EP0282421B1 - Zugspannungsbeständiges Lithium enthaltendes Aluminiumlegierungs-Erzeugnis und Verfahren zu seiner Herstellung - Google Patents

Zugspannungsbeständiges Lithium enthaltendes Aluminiumlegierungs-Erzeugnis und Verfahren zu seiner Herstellung Download PDF

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EP0282421B1
EP0282421B1 EP88420046A EP88420046A EP0282421B1 EP 0282421 B1 EP0282421 B1 EP 0282421B1 EP 88420046 A EP88420046 A EP 88420046A EP 88420046 A EP88420046 A EP 88420046A EP 0282421 B1 EP0282421 B1 EP 0282421B1
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product according
hot
temperature
alloy
dissolving
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EP0282421A2 (de
EP0282421A3 (en
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Bruno Dubost
Philippe Meyer
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Constellium Issoire SAS
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Pechiney Rhenalu SAS
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/057—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 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
    • 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
    • C22F1/053—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 zinc as the next major constituent

Definitions

  • the present invention relates to an Al alloy product containing lithium with high specific mechanical resistance and high damage tolerance, particularly resistant to corrosion under tension in the treated (quenched-tempered) state, in particular in the recrystallized state, and a process for obtaining such a product.
  • Aluminum-lithium alloys which also exhibit excellent mechanical strength, toughness, ductility or fatigue properties (see Ph. MEYER, B. DUBOST - Al.Li Alloys III - Proceedings of the Third International Conference Sponsored by the Institute of Metals. Oxford July 8-11, 1985 - Baker Gregson Harris Peel London- 1986) are likely to exhibit corrosion resistance under insufficient stress, even in the rolling plane of thin sheets, when they are recrystallized.
  • the products according to the invention have a particular microstructure comprising, either in addition to the solid solution, numerous and fairly coarse precipitates of intermetallic phases rich in elements Al, Cu, Li, Mg and possibly Zn, or a solid solution obtained by dissolving at low temperature.
  • the invention applies to all aluminum-based alloys containing lithium, produced by molding, rapid solidification, ingot metallurgy or other production technique. It applies in particular to alloys based on Al, the main elements of which are as follows (by weight%): Li: 1.0 to 4.2% Cu: 0 to 5.5% Mg: 0 to 7.0% Zn: 0 to 15.0% with the following minor elements: Zr: 0 to 0.2 Mn: 0 to 1 Cr: 0 to 0.3 Nb: 0 to 0.2 Ni: 0 to 0.5 Fe: 0 to 0.5 If: 0 to 0.5 Other items: ⁇ 0.05 each Rest Al.
  • the products according to the invention preferably contain (by weight%) from 1.7 to 2.5 Li - 0.8 to 3% Mg - 1.0 to 3.5% Cu - up to 2% Zn, the rest consisting of Al, secondary elements such as Zr (0 to 0.20%), Mn, Cr, Ti and impurities whose total amount is less than or equal to 1% and are treated specifically.
  • the chemical composition by weight of the 2091 alloy is as follows: If ⁇ 0.20%; Fe ⁇ 0.30%; Li: 1.7-2.3%; Cu: 1.8-2.5%; Mn ⁇ 0.10; Mg: 1.1 - 1.9%; Cr ⁇ 0.10%; Zn ⁇ 0.25%; Zr: 0.04 -0.16% Ti ⁇ 0.10%; others: each ⁇ 0.05%, total ⁇ 0.15%, Al: remainder.
  • volume fraction of these particles increases with the overall content of Li, Cu, Mg and Zn and is higher the lower the solution temperature, according to the invention.
  • This volume fraction must generally be greater than 0.6% and preferably between 1 and 4%, especially in alloy 2091. Below 0.6% the resistance to corrosion under stress may be insufficient on recrystallized products. ; above 4%, the mechanical characteristics of resistance and ductility become too weak.
  • thermogram obtained evolves substantially like the baseline of the differential enthalpy analysis device (determined with 2 identical inert samples or without sample no reference), the longer the lower the solution temperature.
  • the temperature at the start of this plateau coincides in practice with the solution temperature according to the invention or annealing, if the alloy is not dissolved, this in the case where the Differential Enthalpy Analysis is performed after these thermal operations. Tempering does not significantly change the thermogram in this high temperature range. This method allows you to find with certainty the solution solution temperature, even annealing, practiced. It thus gives, on a product treated in the final state (dissolved, possibly soaked and hardened), the physical signature of the treatment according to the invention.
  • the method according to claim 1 of the invention consists of dissolution carried out in a range of temperatures T MS lower than the usual dissolution temperature which the person skilled in the art considers to be the highest. possible to obtain the maximum mechanical resistance, due to the increased dissolution of the hardening elements.
  • the dissolution time can be the same as that usually practiced at high temperature on aluminum-lithium alloys according to the prior art, generally from 10 min to 7 hours depending on the products (thin sheet to thick forged).
  • Dissolution is followed by quenching carried out under the usual conditions.
  • the income treatment is not modified compared to the usual practices for aluminum alloys containing lithium.
  • the dissolution is preferably preceded during the manufacturing range of a possible hot keeping (with or without plastic deformation).
  • This hot keeping is preferably practiced in a temperature range between 490 and 250 ° C, more particularly between 450 ° C and 350 ° C, for a time between 1 h and 48 hours, preferably between 6 h and 24 hours.
  • the maximum temperature of this hot keeping must be less than or equal to that of the subsequent dissolution.
  • This keeping hot may possibly be multi-level, provided that the last level is carried out according to the invention. It is preferably applied after the hot deformation phase for wrought alloys. It can possibly be followed by a cold deformation.
  • the alloy is cold deformed and if this deformation requires intermediate annealing, the last of them will be carried out under the conditions defined above.
  • the cooling rate after keeping hot must be greater than 10 ° C / hour and preferably greater than 25 ° C / h. This speed is the average speed between the temperature for keeping hot and 100 ° C., the cooling speed below 100 ° C. being not critical.
  • the cooling can be carried out in an oven, under a draft, in calm air, in water, or by any other technique allowing the desired cooling rates to be obtained.
  • the hot keeping is carried out at too high a temperature, the resistance to corrosion under tension is greatly reduced. If the hot keeping is carried out at too low a temperature, this results in difficulties for the subsequent cold deformation or even a reduction in the resistance to corrosion under stress.
  • the microstructures obtained are given in FIG. 1 with regard to the dissolution at 530 ° C. and in FIGS. 2 and 3 with regard to the dissolution at 500 ° C.
  • thermogram we see that the temperature of the start of the detectable pseudo-level (I) - substantially straight part very slightly endothermic compared to the baseline of the device determined beforehand - corresponds, with the accuracy of the measurement and determining the phase transformation temperatures by intersection of the tangents to the thermogram, to the effective solution temperature according to the invention, and this better than 3 ° C.
  • narrow peak (II) of beginning fusion of the eutectic constituents which begins around 535 ° C and ends just before the equilibrium fusion of the alloy (solidus). The latter is marked by a very deep and progressive picendotherm (III).
  • the starting melting peak (endothermic) appears, after thermal analysis, much deeper in the alloys treated according to the invention, than in the alloy treated at 530 ° C according to the conventional solution treatment.
  • Example 1 The combination of this differential thermal analysis method and the metallographic analysis of Example 1 therefore make it possible to characterize in a reliable and new way the products produced according to the invention which is the subject of the main patent.
  • a 2091 alloy with a composition by weight: 1.95% Li - 2.10% Cu - 1.5% Mg - 0.08% Zr - 0.04% Fe - 0.04% Si - aluminum residue is cast in trays 800 ⁇ 300 mm2 section, homogenized 24 hours at 527 ° C, scalped, then hot rolled between 470 and 380 ° C up to 3.6 mm thick and wound in a coil. It is then kept hot according to the invention 1 h 450 ° C. followed by 12 hours at 400 ° C (with oven cooling between the two stages). Cooling after keeping hot is carried out at a speed in the region of 35 ° C / hour to a temperature of 100 ° C. After keeping hot, the sheets are cold rolled to 1.6 mm.
  • FIG. 5 confirm the good level of the fatigue properties of the alloy treated according to the invention, which are superior to those of the reference alloy: 2024.
  • the two types of sheet are then cold rolled up to 1.6 mm.
  • a 2091 alloy of composition (by weight) 2.0% Li - 1.8% Cu - 1.4% Mg - 0.12% Zr - 0.06% Fe - 0.04% Si is cast in ⁇ 50 mm billets (induction heating; spinning at 430 ° C). This bar is machined to lengths of 500 mm; these lengths were reheated and stamped in several passes between 490 and 400 ° C. Before the last stamping pass, the parts are kept hot according to the invention for 6 hours at 450 ° C. and deformed at this temperature. They then undergo cooling, the speed of which is greater than 100 ° C./h up to 100 ° C. according to the invention.
  • An alloy of composition (by weight): 2.5% Li - 1.2% Cu - 1.0% Mg 0.06% Zr - 1.5% Zn - 0.06% Fe - 0.04% Si is poured into a 300 ⁇ 100 mm2 section plate, homogenized for 24 hours at 535 ° C (with rise in homogenization temperature at 25 ° C / h from 500 ° C). It is then scalped, reheated to 490 ° C, hot rolled between 480 and 300 ° C up to 3.6 mm. The raw hot rolling product thus obtained is then kept hot for 1 hour at 450 ° C., cooled by quenching in cold water and cold rolled from 3.6 to 1.2 mm.

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  • Chemical & Material Sciences (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Heat Treatment Of Articles (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)
  • Resistance Welding (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Chemically Coating (AREA)

Claims (15)

1. Verfahren zur Herstellung von (nach Gewicht) 1 bis 4,2% Li, bis zu 5,5% Cu, bis zu 7% Mg, bis zu 15% Zn, bis zu 0,2% Zr, bis zu 1% Mn, bis zu 0,3% Cr, bis zu 0,2% Nb, bis zu 0,5% Ni, bis zu 0,5% Fe, bis zu 0,5% Si, andere Elemente: jedes bis zu 0,05%, Rest Al enthaltenden Aluminiumlegierungen, das es ermöglicht, sie gegen Spannungskorrosion unempfindlich zu machen, und wenigstens die Warmformgebung eines gegossenen oder gekneteten Erzeugnisses, eine eventuelle Kaltverformung, ein Lösungsglühen, ein Abschrecken, ein eventuelles gesteuertes Verformen und ein Anlassen umfaßt, dadurch gekennzeichnet, daß das Lösungsglühen in einem Temperaturbereich zwischen 460 °C und TM (°C) = 474 + 18,2 (%Li) - 2(%Cu) (%Cu-1,7) + (%Mg) (-17,6 + 3,6 (%Li) + 4,3 (%Cu)) - 3 (%Zn) durchgeführt wird.
2. Verfahren nach dem Anspruch 1, dadurch gekennzeichnet, daß dem Lösungsglühen in einer vorausgehenden Stufe der Herstellung ein Warmhalten vorgeschaltet wird, das zwischen 250 und 490 °C mit oder ohne gleichzeitige(r) plastische(r) Verformung mit einer mittleren Abkühlungsgeschwindigkeit nach dem Warmhalten und bis 100 °C von über 10 °C/h und vorzugsweise 25 °C/h durchgeführt wird.
3. Verfahren nach dem Anspruch 2, dadurch gekennzeichnet, daß das Warmhalten zwischen 450 und 350 °C durchgeführt wird
4. Verfahren nach einem der Ansprüche 2 oder 3, dadurch gekennzeichnet, daß die Dauer des Warmhaltens im Bereich von 1 bis 48 Stunden und vorzugsweise von 6 bis 24 h liegt.
5. Verfahren nach einem der Ansprüche 2 bis 4, dadurch gekennzeichnet, daß die Temperatur des Warmhaltens unter oder gleich der des Lösungsglühens ist.
6. Nach einem der Ansprüche 1 bis 5 erhaltenes Erzeugnis, dadurch gekennzeichnet, daß die durch Enthalpiedifferentialanalyse erhaltenen Thermogramme eine Pseudostufe aufweisen, die das effektive Lösungsglühen des Erzeugnisses beginnt, welches unter oder gleich:
TM (°C) = 474 + 18,2% Li - 2% Cu (% Cu - 1,7) + % Mg (3,6% Li + 4,3% Cu - 17,6) - 3% Zn ist und bei der Schmelzbeginntemperatur der Legierung endet.
7. Erzeugnis nach Anspruch 6, dadurch gekennzeichnet, daß auf die in den Thermogrammen sichtbare Pseudostufe ein enger Schmelzbeginnpeak zwischen 532 und 550 °C folgt.
8. Erzeugnis nach einem der Ansprüche 6 oder 7, dadurch gekennzeichnet, daß die Zusammensetzung der Ungleichung % Zn 30 + % Mg 18 + % Li 4,2 + % Cu 7 < 1
Figure imgb0010
 entspricht.
9. Nach einem der Ansprüche 1 bis 5 erhaltenes Erzeugnis, das (als Gewichts%) : 1,7 bis 2,5% Li - 0,8 bis 3,0% Mg1,0 bis 3,5% Cu - bis zu 2% Zn - 0 bis 0,2% Zr und insgesamt 1% andere Elemente, Rest Al enthält und das ungelöste, an Elementen Al, Li, Cu, Mg und ggf. Zn reiche intermetallische Phasen in Form von groben Teilchen enthält, derein Volumenanteil fv (in %) etwa gleich:
Figure imgb0011
 und 2,0 ≦K≦ 4,0 ist.
10. Erzeugnis nach dem Anspruch 9, dadurch gekennzeichnet, daß die Abmessung der gröbsten Teilchen 5 µm übersteigt.
11. Erzeugnis nach einem der Ansprüche 9 oder 10, dadurch gekennzeichnet, daß die Abmessung der gröbsten Teilchen 10 µm übersteigt.
12. Erzeugnis nach einem der Ansprüche 9 bis 11, dadurch gekennzeichnet, daß die ungelösten Teilchen aus an Elementen Al, Cu, Li, Mg reicher Phase R oder Phase T2 bestehen und daß ihr Volumenanteil über 0,6 % ist.
13. Erzeugnis nach einem der Ansprüche 9 bis 12, dadurch gekennzeichnet, daß der Volumenanteil der ungelösten Phasen im Bereich von 1 bis 4% ist.
14. Erzeugnis nach einem der Ansprüche 9 bis 13, dadurch gekennzeichnet, daß sein Gefüge rekristallisiert ist.
15. Erzeugnis nach einem der Ansprüche 9 bis 14, dadurch gekennzeichnet, daß seine Zusammensetzung die der Legierung 2091 ist, wie sie durch die Aluminum Association festgelegt ist.
EP88420046A 1987-02-18 1988-02-16 Zugspannungsbeständiges Lithium enthaltendes Aluminiumlegierungs-Erzeugnis und Verfahren zu seiner Herstellung Expired - Lifetime EP0282421B1 (de)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
FR8702719 1987-02-18
FR8702719A FR2610949B1 (fr) 1987-02-18 1987-02-18 Procede de desensibilisation a la corrosion sous tension des alliages d'al contenant du li
FR8801005 1988-01-20
FR888801005A FR2626009B2 (fr) 1987-02-18 1988-01-20 Produit en alliage d'al contenant du li resistant a la corrosion sous tension

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EP0282421A2 EP0282421A2 (de) 1988-09-14
EP0282421A3 EP0282421A3 (en) 1989-01-18
EP0282421B1 true EP0282421B1 (de) 1992-05-06

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US (1) US4955413A (de)
EP (1) EP0282421B1 (de)
JP (1) JPS63266037A (de)
CA (1) CA1333232C (de)
DE (1) DE3870678D1 (de)
ES (1) ES2032591T3 (de)
FR (1) FR2626009B2 (de)

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GB8926861D0 (en) * 1989-11-28 1990-01-17 Alcan Int Ltd Improvements in or relating to aluminium alloys
USD419765S (en) * 1998-10-15 2000-02-01 Tim Rodgers Arrow fletching protective cover
US7472797B2 (en) 2004-07-28 2009-01-06 Capitol Vial Inc. Container for collecting and storing breast milk
EP2829623B1 (de) 2007-12-04 2018-02-07 Arconic Inc. Verbesserte Aluminium-Kupfer-Lithium-Legierungen
CN103173700B (zh) * 2013-03-15 2016-01-06 中国航空工业集团公司北京航空材料研究院 Al-Cu-Li-X铝锂合金表面脱锂层的制备方法
CN107012374A (zh) * 2017-04-07 2017-08-04 安徽省宁国市万得福汽车零部件有限公司 一种耐磨铝合金衬套材料及其制备方法
US20190233921A1 (en) * 2018-02-01 2019-08-01 Kaiser Aluminum Fabricated Products, Llc Low Cost, Low Density, Substantially Ag-Free and Zn-Free Aluminum-Lithium Plate Alloy for Aerospace Application
CN111690886B (zh) * 2020-05-15 2021-06-29 江苏理工学院 一种提高高锌含量的Al-Zn合金综合力学性能的处理方法
CN112908953B (zh) * 2021-02-03 2022-11-01 百色市彩虹铝业有限公司 一种5g基站芯片散热板及制作方法

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0158769A1 (de) * 1984-02-29 1985-10-23 Allied Corporation Aluminiumlegierung mit niedriger Dichte

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Publication number Priority date Publication date Assignee Title
US4526630A (en) * 1982-03-31 1985-07-02 Alcan International Limited Heat treatment of aluminium alloys
DE3411760A1 (de) * 1983-03-31 1984-10-04 Alcan International Ltd., Montreal, Quebec Verfahren zur herstellung von blech oder band aus einem walzbarren einer aluminiumlegierung
US4640087A (en) * 1983-07-26 1987-02-03 Giorgio Targa Rope-making machine
FR2561264B1 (fr) * 1984-03-15 1986-06-27 Cegedur Procede d'obtention de produits en alliages al-li-mg-cu a ductilite et isotropie elevees
FR2561260B1 (fr) * 1984-03-15 1992-07-17 Cegedur Alliages al-cu-li-mg a tres haute resistance mecanique specifique
US4797165A (en) * 1984-03-29 1989-01-10 Aluminum Company Of America Aluminum-lithium alloys having improved corrosion resistance and method
US4648913A (en) * 1984-03-29 1987-03-10 Aluminum Company Of America Aluminum-lithium alloys and method
JPS61133358A (ja) * 1984-11-30 1986-06-20 Inoue Japax Res Inc 高強度、高張力アルミニウム合金
JPS61166938A (ja) * 1985-01-16 1986-07-28 Kobe Steel Ltd 展伸用Ａｌ−Ｌｉ系合金およびその製造方法
FR2584095A1 (fr) * 1985-06-28 1987-01-02 Cegedur Alliages d'al a hautes teneurs en li et si et un procede de fabrication

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0158769A1 (de) * 1984-02-29 1985-10-23 Allied Corporation Aluminiumlegierung mit niedriger Dichte

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FR2626009A2 (fr) 1989-07-21
DE3870678D1 (de) 1992-06-11
CA1333232C (fr) 1994-11-29
EP0282421A2 (de) 1988-09-14
EP0282421A3 (en) 1989-01-18
FR2626009B2 (fr) 1992-05-29
ES2032591T3 (es) 1993-02-16
JPS63266037A (ja) 1988-11-02
US4955413A (en) 1990-09-11

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