铝合金材料的制备工艺及耐腐蚀铝合金材料
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JPH04263033A (ja) * 1991-02-18 1992-09-18 Furukawa Alum Co Ltd 熱交換器用アルミニウムクラッド材
JP2990027B2 (ja) * 1994-02-24 1999-12-13 古河電気工業株式会社 熱交換器用アルミニウム合金ブレージングシートの製造方法
EP0718072B1 (en) * 1994-12-19 2003-07-09 Corus Aluminium Walzprodukte GmbH Brazing sheet
DE69531229T2 (de) * 1994-12-19 2004-06-03 Corus Aluminium Walzprodukte Gmbh Hartlotfolie
JPH09138093A (ja) * 1995-11-16 1997-05-27 Showa Alum Corp ドロンカップ型熱交換器
EP1059362B1 (en) * 1999-06-11 2009-12-30 Aleris Aluminum Koblenz GmbH Aluminium extrusion alloy
US6391129B1 (en) * 1999-06-11 2002-05-21 Corus Aluminium N.V. Aluminium extrusion alloy
JP2002346770A (ja) * 2001-05-24 2002-12-04 Hitachi Ltd アルミニウム基接合構造物
JP3788768B2 (ja) * 2002-02-08 2006-06-21 株式会社神戸製鋼所 アルミニウム合金クラッド材
JP2004010941A (ja) * 2002-06-05 2004-01-15 Mitsubishi Alum Co Ltd ボトル型飲料缶用アルミニウム合金板
JP4030006B2 (ja) * 2002-07-05 2008-01-09 住友軽金属工業株式会社 アルミニウム合金クラッド材およびその製造方法

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ES2366442T3 (es) 2011-10-20
CA2558108A1 (en) 2005-10-13
EP1730320A1 (de) 2006-12-13
ZA200607545B (en) 2008-05-28
KR20060134189A (ko) 2006-12-27
CA2558108C (en) 2014-07-08
PT1730320E (pt) 2011-08-24
JP2007530794A (ja) 2007-11-01
ATE509127T1 (de) 2011-05-15
CN100519796C (zh) 2009-07-29
BRPI0509358B1 (pt) 2014-02-11
WO2005095660A1 (de) 2005-10-13
CN1938439A (zh) 2007-03-28
BRPI0509358A (pt) 2007-09-11
US20070286763A1 (en) 2007-12-13
PL1730320T3 (pl) 2011-10-31

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