special - ALUMINIUM-Nachrichten – ALU-WEB.DE
special - ALUMINIUM-Nachrichten – ALU-WEB.DE
special - ALUMINIUM-Nachrichten – ALU-WEB.DE
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<strong><strong>ALU</strong>MINIUM</strong> SMELTING INDUSTRY<br />
Casting and solidification<br />
For fabricating aluminium alloys, it is useful<br />
to understanding solidification during casting<br />
and to predict the phases that are likely<br />
to precipitate during cooling. A Scheil solidification<br />
calculation of the alloy AA7075 was<br />
performed by using the real alloy composition<br />
(Al, 0.11 Si, 0.28 Fe, 1.36 Cu, 2.49 Mg, 0.19<br />
Fig. 2: Calculated isothermal section of the Al-Cu-Mg-Zn quaternary<br />
system at 600 °C and 6 wt.% Zn compared with experimental work of<br />
Strawbridge [10]<br />
Cr, 5.72 Zn, wt.%). The calculation predicts<br />
that Al 45 Cr 7 solidifies primarily before the<br />
formation of (Al) although it had not been<br />
experimentally observed. Considering that it<br />
is probably the only Cr-bearing phase in this<br />
alloy, its formation would be almost certain.<br />
Due to its small amount, however, its formation<br />
can hardly be observed in the DTA trace<br />
or in the solidified microstructures. The formation<br />
of (Al) was followed by the Al 13 Fe 4 ,<br />
Mg 2 Si, T and V (MgZn 2 ) phases, which agrees<br />
well with the experimental results. Imposed<br />
on the diagram shown in Fig. 1 (see previous<br />
page) are the accumulated solid phase fractions<br />
at different temperatures, which have<br />
been evaluated from the experimental DTA<br />
trace obtained by Bäckerud et al [8]. It should<br />
be noted that DTA can only allow a qualitative<br />
evaluation. Nevertheless, it is suggested by<br />
the comparison that the real solidification significantly<br />
deviates from the equilibrium solidifi-cation,<br />
but can be reasonably approximated<br />
by a Scheil solidification simulation.<br />
Heat treatment<br />
The controlled heat treatment of aluminium<br />
alloys allows the metallurgist to optimise, control<br />
and generate a reproducible and predictable<br />
change in the microstructure of the alloy.<br />
This serves to influence properties such as<br />
strength, ductility, fracture toughness, thermal<br />
stability, residual stress, dimensional stability<br />
and resistance to corrosion and stress corrosion<br />
cracking [9]. The main heat treatment<br />
procedures for aluminium alloys are homogenisation<br />
and annealing, as<br />
well as precipitation hardening,<br />
which involves the<br />
three steps of solution heat<br />
treatment, quenching and<br />
aging. Computational modelling<br />
tools, such as those<br />
described here, can give<br />
insight into each of these<br />
stages. For example, the purpose<br />
of solution heat treatment<br />
of aluminium alloys is<br />
to put the maximum practical<br />
amount of the hardening<br />
solutes, such as Cu, Mg, Si,<br />
Zn or other elements, into a<br />
state of solid solution in the<br />
Al matrix. Multicomponent<br />
phase diagrams calculated<br />
using Thermo-Calc can aid<br />
this type of analysis without<br />
the need to perform timeconsuming<br />
experiments.<br />
The 7000-series alloys<br />
are heat-treatable wrought aluminium alloys,<br />
and it is useful to perform equilibrium calculations<br />
at solution treating temperatures and<br />
at aging temperatures in order to predict the<br />
phase formations in these alloys. As an example,<br />
Fig. 2 shows a calculated isothermal section<br />
of the Al-Cu-Mg-Zn quaternary system<br />
at the typical solution treating temperature of<br />
460 °C, and at a Zn content of 6 wt.%; the calculation<br />
was in very good agreement with the<br />
experimental data from Strawbridge et al [10].<br />
This diagram can be used to generally account<br />
for the phase constitution at the solution temperature<br />
for a number of 7000 series alloys,<br />
e. g. AA7010, AA7050, AA7075, AA7175,<br />
AA7475 and AA7178, etc. Andreatta [11] reported<br />
that Al7Cu 2 Fe and Al 23 CuFe 4 are the<br />
most abundant of the intermetallics in AA7075<br />
and AA7475, together with traces of Mg 2 Si,<br />
Al 6 Fe, S, T and Al 12 (Fe,Mn) 3 Si, after being<br />
solution treated. In such cases, it is necessary<br />
to perform equilibrium calculations using real<br />
alloy compositions by including other minor<br />
elements. Because of the high Fe content, the<br />
calculation using TCAL1 shows that Al 7 Cu 2 Fe<br />
forms in alloy AA7075 with an amount up to<br />
1%, and Al 13 Fe 4 coexists in a small amount.<br />
However, for alloy AA7475, Al 7 Cu 2 Fe is calculated<br />
to be the only main intermetallic.<br />
Summary<br />
The materials community is increasingly using<br />
computational modelling tools, and is applying<br />
them more widely to material design and process<br />
optimisation. For more than two decades,<br />
CALPHAD- based software and databases<br />
have been employed within the aluminium<br />
industry and they have served to improve<br />
the understanding of existing alloys, to accelerate<br />
the development of new alloys and<br />
also to model and understand better materials<br />
processing routes. The quality of the predictions<br />
depends on the quality of the thermodynamic<br />
and kinetic databases that they use.<br />
Some examples have been given here to illustrate<br />
how these tools are being used within the<br />
aluminium industry in the areas of casting and<br />
solidification as well as heat treatment.<br />
References<br />
[1] N. Saunders, A.P. Miodownik, Calphad (Calculations<br />
of Phase Diagrams): A Comprehensive<br />
guide, Pergamon Materials Series, vol. 1, ed. R.W.<br />
Cahn (Oxford, OX: Elsevier Science Ltd, 1998).<br />
[2] National Research Council, Integrated Computational<br />
Materials Engineering: A Transformational<br />
Discipline for Improved Competitiveness and National<br />
Security. Washington, DC: The National<br />
Academies Press, 2008.<br />
[3] http://www.whitehouse.gov/sites/default/files/<br />
microsites/ostp/materials_genome_initiative-final.<br />
pdf<br />
[4] A.K. Gupta et al., 2006, Materials Science Forum,<br />
519-521, 177<br />
[5] H. Onda et al., 2007, Materials Science Forum,<br />
561-565, 1967<br />
[6] J. Senaneuch et al., 2002, Materials Science Forum,<br />
396-402, 1697<br />
[7] S.N. Samaras, G.N. Haidemenopoulos, 2007,<br />
Journal of Materials Processing Technology, 63-73,<br />
194<br />
[8] L. Bäckerud, G.C. Chai, J. Tamminen, Solidification<br />
Characteristics of Aluminium Alloys, Vol. 1 and<br />
2. Sweden (1990)<br />
[9] H. Moller, 2011, Heat Treatment of Al-7Si-Mg<br />
casting alloys, Aluminium International Today, 16-<br />
18, Vol 23, No 6<br />
[10] D.J. Strawbridge, W. Hume-Rothery, A.T.<br />
Little, The constitution of aluminium-copper-magnesium-zinc<br />
alloys at 460 °C. J. Inst. Metals (London)<br />
74 (1947) 191-225<br />
[11] F. Andreatta, Local electrochemical behaviour<br />
of 7xxx aluminium alloys, PhD thesis, 2004<br />
Authors<br />
Paul Mason is president of Thermo-Calc Software<br />
Inc., based in McMurray, PA, USA.<br />
Hai-Lin Chen is with Thermo-Calc Software AB,<br />
based in Stockholm, Sweden.<br />
66 <strong><strong>ALU</strong>MINIUM</strong> · 1-2/2013