WO2019025227A1 - Produit en feuille laminé de série 6xxxx à formabilité améliorée - Google Patents

Produit en feuille laminé de série 6xxxx à formabilité améliorée Download PDF

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Publication number
WO2019025227A1
WO2019025227A1 PCT/EP2018/069976 EP2018069976W WO2019025227A1 WO 2019025227 A1 WO2019025227 A1 WO 2019025227A1 EP 2018069976 W EP2018069976 W EP 2018069976W WO 2019025227 A1 WO2019025227 A1 WO 2019025227A1
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WO
WIPO (PCT)
Prior art keywords
sheet product
aluminium alloy
alloy sheet
rolled
6xxx
Prior art date
Application number
PCT/EP2018/069976
Other languages
English (en)
Inventor
Aleksandar L. DAVIDKOV
Rainer STEINS
Original Assignee
Aleris Aluminum Duffel Bvba
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 Aleris Aluminum Duffel Bvba filed Critical Aleris Aluminum Duffel Bvba
Priority to CN201880044588.7A priority Critical patent/CN110832092A/zh
Priority to US16/628,303 priority patent/US20200216938A1/en
Priority to EP18755718.6A priority patent/EP3662091A1/fr
Publication of WO2019025227A1 publication Critical patent/WO2019025227A1/fr

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Classifications

    • 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
    • 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
    • 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
    • C22F1/043—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 silicon 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
    • C22F1/047—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
    • C22F1/05—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

Definitions

  • the invention relates to a rolled 6xxx-series aluminium alloy sheet product.
  • the sheet product is ideally suitable for automotive applications.
  • the invention further relates to a method of manufacturing the 6xxx-series aluminium alloy sheet product.
  • body panels of a vehicle require excellent properties in formability, dent-resistance, paint-bake response, corrosion resistance and surface quality properties.
  • the conventional AA5xxx-series alloy sheets have not been favoured because they have low mechanical strength even after press forming and may also exhibit poor surface quality. Therefore, 6xxx-series sheet alloys have been increasingly used.
  • the 6xxx-series alloys provide excellent bake harden- ability after painting and high mechanical strength as a result, thus making it possible to manufacture more thin-gauged and more light-weight sheets in combination with a good corrosion resistance and class-A surface finish.
  • aluminium alloy rolled sheet products suitable for use in automotive panels and exhibiting improved formability.
  • aluminium alloy designations and temper designations refer to the Aluminium Association designations in Aluminium Standards and Data and the Registration Records, as pub- lished by the Aluminium Association in 2016 and are well known to the person skilled in the art.
  • alloy compositions or preferred alloy compositions all references to percentages are by weight percent unless otherwise indicated.
  • the purposive addition of strontium (Sr) in the defined range in combination with the Fe/Sr ratio offers an improved formability, in particular an increased stretch formability assessed by an Erichsen Dome Height test.
  • the rolled sheet product in accordance with the invention allows for the presence of higher amounts of Fe while offering a form- ability commonly found in 6xxx-series alloy sheet products having a lower Fe-con- tent. This enables to maintain balance of strength and a good formability while using a higher content of recycled material and thereby increasing the environmental sus- tainability.
  • Patent document WO 2005/108633 A2 discloses 6xxx-series aluminium alloy having 0.3-0.9% Si, 0.1 -0.5% Mg, up to 0.2% Fe, 0.1 -0.4% Cu, 0.03- 0.2% Mn, 0.01 % Ti, 0.08-0.22% Zr and/or Cr and/or V, up to 0.005% Ag, up to 0.04% Zn, and wherein the ratio (in wt.%) of Si to Mg is 1 .8:1 to 3.3:1 , and the ratio (in wt.%) of Fe to Sr is 3:1 to 5:1 .
  • the strontium addition is to ensure that the alloy can be decoratively anodized and shows no yellowish or cloudy eloxal coating.
  • the strontium is said to alter the Fe-, Zr-, Cr, and/or Fe-containing phases to the extent that they do not cause visible clouding when they are incorporated in the eloxal coating.
  • Patent document US 3,926,690 discloses that the addition of 0.02-
  • the Si content should be at least 0.25%, and preferably at least 0.50%, and more preferably at least 0.65%. In an embodiment, the Si content is at least 0.75%. A preferred upper-limit for the Si content is 1 .4%, and more preferably 1 .3%.
  • the pres- ence of Si enhances also the formability, and excess Si with respect to Mg promotes a fast paint-bake response.
  • the Mg content should be at least 0.10%, and preferably at least 0.20%, and more preferably at least 0.25% to provide sufficient strength to the sheet product.
  • the upper-limit for the Mg content is 1 .3%, and preferably 1 .0%.
  • a too high Mg excess may increase the fraction of undesired second phase particles by the formation of Al-Fe-Mg phases.
  • the rolled 6xxx-series aluminium alloy sheet product has a ratio (in wt.%) of Si/Mg of at least 0.90.
  • the Si/Mg ratio does not exceed 1 .40, and more preferably it does not exceed 1 .30.
  • This embodiment has also a very good corrosion resistance and high bendability and hemmability. In combination with the addition of Sr, a significant improved Erichsen Dome Height is achieved.
  • the rolled 6xxx-series aluminium alloy sheet product has a ratio (in wt.%) of Si/Mg in a range of 2.0 to 7.0.
  • a preferred lower-limit for the Si/Mg ratio is 2.5, and more preferably 3.0, and more preferably 4.0.
  • a preferred upper- limit for the Si/Mg ratio is 6.5.
  • This embodiment has in particular a very good form- ability, more in particular a good Erichsen Dome Height is achieved.
  • the rolled 6xxx-series aluminium alloy sheet product has a ratio (in wt.%) of Si/Mg in a range of 2.0 to 7.0, and with preferred narrow ranges, to provide improved formability, it is preferred that the area fraction of Si- particles having a size of more than 0.35 microns (when observed by Light Optical Microscopy at a magnification of 500x) is less than 0.15%, and preferably less than 0.1 1 %.
  • the equivalent average radius of Si-particles having a size of more than 0.35 microns is less than 1 .4 microns, and preferably less than 1 .3 microns.
  • Copper (Cu) can be present in the rolled 6xxx-series sheet product to enhance in particular the work hardening behaviour and the paint-bake response, but it should not exceed 0.45%.
  • a preferred upper-limit for the Cu-content is 0.40%, and more preferably 0.30%.
  • Cu is purposively added in a range of at least 0.02%, and preferably of at least 0.04%.
  • Iron (Fe) should remain within a range of 0.10% to 0.45%.
  • a too low Fe-content may lead to undesired grain growth in the final sheet product adversely affecting several formability characteristics.
  • the effectivity of the Sr addition is less at a low Fe content.
  • a too high Fe-content has an adverse effect on the formability and mechanical properties and is difficult to compensate by the purposive addition of Sr.
  • a preferred lower-limit for the Fe-content is 0.18%.
  • the Fe- content is at least 0.20%.
  • the Fe-content is at least 0.22%.
  • a preferred upper-limit for the Fe-content is 0.40%, and more preferably 0.35%.
  • the strontium (Sr) content must be within a range of 0.01 % and 0.05%, and furthermore, the ratio (in wt.%) of Fe/Sr is in a range of 4 to 40.
  • a preferred upper- limit for the Sr content is 0.045%, and more preferably 0.04%.
  • a preferred lower- limit for the Sr-content is 0.02%, and more preferably 0.025%.
  • the purposive addition of Sr decreases the area fraction, the number density, and the size (circular equivalent average radius) of coarse Si particles (>0.35 micron), and also the area fraction, the number density, and the size (circular equivalent average radius) of coarse Mg2Si particles (>0.35 micron).
  • the addition of Sr decreases the grain size without increasing the size of the fine second phase particles (these are particles ⁇ 1 micron diameter that give contrast in Light Optical Microscopy at a magnification of 1000x) and of Fe-bearing particles. This contributes to an increased formability of the 6xxx-series aluminium sheet material, in particular the stretch formability as indicated, for example, by the Erichsen Dome Height and also increases the elongation.
  • a preferred lower-limit for the Fe/Sr ratio is 5, and a more preferred lower limit is 6.
  • a preferred upper-limit for the Fe/Sr ratio is 20, and more preferably 15.
  • Any Sr is preferable added to the aluminium alloy in the form of a master-alloy, e.g. AISr3.5 or AISr5 or AlSrl 0, prior to casting of the 6xxx-series alloy into rolling feedstock.
  • Strontium is not a common alloying element in rolled 6xxx-series aluminium alloy products, and consequently, the Sr level in any scrap thereof is very low. Often, the Sr level is not standard measured for scrap material, and if present, the Sr level is commonly well below 0.005%, and more typically below 0.001 %.
  • Each of Mn, Cr, V, and Zr could be present to control the grain size in the rolled aluminium alloy sheet product.
  • At least Mn is present in a range of 0.02% to 0.50%.
  • a preferred lower-limit for the Mn content is about 0.05%.
  • a preferred upper-limit for the Mn content is about 0.20%, and more preferably 0.15%, and more preferably 0.10%.
  • Mn is added for grain size control. A too high addition of Mn may interfere with the positive action of the Sr addition.
  • a preferred upper-limit for the Cr addition is about 0.25%, and more preferably about 0.20%.
  • each of vanadium (V) and zirconium (Zr), each up to 0.20% can be added to control the grain size in the final sheet product.
  • these are preferentially avoided in the rolled aluminium alloy sheet product as they may prevent full recrystallization of the sheet product.
  • Such elements are costly and/or form detrimental intermetallic particles in the aluminium alloy.
  • the rolled aluminium alloy sheet product generally includes not greater than 0.03% V and not greater than 0.03% Zr.
  • the sheet product includes V only up to 0.02%, and more preferably up to 0.005%.
  • the sheet product includes Zr only up to 0.02%, and more preferably only up to 0.01 %.
  • Zn is an impurity element that can be tolerated up to about 0.35% and is preferably as low as possible, for example 0.20% or less, and more preferably 0.10% or less.
  • tin may assist in stabilising the mechanical properties in T4 temper.
  • a preferred addition of Sn is in a range of 0.005% to 0.075%, and more preferably in a range of 0.01 % to 0.06%.
  • Ti can be added to the sheet product amongst others for grain refiner purposes during casting of the alloy ingots.
  • the addition of Ti should not exceed about 0.20%, and preferably, it should not exceed about 0.10%.
  • a preferred lower limit for the Ti addition is about 0.01 %, and typically, a preferred upper-limit for Ti is about 0.05%.
  • the Ti can be added as a sole element or with either boron or carbon serving as a casting aid for grain size control.
  • Unavoidable impurities can be present up to 0.05% each, and a total of 0.15%, the balance is made with aluminium.
  • the rolled 6xxx-series aluminium alloy product in a T4 temper has a tensile strength (R m ) of 200 MPa or more and a yield point (Rpo.2) of 90 MPa or more when measured within 30 days after solution heat treatment and quench.
  • the yield point (Rpo.2) is less than 130 MPa after 6 months storage at ambient (room) temperature.
  • it has an elongation at break (Asomm) of at least 24%, and a uniform elongation (A g ) of at least 20%.
  • the rolled 6xxx-series aluminium alloy product in a T4 condition and having a sheet material thickness of 1 mm has an Erichsen Dome Height of at least 9.0 mm, and preferably of at least 9.2 mm, when tested in accordance with EN ISO 20482 (July 2003).
  • the 6xxx-series aluminium alloy according to this invention can be provided as an ingot or slab for fabrication into rolling feedstock using semi-continuous casting techniques regular in the art for cast products, e.g. direct chill DC-casting and electro-magnetic EMC-casting, and preferably having an ingot thickness in a range of about 220 mm or more, e.g. 400 mm, 500 mm or 600 mm.
  • thin gauge slabs resulting from continuous casting e.g. belt casters or roll casters, also may be used, and having a thickness of up to about 40 mm.
  • the thick semi-continuous as-cast ingot is commonly scalped to remove segregation zones near the cast surface of the ingot.
  • Next homogenisation should be performed at a temperature of 450°C or more.
  • homogenisation temperature is less than 450°C, reduction of ingot segregation and heterogeneity may be insufficient. This results in insufficient dissolution of Mg2Si components which contribute to the strength, and whereby formability may be decreased.
  • Homogenisation is preferably performed at a temperature of 480°C or more, more preferably at least one homogenisation step is performed at a temperature range of 540°C to 580°C.
  • the heat-up rates that can be applied are those which are regular in the art.
  • the soaking times for homogenisation should be at least about 2 hours, and more preferably at least about 5 hours.
  • a preferred upper-limit for the homogenisa- tion soaking time is about 48 hours and more preferably about 24 hours.
  • the hot rolling practice comprises a first hot rolling operation wherein the heated feedstock is subjected to breakdown hot rolling in one or more passes using reversing or non-reversing mill stands that serve to reduce the thickness of the rolling feedstock or ingot to an intermediate gauge range of 15 mm to 40 mm, and preferably of 15 to 35 mm.
  • the breakdown rolling starts preferably at a temperature in the range of about 460°C to 510°C, and more preferably of 470°C to 500°C.
  • the hot-mill process temperature should be controlled such that after the last rolling pass the hot-mill exit temperature of the feedstock is in a range of about 370°C to 480°C.
  • a more preferred lower-limit is about 380°C.
  • a more preferred upper-limit is about 450°C, and more preferably 430°C.
  • the feedstock is supplied to a mill for hot finish rolling in one or more passes to a final gauge in the range of 3 mm to 15 mm, for example, 7 mm or 10 mm.
  • the hot finishing rolling operation can be done, for example, using a reverse mill or a tandem mill.
  • the thickness of the rolling feedstock or ingot is typically reduced by at least about 65%, and more typically in the range of 80% to 97%.
  • the average temperature of the hot rolled feedstock when the feedstock is inputted into the hot finish rolling process is maintained preferably at a temperature of 370°C to 480°C. A more preferred lower-limit is about 400°C. A more preferred upper-limit is about 450°C.
  • Control of the finish hot-mill exit temperature of the rolling feedstock is important to arrive at the desired balance of metallurgical properties.
  • the hot-mill tem- perature should be controlled such that after the last rolling pass the hot-mill exit temperature of the feedstock is in a range of about 300°C to 400°C.
  • a preferred lower-limit is about 310°C.
  • a preferred upper-limit is about 380°C, and more preferably about 360°C.
  • a too low or too high exit-temperature of the hot rolled feedstock adversely affects the formability properties of the final product.
  • the hot-rolled feedstock at final gauge is cooled to below 200°C, more typically to below 100°C, and preferably to ambient temperature.
  • the cooling of the hot-rolled feedstock at final gauge from hot-mill exit temperature is by the immediately coiling of the hot- rolled feedstock and allowing it to cool in an ambient environment to ambient tem- perature and stored.
  • the hot rolled material is further down gauged by cold rolling to final gauge by applying in one or more rolling steps a total cold rolling degree of at least 40%, preferably of at least 60%.
  • a recrystallization annealing (con- tinuous or batch) can be applied to the cold-rolled product at an intermediate gauge.
  • the annealing temperature is in the range of 360°C to 580°C to achieve recrystali- sation in the cold-rolled product which influences the crystallographic texture development.
  • a preferred lower-limit for the annealing temperature is 380°C, and more preferably 400°C.
  • a preferred upper-limit for the annealing temperature is 500°C, and more preferably 460°C.
  • the feedstock is cold rolled in one or more cold rolling steps to a final gauge in a range of 0.7 mm to 4.0 mm.
  • a preferred upper-limit for the sheet thickness is 3.0 mm and more preferably 2.5 mm.
  • the cold rolled aluminium sheet product at final gauge is solution heat treated at a temperature and for a time such that sub- stantial amounts of Mg2Si and Si, if any, are dissolved into solid solution.
  • the solution heat-treatment temperature is at least 500°C, and is preferably in a range of 520°C to 570°C, and more preferably in the range of 530°C to 565°C, and is more preferably just above the solvus temperature of the Mg2Si and Si phases to further improve formability characteristics of the aluminium alloy sheet product.
  • the sheet is quenched, e.g., by means of water such as cold water quenching or cold water spray quenching.
  • the main alloying elements Mg, Si and Cu are mostly dissolved during SHT and retained in solid solution by the quenching operation leading to a good formability and control of the yield strength and the bake hardening behaviour.
  • the evolution of the micro- structure at ambient (room) temperature brings the sheet material from a W (as quenched) to a T4 condition.
  • the sheet product is subjected to artificial ageing or pre-ageing and then natural ageing for 72 hours or longer prior to forming into, e.g., a three-dimen- sional shaped or formed automotive body member.
  • the pre-ageing is preferably performed in a continuous annealing line immediately following the solution heat treatment and quenching by heating up to a temperature in a range of 50°C to 130°C.
  • the pre-ageing treatment provides in time more stable mechanical properties of the sheet product before and after being subjected to a paint bake cycle as well an increased paint-bake response.
  • the sheet product following the solution heat treatment and quenching of the sheet product, is subjected to natural ageing for 72 hours to 6 months, optionally even longer, prior to shaping or forming into, e.g., a three-dimensional shaped or formed automotive body member.
  • Forming operations into three-dimensional shapes includes deep-drawing, pressing, stamping, and stretch forming.
  • the formed part may be made part of an assembly of other metal components as regular in the art for manufacturing vehicle components, and subjected to a paint bake operation to cure any paint or lacquer layer applied.
  • the paint bake operation or cycle comprises one or more sequential short heat treatment in the range of 140°C to 210°C for a period of 10 to less than 40 minutes, and typically of less than 30 minutes.
  • a typical paint bake cycle would comprise a first heat treatment of 180°C@20 minutes, cooling to ambient temperature, then 160°C@20 minutes and cooling to ambient temperature. In dependence of the OEM, such a paint bake cycle may comprise of 2 to 5 sequential steps and includes drying steps.
  • the rolled 6xxx-series aluminium sheet products according to this invention are cast via continuous casting, e.g., belt casters or roll casters, and have a feedstock thickness of up to about 40 mm.
  • the product Downstream of the continuous casting operation, the product can be rolled (hot and/or cold), optionally annealed (e.g., between hot rolling and any cold rolling steps), solution heat treated and quenched, optionally cold worked (post-solution heat treatment) or natural aged and optionally also artificially aged, and all these steps may occur in-line or off-line relative to the continuous casting step.
  • the artificially aged product can be painted (e.g., for an automobile part), and may thus be subjected to a paint-bake cycle.
  • the rolled 6xxx-series aluminium alloy sheet product according to this invention is ideally suitable for manufacturing formed automotive body members.
  • a formed automotive body member includes bumpers, doors, hoods, roofs, trunk lids, fenders, floors, wheels and other portions of an automotive or vehicle body such as body-in-white (e.g., pillars, reinforcements) applications. Due to its combination of excellent deep drawing and stretch forming properties, the rolled 6xxx-series aluminium alloy sheet product is also perfectly suited to produce also inner door panels, wheel arch inner panels, and side panels, spare wheel carrier panels, and similar panels with a high deep drawing height.
  • Each ingot has been homogenised for 10 hours at about 560°C and hot rolled from 80 mm to 10 mm.
  • the hot-mill entry temperature was about 550°C.
  • the sheet products were cold rolled from 10 mm to 3.0 mm, followed by a batch interan- nealing at 380°C@2 hrs, and then cold rolled to a final gauge of 1 .0 mm.
  • the sheet products have been solution heat-treated at 560°C for about 1 minute and then cold water quenched to room temperature.
  • yield strength Rp0.2 tensile strength Rm, uniform elongation Ag, elongation at fracture A80, strain hardening exponent n, r90°-value
  • EDH Erichsen Dome Height
  • alloy no. 8 is an alloy according to the invention and has an Fe/Sr ratio of 10.
  • Each ingot has been homogenised for 9 hours at about 560°C and hot rolled to 7.5 mm.
  • the hot-mill entry temperature was about 490°C.
  • the sheet products were cold rolled to 3 mm, followed by a batch interannealing at 380°C@2 hrs, and then cold rolled to a final gauge of 1 .0 mm.
  • the sheet products have been solution heat-treated at 565°C and then cold water quenched to room temperature.
  • EH Erichsen Dome Height
  • Samples of alloy 7 and 8 in the T4 condition have been analysed for several microstructural features, in particular the average grain size using standard light optical microscopy techniques at a magnification of 100x.
  • the particle distribution of coarse Si particles larger than 0.35 ⁇ has been analysed using standard light opti- cal microscopy techniques at a magnification of 500x, and the results are listed in Table 5.
  • the Mg2Si particles distribution larger than 0.35 ⁇ has been analysed using SEM at a magnification of 500x, and the results are listed in Table 6.
  • the average grain size in the RD direction through thickness for alloy 7 was 58.2 m and for alloy 8 it was 50.2 ⁇ .
  • the average grain size in the ND direction through thickness for alloy 7 was 58.2 m and for alloy 8 it was 39.5 ⁇ .
  • Table 5 Microstructural feature: the coarse Si particles (>0.35 ⁇ ) distribution
  • the purposive addition of Sr decreases the area fraction, the number density, and the size (circular equivalent average radius) of coarse Si particles, and also the area fraction, the number density and the size (circular equivalent average radius) of coarse Mg2Si particles.
  • the addition of Sr decreases also the average grain size. This contributes to an increased formability of the 6xxx-series aluminium sheet material, in particular the stretch formability as indicated, for example, by the Erichsen Dome Height test results and increases also the elongation.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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Abstract

L'invention concerne un produit en feuille d'alliage d'aluminium de série 6xxx laminé, comprenant, en % en poids : Mg : 0,10 à 1,3 %, Si : 0,25 à 1,4 %, Cu : jusqu'à 0,45 %, Mn : jusqu'à 0,50 %, Fe : 0,10 à 0,45 %, Sr : 0,01 à 0,05 %, le rapport Fe/Sr étant dans une plage de 4 à 40, Ti : jusqu'à 0,20 %, Cr : jusqu'à 0,30 %, Zr : jusqu'à 0,20 %, V : jusqu'à 0,20 %, Zn : jusqu'à 0,35 %, Sn : jusqu'à 0,075 %, des impuretés, le reste étant de l'aluminium. L'invention concerne en outre un procédé de fabrication du produit en feuille d'alliage d'aluminium de série 6xxx.
PCT/EP2018/069976 2017-08-01 2018-07-24 Produit en feuille laminé de série 6xxxx à formabilité améliorée WO2019025227A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201880044588.7A CN110832092A (zh) 2017-08-01 2018-07-24 具有改善的成型性的6xxxx-系列轧制片材产品
US16/628,303 US20200216938A1 (en) 2017-08-01 2018-07-24 6xxxx-series rolled sheet product with improved formability
EP18755718.6A EP3662091A1 (fr) 2017-08-01 2018-07-24 Produit en feuille laminé de série 6xxxx à formabilité améliorée

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP17184151.3 2017-08-01
EP17184151 2017-08-01

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WO2019025227A1 true WO2019025227A1 (fr) 2019-02-07

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US (1) US20200216938A1 (fr)
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WO (1) WO2019025227A1 (fr)

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EP3827108B1 (fr) 2018-07-23 2023-01-25 Novelis, Inc. Alliages d'aluminium recyclés à aptitude au formage élevée et leurs procédés de préparation
EP4190932A1 (fr) * 2021-12-01 2023-06-07 Constellium Bowling Green LLC Tôles, plaques ou ébauches en alliage d'aluminium de la série 6xxx à formabilité améliorée
RU2815086C1 (ru) * 2023-10-20 2024-03-11 Общество с ограниченной ответственностью "Институт легких материалов и технологий" Сплав на основе алюминия

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CN112626385B (zh) * 2020-11-04 2022-08-16 佛山科学技术学院 一种高塑性快速时效响应的铝合金及其制备方法和应用
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CN116334455A (zh) * 2023-03-09 2023-06-27 魏桥轻量化(苏州)科技有限公司 一种铝合金挤压型材的制备方法及应用
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CN117587301B (zh) * 2023-10-13 2024-06-25 广东豪美技术创新研究院有限公司 一种高强高导电Al-Si-Mg铝合金及其制备方法

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