EP1435397B1 - Alliage d'aluminium à haute résistance pour des ailettes pour brasage - Google Patents

Alliage d'aluminium à haute résistance pour des ailettes pour brasage Download PDF

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Publication number
EP1435397B1
EP1435397B1 EP03078132A EP03078132A EP1435397B1 EP 1435397 B1 EP1435397 B1 EP 1435397B1 EP 03078132 A EP03078132 A EP 03078132A EP 03078132 A EP03078132 A EP 03078132A EP 1435397 B1 EP1435397 B1 EP 1435397B1
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EP
European Patent Office
Prior art keywords
alloy
brazing
aluminium
strength
subjecting
Prior art date
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Expired - Lifetime
Application number
EP03078132A
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German (de)
English (en)
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EP1435397A1 (fr
Inventor
Torkel Stenqvist
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Granges Sweden AB
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Sapa Heat Transfer AB
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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
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium 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
    • 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
    • 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
    • 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
    • C22F1/047—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 of alloys with magnesium as the next major constituent
    • 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
    • C22F1/05—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 of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Definitions

  • the present invention is related to an aluminium alloy intended as a fin-stock material for brazed products, such as heat exchangers, either as a braze clad material containing said alloy as a core or unclad.
  • the alloy is heat treatable (precipitation hardenable)
  • the material obtained has got a high strength after brazing, especially after an artificial ageing treatment, and gives a high corrosion resistance to the brazed product as it is sacrificial to the tube.
  • the material may be used to make products by any brazing method, in particular the controlled atmosphere brazing method (CAB) when a flux that allows alloys with Mg is used.
  • CAB controlled atmosphere brazing method
  • Mg may form small precipitates that increase the strength of the alloy considerably. This mechanism is called age hardening.
  • the AA6xxx series of alloys are based on the Mg and Si precipitates, but alloys in that series are generally not suitable for brazing, as most of them has a too high Mg content. Others are without Mn, reducing the sag resistance of the alloy.
  • Age hardening alloys have not yet been utilised in a fin stock material to be brazed in the CAB process.
  • a challenge today is to manufacture light-weight components for the automotive market.
  • a lot of research is therefore directed to reduce the weight of heat exchangers by using thinner strip.
  • the new invention shows a higher strength compared to the presently used alloys, while the corrosion protection of the tubes is retained. This will allow thinner fins with retained strength of the brazed product, thereby reducing the weight compared to products brazed today.
  • the higher strength can be utilised to give a more rigid brazed product that will withstand higher stresses, such as vibrations or pulsation of the internal pressure.
  • US-6120848 discloses a method for providing the flux onto the surface of a brazing sheet, by mechanically embedding the flux in the cladding. It is mentioned that CsF fluxes allows a higher Mg in the core materials.
  • a modified flux containing caesium and/or lithium fluoride, and a modified braze cladding is used to braze the standard 1000, 3000, 5000 or 6000 alloys containing up to 3 wt-% Mg by CAB (Controlled Atmosphere Brazing).
  • the braze cladding on the tube surfaces contains, apart from the main alloying element silicon, lithium, magnesium, sodium, and optionally caesium.
  • a fin material with the following composition in wt.-%) is disclosed: 0.7 - 1.2 Si (0.75 - 1.0 preferred), up to 0.8 Fe (0.2 - 0.45 preferred), up to 0.5 Cu (0.2 - 0.4 preferred), 0.7 - 1.2 Mn (0.8 - 1.0 preferred), up to 0.35 Mg (0.2 - 0.35 preferred), up to 3 Zn, up to 0.25 Zr (0.05 - 0.15 preferred), up to 0.2 In (0.01 - 0.1 preferred), up to 1.5 Ni (0.3 - 1.2 preferred), up to 0.2 Ti, and up to 0.25 of Cr and V.
  • the object of the present invention is to provide a high strength, heat treatable, aluminium alloy while keeping the Mg content sufficiently low for brazing in a CAB furnace using a flux that tolerates Mg.
  • Another object is to provide a material with a sufficient corrosion sacrificial action to protect another material brazed to the invention.
  • Preferred applications are fins for heat exchangers, like automotive radiators, heaters, or charge-air coolers. Other applications are not excluded.
  • a quench sensitive alloy must be cooled rapidly after the solutionising treatment (i.e. the brazing operation) in order to keep the Mg and Si atoms in solid solution. A high Mn content will increase the quench sensitivity.
  • the tensile strength of the standard material AA3003 is about 110 MPa and that of the state of the art FA6815 is about 135 MPa.
  • the yield strength of the standard material AA3003 is about 40 MPa and that of the state of the art FA6815 is about 50 MPa.
  • the alloy of the invention has a notably higher strength than the presently available alloys.
  • the concentration of silicon should be 0.5 - 1.0 wt-%, preferably 0.6 - 0.9 wt-%. Below 0.5 wt-% the ageing response is low, above 1.0 wt-% the solidus temperature of the alloy is significantly lowered.
  • the Mg content could therefore be as low as 0.25 wt-% and as high as 0.6 wt-%. Below the lower limit the alloy would not give a sufficient number of the Mg 2 Si precipitates, and a high strength would not be obtained. The more Mg the higher the strength, but with a too high level the brazeability will be reduced, and furthermore there is a risk for incipient melting of the material at the brazing temperature.
  • the preferred Mg level will depend on both the used flux and the used tube material.
  • Zn is added, up to 4 %.
  • Zn will increase the sacrificial action of the fin material and the level must be optimised together with the tube material.
  • zirconium preferably 0.05 - 0.25 wt-% is added to the alloy.
  • Zr is distributed as small Al 3 Zr in the material. They will inhibit the recrystallisation, giving large grains of the material after brazing. Below 0.05 wt-% this effect is negligible, above 0.3 wt-% coarse precipitates are formed which will reduce the effect and the workability of the material.
  • Mn in solid solution increases the strength, however the quench sensitivity is also increased. Thus, a low Mn content is beneficial to the strength if cooling rates are low. Furthermore, Mn is beneficial to the sagging resistance and corrosion resistance.
  • the Mn content should be 0.3 - 0.7 wt-%, preferably 0.4 - 0.7 wt-%, most preferably 0.5 - 0.7 wt-%.
  • Fe has an adverse effect on the corrosion resistance and in higher amounts on the sagging resistance. It is therefore limited to 0.3 wt-%.
  • Nickel is also avoided in the alloy. Nickel increases the risk for obtaining small grains in the product, and thereby reduce the sagging resistance.
  • the claimed material is produced by casting an aluminium alloy according to the invention, and thereafter subjecting the obtained material to a hot rolling and a cold rolling process. After said casting process the material may be scalped and clad with at least one additional layer. The material may be interannealed between two cold rolling passes, and partially or fully annealed after the final cold rolling step. The annealing step may also be omitted.
  • the 0.5 mm material was braze simulated with two different heating cycles, basically giving cooling rates of 2.5°C/s and 0.7°C/s between 400 and 200°C. This represents both an optimal cooling rate and one usually surpassed by brazing furnaces in practice.
  • Example 2 Material from the same braze simulations as in Example 1 was artificially aged at different temperatures after a delay of one day. Three temperatures were used: 160, 180, and 195°C. The tensile strength of the samples is shown in Figure 2 and the yield strength in figure 3. As can be seen, tensile strengths of 250 MPa and yield strengths surpassing 200 MPa may be obtained.
  • the material show a substantial age hardening response, and yield strengths more than three times as high as that of the standard materials in brazing of today were achieved.
  • the sagging resistance of the material was measured by mounting thin strip samples (gauge 0.1 mm) in a special jig, allowing 60 mm lever length ( Figure 4). The material in the jig was then subjected to a braze cycle with a 10 minute dwell at 600°C. The deflection is measured when the material has cooled off.
  • the mean deflection for the new invention was 27.6 mm, which may be compared to 17 to 23 mm for FA6815 and 35 to 40 mm for the standard heat treatable material AA6063.
  • the new invention shows a reasonable sagging resistance.

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Details Of Heat-Exchange And Heat-Transfer (AREA)
  • Laminated Bodies (AREA)
  • Details Of Measuring And Other Instruments (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)

Claims (14)

  1. Alliage d'aluminium pour des produits brasés ayant une force élevée, caractérisé en ce que l'alliage comporte 0,5 à 1,0 % en poids de silicium, 0,25 à 0,6 % en poids de magnésium, 0,3 à 0,7 % en poids de manganèse, et 0,05 à 0,25 % en poids de zirconium, et de manière facultative jusqu'à 4 % de Zn, le reste étant constitué d'aluminium et d'impuretés inévitables, Fe dans lesdites impuretés étant commandé à une valeur allant jusqu'à 0,3 %.
  2. Alliage d'aluminium selon la revendication 1, caractérisé en ce que la teneur en manganèse est comprise entre 0,4 et 0,7 % en poids.
  3. Alliage d'aluminium selon la revendication 1, caractérisé en ce que la teneur en manganèse est comprise entre 0,5 et 0,7 % en poids.
  4. Alliage d'aluminium selon l'une quelconque des revendications 1 à 3, caractérisé en ce que la teneur en silicium est comprise entre 0,6 et 0,9 % en poids.
  5. Matériau de gainage pour des produits brasés ayant une force élevée, caractérisé en ce que l'alliage de coeur comporte 0,5 à 1,0 % en poids de silicium, 0,25 à 0,6 % en poids de magnésium, 0,3 à 0,7 % en poids de manganèse, et 0,05 à 0,25 % en poids de zirconium et de manière facultative jusqu'à 4 % de Zn, le reste étant constitué d'aluminium et d'impuretés inévitables, Fe dans lesdites impuretés étant commandé à une valeur allant jusqu'à 0,3 %.
  6. Matériau de gainage selon la revendication 5, caractérisé en ce que la teneur en manganèse est comprise entre 0,4 et 0,7 % en poids.
  7. Matériau de gainage selon la revendication 5 ou 6, caractérisé en ce que la teneur en manganèse est comprise entre 0,5 et 0,7 % en poids.
  8. Matériau de gainage selon l'une quelconque des revendications 5 à 7, caractérisé en ce que la teneur en silicium est comprise entre 0,6 et 0,9 % en poids.
  9. Procédé pour produire un matériau à partir de l'alliage selon l'une quelconque des revendications 1 à 8, caractérisé par les étapes consistant à :
    soumettre ledit alliage à un processus de coulée,
    soumettre le matériau obtenu à un processus de roulage à chaud,
    soumettre le matériau obtenu à un processus de roulage à froid.
  10. Procédé selon la revendication 9, caractérisé en ce que, après ledit processus de coulée, le matériau est écroûté et gainé à l'aide d'au moins une couche supplémentaire.
  11. Procédé selon la revendication 9 ou 10, caractérisé en ce que, après ledit roulage à froid, le matériau est soumis à un processus de recuit.
  12. Utilisation du matériau selon l'une quelconque des revendications 1 à 8, pour produire une tôle à ailettes pour des échangeurs thermiques.
  13. Utilisation du matériau selon l'une quelconque des revendications 1 à 8, dans un processus de brasage où une atmosphère inerte est utilisée.
  14. Utilisation du matériau selon l'une quelconque des revendications 1 à 8, dans un processus de brasage utilisant une atmosphère commandée et un flux appropriée.
EP03078132A 2002-10-14 2003-10-07 Alliage d'aluminium à haute résistance pour des ailettes pour brasage Expired - Lifetime EP1435397B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE0203009A SE0203009D0 (sv) 2002-10-14 2002-10-14 High strenth aluminium fin material for brazing
SE0203009 2002-10-14

Publications (2)

Publication Number Publication Date
EP1435397A1 EP1435397A1 (fr) 2004-07-07
EP1435397B1 true EP1435397B1 (fr) 2005-09-14

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ID=20289240

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EP03078132A Expired - Lifetime EP1435397B1 (fr) 2002-10-14 2003-10-07 Alliage d'aluminium à haute résistance pour des ailettes pour brasage

Country Status (5)

Country Link
US (1) US20040118492A1 (fr)
EP (1) EP1435397B1 (fr)
AT (1) ATE304617T1 (fr)
DE (1) DE60301614T2 (fr)
SE (1) SE0203009D0 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2177638A1 (fr) 2008-10-15 2010-04-21 "Impexmetal" S.A. Alliage d'aluminium, en particulier pour la fabrication d'échangeurs thermiques

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1666620B1 (fr) * 2003-09-26 2012-01-18 Kobe Steel, Ltd. Feuille de brasage d'aluminium
CN101408757B (zh) * 2007-10-11 2010-10-13 上海梅山钢铁股份有限公司 一种热轧生产管理级图形化轧线物料跟踪的方法
DE102008056819B3 (de) * 2008-11-11 2010-04-29 F.W. Brökelmann Aluminiumwerk GmbH & Co. KG Aluminiumlegierung und Verfahren zur Herstellung eines Produkts aus einer Aluminiumlegierung
JP6247225B2 (ja) 2011-12-16 2017-12-13 ノベリス・インコーポレイテッドＮｏｖｅｌｉｓ Ｉｎｃ． アルミニウムフィン合金およびその製造方法
US9732169B2 (en) 2014-07-22 2017-08-15 University Of South Carolina Raft agents and their use in the development of polyvinylpyrrolidone grafted nanoparticles
WO2016022457A1 (fr) 2014-08-06 2016-02-11 Novelis Inc. Alliage d'aluminium pour ailettes d'échangeur de chaleur
US20210310754A1 (en) * 2018-09-24 2021-10-07 Aleris Rolled Products Germany Gmbh Aluminium alloy fin stock material

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1335309A (en) * 1970-12-21 1973-10-24 Olin Corp Heat exchanger
AU663819B2 (en) * 1993-08-03 1995-10-19 Denso Corporation A1 alloy brazing material and brazing sheet for heat-exchangers and method for fabricating A1 alloy heat-exchangers
FR2713664B1 (fr) * 1993-11-17 1996-05-24 Pechiney Rhenalu Alliage type Al-Si-Mg à ductilité et emboutissabilité améliorées et procédé d'obtention.
US5771962A (en) * 1996-04-03 1998-06-30 Ford Motor Company Manufacture of heat exchanger assembly by cab brazing
DE69805527T2 (de) * 1997-08-04 2002-11-28 Corus Aluminium Walzprod Gmbh Hochverformbare, korrosionsbeständige al-legierung
US6120848A (en) * 1998-11-17 2000-09-19 Ford Motor Company Method of making a braze sheet
US6800244B2 (en) * 1999-11-17 2004-10-05 Corus L.P. Aluminum brazing alloy
US6234243B1 (en) * 1999-12-14 2001-05-22 Visteon Global Technologies, Inc. Heat exchanger assembly with magnesium barrier

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2177638A1 (fr) 2008-10-15 2010-04-21 "Impexmetal" S.A. Alliage d'aluminium, en particulier pour la fabrication d'échangeurs thermiques

Also Published As

Publication number Publication date
ATE304617T1 (de) 2005-09-15
DE60301614D1 (de) 2005-10-20
SE0203009D0 (sv) 2002-10-14
DE60301614T2 (de) 2006-03-16
US20040118492A1 (en) 2004-06-24
EP1435397A1 (fr) 2004-07-07

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