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
  • C22F1/05—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 ⁇ -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 ⁇ -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 Rp 0 ,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.
• the invention relates to forgings manufactured through a process including, besides subsequent extrusion and forging steps, multiple solutionising and quench steps, to achieve exceUent solutionising and strong retention of the fibrous structure on 6xxx type aUoys, 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 exceUent corrosion resistance.
• T6 temper typically, after last step age hardening
• UTS ultimate tensile strength
• SoUdus Ts is the temperature below which the aUoy exhibits a solid fraction equal to 1.
• Solvus defines the temperature, which is the Umit of soUd solubility in the equiUbrium phase diagram of the aUoy.
• eutectic alloying elements such as Si, Mg and Cu should be added to form precipitated hardening phases.
• alloying elements generaUy results in a decrease in the difference between soUdus and solvus temperatures.
• soUdus to solvus range of the aUoy becomes a narrow "window", with typically a soUdus 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 soUdus Ts.
• 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.
• a first object of the invention is an aluminium alloy forged product obtained by following steps:
• a) 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 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 ⁇ 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 ⁇ 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.%
• Si 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 l.lwt.% 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 Al 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 Th 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.
• the process and chemical composition of the invention permits to obtain a forged product displaying a near to fully wrought structure by retaining the wrought structure generated during extrusion in parts of the forged component submitted to limited or no deformation during forging and by limiting the extent of recrystallization occurring during the ultimate separate solutionising step.
• 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. %, and especially if copper content lies between 0.4 wt.% and 1.5 wt.%, which gives a solvus to solidus temperature difference approximately equal to or even lower than 10°C, and renders such alloy almost impossible to extrude when processed according to the prior art route.
• 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.
• 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.
• Forged suspension arms were obtained by following a conventional route for AA6082 alloys: a) homogenising the cast billet at a temperature TH close to 480°C, for a duration of 5 hours; b) cooling said billet down to room temperature;
• Table 2 [0033] The results of table 2 show that the process route according to the invention enables the manufacture of aluminium alloy forged products having significantly higher strength (UTS and YS) than products obtained by a conventional route, and similar elongation.
• 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)

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• 2014
  • 2014-11-05 EP EP14003717.7A patent/EP3018226A1/de not_active Withdrawn
• 2015
  • 2015-11-02 SI SI201530705T patent/SI3215648T1/sl unknown
  • 2015-11-02 WO PCT/EP2015/075401 patent/WO2016071257A1/en active Application Filing
  • 2015-11-02 HU HUE15790515A patent/HUE043253T2/hu unknown
  • 2015-11-02 PL PL15790515T patent/PL3215648T3/pl unknown
  • 2015-11-02 EP EP15790515.9A patent/EP3215648B1/de active Active
  • 2015-11-02 US US15/522,808 patent/US20170314113A1/en not_active Abandoned
  • 2015-11-02 MX MX2017005153A patent/MX2017005153A/es unknown
  • 2015-11-02 CA CA2965738A patent/CA2965738C/en active Active

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