EP3018226A1 - Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion - Google Patents

Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion Download PDF

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Publication number
EP3018226A1
EP3018226A1 EP14003717.7A EP14003717A EP3018226A1 EP 3018226 A1 EP3018226 A1 EP 3018226A1 EP 14003717 A EP14003717 A EP 14003717A EP 3018226 A1 EP3018226 A1 EP 3018226A1
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EP
European Patent Office
Prior art keywords
temperature
aluminium alloy
billet
typically
room temperature
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.)
Withdrawn
Application number
EP14003717.7A
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German (de)
English (en)
Inventor
Alexis Skubich
Martin Jarrett
Marc Bertherat
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 Valais AG
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Constellium Valais AG
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 Constellium Valais AG filed Critical Constellium Valais AG
Priority to EP14003717.7A priority Critical patent/EP3018226A1/fr
Priority to HUE15790515A priority patent/HUE043253T2/hu
Priority to US15/522,808 priority patent/US20170314113A1/en
Priority to MX2017005153A priority patent/MX2017005153A/es
Priority to EP15790515.9A priority patent/EP3215648B1/fr
Priority to PL15790515T priority patent/PL3215648T3/pl
Priority to PCT/EP2015/075401 priority patent/WO2016071257A1/fr
Priority to CA2965738A priority patent/CA2965738C/fr
Priority to SI201530705T priority patent/SI3215648T1/sl
Publication of EP3018226A1 publication Critical patent/EP3018226A1/fr
Withdrawn legal-status Critical Current

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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
    • C22F1/05—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/001—Extruding metal; Impact extrusion to improve the material properties, e.g. lateral extrusion
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
    • 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
    • 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
    • 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
    • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor

Definitions

  • the invention relates to ultra-high strength AA6xxx-series aluminium alloy forgings particularly suitable for automotive, rail or transportation structural components, exhibiting an ultimate tensile strength UTS typically higher than 400 MPa in T6 temper, preferably higher than 450 MPa, and excellent corrosion resistance. More particularly such forgings are produced through a manufacturing process which, besides including subsequent extrusion and forging steps, includes multiple solutionising and quench steps in order to achieve, after ultimate age hardening, high strength and excellent corrosion resistance on Cu-doped AA6xxx-series alloys.
  • Static tensile mechanical characteristics in other words, the ultimate tensile strength R m (or UTS), the tensile yield strength at 0.2% plastic elongation R p0,2 (or YTS), and elongation A% (or E%), are determined by a tensile test according to NF EN ISO 6892-1.
  • Aluminium alloy compositions and tempers have been developed for obtaining satisfying strength and corrosion behavior in car components such as chassis-suspension or body structure parts, but also rail or transportation structural components in particular when they are made from forgings obtained from extruded rough products.
  • car components such as chassis-suspension or body structure parts, but also rail or transportation structural components in particular when they are made from forgings obtained from extruded rough products.
  • it is essential to maximise both the ageing response through an adequate solutionising of solute elements, predominantly Mg, Si and Cu, while maximising retention of the fibrous structure through minimal recrystallisation.
  • Said recrystallisation is controlled through the addition of dispersoid elements, typically Mn, Cr and Zr and appropriate homogenisation temperatures. It is also controlled through alloy processing conditions, which are defined so as to minimise stored-energy and thereby maximise recrystallization temperature.
  • dispersoid elements typically Mn, Cr and Zr and appropriate homogenisation temperatures.
  • alloy processing conditions which are defined so as to minimise stored-energy and thereby maximise recrystallization temperature.
  • highly alloyed 6xxx alloys are usually separately solutionised and quenched after the ultimate hot forming step (in this case forging).
  • Such a solution can be found in the patent application EP 2548933 A1 by "Nissan Motor Co".
  • an extended solutionising treatment in excess of 90min
  • high temperature 530-560°C
  • the invention relates to forgings manufactured through a process including, besides subsequent extrusion and forging steps, multiple solutionising and quench steps, to achieve excellent solutionising and strong retention of the fibrous structure on 6xxx type alloys, achieving typically, after last step age hardening (T6 temper), an ultimate tensile strength UTS higher than 400 MPa, and preferably higher than 450 MPa, and an excellent corrosion resistance.
  • T6 temper last step age hardening
  • Solidus Ts is the temperature below which the alloy exhibits a solid fraction equal to 1.
  • Solvus defines the temperature, which is the limit of solid solubility in the equilibrium phase diagram of the alloy.
  • eutectic alloying elements such as Si, Mg and Cu should be added to form precipitated hardening phases.
  • the addition of alloying elements generally results in a decrease in the difference between solidus and solvus temperatures.
  • the solidus to solvus range of the alloy becomes a narrow "window", with typically a solidus to solvus difference lower than 20°C, and consequently the solution heat treatment of the aforementioned elements usually achieved during extrusion cannot be obtained without observing incipient melting. Indeed local temperature gradients achieved during extrusion and forging, generally exceed 20°C implying that, as solvus is reached, parts of the product will display temperatures in excess of solidus Ts.
  • high strength forgings obtained from extruded rough products, and from 6xxx-series aluminium alloys characterised by a minimum Silicon content of 0.7 % and minimum Magnesium content of 0.6 %, for example of the AA 6082, 6182, 6110, or 6056 type, are produced by:
  • a first object of the invention is an aluminium alloy forged product obtained by following steps:
  • the aluminium alloy extruded product is obtained by casting a billet from a 6xxx aluminium alloy comprising: Si: 0.7-1.3 wt. %; Fe: ⁇ 0.5 wt. %; Cu: 0.1-1.5 wt. %; Mn: 0.4-1.0 wt. %; Mg: 0.6-1.2 wt. %; Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: ⁇ 0.2 wt.%; Ti: ⁇ 0.2 wt.%, the rest being aluminium and inevitable impurities.
  • the aluminium alloy according to the invention is of the AlMgSi type, which, compared with other such as e.g. AlZnMg alloys, provides an excellent combination of high tensile strength and resistance to corrosion.
  • the process according to the invention consists in particular in replacing conventional homogenising followed by slow cooling, heating and extruding followed again by slow cooling of AA6xxx alloy billets, by high temperature homogenising and quenching followed by heating, extruding and quenching again, and does not comprise a separate post-extrusion solution heat treatment, because, as a result of steps b) and c), most part of the alloying elements which contribute to the formation of hardening particles are in solid solution in the lattice of the extrudate.
  • the present invention therefore provides a process to manufacture a range of 6xxx alloys with superior mechanical properties, especially if applied to a sufficiently copper-doped AlMgSiCu, with strength levels in excess of 400 MPa and even 450 or 480 MPa, hitherto not achieved through a conventional route.
  • good extrudability and forgeability is maintained because the limitation with extrusion speed due to premature speed cracking resulting from incipient melting is minimised due to a higher level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases prior to extrusion.
  • a billet is provided resulting from casting a 6xxx aluminium alloy, i.e. an aluminium alloy having magnesium and silicon as major alloying elements.
  • this aluminium alloy is a high-strength 6xxx aluminium alloy, such as AA6082, AA6182, AA6056, AA6110 or any copper-doped alloy derived from the said AA6xxx aluminium alloys.
  • This alloy has preferably a high Cu content, typically between 0.1 and 1.5 wt. %, more preferably between 0.4 and 1.2 wt. %, even more preferably between 0.6 and 1.0 wt. %.
  • Dispersoid elements Mn with a content of 0.4-1.0 wt. %, Cr with a content of 0.05-0.25 wt. % and Zr with a content of 0.05-0.2 wt. %, are added to control recrystallization and maximize the retention of fibrous structure of the extrudate and the forged component.
  • Si and Mg content are defined so as to ensure high level of dissolved Mg2Si while minimising presence of undissolved Mg2Si in the forged component after ultimate solutionising step, with a maximum content of 0.5 wt.%.
  • the content of dissolved Mg is 0.623 wt.%
  • dissolved Si is 0.977 wt.%
  • undissolved Mg2Si 0.45wt.%.
  • Mg2Si is combined with Mg to form Mg2Si.
  • the precipitation of Mg2Si contributes to increasing the strength of the final aluminium alloy forged product.
  • the final product does not have a sufficiently high strength, it means a tensile strength not higher than 400 MPa. If it is lower than 0.9 wt.%, tensile strength will be at most 450 MPa and with less than 1.1wt.% it will be lower than 480 MPa.
  • the Si content is more than 1.3 wt.%, the level of undissolved Mg2Si is too high and extrudability is reduced as well as corrosion resistance and toughness of the resultant final forged product.
  • Mg is combined with Si to form Mg2Si. Therefore Mg is indispensable for strengthening the product of the present invention. If the Mg content is lower than 0.7 wt.%, the effect is too weak. On the other hand, if the Mg content is higher than 1.2 wt.%, the billet becomes difficult to be extruded and the extruded bar to be forged. Moreover, a large amount of Mg2Si particles tends to precipitate during quenching process after the solution treatment.
  • the Mg content is preferably between 0.7 wt.% and 1.1 wt.% and more preferably between 0.8 wt.% and 1.0 wt.%.
  • Fe is an impurity and combines with other elements to form intermetallic compounds. These precipitated particles lower fracture toughness and fatigue strength of the final forged product. Especially, if the Fe content is higher than 0.5 wt.% it is difficult to obtain an aluminium alloy forged product with both high strength and high toughness as required for automotive structure and suspension applications. Preferably, its content is lower than or equal to 0.3 wt.% and more preferably, lower than or equal to 0.2 wt.%.
  • Mn also combines with A1 to form intermetallic compounds which control recrystallisation. However, if the Mn content is less than 0.4 wt.%, the effect is not sufficient. On the other hand, if the content of Mn is higher than 1.0 wt.%, coarse precipitated particles are formed and both the workability and the toughness of the aluminium alloy are reduced.
  • the Mn content is preferably between 0.5 wt.% and 0.9 wt.% and more preferably between 0.5 wt.% and 0.7 wt.%.
  • the cast billet according to the invention is homogenised for a duration between 2 and 10 hours at a temperature between 5°C and 80°C lower than solidus, and then water quenched.
  • the homogenised and quenched cast billet to be extruded is heated to a soaking temperature T h below the solidus temperature Ts, between Ts-5°C and Ts-125°C.
  • solidus temperature is near 575°C for alloys AA6082 and AA6182.
  • the billets are preferably heated and held at the soaking temperature during ten seconds to several minutes.
  • the billet is then introduced in the extrusion press and extruded through a die to form a solid extruded product or extrudate.
  • the extrusion speed is controlled to have an extrudate surface exit temperature lower than solidus temperature Ts, respectively 530 and 550°C approximately.
  • the exit temperature should be high enough to merely avoid precipitation.
  • the targeted extrudate surface temperature is commonly ranging from 530°C to 550°C, to have an extrusion speed compatible with a satisfying productivity and avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles.
  • the extrusion ratio (starting cross-sectional area divided by final cross-sectional area) is at least 8 to maximize the fibrous structure of the extrudate.
  • the extruded product is then water quenched at the exit of the extrusion press, i.e. in an area located between 500 mm and 5 m of the exit from the die. It is cooled down to room temperature with an intense cooling device, for example a device projecting sprayed water or a water based cooling liquid on the extrudate.
  • an intense cooling device for example a device projecting sprayed water or a water based cooling liquid on the extrudate.
  • the extrudate is then stretched to obtain a plastic deformation typically between 0.5% and 10%, preferably up to 5%, in order to have stress-relieved straight profiles.
  • the extruded bar is then cut to length, heated to forging temperature, typically between 400 and 520°C, and then forged in a heated mould typically between 150 and 350°C.
  • parts undergo a separate solutionising at a temperature between 530 and 560°C for a duration comprised between 2 min. and 1 hour and then water quenched with an intense cooling device, for example a device projecting sprayed water or a water based cooling liquid, down to room temperature.
  • an intense cooling device for example a device projecting sprayed water or a water based cooling liquid
  • the product is then aged at room temperature for a duration between 6 hours and 30 days , after which artificial ageing is applied to achieve T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200°C for holding times ranging from 2 to 20 hours.
  • the process according to the invention allows to obtain forged products made from Cu-doped 6xxx alloys, which were until now very difficult to solutionise because of their very narrow solvus-solidus temperature window and the risk of recrystallization during ultimate separate solutionising prior to final age-hardening treatment.
  • This process is particularly well suited to alloys with Mg2Si content comprised between 1.2 wt. % and 1.6 wt. %, Si excess up to 0.7%, particularly if comprised between 0.2 wt. % and 0.7 wt.
  • this alloy comprises, further to Mn, additional dispersoid elements zirconium, between 0.05 and 0.2 wt. %, and Cr, between 0.05 and 0.25 wt. %, the microstructures of the extrudates show a strong fibrous retention providing an additional strengthening contribution, considered important in meeting such high mechanical property values.
  • a forged product manufactured according to the invention also displays a limited sensitivity to intergranular corrosion as assessed according to ISO 11846B and opposed to what the copper level would lead a corrosion expert to expect.
  • Such forged products are particularly suitable as automotive body structure or chassis-suspension parts and especially suspension arms.
  • Forged suspension arms were made from two 6xxx aluminium alloys, the first one being of the AA6082 type, the other one according to the invention, starting from extruded round bars with a diameter of 40 mm. Said bars were extruded by following two different process routes: the current prior art route for AA6082 alloys and the route according to the invention for others.
  • Homogenised cast billets having a diameter of 308 mm and a length of 1200 mm were heated, introduced into an extrusion press and pressed to form 40 mm in diameter bars.
  • Table 2 shows the ultimate tensile strength (UTS), the yield strength (YS) and the elongation of forged products.
  • Table 2 Alloy Solutionising Ageing Temper Rm [MPa] Rp0,2 [MPa] A [%] AA 6082 530°C/30 min. 175°C/8h T6 378 358 11 AA 6082 530°C/30 min. 175°C/8h T6 376 354 12.5
  • Corrosion tests were performed using the ISO 11846B test for 24 hours of exposure time on suspension arms as above, the ones obtained from AA6082 alloy following the prior art route, the other ones according to the invention.
  • Figure 1 shows no significant difference for products according to the invention, with a maximum surface attack depth of 310 microns and a maximum end grain attack depth of 380 microns for the product according to the invention compared to respectively 390 and and 320 microns for AA6082 alloys processed through a prior art route.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)
  • Extrusion Of Metal (AREA)
EP14003717.7A 2014-11-05 2014-11-05 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion Withdrawn EP3018226A1 (fr)

Priority Applications (9)

Application Number Priority Date Filing Date Title
EP14003717.7A EP3018226A1 (fr) 2014-11-05 2014-11-05 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion
HUE15790515A HUE043253T2 (hu) 2014-11-05 2015-11-02 Ultranagy szilárdságú kovácsolt 6XXX alumíniumötvözetek
US15/522,808 US20170314113A1 (en) 2014-11-05 2015-11-02 Ultra high strength 6xxx forged aluminium alloys
MX2017005153A MX2017005153A (es) 2014-11-05 2015-11-02 Aleaciones de aluminio forjado 6xxx de ultra alta resistencia.
EP15790515.9A EP3215648B1 (fr) 2014-11-05 2015-11-02 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion
PL15790515T PL3215648T3 (pl) 2014-11-05 2015-11-02 Nadwytrzymały stop aluminium 6xxx kuty
PCT/EP2015/075401 WO2016071257A1 (fr) 2014-11-05 2015-11-02 Alliages d'aluminium forgés de série 6xxx à résistance ultra-élevée
CA2965738A CA2965738C (fr) 2014-11-05 2015-11-02 Alliages d'aluminium forges de serie 6xxx a resistance ultra-elevee
SI201530705T SI3215648T1 (sl) 2014-11-05 2015-11-02 Ultravisokotrdne kovane 6xxx aluminijeve zlitine

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP14003717.7A EP3018226A1 (fr) 2014-11-05 2014-11-05 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion

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EP3018226A1 true EP3018226A1 (fr) 2016-05-11

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EP14003717.7A Withdrawn EP3018226A1 (fr) 2014-11-05 2014-11-05 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion
EP15790515.9A Active EP3215648B1 (fr) 2014-11-05 2015-11-02 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion

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EP15790515.9A Active EP3215648B1 (fr) 2014-11-05 2015-11-02 Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion

Country Status (8)

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US (1) US20170314113A1 (fr)
EP (2) EP3018226A1 (fr)
CA (1) CA2965738C (fr)
HU (1) HUE043253T2 (fr)
MX (1) MX2017005153A (fr)
PL (1) PL3215648T3 (fr)
SI (1) SI3215648T1 (fr)
WO (1) WO2016071257A1 (fr)

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CN106938310A (zh) * 2017-03-23 2017-07-11 遵义航天新力精密铸锻有限公司 航空飞行器用连接座的精锻加工方法
EP3299482A1 (fr) 2016-09-21 2018-03-28 Aleris Aluminum Duffel BVBA Alliage de 6xxx séries de haute résistance pour forger.
WO2019122076A1 (fr) 2017-12-21 2019-06-27 Constellium Extrusion Decin S.R.O. Ébauche de forgeage extrudé en alliage d'aluminium 6xxx et son procédé de fabrication
CN110129636A (zh) * 2019-05-29 2019-08-16 安徽生信铝业股份有限公司 一种高铁风挡用铝合金及其制备方法
CN110408805A (zh) * 2019-04-10 2019-11-05 广东坚美铝型材厂（集团）有限公司 一种铝合金棒材及其制备方法
CN110938765A (zh) * 2019-12-18 2020-03-31 东北轻合金有限责任公司 一种汽车底盘用高强Al-Mg-Si铝合金棒材及其制造方法
AT522376A1 (de) * 2019-04-05 2020-10-15 Hammerer Aluminium Ind Extrusion Gmbh Stranggussbolzen aus einer Aluminiumbasislegierung, extrudiertes Profil und Verfahren zur Herstellung desselben
EP3981893A1 (fr) * 2020-10-07 2022-04-13 AMAG rolling GmbH Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque
CN115572871A (zh) * 2022-10-31 2023-01-06 山东骏程金属科技有限公司 商用铝合金锻造车轮及其制备方法
CN117265342A (zh) * 2023-09-26 2023-12-22 南京长澄科技制造有限公司 一种铝合金刹车座材料及其制备方法和应用

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CA3032261A1 (fr) 2016-08-26 2018-03-01 Shape Corp. Procede de formage a chaud et appareil de pliage transversal d'une poutre d'aluminium profilee pour former a chaud un composant structural de vehicule
US11072844B2 (en) 2016-10-24 2021-07-27 Shape Corp. Multi-stage aluminum alloy forming and thermal processing method for the production of vehicle components
CN108188192B (zh) * 2018-01-02 2019-09-10 龙口市丛林铝材有限公司 一种大规格大壁厚差多腔铝型材侧弯问题精准控制方法
JP7380127B2 (ja) * 2019-11-20 2023-11-15 株式会社レゾナック 自動車足回り用アルミニウム合金鍛造材の製造方法
JP7380134B2 (ja) * 2019-11-27 2023-11-15 株式会社レゾナック 自動車足回り用アルミニウム合金鍛造材の製造方法
CN110885942B (zh) * 2019-12-17 2021-05-07 中铝材料应用研究院有限公司 一种适用于热冲压成形-淬火一体化工艺的中强7xxx系铝合金板材
CN113088773A (zh) * 2021-03-05 2021-07-09 长春市吉通凯撒铝业有限责任公司 一种高强度铝合金及其生产工艺和应用
CN115449652A (zh) * 2022-08-04 2022-12-09 广东伟业铝厂集团有限公司 一种新能源汽车异型多腔体底盘型材及其制备方法
CN115283593B (zh) * 2022-08-18 2024-06-25 重庆新钰立金属科技有限公司 一种发电机油箱框铝锻件的成型方法

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EP3299482A1 (fr) 2016-09-21 2018-03-28 Aleris Aluminum Duffel BVBA Alliage de 6xxx séries de haute résistance pour forger.
CN106938310A (zh) * 2017-03-23 2017-07-11 遵义航天新力精密铸锻有限公司 航空飞行器用连接座的精锻加工方法
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CN110938765A (zh) * 2019-12-18 2020-03-31 东北轻合金有限责任公司 一种汽车底盘用高强Al-Mg-Si铝合金棒材及其制造方法
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WO2016071257A1 (fr) 2016-05-12
US20170314113A1 (en) 2017-11-02
EP3215648B1 (fr) 2019-01-23
EP3215648A1 (fr) 2017-09-13
SI3215648T1 (sl) 2019-07-31
MX2017005153A (es) 2018-01-23
CA2965738C (fr) 2023-09-12

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