Next Article in Journal
Peculiar Spatiotemporal Behavior of Unstable Plastic Flow in an AlMgMnScZr Alloy with Coarse and Ultrafine Grains
Next Article in Special Issue
Strongly Orthotropic Open Cell Porous Metal Structures for Heat Transfer Applications
Previous Article in Journal
Influence of Alkali Treatment on Anodized Titanium Alloys in Wollastonite Suspension
Previous Article in Special Issue
Coalescence Avalanches in Liquid Aluminum Foams
Article Menu
Issue 9 (September) cover image

Export Article

Metals 2017, 7(9), 323; doi:10.3390/met7090323

Influence of the Heating Rate on the Foaming Behavior of Various Aluminium Alloys
Chair of Structure and Properties of Materials, Technische Universität Berlin, Hardenbergstraße 36, 10623 Berlin, Germany
Institute of Applied Materials, Helmholtz-Centre Berlin for Materials and Energy GmbH, Hahn-Meitner-Platz 1, 14109 Berlin, Germany
Author to whom correspondence should be addressed.
Received: 14 July 2017 / Accepted: 11 August 2017 / Published: 23 August 2017


Powders of metallurgically prepared precursors expand to a foam differently depending on how fast they are heated to their foaming temperature. The foaming behavior of four alloys was studied with heating rates varying from 0.1 K/s to 18 K/s. It was found that each alloy shows its own non-linear behavior of expansion values. Alloys not containing magnesium exhibit a maximum at intermediate heating rates, whereas Mg-containing alloys tend to expand more for higher heating rates.
aluminium alloy foams; heating rate; powder processing

1. Introduction

The powder metallurgical route for the preparation of foamable metallic precursors is comprised of mixing metal powders and a blowing agent, densifying the powder blend (mostly in air) yielding a dense precursor, after which the foaming process is initiated by heating up to the melting range of the alloy in question. The resulting foam expansion and the final structure of the solidified foam are influenced by many conditions along this way such as alloy composition, type of compaction, compaction temperature or pressure, foaming temperature or holding time, and also by the heating rate up to the foaming temperature. The heating conditions are usually determined by the foaming set-up (e.g., furnace type, heat capacity of the system etc.) and can strongly vary.
The influence of the heating rate has been studied for the aluminium alloys 6061 [1] and AlSi6Cu4 [2]. Both studies concluded that there is a minimum heating rate needed to reach maximum expansion of foams. AlSi alloys with varying Cu and Mg additions were investigated at two heating rates. A slight improvement of expansion at higher heating rates was found [3]. Another study focused mainly on collapse mechanisms but also reported a dependence of the foaming behavior of AlSi7, AlSi9Cu3, and three more Al-Si-Cu alloys containing Zn additions on the heating rate [4]. However, no systematic study has been performed so far for heating rates covering a wide range of values.

2. Experimental

The alloys used in this study were AlSi7, AlCu13Mg4, AlSi6Cu4, and AlSi8Mg4 (all in wt %). Powders of aluminium (Alpoco Ltd., Sutton Coldfield, UK, 99.7% purity, D90 = 76 µm), silicon (Alchem Ltd., Burlington, ON, Canada, 99.5% purity, D90 = 50 µm), copper (Chempur GmbH, Karlsruhe, Germany, 99.7% purity, D90 = 53 µm), prealloyed AlMg50 master alloy (Possehl Erzkontor GmbH, Lübeck, Germany, D90 = 72 µm), and TiH2 serving as blowing agent (Chemetall GmbH, Frankfurt am Main, Germany, 98.8% pure, D90 = 31 µm) were used to prepare foamable precursors. The TiH2 was heat-treated at 480 °C for 180 min in air in order to allow for the creation of a surface oxide layer and to shift the hydrogen release range to higher temperatures [5,6]. The powders were mixed in air for 30 min. For compaction, 30 g of powder blend were subjected to 300 MPa uniaxial pressure: first at 20 °C for 10 s and then at 400 °C for 5 min. The resulting cylindrical tablets of 36 mm diameter were eventually cut to samples of (10 × 10 × 4) mm3 size. The density of the compacted samples was 97.2 ± 0.2% of their theoretical density.
Foaming was performed in air in an X-ray imaging system on a ceramic plate that could be resistively heated. The radioscopy set-up consists of a microfocus X-ray source operated at 100 kV, and a 2240 × 2368 pixel flat panel detector [2], both from Hamamatsu, Japan. Analysis of the images allows for the calculation of the expansion profiles. The temperature used to control the heating power was measured by a thermocouple embedded directly in the plate beneath the sample. The set point temperatures were chosen individually for each alloy and were 80 K above the respective liquidus temperatures. After reaching the set point, the temperature was held for 240 s before heating was turned off and natural cooling started. Investigations were performed using controlled heating rates from 0.1 K/s to 16 K/s. Additionally, heating with full power was carried out, which results in a non-linear heating profile, but averages to 18 K/s and will hereinafter be referred to as 18 K/s. The given heating rate is controlled by the ceramic heating plate. The temperature difference for the unmelted precursor for all heating rates is smaller than 30 K. A minimum of three foaming experiments were performed for each heating rate and each alloy.

3. Results

Figure 1 visualises the dependence of the projected area expansion of foams on the heating rate for four different alloys. Values for the highest expansion are presented along with expansion values measured during cooling. Selected X-ray radiographs are given to illustrate the structure of the foams in the moment of maximum expansion. For AlSi7 (Figure 1a), a maximum expansion level of around 440% area expansion can be observed for heating rates of 1 K/s to 3 K/s. Higher (>3 K/s) and lower (<1 K/s) heating rates yield slightly lower maximum expansion values. The values for the end expansion are lower than the maximum values, indicating collapse. For most heating rates the end area expansion is only around 10% smaller than the maximum area expansion, except for heating rates of 5 K/s to 10 K/s, where collapse values of up to 17% can be found. For higher rates, starting from 5 K/s, the end area expansion remains almost constant due to less collapse.
The curves for AlSi6Cu4 in Figure 1b also exhibit a maximum at intermediate heating rates. The highest area expansion values (~375%) were reached by using heating rates of 5 K/s and 7 K/s. Lower or higher heating rates yield lower maximum area expansion values. However, the highest end area expansions were reached for lower heating rates of 0.5 K/s to 3 K/s due to a lower collapse of only ~10%. In contrast, the collapse values increase continuously for heating rates higher than 3 K/s, whereby the highest collapse values (~28%) were found for the highest heating rates of 13 K/s and 18 K/s. Thus, the lowest end area expansion was gained by using the highest heating rate (18 K/s).
For AlCu13Mg4, the highest heating rate (18 K/s) gives the highest expansion (maximum: 375%; end: 270%), as shown in Figure 1c. Decreasing the heating rate leads to a continuous decrease of area expansion, revealing an almost monotonic dependence of expansion on heating rate. The collapse of foams also increases continuously with the rise of the heating rate: from 12% at 0.17 K/s to more than 35% at 16 K/s.
Contrary to the results in the previous cases, the curve for AlSi8Mg4, depicted in Figure 1d, does not assume its minimum at the lowest heating rate, but rather a local minimum at intermediate heating rates at 2–2.5 K/s is observed. This unexpected behavior was confirmed in 10 individual experiments. Nevertheless, the curves of maximum and end area expansion show an increase up to 0.5 K/s, a decrease up to 2 K/s, and a re-increase up to 16 K/s. For heating rates from 2 K/s to 4 K/s the maximum area expansion markedly increases from 143% to 307%, respectively. Similarly high is the difference in the end area expansion which is increased by 137%, whereas the magnitude of collapse remains roughly constant (~13%). A further increase of the heating rate leads to slightly larger expansion values until the highest maximum of 378% at 16 K/s is reached, associated with a stronger collapse (~20%).

4. Discussion

All four alloys exhibit poor foam expansion at low heating rates. This behavior is probably caused by the long exposure of the sample to temperatures in the range of the decomposition range of the blowing agent (in AlSi11 precursor at 0.67 K/s: Onset 531 °C, peak 585 °C [7]) and gas losses before the alloy starts to melt and foaming occurs. Especially for Mg-free alloys, it was found that the weak solid metal matrix starts cracking at around 550 °C (Figure 2), which allows for the loss of hydrogen either through open fissures or by diffusion to the outside through thinner material layers. Another reason for poor expansion is the growing outer oxide skin. This effect has also been reported for the foaming of alloy AlSi7 in air [8]. When foams are heated slowly in air, their surface oxide layer will grow—starting already in the solid state [9] and increasingly higher forces are required to stretch or tear them [10], which is necessary to expand the foam [11]. This mechanism is effective even if new surface areas are created during expansion through tearing of old surface regions as those will oxidize immediately in the presence of air and at high temperatures. In particular, the alloy AlCu13Mg4 represents this trend as Mg is known to increase oxidation markedly [12], thus hindering expansion even more, as it can be seen in Figure 1c at slow heating rates. This effect was also found for other Mg-containing alloys [13]. As Mg-free alloys already show pronounced expansions at low heating rates—compare Figure 1a–d for <0.4 K/s—this supports the theory of a hindered expansion due to a growing oxide layer. Untreated as well as heat-treated TiH2 powders release slightly more gas when heated at 40 K/min in comparison to heating at 10 K/min [14]. Assuming that powder particles embedded in a compacted precursor show the same behavior provides another explanation for the poor expansion at low heating rates.
Faster heating rates (>3 K/s) were found to lead to lower end expansions and strong collapse for Mg-free alloys. This may be a product of the stabilization mechanisms of PM foams as suggested previously [15]. A stabilising oxide network, although able to withstand a certain strain, could be fragmented during foaming at high heating rates by higher hydrodynamic forces. This would lead to more drainage, coalescence, and thus collapse. Another phenomenon was observed at the heating rate transition from 2.5 K/s to 3 K/s for AlSi6Cu4. Aluminium alloy protrusions consisting of the lowest melting eutectic are pushed out on the sample surface at the beginning of expansion at ~500 °C. They are reabsorbed before the main expansion starts for heating rates of 2.5 K/s or less, whereas they remain on the surface when heating with 3 K/s and higher rates. The ternary eutectic consists of 68.1 wt % Al, 26.6 wt % Cu, and 5.3 wt % Si and melts at 524 °C [16]. This implies that near-surface areas, from where the melt originates, possesses a different phase composition—especially with less Cu—than the inner volume of the foam when heated at 3 K/s or faster. This could not only alter the expansion behavior, but also and even more pronouncedly alter the collapse behavior since near-surface areas are concerned.
For alloys containing Mg, see Figure 1c,d, fast heating rates between >4 K/s are found to produce higher foam expansions than slow heating rates. Heating rates below 4 K/s indeed give rise to a small collapse, but also to very dense areas with incompletely expanded material at the bottom. The expansion behavior of AlSi8Mg4 does not increase monotonically with heating rate but shows a local minimum around 2 K/s, see Figure 1d. Samples foamed at such heating rates exhibited dense, hardly expanded alloy already at the beginning of the expansion process. Increasing the heating rate from 0.1 to 0.5 K/s or 4 to 16 K/s improves expansion due to the decrease of negative effects—e.g., premature decomposition of TiH2—as explained earlier. For heating rates from 0.5 to 2 K/s, it seems that such negative effects become more prominent and cannot be compensated by positive effects such as improved sintering between particles, which would prevent gas losses, possibly aided by the formation of MgAl2O4 [17]. Beyond 2 to 4 K/s, a certain threshold is exceeded, above which gas losses are reduced again and foam expansion is improved quickly up to a constant rise of expansion for 0.1 to 0.5 K/s or 4 to 16 K/s.

5. Conclusions

The relationship between the rate at which a foamable precursor is heated to the foaming temperature and the resulting foam expansion was investigated for four different aluminium alloys:
  • All four alloys investigated exhibit a pronounced and non-linear dependence of expansion values on the heating rate.
  • The collapse increases for all alloys when the heating rate exceeds approximately 3 K/s.
  • Low heating rates lead to low expansions.
  • High heating rates (<4 K/s) improve expansion only in Mg-containing alloys.

Author Contributions

Francisco Garcia-Moreno and John Banhart conceived and designed the experiments; Beate Pfretzschner performed the experiments and analyzed the data; Tillmann R. Neu wrote the paper.

Conflicts of Interest

The authors declare no conflict of interest.


  1. Duarte, I.; Banhart, J. A study of aluminium foam formation-Kinetics and microstructure. Acta Mater. 2000, 48, 2349–2362. [Google Scholar] [CrossRef]
  2. Garcia-Moreno, F.; Fromme, M.; Banhart, J. Real-time X-ray Radioscopy on Metallic Foams Using a Compact Micro-Focus Source. Adv. Eng. Mater. 2004, 6, 416–420. [Google Scholar] [CrossRef]
  3. Helwig, H.M.; Garcia-Moreno, F.; Banhart, J. A study of Mg and Cu additions on the foaming behaviour of Al-Si alloys. J. Mater. Sci. 2011, 46, 5227–5236. [Google Scholar] [CrossRef]
  4. Lehmhus, D. Dynamic collapse mechanisms in metal foam expansion. Adv. Eng. Mater. 2010, 12, 465–471. [Google Scholar] [CrossRef]
  5. Jiménez, C.; Garcia-Moreno, F.; Pfretzschner, B.; Klaus, M.; Wollgarten, M.; Zizak, I.; Schumacher, G.; Tovar, M.; Banhart, J. Decomposition of TiH2 studied in situ by synchrotron X-ray and neutron diffraction. Acta Mater. 2011, 59, 6318–6330. [Google Scholar] [CrossRef]
  6. Matijasevic, B.; Banhart, J. Improvement of aluminium foam technology by tailoring of blowing agent. Scr. Mater. 2006, 54, 503–508. [Google Scholar] [CrossRef]
  7. Jiménez, C.; Garcia-Moreno, F.; Pfretzschner, B.; Kamm, P.H.; Neu, T.R.; Klaus, M.; Genzel, C.; Hilger, A.; Manke, I.; Banhart, J. Metal foaming studied in situ by energy dispersive X-ray diffraction of synchrotron radiation, X-ray radioscopy, and optical expandometry. Adv. Eng. Mater. 2013, 15, 141–148. [Google Scholar] [CrossRef]
  8. Weigand, P. Untersuchung Der Einflußfaktoren Auf Die Pulvermetallurgische Herstellung Von Aluminiumschäumen; Verl. MIT: Bremen, Germany, 1999. [Google Scholar]
  9. Field, D.J.; Scamans, G.M.; Butler, E.P. The high temperature oxidation of Al-4.2 Wt Pct Mg alloy. Metall. Trans. A 1987, 18, 463–472. [Google Scholar]
  10. Kahl, W.; Fromm, E. Examination of the Strength of Oxide Skins on Aluminum Alloy Melts. Metall. Trans. B 1985, 16, 47–51. [Google Scholar] [CrossRef]
  11. Dudka, A.; García-Moreno, F.; Wanderka, N.; Banhart, J. Structure and distribution of oxides in aluminium foam. Acta Mater. 2008, 56, 3990–4001. [Google Scholar] [CrossRef]
  12. Drouzy, M.; Mascré, C. The oxidation of liquid non-ferrous metals in air or oxygen. Int. Mater. Rev. 1969, 14, 25–46. [Google Scholar] [CrossRef]
  13. Simančík, F.; Behulová, K.; Borš, L. Effect of ambient atmosphere on the foam expansion. In Cellular Metals and Metal Foaming Technology; Banhart, J., Ashby, M., Fleck, N., Eds.; MIT Publishing: Bremen, Germany, 2001; pp. 89–92. [Google Scholar]
  14. Jiménez, C. Characterization and Modification of Powders Used to Make Aluminium-Based Metal Foams. Ph.D. Thesis, Technische Universität, Berlin, Germany, 2010. [Google Scholar]
  15. Körner, C.; Arnold, M.; Singer, R.F. Metal foam stabilization by oxide network particles. Mater. Sci. Eng. A 2005, 396, 28–40. [Google Scholar] [CrossRef]
  16. Lukas, H.L.; Lebrun, N. Aluminium–Copper–Silicon. Landolt-Börnstein Group IV Phys. Chem. 2003, 11, 135–147. [Google Scholar]
  17. Guo, Z.Q.; Ma, D.H.; Yuan, X.G.; Dong, X. Effect of Mg Addition on the Foaming Behaviour of AlSi7 Based Alloy Prepared by Powder Metallurgy Method. Rare Met. Mater. Eng. 2016, 45, 3068–3073. [Google Scholar]
Figure 1. Maximum area expansion and end area expansion (measured during cooling at ~300 °C) as a function of the heating rate (logarithmic scale) applied to precursors of the alloys (a) AlSi7, (b) AlSi6Cu4, (c) AlCu13Mg4, and (d) AlSi8Mg4. Averages over all experiments carried out on a particular alloy are given. X-ray radioscopic images for one representative sample at the state of maximum expansion for the indicated heating rates are also displayed.
Figure 1. Maximum area expansion and end area expansion (measured during cooling at ~300 °C) as a function of the heating rate (logarithmic scale) applied to precursors of the alloys (a) AlSi7, (b) AlSi6Cu4, (c) AlCu13Mg4, and (d) AlSi8Mg4. Averages over all experiments carried out on a particular alloy are given. X-ray radioscopic images for one representative sample at the state of maximum expansion for the indicated heating rates are also displayed.
Metals 07 00323 g001
Figure 2. X-ray radiograms of foams after the first visible crack has been detected (a,c) and at the end of the heating ramp after 695 °C has been reached (b,d) at heating rates of 0.5 K/s (left) and 1 K/s (right).
Figure 2. X-ray radiograms of foams after the first visible crack has been detected (a,c) and at the end of the heating ramp after 695 °C has been reached (b,d) at heating rates of 0.5 K/s (left) and 1 K/s (right).
Metals 07 00323 g002
Metals EISSN 2075-4701 Published by MDPI AG, Basel, Switzerland RSS E-Mail Table of Contents Alert
Back to Top