EP3196324B1 - Curable aluminium alloy on an al-mg-si-basis - Google Patents
Curable aluminium alloy on an al-mg-si-basis Download PDFInfo
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- EP3196324B1 EP3196324B1 EP16152467.3A EP16152467A EP3196324B1 EP 3196324 B1 EP3196324 B1 EP 3196324B1 EP 16152467 A EP16152467 A EP 16152467A EP 3196324 B1 EP3196324 B1 EP 3196324B1
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- 229910000838 Al alloy Inorganic materials 0.000 title claims description 60
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 19
- 229910052710 silicon Inorganic materials 0.000 claims description 16
- 239000011651 chromium Substances 0.000 claims description 14
- 229910052718 tin Inorganic materials 0.000 claims description 12
- 239000010949 copper Substances 0.000 claims description 11
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 10
- 239000011777 magnesium Substances 0.000 claims description 10
- 239000006104 solid solution Substances 0.000 claims description 10
- 239000010936 titanium Substances 0.000 claims description 10
- 229910052738 indium Inorganic materials 0.000 claims description 9
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 239000011572 manganese Substances 0.000 claims description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 229910052749 magnesium Inorganic materials 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 claims description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- 239000013078 crystal Substances 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 239000010703 silicon Substances 0.000 claims description 2
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 claims description 2
- 229910019064 Mg-Si Inorganic materials 0.000 claims 1
- 229910019406 Mg—Si Inorganic materials 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 description 20
- 239000000956 alloy Substances 0.000 description 20
- 238000003860 storage Methods 0.000 description 19
- 229920001187 thermosetting polymer Polymers 0.000 description 7
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 6
- 230000032683 aging Effects 0.000 description 5
- 238000005275 alloying Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000000171 quenching effect Effects 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 239000011573 trace mineral Substances 0.000 description 4
- 235000013619 trace mineral Nutrition 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- 101000993059 Homo sapiens Hereditary hemochromatosis protein Proteins 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 229910001094 6061 aluminium alloy Inorganic materials 0.000 description 1
- 229910018594 Si-Cu Inorganic materials 0.000 description 1
- 229910008465 Si—Cu Inorganic materials 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000029142 excretion Effects 0.000 description 1
- 238000009998 heat setting Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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- 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
- C22C21/06—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
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/04—Alloys containing less than 50% by weight of each constituent containing tin or lead
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/06—Alloys containing less than 50% by weight of each constituent containing zinc
-
- 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 hardenable aluminum alloy based on Al-Mg-Si.
- Comparable alloys of the type 6xxx are moreover from the WO 2015/034024 A1 known.
- main and minor alloying elements can not be arbitrarily varied in their content in the aluminum alloy, because in addition to a desirable high age hardening ability other mechanical and / or chemical requirements - such as formability, strength, ductility and / or corrosion resistance - are met. This requires, for example, high concentrations of main alloying elements in the aluminum alloy in order to form certain hot excretions.
- the aluminum alloy should be particularly suitable for the use of secondary aluminum.
- the aluminum alloy contains from 0.6 to 1% by weight of magnesium (Mg), from 0.2 to 0.7% by weight of silicon (Si), from 0.16 to 0, 7 wt .-% iron (Fe), from 0.05 to 0.4 wt .-% copper (Cu), at most 0.15 wt .-% (or from 0 to 0.15 wt .-%) manganese (Mn), at most 0.35 wt .-% (or from 0 to 0.35 wt .-%) chromium (Cr), at most 0.2 wt .-% (or from 0 to 0.2 wt.
- Mg magnesium
- Si silicon
- Fe iron
- Cu copper
- Mn manganese
- Cr chromium
- zirconium Zr
- Zn zirconium
- Ti titanium
- Sn tin
- In indium
- thermosetting 1 can be seen, namely, due to the upper limit of that provision for a sufficient solubility of tin and / or indium in the solid solution of the aluminum alloy, which slows the precipitation behavior during cold curing and thus the storage stability of the aluminum alloy is conducive.
- a sufficient precipitation behavior in the thermosetting is to be expected - whereby high strength values can be achieved in the thermosetting and the aluminum alloy itself can achieve or improve those mechanical and chemical properties of 6xxx aluminum alloy with a higher content of main and Secondary alloy elements are known.
- this method can be used to observe a much slower precipitation behavior at room temperature.
- a comparatively low Si content may be responsible for delayed cold curing
- the tuning of the Si content according to the invention leads far beyond these known effects and shows an unusually high storage stability of the aluminum alloys. According to the invention, therefore, the advantages of a particularly high storage stability at room temperature and good heat-setting ability of the aluminum alloy can be combined.
- this composition of the invention can also be particularly suitable for the use of secondary aluminum for this purpose due to the comparatively high Fe content.
- the storage stability and the thermosetting ability of the aluminum alloy can be further improved when the parameter A is in the range of 0.26 to 0.34 wt%.
- the solubility of Sn can be relatively large and Si exercise only a small impact on cold curing. This allows an unexpectedly high stability at room temperature.
- this alloy set in this way can attain surprisingly high strength after hot curing, for example by means of heat aging, although this alloy has a comparatively low Si content.
- Ti can form phases with Si, which can have a positive influence on the solubility of Sn. The storage stability of the aluminum alloy is thus further improved.
- the ratio of the weight percent of Si / Fe is less than 2, by increasing the setting of Si by Fe, the content of dissolved Si in the aluminum alloy can be significantly reduced.
- the solubility of tin and / or indium in the solid solution of the Al-Mg-Si-aluminum alloy can be improved, which can further increase the storage stability.
- a comparatively high solubility of tin and / or indium in the solid solution of the Al-Mg-Si-aluminum alloy can be achieved when the ratio of the weight percent of Si / Mg is in the range of 0.3 to 0.9.
- the aluminum alloy has at least 0.25% by weight of copper (Cu), on the basis of this comparatively high content of Cu, it can compensate for the adverse effects of Mg and Si on the solubility of Sn in the solid solution of Al-Mg-Si Aluminum alloy are intervened.
- Cu copper
- solid solution may denote a state in which an alloying element is distributed in a solid matrix.
- the aluminum alloy belongs to the 6xxx series.
- the aluminum alloy is an EN AW-6061 aluminum alloy.
- the aluminum alloy has at most 0.05% by weight of chromium (Cr) and more than 0.05% by weight of zirconium (Zr), the quenching sensitivity for Sn can be reduced and Sn can be kept in solid solution in the mixed aluminum crystal even at comparatively low quenching rates become. In addition, it is thus possible, even with heavy plates, to achieve optimum storage stability and heat-hardening capability.
- the aluminum alloy may have at least 0.02 wt% chromium (Cr) to eventually improve the corrosion performance.
- Table 1 Overview of the investigated alloys in% by weight alloys sn mg Si Cu Fe Mn Cr Zn Ti 1 0.04 0.8 0.64 0.22 0.47 0.11 0.16 0.05 0.05 2 0.04 0.78 0.43 0.36 0.46 0.11 0.14 0.05 0.06
- the aluminum alloy 1 of Table 1 essentially corresponds to a standard alloy AA6061 after addition of the trace element Sn, it being conceivable instead of tin to use indium or a combination of Sn and In.
- Alloy 2 represents the composition according to the invention of the 6xxx series and is relatively recycling-friendly due to the comparatively high Fe content.
- the aluminum alloy 1 is well outside the inventively tuned Si / Fe content, this is for example in the Fig. 1 can be seen.
- the aluminum alloy 2 is placed substantially centrally in this tuned Si / Fe content.
- Both aluminum alloys 1 and 2 were solution-annealed in solid solution, quenched, and cold-cured by aging at room temperature and then thermoset. Solution heat treatment was carried out at a temperature greater than 530 degrees Celsius - quenching at a quench rate greater than 20 degrees Celsius / second. Both alloys 1 and 2 were subjected to a storage time or cold curing of 180 days [d] and a 30-minute thermosetting at different temperatures. Brinell hardness [HBW] was determined during cold aging and after hot aging.
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- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
Description
Die Erfindung betrifft eine aushärtbare Aluminiumlegierung auf Al-Mg-Si-Basis.The invention relates to a hardenable aluminum alloy based on Al-Mg-Si.
Um die Warmaushärtungsfähigkeit einer durch Lagerung bei Raumtemperatur kaltausgehärteten A6061 Aluminiumlegierung auf Al-Mg-Si-Basis zu verbessern, schlägt die
Vergleichbare Legierungen vom Typ 6xxx sind darüber hinaus aus der
Zudem ist es bekannt ("Statistical and thermodynamic optimization of trace-element modified Al-Mg-Si-Cu Alloys", Stefan Pogatscher et. al.), dass bestimmte Haupt- und Nebenlegierungselemente der A6061-Aluminiumlegierung die Löslichkeit von Zinn oder Indium in der Aluminiumlegierung reduzieren, was negative Auswirkungen auf die Lagerstabilität bei Raumtemperatur der 6xxx-Aluminiumlegierungen hat. So soll beispielsweise ein erhöhter Gehalt von Mg, Si, Cu oder Zn in der 6xxx-Aluminiumlegierung die Löslichkeit verringern, wohingegen ein erhöhter Gehalt von Fe, Ti und Mn die Löslichkeit erhöht. Zudem haben auch Interaktionseffekte, beispielsweise zwischen Si und Mg und/oder zwischen Cu und Mg, bei der Löslichkeit von Sn in der Aluminiumlegierung eine bedeutende Rolle.In addition, it is known ("Statistical and thermodynamic optimization of trace-element modified Al-Mg-Si-Cu Alloys", Stefan Pogatscher et al.) That certain main and minor alloying elements of the A6061 aluminum alloy solubility of tin or indium in of the aluminum alloy, which negatively affects the storage stability at room temperature of the 6xxx aluminum alloys. For example, an increased content of Mg, Si, Cu or Zn in the 6xxx aluminum alloy is believed to reduce solubility, whereas an increased content of Fe, Ti and Mn increases solubility. In addition, interaction effects, for example, between Si and Mg and / or between Cu and Mg, also play an important role in the solubility of Sn in the aluminum alloy.
Allerdings können die Haupt- und Nebenlegierungselemente in ihrem Gehalt in der Aluminiumlegierung nicht beliebig variiert werden, weil neben einer wünschenswert hohen Warmaushärtungsfähigkeit auch andere mechanische und/oder chemische Anforderungen - wie beispielsweise Umformbarkeit, Festigkeit, Duktilität und/oder Korrosionsbeständigkeit - zu erfüllten sind. Dies bedarf beispielsweise hoher Konzentrationen von Hauptlegierungselementen in der Aluminiumlegierung, um bestimmte Warmausscheidungen bilden zu können.However, the main and minor alloying elements can not be arbitrarily varied in their content in the aluminum alloy, because in addition to a desirable high age hardening ability other mechanical and / or chemical requirements - such as formability, strength, ductility and / or corrosion resistance - are met. This requires, for example, high concentrations of main alloying elements in the aluminum alloy in order to form certain hot excretions.
In der Einstellung der Komposition einer Aluminiumlegierung auf Al-Mg-Si-Basis sind daher bei den Haupt- und Nebenlegierungselementen meist zueinander gegenläufige Mengenverhältnisse erforderlich - nämlich einerseits solche Mengenverhältnisse, die der Löslichkeit von Sn in der Aluminiumlegierung dienlich sind, um eine hohe Lagerstabilität bei Raumtemperatur zu ermöglichen, und andererseits jene Mengenverhältnisse, die für hohe mechanische und/oder chemische Kennwerte bzw. Eigenschaften der Aluminiumlegierung sorgen, meist jedoch auf die Löslichkeit von Sn nachteilig wirken.In the setting of the composition of an aluminum alloy based on Al-Mg-Si, countercurrent proportions are usually required in the case of the main and minor alloying elements - on the one hand, those proportions which are beneficial for the solubility of Sn in the aluminum alloy, ensuring a high storage stability Room temperature to allow, and on the other hand those proportions that provide high mechanical and / or chemical characteristics or properties of the aluminum alloy, but usually have a negative effect on the solubility of Sn.
Es ist daher die Aufgabe der Erfindung, eine aushärtbare Aluminiumlegierung auf Basis von Al-Mg-Si mit Sn als Spurenelement in der Komposition derart zu verändern, dass eine hohe mechanische und chemische Eigenschaft der Aluminiumlegierung nach der Warmaushärtung mit einer hohen Lagerstabilität bei Raumtemperatur kombiniert werden kann. Zudem soll die Aluminiumlegierung besonders geeignet für die Verwendung von Sekundäraluminium sein.It is therefore an object of the invention to modify a curable aluminum alloy based on Al-Mg-Si with Sn as a trace element in the composition such that a high mechanical and chemical properties of the aluminum alloy are combined after hot curing with a high storage stability at room temperature can. In addition, the aluminum alloy should be particularly suitable for the use of secondary aluminum.
Die Erfindung löst die gestellte Aufgabe dadurch, dass die Aluminiumlegierung von 0,6 bis 1 Gew.-% Magnesium (Mg), von 0,2 bis 0,7 Gew.-% Silizium (Si), von 0,16 bis 0,7 Gew.-% Eisen (Fe), von 0,05 bis 0,4 Gew.-% Kupfer (Cu), maximal 0,15 Gew.-% (bzw. von 0 bis 0,15 Gew.-%) Mangan (Mn), maximal 0,35 Gew.-% (bzw. von 0 bis 0,35 Gew.-%) Chrom (Cr), maximal 0,2 Gew.-% (bzw. von 0 bis 0,2 Gew.-%) Zirkon (Zr), maximal 0,25 Gew.-% (bzw. von 0 bis 0,25 Gew.-%) Zink (Zn), maximal 0,15 Gew.-% (bzw. von 0 bis 0,15 Gew.-%) Titan (Ti), 0,005 bis 0,075 Gew.-% Zinn (Sn) und/oder Indium (In) und als Rest Aluminium sowie herstellungsbedingt unvermeidbare Verunreinigungen, wobei das Verhältnis der Gewichtsprozente von Si/Fe kleiner 2,5 ist und sich der Gehalt von Si nach der Gleichung Gew.-% Si = A + [0,3 * (Gew.-% Fe)] mit dem Parameter A im Bereich von 0,17 bis 0,4 Gew.-% bestimmt.The invention achieves the stated object in that the aluminum alloy contains from 0.6 to 1% by weight of magnesium (Mg), from 0.2 to 0.7% by weight of silicon (Si), from 0.16 to 0, 7 wt .-% iron (Fe), from 0.05 to 0.4 wt .-% copper (Cu), at most 0.15 wt .-% (or from 0 to 0.15 wt .-%) manganese (Mn), at most 0.35 wt .-% (or from 0 to 0.35 wt .-%) chromium (Cr), at most 0.2 wt .-% (or from 0 to 0.2 wt. -%) zirconium (Zr), at most 0.25 wt .-% (or from 0 to 0.25 wt .-%) zinc (Zn), at most 0.15 wt .-% (or from 0 to 0 , 15% by weight) of titanium (Ti), 0.005 to 0.075% by weight of tin (Sn) and / or indium (In) and the remainder being aluminum as well as unavoidable impurities due to production, the ratio of the weight percent of Si / Fe being less than 2 , 5 and the content of Si is in accordance with the equation wt .-% Si = A + [0.3 * (wt .-% Fe)] with the parameter A in the range of 0.17 to 0.4 wt. % certainly.
Durch die Vorschrift des Beschränkens des Si-Gehalts auf 0,2 bis 0,7 Gew.-% und des Fe-Gehalts auf 0,16 bis 0,7 Gew.-% sowie der Abstimmung des Si-Gehalts mit dem Fe-Gehalt kann auf die Lagerstabilität und Warmaushärtungsfähigkeit der Al-Mg-Si-Aluminiumlegierung in besonders hohem Maße vorteilhaft Einfluss genommen werden, wenn diese Abstimmung sowohl dem Verhältnis der Gewichtsprozente von Si/Fe kleiner 2,5 als auch der Gleichung Gew.-% Si = A + [0,3 * (Gew.-% Fe)] mit dem Parameter A im Bereich von 0,17 bis 0,4 Gew.-% genügt.
Eine derart eng in Si- und Fe-Gehalt abgestimmte Aluminiumlegierung, welche Abstimmung beispielsweise am schraffierten Bereich in
Überraschend hat sich jedoch herausgestellt, dass mit diese Vorschrift im Vergleich mit bekannten 6xxx-Aluminiumlegierungen, aufweisend Sn zur Unterdrückung der Kaltaushärtung, ein um ein Vielfaches verlangsamtes Ausscheidungsverhalten bei Raumtemperatur beobachtet werden kann. Zwar ist bekannt, dass ein vergleichsweise niedriger Si-Gehalt für ein verzögertes Kaltaushärtung verantwortlich sein kann, die erfindunsgemäße Abstimmung des Si-Gehalts führt jedoch weit über diese bekannten Effekte hinaus und zeigt eine ungewöhnlich hohe Lagerstabilität an der Aluminiumlegierungen.
Erfindungsgemäß können daher die Vorteile einer besonders hohen Lagerstabilität bei Raumtemperatur sowie guter Warmaushärtungsfähigkeit der Aluminiumlegierung kombiniert werden.
Zudem kann sich diese erfindungsgemäße Komposition durch den vergleichsweise hohen Fe Gehalt auch besonders gut für die Verwendung von Sekundäraluminium hierfür eignen.By the rule of restricting the Si content to 0.2 to 0.7 wt .-% and the Fe content to 0.16 to 0.7 wt .-% and the vote of the Si content with The Fe content can be influenced to a particularly great extent on the storage stability and heat-hardening ability of the Al-Mg-Si-aluminum alloy if this coordination both the ratio of the weight percent of Si / Fe less than 2.5 and the equation wt. % Si = A + [0.3 * (wt% Fe)] satisfies the parameter A in the range of 0.17 to 0.4 wt%.
Such a closely matched in Si and Fe content aluminum alloy, which vote, for example, the hatched area in
Surprisingly, however, it has been found that, compared with known 6xxx aluminum alloys, comprising Sn to suppress cold hardening, this method can be used to observe a much slower precipitation behavior at room temperature. Although it is known that a comparatively low Si content may be responsible for delayed cold curing, the tuning of the Si content according to the invention, however, leads far beyond these known effects and shows an unusually high storage stability of the aluminum alloys.
According to the invention, therefore, the advantages of a particularly high storage stability at room temperature and good heat-setting ability of the aluminum alloy can be combined.
In addition, this composition of the invention can also be particularly suitable for the use of secondary aluminum for this purpose due to the comparatively high Fe content.
Im Allgemeinen wird erwähnt, dass in der Al-Mg-Si-Aluminiumlegierung Verunreinigungen mit jeweils maximal 0,05 Gew.-% und gesamt höchstens 0,15 Gew.-% vorkommen können. Zudem wird im Allgemeinen erwähnt, dass maximale Gew.-% Angaben, wie diese bei Mn, Cr, Zr, Zn oder Titan beispielsweise zu finden sind, als von 0 ausgehend betrachtet werden können.
Der Vollständigkeit halber wird weiter erwähnt, dass als Sekundaraluminium Aluminium bzw. eine Aluminiumlegierung, gewonnen aus Aluminiumschrott, verstanden werden kann.In general, it is mentioned that in the Al-Mg-Si-aluminum alloy, impurities each having a maximum of 0.05 wt% and a total of at most 0.15 wt% may occur. In addition, it is generally mentioned that maximum weight percentages, such as those found with Mn, Cr, Zr, Zn or titanium, for example, can be considered as starting from 0.
For the sake of completeness, it is further mentioned that aluminum or an aluminum alloy, obtained from aluminum scrap, can be understood as the secondary aluminum.
Die Lagerstabilität und die Warmaushärtungsfähigkeit der Aluminiumlegierung können weiter verbessert werden, wenn der Parameter A im Bereich von 0,26 bis 0,34 Gew.-% liegt. Durch diese Vorschrift, kann nämlich die Löslichkeit von Sn verhältnismäßig groß werden und Si nur mehr einen geringen Einfluss auf eine Kaltaushärtung ausüben. Damit kann eine unerwartet hohe Stabilität bei Raumtemperatur ermöglicht werden. Zudem kann sich zeigen, dass diese derart eingestellte Legierung nach einer Warmaushärtung - beispielsweise durch Warmauslagerung - eine überraschend hohe Festigkeit erreichen kann, obwohl diese Legierung einen vergleichsweise niedrigen Si-Gehalt aufweist.The storage stability and the thermosetting ability of the aluminum alloy can be further improved when the parameter A is in the range of 0.26 to 0.34 wt%. By this rule, namely, the solubility of Sn can be relatively large and Si exercise only a small impact on cold curing. This allows an unexpectedly high stability at room temperature. In addition, it can be shown that this alloy set in this way can attain surprisingly high strength after hot curing, for example by means of heat aging, although this alloy has a comparatively low Si content.
Ein Optimum an Lagerstabilität und Warmaushärtungsfähigkeit kann sich zeigen, wenn der Parameter A 0,3 Gew. -% ist.An optimum of storage stability and thermosetting ability may be exhibited when the parameter A is 0.3% by weight.
Bestimmt sich der Gehalt von Si nach der Gleichung Gew.-% Si = A + [0,3 * (Gew.-% Fe)] - Gew.-% Ti, können die, die Löslichkeit von Sn beeinfussenden Komponenten noch weiter verbessert aufeinander abgestimmt werden. Insbesondere kann Ti Phasen mit Si ausbilden, was einen positiven Einfluss auf die Löslichkeit von Sn haben kann. Die Lagerstabilität der Aluminiumlegierung ist damit weiter verbesserbar.If the content of Si is determined by the equation wt% Si = A + [0.3 * (wt% Fe)] -% by weight of Ti, the components affecting the solubility of Sn can be further improved on each other be matched. In particular, Ti can form phases with Si, which can have a positive influence on the solubility of Sn. The storage stability of the aluminum alloy is thus further improved.
Ist das Verhältnis der Gewichtsprozente von Si/Fe kleiner 2, kann durch erhöhtes Abbinden von Si durch Fe der Anteil an gelöstem Si in der Aluminiumlegierung erheblich verringert werden. Damit kann die Löslichkeit von Zinn und/oder Indium in der festen Lösung der Al-Mg-Si-Aluminiumlegierung verbessert werden, was die Lagerstabilität weiter erhöhen kann.If the ratio of the weight percent of Si / Fe is less than 2, by increasing the setting of Si by Fe, the content of dissolved Si in the aluminum alloy can be significantly reduced. Thus, the solubility of tin and / or indium in the solid solution of the Al-Mg-Si-aluminum alloy can be improved, which can further increase the storage stability.
Eine vergleichsweise hohe Löslichkeit von Zinn und/oder Indium in der festen Lösung der Al-Mg-Si-Aluminiumlegierung kann erreicht werden, wenn das Verhältnis der Gewichtsprozente von Si/Mg im Bereich von 0,3 bis 0,9 liegt.A comparatively high solubility of tin and / or indium in the solid solution of the Al-Mg-Si-aluminum alloy can be achieved when the ratio of the weight percent of Si / Mg is in the range of 0.3 to 0.9.
Weist die Aluminiumlegierung mindestens 0,25 Gew.-% Kupfer (Cu) auf, kann auf Basis dieses vergleichsweise hohen Gehalts an Cu kompensierend auf die nachteiligen Effekte von Mg und Si hinsichtlich der Löslichkeit von Sn in der festen Lösung der Al-Mg-Si-Aluminiumlegierung eingegriffen werden.If the aluminum alloy has at least 0.25% by weight of copper (Cu), on the basis of this comparatively high content of Cu, it can compensate for the adverse effects of Mg and Si on the solubility of Sn in the solid solution of Al-Mg-Si Aluminum alloy are intervened.
Eine hervorragende Lagerstabilität der Aluminiumlegierung kann erreicht werden, wenn diese im Bereich von 0,005 bis 0,05 Gew.-% Zinn (Sn) in fester Lösung im Aluminiummischkristall aufweist. Im Allgemeinen wird erwähnt, dass der Begriff "fester Lösung" einen Zustand bezeichnen kann, in welchem ein Legierungselement in einer festen Matrix verteilt ist.An excellent storage stability of the aluminum alloy can be achieved if it has in the range of 0.005 to 0.05 wt .-% tin (Sn) in solid solution in the aluminum mixed crystal. In general, it is mentioned that the term "solid solution" may denote a state in which an alloying element is distributed in a solid matrix.
Vorzugsweise gehört die Aluminiumlegierung der 6xxx Reihe an. Vorzugsweise ist die Aluminiumlegierung eine EN AW-6061 Aluminiumlegierung.Preferably, the aluminum alloy belongs to the 6xxx series. Preferably, the aluminum alloy is an EN AW-6061 aluminum alloy.
Weist die Aluminiumlegierung maximal 0,05 Gew.-% Chrom (Cr) und mehr als 0,05 Gew.-% Zirkon (Zr) auf, kann die Abschreckempfindlichkeit für Sn reduzieren und Sn auch bei vergleichsweise niedrigen Abschreckraten in fester Lösung im Aluminiummischkristall gehalten werden. Außerdem ist damit ermöglichbar, selbst bei Grobblechen ein Optimum an Lagerstabilität und Warmaushärtungsfähigkeit zu erreichen.If the aluminum alloy has at most 0.05% by weight of chromium (Cr) and more than 0.05% by weight of zirconium (Zr), the quenching sensitivity for Sn can be reduced and Sn can be kept in solid solution in the mixed aluminum crystal even at comparatively low quenching rates become. In addition, it is thus possible, even with heavy plates, to achieve optimum storage stability and heat-hardening capability.
Die Aluminiumlegierung kann mindestens 0,02 Gew.-% Chrom (Cr) aufweisen, um damit eventuell das Korrosionsverhalten zu verbessern.The aluminum alloy may have at least 0.02 wt% chromium (Cr) to eventually improve the corrosion performance.
Zum Nachweis der erzielten Effekte wurden Feinbleche aus verschiedenen Aluminiumlegierungen auf Al-Mg-Si-Basis (6xxx-Reihe) hergestellt. Die Zusammensetzungen der untersuchten Legierungen sind in der Tabelle 1 angeführt.
Die Aluminiumlegierung 1 der Tabelle 1 entspricht im Wesentlichen einer Standard-Legierung AA6061 nach Zugabe des Spurenelements Sn, wobei vorstellbar ist anstatt von Zinn Indium oder eine Kombination von Sn und In zu verwenden. Legierung 2 stellt die erfindungsgemäße Komposition der 6xxx-Reihe dar und ist durch den vergleichsweise hohen Fe Gehalt vergleichsweise recyclingfreundlich.
Die Aluminiumlegierung 1 liegt deutlich außerhalb des erfindungsgemäß abgestimmten Si/Fe-Gehalts, wir dies beispielsweise in der
The
Beide Aluminiumlegierungen 1 und 2 wurden in feste Lösung durch Lösungsglühen gebracht, abgeschreckt und durch Auslagern bei Raumtemperatur kalt- sowie anschließend warmausgehärtet. Das Lösungsglühen erfolgte bei einer Temperatur größer 530 Grad Celsius - das Abschrecken mit einer Abschreckrate größer 20 Grad Celsius/Sekunde. Beide Legierungen 1 und 2 wurden einer Lagerzeit bzw. einer Kaltaushärtung von 180 Tagen [d] und einer Warmaushärtung von 30 Minuten bei unterschiedlichen Temperaturen unterworfen. Während der Kalt- bzw. nach der Warmauslagerung wurden Brinellhärten [HBW] bestimmt.Both
In Bezug auf die Lagerstabilität ist nach
Im Gegensatz dazu zeichnet sich bei der Legierung 2 erst nach ca. 180 Tagen eine beginnende Kaltaushärtung ab, wodurch die erfindungsgemäße Legierung 2 als besonders lagerbeständig gilt. Eine derart überraschend hohe Lagerbeständigkeit wurde bis dato noch bei keiner 6xxx-Legierung beobachtet. Dies führt zu einem unerwarteten, enormen Gewinn in der Manipulationszeit der Legierung nach dem Abschrecken in weichem Zustand.In terms of storage stability is after
In contrast, in the case of
Bei der anschließenden Warmaushärtung ist im Vergleich der beiden Legierungen nach
Claims (10)
- A hardenable AI-Mg-Si-based aluminum alloy, comprising
from 0.6 to 1% by weight of magnesium (Mg),
from 0.2 to 0.7% by weight of silicon (Si),
from 0.16 to 0.7% by weight of iron (Fe),
from 0.05 to 0.4% by weight of copper (Cu),
a maximum of 0.15% by weight of manganese (Mn),
a maximum of 0.35% by weight of chromium (Cr),
a maximum of 0.2% by weight of zirconium (Zr),
a maximum of 0.25% by weight of zinc (Zn),
a maximum of 0.15% by weight of titanium (Ti),
0.005 to 0.075% by weight of tin (Sn) and/or indium (In),
and the aluminum as the remainder as well as production-related unavoidable impurities, wherein
the ratio of the weight percentages of Si/Fe is less than 2.5
and the content of Si is determined according to the equation - Aluminum alloy according to claim 1, characterized in that the parameter A is in the range of 0.26 to 0.34% by weight.
- Aluminum alloy according to claim 1 or 2, characterized in that the parameter A is 0.3% by weight.
- Aluminum alloy according to one of claims 1 to 4, characterized in that the ratio of the weight percent of Si/Fe is less than 2.
- Aluminum alloy according to one of claims 1 to 5, characterized in that the ratio of the weight percentages of Si/Mg is in the range of 0.3 to 0.9.
- Aluminum alloy according to one of claims 1 to 6, characterized in that the aluminum alloy has at least 0.25% by weight of copper (Cu).
- Aluminum alloy according to one of claims 1 to 7, characterized in that the aluminum alloy comprises tin (Sn) in the range of 0.005 to 0.05% by weight in solid solution in the aluminum mixed crystal.
- Aluminum alloy according to one of claims 1 to 8, characterized in that the aluminum alloy has a maximum of 0.05% by weight of chromium (Cr) and more than 0.05% by weight of zirconium (Zr).
- Aluminum alloy according to one of claims 1 to 9, characterized in that the aluminum alloy has at least 0.02% by weight of chromium (Cr).
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PL16152467T PL3196324T3 (en) | 2016-01-22 | 2016-01-22 | Curable aluminium alloy on an al-mg-si-basis |
ES16152467T ES2702729T3 (en) | 2016-01-22 | 2016-01-22 | Hardenable aluminum alloy based on Al-Mg-Si |
SI201630138T SI3196324T1 (en) | 2016-01-22 | 2016-01-22 | Curable aluminium alloy on an al-mg-si-basis |
EP16152467.3A EP3196324B1 (en) | 2016-01-22 | 2016-01-22 | Curable aluminium alloy on an al-mg-si-basis |
US16/071,600 US20190024219A1 (en) | 2016-01-22 | 2017-01-20 | HARDENABLE Al-Mg-Si-BASED ALUMINUM ALLOY |
KR1020187024165A KR102649425B1 (en) | 2016-01-22 | 2017-01-20 | Al-Mg-Si hardenable aluminum alloy |
PCT/EP2017/051243 WO2017125582A1 (en) | 2016-01-22 | 2017-01-20 | Hardenable almgsi-based aluminum alloy |
CN201780007533.4A CN108779522B (en) | 2016-01-22 | 2017-01-20 | Age-hardenable aluminium alloys based on Al-Mg-Si |
EP17712414.6A EP3443134A1 (en) | 2016-01-22 | 2017-01-20 | Hardenable almgsi-based aluminum alloy |
SG10202007019WA SG10202007019WA (en) | 2016-01-22 | 2017-01-20 | Hardenable al-mg-si-based aluminum alloy |
AU2017208641A AU2017208641A1 (en) | 2016-01-22 | 2017-01-20 | Hardenable AlMgSi-based aluminum alloy |
MX2018008973A MX2018008973A (en) | 2016-01-22 | 2017-01-20 | Hardenable almgsi-based aluminum alloy. |
RU2018130158A RU2737646C2 (en) | 2016-01-22 | 2017-01-20 | THERMALLY HARDENED ALUMINIUM ALLOY BASED ON Al-Mg-Si |
JP2018537443A JP7208005B2 (en) | 2016-01-22 | 2017-01-20 | Age hardening type Al-Mg-Si based aluminum alloy |
SG11201806220YA SG11201806220YA (en) | 2016-01-22 | 2017-01-20 | Hardenable al-mg-si-based aluminum alloy |
BR112018014843-1A BR112018014843B1 (en) | 2016-01-22 | 2017-01-20 | AL-MG-SI-BASED CURABLE ALUMINUM ALLOY |
CA3011631A CA3011631A1 (en) | 2016-01-22 | 2017-01-20 | Hardenable al-mg-si-based aluminum alloy |
TR2018/14631A TR201814631T1 (en) | 2016-01-22 | 2017-01-20 | Al-mg-si-based hardenable aluminum alloy. |
ZA2018/04669A ZA201804669B (en) | 2016-01-22 | 2018-07-12 | Hardenable almgsi-based aluminum alloy |
CL2018001954A CL2018001954A1 (en) | 2016-01-22 | 2018-07-19 | Hardenable aluminum alloy based on al-mg-si. |
IL260680A IL260680B (en) | 2016-01-22 | 2018-07-19 | Hardenable almgsi-based aluminum alloy |
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CN109706351A (en) * | 2017-10-26 | 2019-05-03 | 遵义市吉祥富康门窗有限公司 | A kind of aluminium alloy and preparation method thereof |
CN108977700B (en) * | 2018-08-20 | 2020-04-17 | 广东润盛科技材料有限公司 | Aluminum alloy plate and preparation method thereof |
CN113574192A (en) | 2019-03-13 | 2021-10-29 | 诺维尔里斯公司 | Age-hardenable, highly formable aluminium alloy and method for producing the same |
CN110951998B (en) * | 2019-11-28 | 2020-12-08 | 辽宁忠旺集团有限公司 | Production process of high-temperature stable 6-series aluminum alloy section |
CN113737064B (en) * | 2021-08-31 | 2022-04-08 | 华中科技大学 | Al-Mg-Si alloy for high-performance forge piece and preparation method thereof |
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Family Cites Families (21)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60230952A (en) * | 1984-04-27 | 1985-11-16 | Daido Metal Kogyo Kk | Sliding aluminum alloy |
JP3684245B2 (en) * | 1993-11-24 | 2005-08-17 | 昭和電工株式会社 | Aluminum alloy for cold forging |
JPH07207396A (en) * | 1994-01-20 | 1995-08-08 | Nippon Steel Corp | Aluminum alloy sheet excellent in press formability and baking hardenability for coating |
US5587029A (en) * | 1994-10-27 | 1996-12-24 | Reynolds Metals Company | Machineable aluminum alloys containing In and Sn and process for producing the same |
JPH08199276A (en) * | 1995-01-25 | 1996-08-06 | Showa Denko Kk | Aluminum alloy for cold forging |
US6231809B1 (en) * | 1998-02-20 | 2001-05-15 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Al-Mg-Si aluminum alloy sheet for forming having good surface properties with controlled texture |
JP4328996B2 (en) | 1999-06-16 | 2009-09-09 | 日本軽金属株式会社 | Al-Mg-Si aluminum alloy cold forging manufacturing method |
JP5088703B2 (en) | 1999-06-16 | 2012-12-05 | 日本軽金属株式会社 | Al-Mg-Si aluminum alloy cold forging with excellent appearance quality |
JP2002235158A (en) * | 2001-02-05 | 2002-08-23 | Nippon Steel Corp | Method for producing high strength aluminum alloy extrusion shape material having excellent bending workability |
RU2221891C1 (en) * | 2002-04-23 | 2004-01-20 | Региональный общественный фонд содействия защите интеллектуальной собственности | Aluminum-based alloy, article made from such alloy and method of manufacture of such article |
JP2004277786A (en) | 2003-03-14 | 2004-10-07 | Nippon Light Metal Co Ltd | Method for manufacturing heat treatment type aluminum alloy material for cold working superior in machinability |
FR2862894B1 (en) * | 2003-11-28 | 2007-02-16 | Pechiney Rhenalu | ALLUMINIUM ALLOY BAND FOR BRAZING |
RU2394113C1 (en) * | 2008-11-13 | 2010-07-10 | Общество с ограниченной ответственностью "ИНТЕЛЛ-СЕРВИС" | High-tensile deformed alloy on base of aluminium and item out of this alloy |
EP2631317A1 (en) | 2012-02-23 | 2013-08-28 | AMAG rolling GmbH | Annealable aluminium alloy and method for improving artificial ageing ability |
JP5918187B2 (en) | 2013-09-06 | 2016-05-18 | 株式会社神戸製鋼所 | Aluminum alloy sheet with excellent bake hardenability |
JP6005613B2 (en) | 2013-09-06 | 2016-10-12 | 株式会社神戸製鋼所 | Aluminum alloy sheet with excellent bake hardenability |
KR101802677B1 (en) * | 2013-09-06 | 2017-11-28 | 가부시키가이샤 고베 세이코쇼 | Aluminum alloy plate having excellent bake hardening properties |
CN104532089B (en) * | 2014-12-26 | 2016-08-24 | 中国石油天然气股份有限公司 | Anticorrosive alloy composition and device, preparation and application thereof |
CN104975209A (en) * | 2015-03-13 | 2015-10-14 | 宝山钢铁股份有限公司 | 6000 series aluminum alloy material with high natural aging stability, aluminum alloy plate and preparing method of aluminum alloy plate |
CN104975208A (en) * | 2015-03-13 | 2015-10-14 | 宝山钢铁股份有限公司 | 6000-series aluminum alloy material with high strength and elongation, aluminum alloy plate and manufacturing method thereof |
CN105207596B (en) * | 2015-10-26 | 2018-05-04 | 阿特斯阳光电力集团有限公司 | Novel photovoltaic module |
-
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