WO2002050329A1 - Alliages a l'aluminium a durcissement par vieillissement - Google Patents

Alliages a l'aluminium a durcissement par vieillissement Download PDF

Info

Publication number
WO2002050329A1
WO2002050329A1 PCT/GB2001/005686 GB0105686W WO0250329A1 WO 2002050329 A1 WO2002050329 A1 WO 2002050329A1 GB 0105686 W GB0105686 W GB 0105686W WO 0250329 A1 WO0250329 A1 WO 0250329A1
Authority
WO
WIPO (PCT)
Prior art keywords
alloy
casting
temperature
hot
hot working
Prior art date
Application number
PCT/GB2001/005686
Other languages
English (en)
Inventor
Gary John Mahon
Original Assignee
Alcan International Ltd.
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Alcan International Ltd. filed Critical Alcan International Ltd.
Priority to AU2002216221A priority Critical patent/AU2002216221A1/en
Priority to JP2002551203A priority patent/JP2004522854A/ja
Priority to CA002431029A priority patent/CA2431029A1/fr
Priority to EP01271462A priority patent/EP1346075B1/fr
Priority to AT01271462T priority patent/ATE279546T1/de
Priority to DE60106488T priority patent/DE60106488T2/de
Priority to US10/451,217 priority patent/US20040089379A1/en
Publication of WO2002050329A1 publication Critical patent/WO2002050329A1/fr

Links

Classifications

    • 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent

Definitions

  • This invention concerns AA5000 series alloys with the addition of Cu that can be retained in a solution treated condition after hot working, for example by hot rolling on a hot mill or by hot extruding.
  • the novel feature of this invention is the discovery that for certain Cu - containing 7 ⁇ A5000 series alloys sufficient solution treatment occurs during hot working, for example hot rolling, to render the alloys age hardenable without a further expensive solution treating step. This gives a very significant economic advantage especially for commodity products such as can end stock, automotive sheet products, or extruded products such as structural sections.
  • EP-A-0605947 describes manufacturing can body sheet using two sequences of continuous operations. The described additional steps of uncoiling the hot coiled sheet, quenching the sheet without intermediate cooling, cold rolling and re-coiling the sheet are required, but these additional steps are not needed in the method of the present invention.
  • WO-A-99/39019 describes a method for making can end and tab stock but annealing of the sheet is required as a separate operation after hot rolling which is not needed in the method of the present invention.
  • WO-A-98/01593 describes a process for producing aluminium alloy can body stock but again a separate annealing step is required.
  • JP-A-100121179 describes aluminium alloy sheet for carbonated beverage can lids but a formal solution heat treatment is required, which is not needed in the method of the present invention.
  • US-A-5655593 describes aluminium alloy sheet manufacture in which the hot strip is cooled rapidly to minimise the precipitation of the alloying elements. This teaching of rapid cooling is contrary to that of the present invention.
  • US-A-3464866 describes a process for obtaining aluminium alloy conductors but again teaches rapid cooling.
  • Chromium up to 0.15%
  • Titanium up to 0.15%, preferably up to
  • the intermediate product is generally maintained at a temperature below the solvus temperature of the alloy, provided that if the intermediate product is heated above the alloy's solvus temperature then cooling thereof is effected at a rate less than 2°C/sec.
  • the solvus temperature of the alloy is meant the temperature below which under equilibrium conditions the copper begins to be removed from solid solution to form a precipitate. However, as to the rate of copper removed that will depend on the kinetics of the reaction.
  • the precipitation phase if formed is believed to be S phase (an AlCuMg phase) or its metastable precursors.
  • the alloy may be cast by DC casting to form an ingot or by continuous casting, for example in a belt caster or a twin roll casting machine, to form a sheet.
  • the cast and preferably homogenised alloy can be extruded but for the production of can end stock it is generally hot rolled. After casting the preferred steps are:
  • the casting optionally homogenising the casting at a temperature of at least 480°C, and preferably 500 to 600°C, so that substantially all of the magnesium and copper in the casting are in solid solution,
  • hot rolling the casting with a rolling mill entry temperature of the casting of at least 400, and preferably from 450° to 580°C, continuing rolling the casting to the desired thickness to form a sheet so that at least part of the rolling reduction is carried out above the solvus temperature of the alloy and cooling the alloy, either while rolling or subsequently, slow enough so as to form at least a partially recovered or recrystallised structure but fast enough to ensure that sufficient of the Cu is retained in solid solution to provide an age hardening effect if a subsequent precipitation treatment is carried out, optionally cold rolling the hot rolled sheet, and optionally age hardening the cold rolled alloy, wherein preferably after the essential hot rolling step the rolled ingot is always maintained at a temperature below its solvus temperature.
  • the metal temperature generally rises to about 100-200°C as it is passed through the mill.
  • the metal is coiled and being so massive the coiled metal takes a long time to cool down to room temperature. Phase precipitation and hardening can occur during this cooling down period without the need forcibly to cool the coil. Additional cooling can, however, be used if required.
  • re-heating can be effected if desired, for example to control the amount of cold work in the alloy. If this re-heating takes the alloy above its solvus temperature then cooling is preferably effected at a rate less than 2°C/sec to avoid distortion or to avoid the need for a separate quench stage.
  • the alloy could be cast continuously by for example belt casting or twin roll casting. These techniques allow thin strip to be produced of a thickness of generally as low as 5mm, and sometimes as low as 2mm. Such thin cast strip may or may not require homogenisation before hot rolling since it tends to cool so quickly that the Cu and Mg present are likely to remain in solid solution.
  • the casting could be extruded using direct or indirect extrusion.
  • the casting is homogenised as described above and then cooled to room temperature before being re-heated to 400 to 500°C for extrusion.
  • the casting can be cooled directly from its homogenisation temperature to the desired extrusion temperature.
  • the extrudate is cooled preferably with still air or with forced air. If desired, the extrudate can be reheated to above the solvus temperature of the alloy and then cooled at a rate of less than 2°C/sec. This reheating treatment may be needed for texture and/or grain size control. After extrusion the extrudate is generally stretched by about to 2% and then aged.
  • the present invention has particular applicability for the production of can stock, especially can end stock (CES) which possesses a combination of high strength and formability.
  • CES can end stock
  • the combination of composition and process of the present invention overcomes many of the manufacturing difficulties of the conventional AA5182 sheet currently in use and is capable of producing CES at lower cost. It also improves the subsequent performance of the can end, most notably its scoreline corrosion resistance.
  • the invention is particularly suitable for downgauging to produce lighter weight can ends, i.e. gauges down to say 0.150mm.
  • the preferred method is to cast an ingot, homogenise it, and hot roll to, say, 2mm to form strip.
  • a key aspect of the invention is that the strip does not need an additional solution heat treatment step.
  • the material does not need to be rapidly cooled, e.g. does not need to be quenched into water; the cooling is generally air cooled (possible forced air) .
  • the coil is then cold rolled to final gauge and lacquered.
  • Magnesium 1.0 - 4.0 wt.%, preferably 2.0 - 4.0, still more preferably 2.5 to 4.0%
  • Copper 0.1 - 0.6 wt.%, preferably 0.2 - 0.5, still more preferably 0.2 to 0.4%
  • Manganese up to 0.8 wt.%, preferably up to 0.6, more preferably up to 0.5, still more preferably up to 0.4%. For some alloys a minimum Mn content of 0.1% is preferred.
  • Iron up to 0.5 wt.%, preferably 0.1 - 0.3%
  • Silicon up to 0.3wt.%, preferably up to 0.2%
  • Chromium up to 0.15%, preferably trace Titanium: up to 0.15, preferably up to 0.05%
  • Carbon up to 0.05, preferably up to 0.01%
  • TiB 2 or TiC can be used, but generally not together.
  • Figure 1 shows a thermodynamic calculation of the solvus temperature for S-phase precipitation in Al-x%Mg-y%Cu- 0.25Mn-0.2Fe-0.12Si
  • Figure 2 shows the conductivity changes (%IACS) during isothermal annealing of an Al-3Mg-0.4Cu-0.25Mn-0.2Fe- 0.12Si alloy after solution heat treatment and cold water quenching,
  • Figure 3 shows the conductivity changes (%IACS) during isothermal annealing of an Al-3Mg-0.4Cu-0.25Mn-0.2Fe- 0.12Si alloy after solution heat treatment, cold water quenching and cold rolling, and
  • Figure 4 are curves showing the effect of time and temperature on the extent of recrystallisation during isothermal annealing of an Al-3Mg-0.4Cu-0.25Mn-0.2Fe- 0.12Si alloy after solution heat treatment, cold water quenching and cold rolling.
  • the basic premise is to select an alloy composition which will enable solute to be kept in solid solution during cooling from hot rolling temperatures (250°C to 400°C, say) .
  • the strip is then processed to bring out a precipitation hardening phase which provides extra strength.
  • This precipitation forms preferentially on the dislocation structure introduced during cold deformation In the case of CES this cold deformation is cold rolling, for extrusions it is stretching, and for sheet it is during forming of the sheet when it is fabricated into a component .
  • the nucleation and diffusion effects are such to keep a substantial amount of solute in solution, i.e. 'missing the nose of the c- curve' .
  • the hot rolling conditions are selected to ensure that the hot rolled sheet recrystallises on or before coiling or very shortly thereafter.
  • the sheet is fully recrystallised resulting in a low dislocation density. Recrystallisation is encouraged by arranging for the minimum temperature of the sheet as it exits from the rolling mill to be 250°C, preferably 270°C and more preferably 300°C and/or arranging for the cooling rate of the sheet to be sufficiently slow to allow time for the sheet to recrystallise when in its coiled form or during coiling.
  • the coiling temperature is approximately the same as the exit rolling mill temperature. Where additional cooling means are provided after the mill the minimum coiling temperature should be in the range of minimum mill exit temperatures mentioned above.
  • cooling rates are found to be of the order of 0.1 to 10°C/minute and preferably 0.2 to 5°C/minute over the temperature range of 400-200°C. There is no need to uncoil the sheet during cooling in order, for example, to quench it.
  • a high rolling mill exit temperature encourages precipitation of S phase or its precursors while the strip or coil is cooling. Cooling more quickly can counter this and prevent precipitation but if the exit temperature becomes too high, the cooling rate required is too fast to be practically useful.
  • the upper limit to the mill exit temperature especially for the alloys richer in Cu and Mg, should preferably be lower than the solvus temperature of the alloy.
  • Figure 1 gives an indication of the solvus temperature as a function of the Mg and Cu contents.
  • the maximum exit temperature should be between 340°C and 360°, although up to 380°C is possible for some alloys.
  • the location of the nose of the c-curve for these alloys when recrystallised varies with the composition of the alloy.
  • the nose of the curve is located at a time of around 100 to 1000 seconds.
  • the nose is moved to longer times whilst for more concentrated alloys the nose is moved to shorter times.
  • the time indicated in Figure 2 compares with times of between 1 and 100 seconds for conventional age hardening systems such as AA7075, AA2017, AA6061 and AA6063.
  • this provides longer times at temperatures below the solvus temperature in which to cool the strip and still maintain the Cu (and Mg) in solid solution.
  • a cooling rate of l°C/min and preferably 5°C/min is sufficient substantially to miss the nose of the c-curve and provide a substantial age hardening response during subsequent processing.
  • This cooling rate can be achieved by, for example, forced air cooling of a coil.
  • Previous art regarding solution heat treatment of these Al-Mg-Cu alloys teaches that, not only is a separate solution heat treatment stage required, but that the strip must be quenched with a cooling rate of 2°C/second or faster. For the present invention it has been found that neither of these steps need to be used, thereby providing a lower cost manufacturing route for these alloys. Likewise no separate annealing step is needed after the hot working step and before the cooling step.
  • This solute is then used to give a significant precipitation hardening effect during subsequent thermomechanical processing.
  • an increased dislocation density is introduced giving enhanced nucleation sites for the strengthening phase.
  • This deformation may not be needed for all applications of this invention, since for these compositions it is known that the precipitation can also occur in the absence of dislocations, albeit at slower rates.
  • the precipitating phase is believed to be S-phase which can form as needles or rods on the dislocation structure. In the case of CES this precipitation could occur during a separate ageing step or during the thermal history which the material would experience during deformation in, for example, strip rolling.
  • Mn can be added as a strengthening element and to control grain size and is therefore desirably kept as high as possible.
  • Mn inhibits recrystallisation after hot rolling or during annealing, and so a maximum Mn content of 0.4% may have to be set in order to achieve full recrystallisation for some alloys under certain conditions.
  • it may be desirable to have a minimum of at least 0.05%Mn and preferably at least 0.1%Mn present in the alloy.
  • Recrystallisation may also be important for crystallographic texture control in CES, but this may not be necessary if the can end tooling is modified to take significantly higher levels of earing into account. Crystallographic texture control can also be important for automotive sheet for ⁇ iability; another potential application of this invention.
  • Another feature of the composition used in the present invention is the importance of having low Fe and Si in the alloy, since this will prevent the presence of excessive numbers of coarse constituent particles in the sheet. These form during solidification and cannot be fully dissolved during homogenisation of the ingot. Although they break up during rolling, their presence is sufficient adversely to affect formability. Since this invention has been found to produce improved formability over existing AA5182 CES, the strip may be able to tolerate higher levels of these elements, thus reducing cost.
  • Si and Fe may allow greater use of recycled aluminium scrap and this is another important aspect of this invention.
  • Up to 0.5%Fe may be tolerated in the alloy and preferably up to 0.3%Fe.
  • the minimum amount of Fe present will be dictated by cost and there is unlikely to be less than O.lFe.
  • Silicon up to 0.3% may be present, preferably up to 0.2%.
  • Another advantage over conventional AA5182 CES is that the lower Mg content will also make the can end less susceptible to stress corrosion cracking (SCC) , which can lead to catastrophic failure of the end under the stressed conditions which are encountered in the pressurised can.
  • SCC stress corrosion cracking
  • the invention described here will make the end less sensitive to these conditions, since the lower Mg content reduces beta-phase precipitation, which has been linked to SCC. Avoidance of SCC is also important in many other applications including car body sheet.
  • CES is currently made from AA5182 and gets its strength predominantly from a combination of solute hardening and strain hardening. This makes it difficult to roll and gives a relatively high manufacturing cost.
  • the alloy used in the present invention has lower strength during the rolling operations, but develops its strength during subsequent thermal exposure during fabrication. Thus there is the benefit of rolling a lower strength sheet, but still enabling the desired sheet properties to be obtained ultimately. It is also possible to produce a higher strength sheet suitable for downgauging without a reduction in rollability (higher rolling loads, more difficulties in performing the rolling operation) encountered in higher Mg containing alloys such as AA5182 and AA5019A.
  • the present invention is also applicable to production of low cost automotive sheet where the material could be used in the hot rolled condition
  • the sheet could be cold rolled to gauge, as for CES, with a final continuous anneal to impart the formability required for this application and to take the solute into solution. Cooling after annealing should be sufficiently rapid to retain substantially all of the solute in solution. Ageing could be carried out in a separate operation before or after forming, for example during the paint bake stoving of the automotive part.
  • Example 1 Some embodiments of the present invention will now be described by way of example: Example 1
  • the strip was either solution heat treated (SHT) (5 minutes at 550°C) and cold water quenched (CWQ) or it was solution heat treated and then air cooled to temperatures in the range 300 to 340°C and then cooled at l°C/min. Conductivity was measured at this stage to determine how much solute remained in solid solution. These conditions were selected to simulate the conditions which might be expected to exist during commercial use of this invention. Until the strip temperature drops below the solvus temperature for the alloy the S phase therein cannot precipitate and therefore the Cu (and Mg) would be substantially in solid solution. The strip could then be quenched at the end of hot rolling or, preferably, cooled after coiling.
  • SHT solution heat treated
  • CWQ cold water quenched
  • the starting temperature could be in the range 300 to 340°C and a typical initial cooling rate would be l°C/min.
  • the temperature range between the solvus temperature (about 390°C for the alloy) and the coiling temperature is passed through very quickly since this is when the strip might typically be in the hot tandem mill and, hence, there is lubricant applied to the strip which acts as a coolant. This phase was simulated using the air cool from the solution heat treatment temperature.
  • the strip was then cold rolled to 0.24mm and given a simulation of a coil cool down to ambient temperature from 150°C at 0.4°C/min. It was then given a simulation of a lacquer curing cycle for 3 minutes at 205°C. Tensile testing was performed at each stage of the treatment and the results compared with results on conventional AA5182 CES materials processed in the laboratory.
  • the levels of cold reduction needed to generate the desired strength level are lower and thus the weakest direction is likely to be this longitudinal value.
  • the combination of the composition and processing route of the present invention is capable of producing a strength level approximately 45 MPa stronger than existing AA5182.
  • Table 3 Strength developed after processing to 0.24mm after various thermal treatments at 2mm ⁇ hotband' gauge.
  • An alloy of the following composition was DC cast for processing within an industrial plant:
  • the ingots were cast with additional grain refiner.
  • the ingot were homogenised at 540°C and hot rolled on a single stand reversing mill to a thickness of 38mm at which point the temperature was around 480°C.
  • the strip was then hot rolled through a 3-stand hot tandem mill to a gauge of 2.5mm.
  • the conditions were adjusted to give two different coiling temperatures in order to show the effects at opposite extremes of this invention. In both cases the coils were forced-air cooled, giving a cooling rate measured on the outer laps of the coil of around 0.7°C/min.
  • the cooler coil was processed to give a sidewall temperature of 280-290°C.
  • the microstructure of the strip was largely unrecrystallised.
  • the solute was easily removed from solid solution on the pre-existing dislocation structure from the hot deformation.
  • the conductivity of this strip is shown in Table 4, showing that the %IACS value is similar to that in which all of the precipitation has been allowed to occur.
  • Table 4 is presented the conductivity obtained by using a still-air cool on strips of the 2.5mm thick metal at the end of the hot rolling (approximately 60°C per minute) , showing that at these cooling rates a significant amount of the solute can be kept in solid solution.
  • the hotter coil was processed to give a coil sidewall temperature of 330-340°C.
  • Table 4 shows that in this case the forced air cooling leaves more solute in solid solution as a consequence of the fully recrystallised grain structure achieved with the higher coiling temperature.
  • the amount of solute in solid solution with the faster cool is even higher and approaches that of the conventional solution heat treated (SHT) and cold water quenched (CWQ) material.
  • SHT solution heat treated
  • CWQ cold water quenched

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Continuous Casting (AREA)
  • Metal Rolling (AREA)
  • Materials For Medical Uses (AREA)
  • Extrusion Of Metal (AREA)
  • Laminated Bodies (AREA)
  • Cookers (AREA)
  • Table Devices Or Equipment (AREA)

Abstract

La présente invention concerne des alliages de série AA5000 auxquels a été ajouté du Cu qui peut être maintenu dans un état de traitement de solution après traitement à chaud, par exemple par laminage à chaud sur un laminoir à chaud ou par extrusion à chaud. L'invention a pour objet un procédé permettant la production d'un alliage à l'aluminium à durcissement par vieillissement, comprenant les étapes suivantes: a) coulée d'un alliage ayant une composition comprenant les éléments suivants exprimés en pourcents: magnésium: 1,0 à 4,0, cuivre: 0,1 à 0,6, manganèse: jusqu'à 0,8, fer: jusqu'à 0,5, silicium: jusqu'à 0,3, chrome: jusqu'à 0,15, titane: jusqu'à 0,15, complément: aluminium avec les impuretés associées; b) éventuellement homogénéisation de l'alliage coulé; c) traitement à chaud de l'alliage coulé à une température initiale d'au moins 400 °C pour former un produit intermédiaire, au moins une partie du traitement à chaud étant réalisé alors que l'alliage coulé se trouve à une température supérieure à la température de solvus de l'alliage; d) refroidissement du produit intermédiaire soit durant le traitement à chaud, soit au cours d'une étape ultérieure à une vitesse telle qu'au moins une structure partiellement rétablie ou recristallisée est formée et que suffisamment de cuivre est maintenu en solution solide dans l'alliage pour provoquer un effet de durcissement par vieillissement sur l'alliage si la précipitation de phase se déroule durant l'évolution thermique ultérieure de l'alliage; et e) éventuellement précipitation de phase rendue possible ou mise en place dans l'alliage. Le procédé de l'invention convient particulièrement à la production de pièces d'extrémité de boîtes de conserve et de tôles pour des applications dans l'industrie automobile.
PCT/GB2001/005686 2000-12-20 2001-12-20 Alliages a l'aluminium a durcissement par vieillissement WO2002050329A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
AU2002216221A AU2002216221A1 (en) 2000-12-20 2001-12-20 Age-hardenable aluminium alloys
JP2002551203A JP2004522854A (ja) 2000-12-20 2001-12-20 時効硬化性アルミニウム合金
CA002431029A CA2431029A1 (fr) 2000-12-20 2001-12-20 Alliages a l'aluminium a durcissement par vieillissement
EP01271462A EP1346075B1 (fr) 2000-12-20 2001-12-20 Alliages a l'aluminium a durcissement par vieillissement
AT01271462T ATE279546T1 (de) 2000-12-20 2001-12-20 Aushärtbare aluminium-legierungen
DE60106488T DE60106488T2 (de) 2000-12-20 2001-12-20 Aushärtbare aluminium-legierungen
US10/451,217 US20040089379A1 (en) 2000-12-20 2001-12-20 Age-hardenable aluminium alloys

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
GBGB0031104.3A GB0031104D0 (en) 2000-12-20 2000-12-20 Age hardened aluminium alloys
GB0031104.3 2000-12-20

Publications (1)

Publication Number Publication Date
WO2002050329A1 true WO2002050329A1 (fr) 2002-06-27

Family

ID=9905491

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/GB2001/005686 WO2002050329A1 (fr) 2000-12-20 2001-12-20 Alliages a l'aluminium a durcissement par vieillissement

Country Status (9)

Country Link
US (1) US20040089379A1 (fr)
EP (1) EP1346075B1 (fr)
JP (1) JP2004522854A (fr)
AT (1) ATE279546T1 (fr)
AU (1) AU2002216221A1 (fr)
CA (1) CA2431029A1 (fr)
DE (1) DE60106488T2 (fr)
GB (1) GB0031104D0 (fr)
WO (1) WO2002050329A1 (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2004001085A1 (fr) * 2002-06-19 2003-12-31 Alcan International Ltd. Procede de production d'alliages d'aluminium formables
CN110055478A (zh) * 2019-05-10 2019-07-26 贵州正合可来金科技有限责任公司 一种铝合金的制作工艺
WO2021119804A1 (fr) * 2019-12-16 2021-06-24 Rio Tinto Alcan International Limited Alliages d'aluminium à haute résistance
US11535919B2 (en) 2016-07-14 2022-12-27 Constellium Neuf-Brisach Method of making 6XXX aluminium sheets

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007048250A1 (fr) * 2005-10-28 2007-05-03 Novelis Inc. Homogénéisation et traitement thermique de métaux coulés
CN101440448B (zh) * 2008-10-23 2010-06-16 无锡麟龙铝业有限公司 一种能在±125℃下使用的铸铝合金及其制造方法
CN102639733A (zh) * 2009-07-24 2012-08-15 美铝公司 改进的5xxx铝合金和由其制成的形变铝合金产品
KR101191772B1 (ko) 2010-01-08 2012-10-16 (주)일우정밀 자동차 핸들용 알루미늄 합금 조성물의 제조방법
RU2468113C1 (ru) * 2011-11-09 2012-11-27 Федеральное государственное автономное образовательное учреждение высшего профессионального образования "Российский государственный профессионально-педагогический университет" (РГППУ) Способ обработки изделий из алюминиевых сплавов (варианты)
US9587298B2 (en) * 2013-02-19 2017-03-07 Arconic Inc. Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same
CN104451285A (zh) * 2014-11-28 2015-03-25 苏州有色金属研究院有限公司 车身用Al-Mg合金板材及其制造方法
CN105896118A (zh) * 2016-04-15 2016-08-24 河北欣意电缆有限公司 Al-Fe-B-RE铝合金电缆铜铝过渡端子及其制备方法
CN105896119A (zh) * 2016-04-15 2016-08-24 河北欣意电缆有限公司 Al-Fe-Be-RE铝合金电缆铜铝过渡端子及其制备方法
CN109280817A (zh) * 2018-10-31 2019-01-29 宁波汇通机械联接件有限公司 一种双向接头
CA3128732A1 (fr) * 2019-02-07 2020-08-13 Equispheres Inc. Alliages ayant une faible densite de precipites destines a etre utilises dans des applications qui comprennent des procedes de refusion, et procede de preparation associe
CN109772893B (zh) * 2019-02-18 2020-02-14 重庆大学 最大化轧辊利用的多热轧单元批量计划优化方法及控制系统
CN113106309A (zh) * 2021-04-19 2021-07-13 深圳市华加日西林实业有限公司 铝合金、铝合金型材的制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56102568A (en) * 1980-01-21 1981-08-17 Sumitomo Light Metal Ind Ltd Manufacture of aluminum alloy hard plate with superior strength and anisotropy
EP0773303A1 (fr) * 1995-11-10 1997-05-14 Nkk Corporation TÔle d'alliage d'aluminium et procédé pour sa production
WO1999039019A1 (fr) * 1998-01-29 1999-08-05 Alcoa Inc. Procede de fabrication de materiau pour extremites et pour pattes de boites-boisson

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4282044A (en) * 1978-08-04 1981-08-04 Coors Container Company Method of recycling aluminum scrap into sheet material for aluminum containers
US4976790A (en) * 1989-02-24 1990-12-11 Golden Aluminum Company Process for preparing low earing aluminum alloy strip
US5913989A (en) * 1996-07-08 1999-06-22 Alcan International Limited Process for producing aluminum alloy can body stock

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56102568A (en) * 1980-01-21 1981-08-17 Sumitomo Light Metal Ind Ltd Manufacture of aluminum alloy hard plate with superior strength and anisotropy
EP0773303A1 (fr) * 1995-11-10 1997-05-14 Nkk Corporation TÔle d'alliage d'aluminium et procédé pour sa production
WO1999039019A1 (fr) * 1998-01-29 1999-08-05 Alcoa Inc. Procede de fabrication de materiau pour extremites et pour pattes de boites-boisson

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
DATABASE WPI Section Ch Week 198140, Derwent World Patents Index; Class M26, AN 1981-72431D, XP002198010 *

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2004001085A1 (fr) * 2002-06-19 2003-12-31 Alcan International Ltd. Procede de production d'alliages d'aluminium formables
US11535919B2 (en) 2016-07-14 2022-12-27 Constellium Neuf-Brisach Method of making 6XXX aluminium sheets
CN110055478A (zh) * 2019-05-10 2019-07-26 贵州正合可来金科技有限责任公司 一种铝合金的制作工艺
WO2021119804A1 (fr) * 2019-12-16 2021-06-24 Rio Tinto Alcan International Limited Alliages d'aluminium à haute résistance

Also Published As

Publication number Publication date
ATE279546T1 (de) 2004-10-15
US20040089379A1 (en) 2004-05-13
AU2002216221A1 (en) 2002-07-01
JP2004522854A (ja) 2004-07-29
GB0031104D0 (en) 2001-01-31
CA2431029A1 (fr) 2002-06-27
EP1346075A1 (fr) 2003-09-24
DE60106488D1 (de) 2004-11-18
EP1346075B1 (fr) 2004-10-13
DE60106488T2 (de) 2005-12-01

Similar Documents

Publication Publication Date Title
EP1346075B1 (fr) Alliages a l'aluminium a durcissement par vieillissement
EP3299482B1 (fr) Procédé de fabrication d'un alliage de 6xxx series de haute résistance pour forger.
JP4939093B2 (ja) ヘム曲げ性およびベークハード性に優れる自動車パネル用６０００系アルミニウム合金板の製造方法
US4645544A (en) Process for producing cold rolled aluminum alloy sheet
EP3464659B1 (fr) Matériau de stockage forgé en alliage d'aluminium de la série 6xxx et son procédé de fabrication
EP2563944B1 (fr) Materiau en aluminium resistant aux dommages avec une microstructure multi-couches
EP0259700B1 (fr) Procédé de production d'une feuille laminée en alliage à base d'aluminium
US6086690A (en) Process of producing aluminum sheet articles
JP2008542526A (ja) アルミニウム合金板、及びその製造方法
US7048816B2 (en) Continuously cast magnesium containing, aluminum alloy sheet with copper addition
US5098490A (en) Super position aluminum alloy can stock manufacturing process
WO2020182506A1 (fr) Procédé de fabrication d'un produit de tôle de série 5xxx
US20040011438A1 (en) Method and apparatus for producing a solution heat treated sheet
WO1991008319A1 (fr) Ameliorations apportees aux alliages d'aluminium
JP2844411B2 (ja) 冷間予成形可能な超塑性成形用アルミニウム合金板およびその製造方法
JPH0447019B2 (fr)
JPH0672295B2 (ja) 微細結晶粒を有するアルミニウム合金材料の製造方法
US11746400B2 (en) Ultra-high strength aluminum alloy products and methods of making the same
JP2003328095A (ja) 成形加工用アルミニウム合金板の製造方法
US20230016262A1 (en) High Strength Aluminum Alloys
JPH04362151A (ja) 局部張出性に優れたアルミニウム合金硬質板およびその製造方法
CA3239615A1 (fr) Feuilles ou flans d'alliage d'aluminium serie 6xxx a formabilite amelioree
CN117280059A (zh) 用于具有高可加工性的高强度挤出产品的6xxx合金

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE ES FI GB GD GE GH GM HR HU ID IL IN IS JP KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NO NZ OM PH PL PT RO RU SD SE SG SI SK SL TJ TM TN TR TT TZ UA UG US UZ VN YU ZA ZM ZW

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): GH GM KE LS MW MZ SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE CH CY DE DK ES FI FR GB GR IE IT LU MC NL PT SE TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG

DFPE Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed before 20040101)
121 Ep: the epo has been informed by wipo that ep was designated in this application
WWE Wipo information: entry into national phase

Ref document number: 2001271462

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2431029

Country of ref document: CA

WWE Wipo information: entry into national phase

Ref document number: 2002551203

Country of ref document: JP

WWP Wipo information: published in national office

Ref document number: 2001271462

Country of ref document: EP

REG Reference to national code

Ref country code: DE

Ref legal event code: 8642

WWE Wipo information: entry into national phase

Ref document number: 10451217

Country of ref document: US

WWG Wipo information: grant in national office

Ref document number: 2001271462

Country of ref document: EP