EP2175042B1 - Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component - Google Patents
Corrosion-resistant aluminium extrusion profile and method for manufacturing a structure component Download PDFInfo
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- EP2175042B1 EP2175042B1 EP20090011984 EP09011984A EP2175042B1 EP 2175042 B1 EP2175042 B1 EP 2175042B1 EP 20090011984 EP20090011984 EP 20090011984 EP 09011984 A EP09011984 A EP 09011984A EP 2175042 B1 EP2175042 B1 EP 2175042B1
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- 229910052782 aluminium Inorganic materials 0.000 title claims description 12
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims description 9
- 238000001125 extrusion Methods 0.000 title claims description 9
- 230000007797 corrosion Effects 0.000 title claims description 8
- 238000005260 corrosion Methods 0.000 title claims description 8
- 238000000034 method Methods 0.000 title claims description 8
- 238000004519 manufacturing process Methods 0.000 title claims description 5
- 239000004411 aluminium Substances 0.000 title claims 2
- 229910045601 alloy Inorganic materials 0.000 claims description 30
- 239000000956 alloy Substances 0.000 claims description 30
- 239000011777 magnesium Substances 0.000 claims description 18
- 229910052749 magnesium Inorganic materials 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 5
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 4
- 238000000265 homogenisation Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 239000000155 melt Substances 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 229910016570 AlCu Inorganic materials 0.000 claims description 2
- 229910019752 Mg2Si Inorganic materials 0.000 claims description 2
- 238000009749 continuous casting Methods 0.000 claims description 2
- 239000010949 copper Substances 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 239000011651 chromium Substances 0.000 description 7
- 239000011572 manganese Substances 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 5
- 229910000838 Al alloy Inorganic materials 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 3
- 238000007792 addition Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 230000006735 deficit Effects 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005660 chlorination reaction Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- NLYAJNPCOHFWQQ-UHFFFAOYSA-N kaolin Chemical compound O.O.O=[Al]O[Si](=O)O[Si](=O)O[Al]=O NLYAJNPCOHFWQQ-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
Images
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
- 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
Definitions
- the invention relates to a corrosion-resistant aluminum extruded profile of an ALSiMg alloy, preferably a multi-chamber hollow profile and method for
- the strength of aluminum wrought alloys of the AlMgSi type (6xxxx alloys) is essentially set by the alloying process (D. Altenpohl: "Aluminum viewed from the inside", Aluminum-Verlag). In this case, foreign atoms or precipitates act as impurities in the lattice of the Al microstructure. In the AlMgSi alloy type, it is the Mg 2 Si intermetallic compound which increases strength.
- N.C. Parson et al. investigated Alloy Extrusion Ingots' microstructural alterations of 6000 series aluminum alloys at different homogenization parameters in The Effect of Heat Treatment.
- JP 11181539 discloses an Al-Mg-Si-Cu alloy which is free of a recrystallized structure in the surface layer.
- the aluminum alloy is composed of 0.8-1.2 wt.% Mg, 0.4 to 0.8 wt.% Si, 0.15 to 0.4 wt.% Cu, Al and other substances.
- JP 2000282162 discloses 6000 series Al alloys with high corrosion protection even in an aggressive environment of Cl ions.
- the object of the present invention was to produce an extruded profile, with which at least the previously known deformation and corrosion properties are achieved, but with higher strength properties, namely Rp 0.2> 280 MPa, Rm ⁇ 300 MPa and A ⁇ 10%.
- the extruded profile according to the invention also has a microstructure with molded intermetallic phases of the type alpha-AlFeSi, beta-AlFeSi, Al15FeMn3Si2, Mg2Si, theta-AlCu, the particles of intermetallic phases being globulitically shaped and having a diameter ⁇ 1 ⁇ m.
- the H 2 content of the melt is adjusted in the usual way by chlorination, by nitrogen or argon rinsing treatment.
- the alloy is characterized by an excess of Mg, with the preferred weight ratio of magnesium to silicon in the alloy composition ranging from 1 to 2 at an alloy content of Si 0.30-0.60%.
- the deformation properties and the ductility can be significantly improved if the contents of Mn, Fe, Cu and optionally Ti and Cr are significantly limited (see claim 1).
- Mn and Cr are added during homogenization form dispersoids which can prevent recrystallization of the microstructure. These dispersoids reduce the local stresses in the structure and thereby increase the ductility.
- the optimum content for Mn is between 0.05 and 0.10 and for Cr between 0.01 and 0.12%.
- Titanium also increases ductility, with the content being between 0.01-0.12%.
- the alloy is cast in a continuous casting process and then homogenized in the temperature range between 450 and 600 ° C in 1-10h.
- the extruded profile is subjected to an immediate heat treatment in the temperature range 160-250 ° C for 20-1800min.
- Table 1 Heat treatment and technological properties for four types of alloys according to the invention and two comparative alloys
- Table 2 Alloy composition of the alloys according to the invention and of the comparative alloys in% by weight
- Image 1 Microstructure of a structural component produced according to the invention
- Picture 2 Microstructure of a structural component according to the prior art
- Picture 3 Profile cross-section of the examined structural component
- test numbers I to VI Six different hollow profiles (test numbers I to VI) with the homogenization conditions specified in Table 1 were produced by extrusion and subsequently heat-treated.
- test numbers III, IV, V and VI showed good deformation and corrosion properties with increased strength and acceptable elongation values.
- the special properties are based on the fact that the intermetallic phases of the type Mg 2 Si, Al 3 Fe, Al 2 Cu were formed during the heat treatment, so that globulitic particles ⁇ 1 ⁇ were uniformly distributed. This is shown by the micrograph Figure 1 for a hollow profile of the invention produced according to the invention V1 according to Table 2.
- the hollow profile produced according to the prior art by heat treatment to the state T6 with Mg deficit according to test number I shows a significantly poorer deformation behavior.
- the reason for this lies in the needle-shaped to plate-shaped structures of the intermetallic compounds, as the micrograph figure 2 shows.
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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)
- Extrusion Of Metal (AREA)
- Continuous Casting (AREA)
- Powder Metallurgy (AREA)
Description
Die Erfindung betrifft ein korrosionsbeständiges Aluminiumstrangpressprofil aus einer ALSiMg-Legierung, vorzugsweise ein Mehrkammerhohlprofil und Verfahren zurThe invention relates to a corrosion-resistant aluminum extruded profile of an ALSiMg alloy, preferably a multi-chamber hollow profile and method for
Herstellung eines Strangpressprofils.Production of an extruded profile.
Die Festigkeit bei Aluminium-Knetlegierungen vom Typ AlMgSi (6xxxx-Legierungen) wird im Wesentlichen durch die Legierungsverfestigung eingestellt (D. Altenpohl: "Aluminium von innen betrachtet", Aluminium-Verlag). Dabei wirken Fremdatome oder Ausscheidungen wie Störstellen im Gitter des Al-Gefüges. Bei dem Legierungstyp AlMgSi ist es die intermetallische Verbindung Mg2Si, die festigkeitssteigernd wirkt.The strength of aluminum wrought alloys of the AlMgSi type (6xxxx alloys) is essentially set by the alloying process (D. Altenpohl: "Aluminum viewed from the inside", Aluminum-Verlag). In this case, foreign atoms or precipitates act as impurities in the lattice of the Al microstructure. In the AlMgSi alloy type, it is the Mg 2 Si intermetallic compound which increases strength.
Viele der derzeit in Europa etablierten Al-Mg-Si-Knetlegierungen orientieren sich daher an der Mg2Si-Gleichgewichtsphase, besitzen aber zusätzlich einen Si-Überschuss. Das frei verfügbare Si bewirkt durch die Mischkristallbildung eine weitere Festigkeitssteigerung. Diese ist mit einem Si-Überschuss effektiver als bei einem gleichgroßen Mg-Überschuss (
Ein Si-Überschuss erhöht jedoch die Abschreckempfindlichkeit der Legierung. Weiterhin neigen diese Legierungen zur Bildung von Korngrenzenausscheidungen, die die Duktilität negativ beeinflussen (F. Ostermann: "Anwendungstechnologie Aluminium", Springer-Verlag). Das Si/Mg-Verhältnis besitzt ferner einen Einfluss auf das Verformungsverhalten (
Duktilität (
N.C. Parson et al. untersuchten in The Effect of Heat Treatment on the Microstructure and Properties of 6000 Series Alloy Extrusion Ingots' mikrostrukturelle Veränderungen von Aluminiumlegierungen der Serie 6000 bei unterschiedlichen Homogenisierungsparametern.N.C. Parson et al. investigated Alloy Extrusion Ingots' microstructural alterations of 6000 series aluminum alloys at different homogenization parameters in The Effect of Heat Treatment.
Die Aufgabe wird erfindungsgemäß gelöst durch ein Strangpressprofil aus der Aluminiumlegierung:
- Si
- 0,30 - 0,60%
- Mg
- 0,8-1,2%
- Mn
- 0,05-0,10%
- Fe
- 0,1-0,3%
- Cu
- 0,1-0,3%
- Ti
- 0,01 - 0,12%
- Si
- 0.30 - 0.60%
- mg
- 0.8-1.2%
- Mn
- 0.05-0.10%
- Fe
- 0.1-0.3%
- Cu
- 0.1-0.3%
- Ti
- 0.01 - 0.12%
Rest Reinaluminium mit den üblichen Verunreinigungen, dem wahlweise ein Gehalt an Cr 0,01-0,12% zugesetzt werden kann.The balance pure aluminum with the usual impurities, which can optionally be added to a content of Cr 0.01-0.12%.
Das erfindungsgemäße Strangpressprofil weist ferner eine Gefügestruktur mit eingeformten intermetallischen Phasen des Typs alpha-AlFeSi, beta-AlFeSi, Al15FeMn3Si2, Mg2Si, theta-AlCu auf, wobei die Partikel aus intermetallischen Phasen globulitisch geformt sind und einen Durchmesser ≤ 1 µm aufweisen.The extruded profile according to the invention also has a microstructure with molded intermetallic phases of the type alpha-AlFeSi, beta-AlFeSi, Al15FeMn3Si2, Mg2Si, theta-AlCu, the particles of intermetallic phases being globulitically shaped and having a diameter ≦ 1 μm.
Vorzugsweise beträgt der H2-Gehalt der Schmelze <=0,15ccm/100gr. Al. Der H2-Gehalt der Schmelze wird in üblicher Weise durch Chlorieren, durch Stickstoff- oder Argon-Spülbehandlung eingestellt.Preferably, the H 2 content of the melt is <= 0.15 ccm / 100gr. Al. The H 2 content of the melt is adjusted in the usual way by chlorination, by nitrogen or argon rinsing treatment.
Die Legierung zeichnet sich durch einen Mg-Überschuss aus, wobei das bevorzugte Gew-Verhältnis von Magnesium zu Silizium in der Legierungszusammensetzung im Bereich von 1 bis 2 bei einem Legierungsgehalt von Si 0,30 - 0,60% liegt.The alloy is characterized by an excess of Mg, with the preferred weight ratio of magnesium to silicon in the alloy composition ranging from 1 to 2 at an alloy content of Si 0.30-0.60%.
Neuere Untersuchungen zeigen, dass mit einem Mg/Si-Verhältnis von nahezu 1 gute Festigkeitsergebnisse erzielt werden können, wobei eine Steigerung der Produktivität dieser Legierungen z.B. durch höhere Pressgeschwindigkeit, niedrigerem Anpressdruck und besserer Oberflächenqualität besonders herausgestellt wird (Comalco Aluminium Ltd.: "6xxx series aluminium alloys",
Allerdings lassen sich die Verformungseigenschaften und die Duktivität wesentlich verbessern, wenn die Gehalte an Mn, Fe, Cu sowie ggf. Ti und Cr deutlich eingeschränkt werden (siehe Anspruch 1).However, the deformation properties and the ductility can be significantly improved if the contents of Mn, Fe, Cu and optionally Ti and Cr are significantly limited (see claim 1).
Es wurde beobachtet, dass Zusätze von Mn und Cr während der Homogenisierung Dispersoide bilden, die eine Rekristallisation des Gefüges verhindern können. Diese Dispersoide verringern die lokalen Spannungen im Gefüge und erhöhen dabei die Duktilität. Der optimale Gehalt für Mn liegt dabei zwischen 0,05 und 0,10 und bei Cr zwischen 0,01 und 0,12 %.It has been observed that additions of Mn and Cr during homogenization form dispersoids which can prevent recrystallization of the microstructure. These dispersoids reduce the local stresses in the structure and thereby increase the ductility. The optimum content for Mn is between 0.05 and 0.10 and for Cr between 0.01 and 0.12%.
Titan erhöht auch die Duktilität, wobei der Gehalt zwischen 0,01 - 0,12 % liegt.Titanium also increases ductility, with the content being between 0.01-0.12%.
Die Legierung wird im Stranggussverfahren vergossen und anschließend homogenisiert im Temperaturbereich zwischen 450 und 600°C in 1-10h. Das Strangpressprofil wird einer sofortigen Wärmebehandlung im Temperaturbereich 160-250°C für 20-1800min unterzogen.The alloy is cast in a continuous casting process and then homogenized in the temperature range between 450 and 600 ° C in 1-10h. The extruded profile is subjected to an immediate heat treatment in the temperature range 160-250 ° C for 20-1800min.
Im Folgenden wird die Erfindung anhand mehrerer Ausführungsbeispiele näher erläutert.In the following the invention will be explained in more detail with reference to several embodiments.
Es zeigen:
Es wurden sechs verschiedene Hohlprofile (Versuchsnummer I bis VI) mit den in Tabelle 1 angegebenen Homogenisierungsbedingungen durch Strangpressen hergestellt und anschließend wärmebehandelt.Six different hollow profiles (test numbers I to VI) with the homogenization conditions specified in Table 1 were produced by extrusion and subsequently heat-treated.
Die technologischen Eigenschaften wurden an Probenstäben gemessen und in Tabelle 1 aufgelistet.The technological properties were measured on specimen rods and listed in Table 1.
Die erfindungsgemäßen Hohlprofile (Versuchsnummern III, IV, V und VI) zeigten gute Verformungs- und Korrosionseigenschaften bei erhöhter Festigkeit und akzeptablen Dehnungswerten.The hollow sections according to the invention (test numbers III, IV, V and VI) showed good deformation and corrosion properties with increased strength and acceptable elongation values.
Die besonderen Eigenschaften beruhen darauf, dass während der Wärmebehandlung die intermetallischen Phasen des Typs Mg2Si, Al3Fe, Al2Cu eingeformt wurden, so dass globulitisch geformte Partikel ≤ 1µ in gleichmäßiger Verteilung vorlagen. Dies zeigt die Gefügeaufnahme Bild 1 für ein erfindungsgemäß hergestelltes Hohlprofil der Legierung V1 gemäß Tabelle 2.The special properties are based on the fact that the intermetallic phases of the type Mg 2 Si, Al 3 Fe, Al 2 Cu were formed during the heat treatment, so that globulitic particles ≤ 1μ were uniformly distributed. This is shown by the micrograph Figure 1 for a hollow profile of the invention produced according to the invention V1 according to Table 2.
Im Vergleich dazu wurde ein Hohlprofil nach dem Stand der Technik hergestellt, wobei die Legierung B1 einen Mg-Unterschuss aufwies. Die genaue Zusammensetzung der Legierungsbeispiele ist Tabelle 2 zu entnehmen.In comparison, a hollow profile according to the prior art was produced, wherein the alloy B1 had a Mg deficit. The exact composition of the alloy examples is shown in Table 2.
Das nach dem Stand der Technik durch Wärmebehandlung auf den Zustand T6 hergestellte Hohlprofil mit Mg-Unterschuss nach Versuchsnummer I zeigt ein deutlich schlechteres Verformungsverhalten. Die Ursache hierfür liegt in den nadelförmigen bis plattenförmigen Strukturen der intermetallischen Verbindungen, wie die Gefügeaufnahme Bild 2 erkennen lässt.The hollow profile produced according to the prior art by heat treatment to the state T6 with Mg deficit according to test number I shows a significantly poorer deformation behavior. The reason for this lies in the needle-shaped to plate-shaped structures of the intermetallic compounds, as the micrograph figure 2 shows.
Zusammenfassend lässt sich feststellen, dass nur durch die Kombination der erfindungsgemäßen Legierungsvarianten V1 - V4 mit den Verfahrensmaßnahmen gemäß Patentanspruch 4, die Lösung der vorliegenden Aufgabenstellung möglich ist. Wie die Versuchsauswertung zeigt, ist es gelungen, die Zugfestigkeiten oberhalb von 300 MPa einzustellen. Dies ist in erster Linie durch entsprechende Gehalte an den Legierungselementen Si, Mg und Cu zu erklären. Mit steigendem Si- und Mg-Gehalt verschlechtert sich das Verformungsverhalten. Durch die Zugabe von Cu und der Temperaturführung während des Fertigungsprozesses konnte gutes Stauchverhalten des Materials beibehalten werden.
** Bewertung 1 bis 10 des Stauchverhaltens nach
1 : starke Rissbildung, Abfallen einzelner Profilteile
10: keine Risse, keine Orangenhaut
*** Korrosionstest analog zu DIN 50 905 (Prüfvorschrift nach Fa.Honsel)
**** wärmebehandelt auf den Zustand T6
**
1: severe cracking, falling off of individual profile parts
10: no cracks, no orange peel
*** Corrosion test analogous to DIN 50 905 (test specification according to the company Honsel)
**** heat treated to the state T6
Überraschender Weise zeigten die nach dem erfindungsgemäßen Verfahren hergestellten Strukturbauteile eine Verbesserung der Kerbschlagzähigkeit. Dies wurde insbesondere an den Legierungen der Versuchs-Nr. V und VI festgestellt, deren Ergebnisse bei den Kerbschlagversuchen um mehr als 10% über den Vergleichswerten der Versuche III. und IV. und um mehr als 20% über den Werten der Versuche I. und II. lagen.Surprisingly, the structural components produced by the process according to the invention showed an improvement in notched impact strength. This was especially true of the alloys of the experiment no. V and VI whose results in the notched-bar impact tests exceeded by more than 10% the comparison values of tests III. and IV. and more than 20% above the values of Experiments I. and II.
Claims (6)
- Corrosion-resistant extruded section of an AlSiMg alloy, preferably a multi-chamber hollow section, characterized by the following alloy composition, in % by weightSi 0.30 - 0,60%Mg 0.8 - 1.2%Mn 0.05 - 0.10%Fe 0.1 - 0.3%Cu 0.1 - 0.3%andTi 0.01 - 0.12% and, optionally,Cr 0.01 - 0.12%;balance pure aluminium containing the impurities conditional to manufacturing;
the said extruded section furthermore having a microstructure with globulized intermetallic phases of the alpha-AlFeSi, beta-AlFeSi, Al15FeMn3Si2, Mg2Si, theta-AlCu type, and the particles of the intermetallic phases having a globulitic shape and a cross-section of ≤1 µm. - The extruded section according to claim 1, characterized bySi 0.40 - 0,60%Mg 0.82 - 0.90%Cu 0.15 - 0.25%.
- The extruded section according to any one of the preceding claims, characterized in that the weight ratio of magnesium to silicon in the alloy composition is in the range from 1 to 2.
- Method for producing an extruded section according to any one of the preceding claims by continuous casting, homogenising and a heat treatment immediately following the extrusion, characterised in that an alloy according to the preceding claims is produced, and the homogenisation is performed between 450 °C and 600 °C for 1 to 10 hours, and that then, immediately following the extrusion, a heat treatment in the range from 160 °C to 260 °C is carried out for 20 to 1800 minutes.
- The method according to claim 4, characterized in that the heat treatment which follows the extrusion is carried out at a temperature of 180 °C to 250 °C for 100 to 1000 minutes.
- The method according to claim 4 or 5, characterized in that, prior to extrusion, the melt has an H2 content of <0.15 cm3/100 g Al.
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WO2011134486A1 (en) | 2010-04-26 | 2011-11-03 | Sapa Ab | Damage tolerant aluminium material having a layered microstructure |
PL3339457T3 (en) | 2012-04-25 | 2020-12-14 | Norsk Hydro Asa | Extruded al-mg-si aluminium alloy profile with improved properties |
CA2817425C (en) | 2012-05-31 | 2020-07-21 | Rio Tinto Alcan International Limited | Aluminium alloy combining high strength, elongation and extrudability |
CN103060634A (en) * | 2012-12-31 | 2013-04-24 | 张家港市金邦铝业有限公司 | Light high-strength aluminum ladder section |
US11345980B2 (en) | 2018-08-09 | 2022-05-31 | Apple Inc. | Recycled aluminum alloys from manufacturing scrap with cosmetic appeal |
KR102578561B1 (en) | 2019-03-13 | 2023-09-15 | 노벨리스 인크. | Age-hardenable and highly formable aluminum alloys, monolithic sheets made therefrom and clad aluminum alloy products containing them |
CN118006983A (en) * | 2022-11-09 | 2024-05-10 | 北京车和家汽车科技有限公司 | Aluminum alloy material and preparation method and application thereof |
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US3104189A (en) * | 1960-10-17 | 1963-09-17 | Reynolds Metals Co | Aluminum alloy system |
US3370943A (en) * | 1965-11-04 | 1968-02-27 | Kaiser Aluminium Chem Corp | Aluminum alloy |
US5223050A (en) * | 1985-09-30 | 1993-06-29 | Alcan International Limited | Al-Mg-Si extrusion alloy |
JP3306363B2 (en) | 1997-12-22 | 2002-07-24 | 住友軽金属工業株式会社 | Extruded aluminum alloy with excellent intergranular corrosion resistance and method for producing the same |
CA2266193C (en) | 1998-03-20 | 2005-02-15 | Alcan International Limited | Extrudable aluminum alloys |
SI1155156T1 (en) * | 1999-02-12 | 2003-10-31 | Norsk Hydro Asa | Aluminium alloy containing magnesium and silicon |
JP2000282162A (en) | 1999-03-30 | 2000-10-10 | Nippon Steel Corp | Aluminum alloy extruded material excellent in corrosion fatigue strength |
NO312597B1 (en) * | 2000-11-08 | 2002-06-03 | Norsk Hydro As | A method for forming shaped products of an aluminum alloy and using the same |
US6565984B1 (en) * | 2002-05-28 | 2003-05-20 | Applied Materials Inc. | Clean aluminum alloy for semiconductor processing equipment |
DE102004030021B4 (en) * | 2003-07-09 | 2009-11-26 | Aleris Aluminum Duffel Bvba | Rolled product |
WO2006046677A1 (en) * | 2004-10-25 | 2006-05-04 | Showa Denko K.K. | Continuous casting apparatus, continuous casting method, and aluminum aloy cast rod |
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2008
- 2008-09-22 DE DE200810048374 patent/DE102008048374B3/en active Active
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2009
- 2009-09-21 ES ES09011984.3T patent/ES2537781T3/en active Active
- 2009-09-21 EP EP20090011984 patent/EP2175042B1/en active Active
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DE102008048374B3 (en) | 2010-04-15 |
ES2537781T3 (en) | 2015-06-12 |
EP2175042A1 (en) | 2010-04-14 |
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