EP0282421A2 - 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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Publication number
EP0282421A2
EP0282421A2 EP88420046A EP88420046A EP0282421A2 EP 0282421 A2 EP0282421 A2 EP 0282421A2 EP 88420046 A EP88420046 A EP 88420046A EP 88420046 A EP88420046 A EP 88420046A EP 0282421 A2 EP0282421 A2 EP 0282421A2
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EP
European Patent Office
Prior art keywords
alloy
dissolution
hot
product according
product
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP88420046A
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English (en)
French (fr)
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EP0282421A3 (en
EP0282421B1 (de
Inventor
Bruno Dubost
Philippe Meyer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Constellium Issoire SAS
Original Assignee
Cegedur Societe de Transformation de lAluminium Pechiney SA
Pechiney Rhenalu SAS
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Priority claimed from FR8702719A external-priority patent/FR2610949B1/fr
Application filed by Cegedur Societe de Transformation de lAluminium Pechiney SA, Pechiney Rhenalu SAS filed Critical Cegedur Societe de Transformation de lAluminium Pechiney SA
Publication of EP0282421A2 publication Critical patent/EP0282421A2/de
Publication of EP0282421A3 publication Critical patent/EP0282421A3/fr
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Publication of EP0282421B1 publication Critical patent/EP0282421B1/de
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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 corresponding process essentially consists in dissolving the alloy under consideration at low temperature, generally incomplete. other parameters of the production range, in particular of income, being unchanged, compared to usual practice.
  • 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. It should preferably have:% Zn / 30 +% Mg / 18 +% Li / 4.2 +% Cu / 7 ⁇ 1.
  • the metallographic and structural characteristics of these phases and their characteristic reticular distances in X-ray diffraction are similar to those given by the article by HK HARDY and JM SILCOK in the Al-Li-Cu system free of magnesium (Journal of the Institute of Metals, 1955-56, Vol 84, p. 423-425).
  • the 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.
  • the largest dimension of the largest particles exceeds 5 ⁇ m and preferably 10 ⁇ m.
  • This structure can be checked by differential thermal analysis or differential enthalpy analysis (DSC: Differential Scanning Calorimetry), the trace (thermogram) then having the following characteristics in the field of temperatures of solution and of melting beginning during a sample temperature rise programmed at a speed of 1 to 20 ° C / minute: . an apparent plateau or pseudo-plateau extending between the dissolution temperature actually carried out on the alloy and the starting melting temperature of the alloy.
  • DSC Differential Scanning Calorimetry
  • 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.
  • This pseudo level follows a large endothermic peak representing the re-solution of the small precipitates of equilibrium phase formed during the rise in temperature of the sample in the area preceding that of the dissolution temperatures practiced on the alloy. .
  • the surface of this peak is therefore, as a result, the greater the lower the dissolution temperature according to the invention, prior to the thermal analysis, and is lower than the dissolution temperature usually practiced on the alloy.
  • An alloy free of phases out of solution T2 or R that is to say an alloy of composition such as A ⁇ O having previously undergone complete dissolution of the coarse particles of phases T2 at R at high temperature according to the procedure normally known to those skilled in the art does not exhibit such a peak at around 532-550 ° C.
  • the method according to the invention consists in dissolving carried out in a range of temperatures T MS lower than the usual dissolving 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 rate below 100 ° C. is not critical.
  • the cooling can be carried out in an oven, under an air stream, with calm air, with 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.
  • alloy 2091 The same alloy as above (alloy 2091) was dissolved at various temperatures between 490 ° C and 535 ° C after annealing for 1 hour at 400 ° C and cold rolling, quenching with water and tempering for 12 hours at 135 ° C, before undergoing a differential thermal analysis on a DUPONT de NEMOURS DSC 910 device controlled by a DSC 990 programmer under the following conditions: - samples and reference (Refined aluminum) machined in the form of discs with a diameter of 5 mm and a thickness of 1 mm - dry nitrogen sweeping in the cell - temperature rise rate of 5 ° C / min between 400 and 590 ° 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 endothermic peak (III).
  • the starting melting peak 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 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.
  • the stress corrosion and mechanical strength properties measured are given in Table II.
  • 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)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Chemically Coating (AREA)
  • Heat Treatment Of Articles (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)
  • Resistance Welding (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
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
FR8702719A FR2610949B1 (fr) 1987-02-18 1987-02-18 Procede de desensibilisation a la corrosion sous tension des alliages d'al contenant du li
FR8702719 1987-02-18
FR888801005A FR2626009B2 (fr) 1987-02-18 1988-01-20 Produit en alliage d'al contenant du li resistant a la corrosion sous tension
FR8801005 1988-01-20

Publications (3)

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

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EP88420046A Expired - Lifetime EP0282421B1 (de) 1987-02-18 1988-02-16 Zugspannungsbeständiges Lithium enthaltendes Aluminiumlegierungs-Erzeugnis und Verfahren zu seiner Herstellung

Country Status (7)

Country Link
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)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5374321A (en) * 1989-11-28 1994-12-20 Alcan International Limited Cold rolling for aluminum-lithium alloys
CN112908953A (zh) * 2021-02-03 2021-06-04 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

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
WO2009073794A1 (en) * 2007-12-04 2009-06-11 Alcoa Inc. Improved aluminum-copper-lithium alloys
EP3187603B1 (de) 2011-02-17 2024-06-26 Arconic Technologies LLC Aluminium-lithium-legierungen der serie 2xxx
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

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2121822B (en) * 1982-03-31 1985-07-31 Alcan Int Ltd Al-li-cu-mg alloys
US4624717A (en) * 1983-03-31 1986-11-25 Alcan International Limited Aluminum alloy heat treatment
DE3479525D1 (en) * 1983-07-26 1989-09-28 Giorgio Targa Rope-making machine
US4661172A (en) * 1984-02-29 1987-04-28 Allied Corporation Low density aluminum alloys and method
FR2561260B1 (fr) * 1984-03-15 1992-07-17 Cegedur Alliages al-cu-li-mg a tres haute resistance mecanique specifique
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
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

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5374321A (en) * 1989-11-28 1994-12-20 Alcan International Limited Cold rolling for aluminum-lithium alloys
CN112908953A (zh) * 2021-02-03 2021-06-04 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
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

Also Published As

Publication number Publication date
DE3870678D1 (de) 1992-06-11
JPS63266037A (ja) 1988-11-02
FR2626009B2 (fr) 1992-05-29
CA1333232C (fr) 1994-11-29
FR2626009A2 (fr) 1989-07-21
EP0282421A3 (en) 1989-01-18
ES2032591T3 (es) 1993-02-16
EP0282421B1 (de) 1992-05-06
US4955413A (en) 1990-09-11

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