EP3350355B1 - Verfahren zur herstellung von extrudierten profilen, die mit hochglänzenden oberflächen anodisiert werden können, während die profile aus aushärtbarer, nach kaltumformung rekristallisierbarer 7xxx-aluminiumlegierung extrudiert werden - Google Patents

Verfahren zur herstellung von extrudierten profilen, die mit hochglänzenden oberflächen anodisiert werden können, während die profile aus aushärtbarer, nach kaltumformung rekristallisierbarer 7xxx-aluminiumlegierung extrudiert werden Download PDF

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EP3350355B1
EP3350355B1 EP16846935.1A EP16846935A EP3350355B1 EP 3350355 B1 EP3350355 B1 EP 3350355B1 EP 16846935 A EP16846935 A EP 16846935A EP 3350355 B1 EP3350355 B1 EP 3350355B1
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profile
temperature
extruded
alloy
grain
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French (fr)
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EP3350355A1 (de
EP3350355A4 (de
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Ulf Tundal
Oddvin Reiso
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Norsk Hydro ASA
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Norsk Hydro ASA
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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
    • C22F1/043—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
    • 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
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
    • 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
    • B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences

Definitions

  • the present invention relates to a method for the manufacturing of extruded profiles that can be anodized with high gloss surfaces, the profiles being extruded of an age hardenable aluminium alloy that can be recrystallized after cold deformation, for example 7xxx (Al-Mg-Zn) alloys.
  • the oxide layer (Al203) formed during anodizing is build up by dissolving the outer layer of the aluminium. For each 3 ⁇ of oxide layer formed 2 um of the aluminium is dissolved. Since the oxide layer is bulkier than the aluminium the total thickness will then increase by 1 um.
  • EP3129517 relates to a method for manufacturing products with anodized high gloss surfaces from extruded profiles of Ai-Mg-Si or AS-Mg-Si-Cu. The patent is silent on the use of 7XXX alloys.
  • US 2008/173378 A1 relates to a method of manufacturing a wrought aluminum alloy product of an AA7000-series alloy comprising 3 to 10% Zn, 1 to 3% Mg, at most 2.5% Cu, Fe ⁇ 0.25%, and Si ⁇ 0.12%, the method including hot working the stock by one or more methods selected from the group consisting of rolling, extrusion, and forging.
  • Hardening precipitates are formed during the artificial ageing process (e.g. ⁇ "-MgSi) from the addition of Mg and Si. If Cu is added in sufficient amount other phases than ⁇ " may form (e.g. Q' and L) ⁇ Calin D. Marioara, et. al., Improving Thermal Stability in Cu-Containing Al-Mg-Si Alloys by Precipitate Optimization, METALLURGICAL AND MATERIALS TRANSACTIONS A, March 2014 ). These hardening precipitates are much smaller than 0.3 um and are therefore not reducing the gloss in the same way as the primary AlFeSi particles. The strength requirement for the alloy determines the necessary amount of Mg, Si and Cu in the alloy.
  • Alloying elements such as Mn, Cr, Zr or Sc can be added to form dispersoid particles during homogenization. Frequently, these elements are added in high amounts in order to prevent recrystallization in the extruded profile. However, it can be beneficial to add these elements in smaller amounts to only have some dispersoid particles in the alloy in order to avoid grain growth during homogenization and after the recrystallization process occurring in the extrusion process or in a separate recrystallization and solutionising process for the cold deformed material. The size of these particles is typically between 0.01-0.2 ⁇ . Thus, such particles can be added, at least in a relative low number, without significantly affecting the gloss.
  • the number of dispersoid particles should not be so high that the exposed areas of the profile surface get a mixture of a non- recrystallized and a recrystallized structure or a fully recrystallized structure with a large and uneven grain size. Addition of elements that form dispersoid particles can also give an unwanted color of the anodizing layer, or they can give an unwanted surface appearance due to a strong texture of the recrystallized grains.
  • an anodized surface contains large grains the individual grains can be detected by the naked eye. This surface defect is frequently called mottling. The best surface appearance is obtained when the average grain size is smaller than approximately 70 um and the grains mainly are randomly orientated.
  • the homogenizing temperatures are normally lower than for a 6060 alloy. This may reduce the problem with abnormal grain growth during homogenization.
  • the billet grain size will probably not affect the grain size in the extruded profile much if the extent of deformation is high, for example when extruding thin walled hollow profiles. For solid shapes, and especially for thick walled profiles, the billet grain size will most likely affect the grain size in the extruded profile.
  • An additional challenge is that the billet temperature needs to be rather high in order to dissolve the Mg2Si particles, and a high billet temperature makes it more difficult to obtain a small grain size after extrusion.
  • an extruded profile In an extruded profile, one usually sees a surface layer of mainly randomly oriented grains and typically one or a few grains in thickness. Underneath this layer one typically finds a region of larger grains. The thickness of this layer varies, and is usually thicker for a thick walled and wide solid shape profile and thicker towards the back end of the extruded length.
  • An example of a typical grain structure in a cross section of a thick walled industrially extruded profile can be seen in Figure 2 . Below the layer of larger grains the grain structure is typically more homogeneous. The grains in the homogeneous center region of the cross section are predominantly aligned in one direction, with a strong cube texture.
  • the exposed surface can consist of grains from the coarse grain layer beneath the surface layer of the extruded profile. Due to this the entire coarse grain layer has to be removed before starting to machine the shape of the final product.
  • the thickness of the layer that has to be removed due to coarse grains will vary with the width of the profile and the extrusion conditions and is typically in the range of 0.2 to 1 mm.
  • the present invention deals with the task to get a homogeneous grain structure with an average grain size below approximately 70 um irrespective of the Fe content, the grain size in the billet prior to extrusion and the extrusion conditions.
  • Solid shape profiles which are blanks for consumer electronics will be more or less flat, but could possibly have some features in the cross section in order to save material and machining. Such profiles are therefore very well suited for cold rolling after extrusion. By cold rolling a profile by a minimum of 10% followed by flash annealing a new recrystallization process will take place. With sufficient deformation and a proper annealing process the resulting grain structure will be homogeneous over the cross section with a much more random orientation of the grains than in the as extruded profile.
  • the grain size will in addition to the alloy content, depend on the degree of cold deformation, the annealing temperature, the heat up conditions and the time at the annealing temperature. In an alloy with very low Fe and no dispersoid particles the recrystallization will take place at a low temperature, most likely during heating to the annealing temperature. One issue will then be to avoid grain growth at the annealing temperature when there are almost no particles in the material to pin the grains.
  • the annealing temperature should preferably be above the solvus temperature for Zn2Mg particles (7xxx) in order to avoid particles that can reduce the strength and the gloss of the anodized material.
  • the time at this annealing temperature should be as short as possible in order to avoid grain growth. Therefore, the material should be processed through extrusion in a way that Mg2Si or Zn2Mg particles are avoided. This means sufficiently high billet temperature in combination with a high enough exit temperature from extrusion and fast cooling of the profile after extrusion. With no Mg2Si or Zn2Mg particles in the material prior to cold rolling and annealing there is no need for a holding time for the material at the annealing temperature.
  • Mg-Si containing precipitates or Zn2Mg precipitates larger than approximately 0.3 um may form. These particles will contribute to a reduction in the gloss and in the strength of the material. The amount of this reduction will depend on the actual time-temperature history during the flash annealing and cooling operation and the composition of the alloy.
  • An industrial process to perform the cold rolling and the annealing process could be done as shown schematically in Figure 3 .
  • the cold rolling station should be followed by a station for performing fast heating to the annealing temperature. Using induction heating is probably the best way to do this.
  • the profile In order to avoid precipitation of Mg-Si containing precipitates or Zn2Mg precipitates larger than approximately 0.3 um the profile needs to be cooled rather rapidly down to room temperature. The reason for this is described in a previous section.
  • the profile is flash annealed with a heating time of maximum two minutes to a temperature of between 450 - 530 °C and held at this temperature for not more than 5 minutes and subsequently quenched.
  • Billets with diameter 95 mm were cast in a lab casting facility using the Hycast hot-top gas-slip technology (as described in EP 0 778 097 B1 ) and a T1B2 based grain refiner.
  • the composition of the alloy is shown in Table 1.
  • the billets were homogenized at 575°C for 2 hours and 15 minutes followed by cooling at a rate of approximately 400°C per hour.
  • Extrusion of the billets was performed at an 8 MN laboratory extrusion press with a 100 mm diameter container to a profile with 5x40 mm ⁇ 2>cross section.
  • the billet preheating temperature was approximately 500°C and the extrusion speed 20 m/min.
  • After extrusion the profile was quenched in water.
  • a 50 cm long piece from the front part of the extruded profile was cold rolled to give 10, 20, 40 and 60% reduction in the thickness.
  • the samples that were cold rolled to different thicknesses were then annealed in a salt bath which had been preheated to 500°C.
  • thermocouple A hole was drilled into each of the samples to fit a thermocouple.
  • the heating time to temperature was in the range 5 - 10 seconds, depending on the thickness of the sample.
  • a holding time of 10 seconds started when the temperature reached 490°C.
  • the cross section of all samples were prepared by grinding and mechanical polishing with a final step using 1 um diamond paste.
  • anodising was performed in a Struers Lectropol-5 with the following parameters. Voltage: 45 V; Flow rate: 3; Temperature: -5°C; Time: 2 minutes.
  • the electrolyte had the following ingredients: 74% distilled water; 24% ethanol; 1 % HBF4(35%); 1 % HF (40%).
  • the billets Prior to extrusion the billets had an even and small grain size.
  • the as extruded sample in Figure 4 shows a homogeneous grain size throughout the cross section. In this case there is no significant coarse grain layer below the surface. This is maybe because the sample is smaller than the sample shown in Figure 2 and maybe also because it is taken from the front part of the extruded length. It is evident that the grains under the randomly oriented layer of grains in the profile surface area are predominantly aligned in one direction since the color contrast between the grains is low.
  • the cold rolled and annealed samples show a much more random orientation of the grains than the as extruded sample. This confirms that these samples are fully recrystallized after annealing.
  • the samples that were cold rolled to 10 and 20% reduction in thicknesses clearly have an uneven grain structure with the largest grains in the middle of the cross section.
  • the samples that were cold rolled to 40 and 60% reduction in thicknesses have an even grain structure throughout the cross section.
  • the grain sizes of the samples shown in Figure 4 (measured 250 um below the surface of the cross sections) are shown in Table 2. Table 2. Average grain sizes of the 6060 alloy samples in example 1 as measured 250 um below the surface of the cross section.
  • the as extruded grain size is very uncertain due to the very low contrast between the individual grains.
  • Billets with diameter 95 mm were cast in a lab casting facility using the Hycast hot-top gas-slip technology without using a grain refiner.
  • a picture of a macro etched billet slice is shown in Figure 5 together with a micrograph showing an anodized sample viewed in polarized light in the light optical microscope. Towards the surface there are some relatively large equiaxed grains, but a large part of the cross section of the billet slice consists of feather crystals.
  • the composition of the alloy is shown in Table 3.
  • the cast billets were homogenized at 575°C for 2 hours and 15 minutes followed by cooling at a rate of approximately 400°C per hour.
  • Micrographs of the particle structure in the billets from the two different alloys in examples 1 and 2 are shown in Figure 6 .
  • the material cast without grain refiner shows Fe containing particles (mainly a-AlFeSi) that are smaller and much more evenly distributed than the Fe containing particles (mainly ⁇ -AlFeSi) in material cast with grain refiner (lower picture).
  • the AlFeSi particles mainly are located at the grain boundaries.
  • the Fe/Si ratio is very low, which makes ⁇ -AlFeSi particles very stable in the homogenizing process.
  • a particle structure as shown in the material cast without a grain refiner would be beneficial in avoiding alignment of particles and possible visible dark lines in the extruded and anodized high gloss surface.
  • the billets were extruded at an 8 MN laboratory extrusion press with a 100 mm diameter container to a profile with a cross section of 5x40 mm ⁇ 2>.
  • the billet preheating temperature was approximately 500°C and the extrusion speed 20 m/min. After extrusion the profile was quenched in water.
  • a 100 cm long piece from the back part of the extruded profile was cold rolled to give 20, 30, 40 and 50% reduction in the thickness.
  • the samples that were cold rolled to different thicknesses were then annealed in a salt bath which had been preheated to 500°C.
  • a hole was drilled into each of the samples to fit a thermocouple.
  • the holding time of 10 seconds started when the temperature reached 490°C.
  • the samples were quenched in water.
  • one sample of the material cold rolled to 40 % reduction in thickness was held 5 minutes at 500°C.
  • Figure 8 shows micrographs of the grain structure in the as extruded sample as well as samples that have been cold rolled 20, 30, 40 and 50% and thereafter annealed.
  • the sample that was cold rolled to 20% reduction in thickness clearly has an uneven grain structure with the largest grains in the middle of the cross section.
  • the sample cold rolled to 30% reduction in thickness has smaller grains and a more even grain structure, but the grains in the middle still are somewhat larger than those towards the surfaces.
  • the samples that were cold rolled to 40 and 50% reduction in thicknesses have a smaller grain size and an even grain structure throughout the cross section.
  • Table 4 the grain size seems to be similar for the samples cold rolled to 40 and 50% reduction in thicknesses.
  • Figure 9 shows that the sample heated in an air-circulating furnace (6-7 minutes heating time) has a more uneven grain structure and a slightly larger grain size than the sample that was rapidly heated (5-10 seconds) in a salt bath up to the solutionizing temperature.
  • the reason for this is probably linked to precipitation of Mg-Si particles at the grain boundaries, which are pinning the nuclei for new grains during the heat up process.
  • a sample which is slowly heated in air there is enough time for precipitation of Mg-Si particles to prevent the nuclei for new grains from growing until the particles start to dissolve again, i.e. when the sample is approaching the solvus temperature of the alloy.
  • Example 2 shows that it is beneficial to heat the cold rolled sample fast to the solutionizing temperature to obtain an even grain size and that a holding time of only 10 seconds is sufficient to obtain a fully recrystallized grain structure.
  • Example 2 also shows that the final grain structure in the blanks could be perfect for providing attractive high gloss anodized surfaces even though the billet grain structure is regarded as being far from optimum when it is cast without grain refiner.
  • Billets with diameter 95 mm of a 7030 alloy were cast in a lab casting facility using the Hycast hot-top gas-slip technology and a T1B2 based grain refiner.
  • the chemical composition of the alloy is shown in Table 5.
  • the billets of the 7030 alloy were homogenised for 4 hours at 500°C.
  • the billets were extruded at an 8 MN laboratory extrusion press with a 100 mm diameter container to a profile with a cross section of 5x40 mm ⁇ 2>.
  • the billet preheating temperature was approximately 500°C and the extrusion speed 12.5 m/min. After extrusion the profile was quenched in water.
  • a 100 cm long piece from the extruded profile was cold rolled to give 20, 30, 40 and 50% reduction in the thickness.
  • the cold rolled samples at different thicknesses were then, one by one, put into a salt bath that had been preheated to 500°C. With a thermocouple drilled into each sample it was possible to monitor the temperature of the sample. All samples were held approximately 10 seconds at a temperature above 495°C before quenching in water. The heating rates of the samples depended on the thickness, but in all cases the heating time was less than 10 seconds.
  • Figure 10 shows the grain structure through the transverse cross section of a 7030 sample that has been cold rolled to a 10% reduction in thickness and subsequently flash annealed in a salt bath.
  • the grain structure is very uneven, with some grains being more than 500 ⁇ in diameter. This shows that 10% deformation by rolling is too little to create a uniform grain structure through the cross section of the material.
  • Figure 11 shows the grain structures through the thickness of a transverse cross section of an as extruded 7030 profile as well as of samples that have been cold rolled to 20, 30, 40 and 50% reduction in thicknesses and subsequently flash annealed.
  • the grain structure of the as extruded sample is significantly coarser than the grain structure in the 6060 alloy. This could either be a result of the lower extrusion speed used for the 7030 alloy or a higher solute drag from the high amount of Mg, Zn and Cu in this alloy.
  • the sample rolled 20% show a slightly coarser grain structure than the as extruded sample, especially in the middle of the cross section.
  • the sample rolled 30% has a grain structure that would fulfil the requirements of a grain size below about 70 ⁇ , but the grain size in the middle is somewhat larger than towards the surface.
  • the grain structures in the samples cold rolled by 40 and 50% show a very nice grain structure throughout the cross section. Based on the visual appearance of the anodized grain structures, the as extruded sample of the 7030 alloy does not seem to have the same strong cube texture as the 6060 alloy.
  • the grain structure is also very uniform towards the ends of the cross section when a sample of a 7030 alloy has been cold rolled by 40% before the flash annealing process.
  • the grain sizes of some of the samples depend on the depth below the surface of the cross section. Some samples have very coarse grains in the middle of the cross section and finer grains towards both surfaces. A typical machining depth to remove the coarse surface grain layer in a small profile like this would be around 250 ⁇ , and this depth was chosen for the grain size measurements.
  • Table 6 below the grain sizes for the alloy of Example 3 are listed. By looking at these grain size measurements alone, all the samples seem to fulfil the requirement of a grain size below approximately 70 um. However, the pictures in Figure 1 1 give a better overview of the grain structures in the samples. From the grain size measurements and the pictures one can state that all samples with 30, 40 and 50% cold rolling followed by annealing fulfil the grain structure requirements for the alloy. With less deformation the grain structure seems to be too uneven.
  • the main benefit of the present invention is that it is possible to obtain a grain structure with an even grain size and a close to random texture throughout the cross section of a profile irrespective of the grain size in the profile after it has been extruded and thus also irrespective of the grain structure of the billet before extrusion.
  • This improvement in grain structure is obtained by cold rolling deformation of the extruded profile followed by flash annealing.
  • An extruded thick walled flat profile will in most cases have a coarse grain layer that according to the state of the art has to be removed in order to obtain a smooth anodized surface with a minimum of defects in the final product.
  • the amount of material that would have to be removed in the as extruded cross section is typically in the range 7-15%.
  • the cold rolling will ensure a very accurate thickness and flatness of the profile, and for that reason considerably reduce the need for machining.
  • An extruded profile will have much more variation in the thickness, typically ⁇ 0.15 mm (the variation could also be higher for very wide profiles, especially for 7xxx alloys).
  • the grain size in the billet and the extruded profile is of little importance for the resulting grain size in the cold rolled and annealed blanks there is a possibility of casting the billets with a minimum or even completely without the use of a grain refiner.
  • a grain refiner In order to avoid center cracks in the billets in the startup of the cast it could be beneficial to add some grain refiner in the first metal to cast.
  • the grain refiner itself could be a source for inclusions that can cause failures in the anodized surface.
  • the possibility of reducing the Fe content and still obtain an adequate grain structure will significantly improve with the use of the present invention.
  • the lower Fe content can either be used to improve the gloss, or to keep the current gloss but add a thicker and more wear resistant oxide layer to the anodized product. The latter will make the product more durable.

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Claims (11)

  1. Verfahren zur Herstellung von extrudierten Profilen, die mit hochglänzenden Oberflächen anodisiert werden können, wobei die Profile aus aushärtbarer, nach Kaltumformung rekristallisierbarer Aluminiumlegierung extrudiert werden können, wobei die Legierung zuerst zu Extrusionsknüppeln gegossen wird, wobei die Knüppel bei einer Haltetemperatur zwischen 480 °C und 620 °C homogenisiert und bei dieser Temperatur 0-12 Stunden lang ausgeglichen werden, woraufhin die Knüppel Kühlung von der Homogenisierungstemperatur mit einer Rate von 150 °C/h oder schneller unterworfen werden,
    a) die Knüppel auf eine Temperatur zwischen 400 und 540 °C vorerhitzt und extrudiert und schnell auf Raumtemperatur heruntergekühlt werden,
    b) Umformen des Profils um mehr als 10 % durch einen Kaltwalzvorgang, woraufhin c), das Profil in einer Erhitzungszeit von maximal zwei Minuten auf eine Temperatur zwischen 400 - 530 °C schnellausgeglüht und bei dieser Temperatur nicht länger als 5 Minuten lang gehalten wird, um eine durchschnittliche Korngröße von etwa 100 µm oder weniger zu erhalten, und daraufhin abgeschreckt wird und
    d) das Profil schließlich gealtert wird,
    wobei
    die Legierung eine 7xxx-Legierung ist, die, in Gew. -% :
    Si: 0,00-0,30
    Mg: 0,50-2,00
    Fe: 0,00-0,15
    Cu: 0,00-0,30
    Mn: 0,00-0,20
    Cr: 0,00-0,10
    Zr: 0,00-0,20
    Sc: 0,00-0,10
    Zn: 3,00-7,00
    Ti: 0,00-0,05 und
    einschließlich zufälliger Verunreinigungen und den Rest als Al enthält.
  2. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass das Profil zwischen Schritt c) und d) ferner einem Kaltumformungsvorgang, bevorzugt durch Strecken zum Entfernen restlicher Spannungen von Kühlen unterworfen wird.
  3. Verfahren nach Anspruch 1
    dadurch gekennzeichnet, dass das Profil zwischen Schritt c) und d) zu Rohlingen geschnitten wird, die zu einer Gestalt kaltgeformt werden, die Material und maschinelle Bearbeitungszeit spart, um das Endprodukt herzustellen.
  4. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass
    das Profil Schritt b) entsprechend mehr als 20 % umgeformt wird.
  5. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass das Profil Schritt b) entsprechend bevorzugt 30 bis 50 % umgeformt wird.
  6. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass das Profil Schritt c) entsprechend in einer Erhitzungszeit von maximal 20 Sekunden auf eine Temperatur zwischen 400 - 530 °C schnellausgeglüht und bei dieser Temperatur nicht länger als 1 Minute gehalten wird.
  7. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass
    das Schnellausglüherhitzen Schritt c) entsprechend durch Induktionserhitzen des Profils erhalten wird.
  8. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass das Schnellausglüherhitzen Schritt c) entsprechend durch Unterwerfen des Profils einem Salzbad- oder anderen Konvektions- oder
    Strahlungserhitzungsmittel, das hohe Erhitzungsraten bereitstellt, erhalten wird.
  9. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass die Legierung ohne Verwendung von Kornfeiner, mit Ausnahme des Anfahrens des Gießvorgangs, gegossen wird.
  10. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass die Alterung, Schritt d), ein Einschritt-, Zweischritt- oder Dualratealterungsvorgang auf eine endgültige Haltetemperatur zwischen 100 °C und 220 °C ist und wobei der gesamte Alterungszyklus innerhalb einer Zeitspanne zwischen 3 und 24 Stunden ausgeführt wird.
  11. Verfahren nach Anspruch 1,
    dadurch gekennzeichnet, dass die durchschnittliche Korngröße Verfahrensschritt c) entsprechend 70 µm oder weniger beträgt.
EP16846935.1A 2015-09-18 2016-04-20 Verfahren zur herstellung von extrudierten profilen, die mit hochglänzenden oberflächen anodisiert werden können, während die profile aus aushärtbarer, nach kaltumformung rekristallisierbarer 7xxx-aluminiumlegierung extrudiert werden Active EP3350355B1 (de)

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NO20151232 2015-09-18
PCT/NO2016/000014 WO2017048130A1 (en) 2015-09-18 2016-04-20 Method for the manufacturing of extruded profiles that can be anodized with high gloss surfaces, the profiles being extruded of an age hardenable aluminium alloy that can be recrystallized after cold deformation, for example a 6xxx or a 7xxx alloy

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EP3350355A1 EP3350355A1 (de) 2018-07-25
EP3350355A4 EP3350355A4 (de) 2019-03-27
EP3350355B1 true EP3350355B1 (de) 2020-08-19

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EP16846935.1A Active EP3350355B1 (de) 2015-09-18 2016-04-20 Verfahren zur herstellung von extrudierten profilen, die mit hochglänzenden oberflächen anodisiert werden können, während die profile aus aushärtbarer, nach kaltumformung rekristallisierbarer 7xxx-aluminiumlegierung extrudiert werden

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CN112676550B (zh) * 2019-10-17 2022-09-27 北京小米移动软件有限公司 铝合金构件加工方法
CN110735073B (zh) * 2019-11-04 2020-12-18 苏州大学 一种高质量6系铝合金挤压铸坯及其制备方法
CN110983084A (zh) * 2019-12-28 2020-04-10 东北轻合金有限责任公司 一种低淬火敏感性超厚板的制造方法
CN115318859A (zh) * 2022-07-14 2022-11-11 栋梁铝业有限公司 一种低温高速挤出的铝合金制备方法
CN115747540B (zh) * 2022-12-09 2023-12-22 东莞市铝美铝型材有限公司 一种热挤压铝合金型材的制备工艺

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JPS58224141A (ja) * 1982-06-21 1983-12-26 Sumitomo Light Metal Ind Ltd 成形用アルミニウム合金冷延板の製造方法
NL9100565A (nl) * 1991-04-02 1992-11-02 Hoogovens Aluminium Nv Aluminium plaat en werkwijze voor het vervaardigen daarvan.
JPH10306336A (ja) * 1997-05-01 1998-11-17 Sumitomo Light Metal Ind Ltd 陽極酸化処理後の表面光沢性に優れたアルミニウム合金押出材およびその製造方法
FR2902442B1 (fr) * 2006-06-16 2010-09-03 Aleris Aluminum Koblenz Gmbh Alliage de la serie aa6xxx, a grande tolerance aux dommages pour l'industrie aerospatiale
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US20170009322A1 (en) * 2014-03-27 2017-01-12 Norsk Hydro Asa Method for the manufacturing of products with anodized high gloss surfaces from extruded profiles of al-mg-si or al-mg-si cu extrusion alloys

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