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Metals 2012, 2(3), 265-273; doi:10.3390/met2030265
Published: 9 August 2012
Abstract: Because of their excellent thermal and electric conductivities, copper foams are ideally suited for applications such as heat exchangers, catalyst supports and EMI-shields. Here, we demonstrate the preparation of copper with ~80% aligned, elongated, interconnected pores via directional freeze casting, a well established processing technique for porous ceramics. First, an aqueous slurry of 40−80 nm cupric oxide powders was directionally solidified, resulting in a preform consisting of elongated, aligned dendrites of pure ice separated by interdendritic ice walls with high oxide powder content. Oxide rather than metallic nanometric particles are used, as the latter would oxidize rapidly and uncontrollably when suspended in the aqueous solution used during directional casting. The preforms were then freeze-dried to sublimate the ice and sintered in a hydrogen-bearing atmosphere to reduce the copper oxide to metallic copper particles and densify these copper particles. Microstructural analysis of the copper foams shows that three types of porosities are present: (i) aligned, elongated pores replicating the ice dendrites created during the freeze-casting process; (ii) micro-porosity in the partially sintered copper walls separating the elongated pores; and (iii) cracks in these copper walls, probably created because of shrinkage associated with the reduction of the oxide powders.
Copper foams, due to the excellent thermal and electric conductivities of the copper matrix, are ideally suited for a wide range of industrial applications, such as heat exchangers, catalyst supports and EMI-shielding, while the ductility of copper leads to good foam mechanical energy absorption in compression.
Research in recent years has been directed towards developing new methods and optimizing existing processing techniques to create copper foams. Typical processing routes to produce copper foams include space-holder techniques, dissolution of a less noble element in binary copper alloys, investment casting and melt gas injection [1,2,3,4,5,6,7,8,9,10].
The present work aims to create copper foams via freeze casting [11,12,13]. This processing technique consists of freezing an aqueous suspension of powders such that pure ice dendrites push the powders in interdendritic space, sublimation of the ice, and sintering of the resulting green body, where pores replicate the dendrites. This method is well established for producing porous ceramics but had never been applied to metals, until recently when Chino and Dunand and Li and Dunand [14,15] used it to create titanium with elongated pores, starting from titanium powders.
In comparison with the established processing techniques for copper foams mentioned above, directional freeze casting as a processing route for creating copper foams offers the opportunity to create aligned, elongated pores, using space holders (ice) which are created in situ during solidification. This method further offers the ability to manipulate the pore fraction, diameter, spacing and orientation.
Here, we demonstrate for the first time that directional freeze casting can be used to create copper foams with aligned, elongated pores, using copper oxide powders suspended in water which are subsequently sintered in a hydrogen atmosphere to simultaneously reduce the copper oxide to pure copper and densify the copper particles. Oxide rather than metallic particles are selected here to avoid uncontrolled oxidation in aqueous solutions, and reduce the tendency for powder settling. The resulting microstructure of the copper foam is analyzed, and some factors affecting the formation of the porous structure are further investigated.
2. Results and Discussion
2.1. Foam Microstructure
Optical micrographs of longitudinal cross-sections of a copper foam obtained from a 10 vol % cupric oxide (CuO) suspension (sample 1) and from a 15 vol % CuO suspension (sample 2) are depicted in Figure 1 a–c and Figure 2 a–c, respectively. The micrographs show a high amount of porosity in the foams, which is highly aligned in some regions of the samples.
The longitudinal cross-sections at low magnification in Figure 1a and Figure 2a show that, in up to about one third of the total height of the sample 1, the copper walls are aligned in the freezing direction, followed by a zone where the structure appears to be more isotropic and the pores are much smaller. For sample 2, elongated pores start at the bottom of the sample and extend up to about 90% of the total height of the sample, followed by a thin layer where solidification was non-directional. The optical analysis indicates that significant particle settling occurred during solidification of the 10 vol % slurry, causing a gradient in solids content and consequently in the density of the freeze-cast structure. By contrast, an initial CuO powder loading of 15 vol % in the slurry is sufficient to create ice dendrites over most of the sample height, and particle pushing in the interdendritic space indicates that electrostatic stabilization of the powders by adjusting the pH value to 10 through addition of KOH is successful. The optical micrographs at higher magnifications (Figure 1b, c and Figure 2b, c) reveal the structure of the copper walls which consist of sintered copper particles and micro-pores within the walls. Cracks and some larger pores are visible within the walls as well. These cracks were not observed in the microstructure of the directionally freeze-cast titanium foams prepared by sintering of metallic Ti powders by Chino and Dunand and by Li and Dunand [14,15]. One possible explanation might be that these cracks form during the reduction of the cupric oxide, which involves a volume decrease due to the higher density of copper compared to cupric oxide.
Three populations of pores can be distinguished: aligned, elongated pores; cracks in the copper walls and micro-porosity within the copper walls. In addition, Figure 2d and 2e show optical micrographs of transverse cross-sections of the sample 2. There are several regions were pores are aligned. These regions replicate colonies of parallel ice dendrites, as also observed in titanium foams [14,15].
The average pore diameter for sample 1 and sample 2 is 75 ± 36 μm and 91 ± 33 μm, respectively. It should be noted that the average pore diameter for sample 1 has been measured only for the area where directional solidification occurred. Archimedes measurements revealed a total porosity of ~80% and were verified by means of the software ImageJ. The relative density of ~20% is higher than the loading fraction of 15% as expected from densification during sintering.
2.2. Influence of Sintering Parameters
Through control of the temperature gradient and powder characteristics, it has been shown that the pore fraction, diameter, spacing and orientation could be manipulated in titanium foams created by a similar freeze-casting method [14,15]. It is expected that the pore characteristics of the present copper foam can be similarly controlled.
Figure 3 shows the effect of additional sintering upon the microstructure of the copper foam walls. The figure depicts two pieces of the same foam obtained from a 15 vol % CuO slurry, from which the second piece (Figure 3b) was re-sintered for 4 h at 800 °C. It is evident that micro-porosity was significantly reduced after the re-sintering step. This densification is expected due to the high homologous temperature at which small pores sinter by flux of vacancies.
3. Experimental Procedures
3.1. Slurry Preparation
Powders of cupric oxide (6.31 g·cm−3 density) with an average particle size of 40–80 nm and with 99.9% purity were purchased from Inframat Advanced Materials (Manchester, CT, USA). For all experiments, 0.2 wt % agar binder (Eden Foods Inc., Clinton, MI, USA) was stirred in deionized water. The mixture was then boiled to dissolve the agar and degas the water and subsequently allowed to cool down. The slurries for freeze casting were prepared in a polypropylene test tube with 13 mm inner diameter and 1.2 mm average wall thickness. To improve heat conduction and promote unidirectional freezing, the conical bottom of the test tubes was sectioned and replaced by a copper cylinder of 12.7 mm diameter and ~1 cm height that was glued in place with silicone.
For the first set of experiments, 2.1 g of cupric oxide powders and 1 μL of neutral detergent as a dispersant were stirred in 3.0 mL of the prepared water/agar mixture. The resulting slurry contained 10 vol % of copper oxide powders and was subsequently degassed in a vacuum desiccator. The slurry was cooled to a few degrees above the freezing point of water and was then stirred for about 30 s to suspend the powders homogeneously before freeze-casting.
In the second set of freeze-cast experiments, aqueous suspensions containing 15 vol % CuO were prepared. In order to increase the amount of solids content from 10 to 15 vol %, it became necessary to reduce particle-particle attraction and to improve the stability of the suspension. Ceramic suspensions can be stabilized in both basic and acid electrolytes. Initial tests, where hydrochloric acid (HCl) and potassium hydroxide (KOH) were added to decrease or increase the pH value of the suspension, respectively, revealed that stabilization in the basic range was easier to achieve. Therefore, sedimentation experiments in the basic range were conducted. For this purpose, six different dilute suspensions were prepared. In each case, 6 mL of deionized water and 2 g of CuO powders were used. The water was filled into small cylindrical glass beakers and KOH was added to five of the six testing solutions to vary the pH values from 8 to 9, 10, 11 and 12. Powders were stirred in and the suspensions were sonicated for 30 min to break down large agglomerates. When stirring in the powders, it was observed, that suspensions of pH 10 and 11 were less viscous, and powders dispersed more easily. Finally, 2 μL of neutral detergent were added for steric stabilization, and suspensions were stirred one more time. The dispersant was added after sonicating, to avoid foaming of the slurries. The suspensions were allowed to stand for 3 h. The height of the sedimentation layer was subsequently measured for the individual suspensions. Comparison of the results showed that the height of the sedimentation layer was minimal for the suspensions with pH 10 and 11. This indicates that these suspensions are well deflocculated, because they settled relatively slowly and the sediment was relatively dense. Suspensions of pH 7, 8, 9 and 12 appeared more coagulated, since they settled rapidly and the sediment was of relatively low density. These results are in good agreement with the observations made when stirring the powders in the water.
Consequently, in the second set of freeze-cast experiments, the pH value of the water/agar mixture was adjusted to pH 10 by adding KOH. Afterwards, 2.0 g of cupric oxide powders were stirred in 3.0 mL of the prepared water/agar/KOH mixture and sonicated for 30 min. Thereafter, 1.34 g of cupric oxide powders were stirred in the slurry and the resulting 15 vol % slurry was sonicated again for 30 min. Finally, 1 μL of neutral detergent was added and the slurry was degassed in a vacuum desiccator. As in the first set of experiments, the slurry was cooled to a few degrees above the freezing point of water and was then stirred for about 30 s to suspend the powders homogeneously before freeze-casting.
3.2. Freeze Casting and Sintering
The setup designed for freezing the aqueous slurries consisted of a secondary container filled with a sodium chloride (NaCl)/ice/water cooling bath mixture and is illustrated in Figure 4. The initial temperature of the cooling bath varied in the range of −14 °C to −19 °C and stayed almost constant during the whole freezing stage. The sides and the bottom of the secondary container were insulated with polystyrene foam to delay the rise in temperature of the cooling bath mixture. A small copper rod was attached to the bottom center of the secondary container and served as a conductor between the cooling bath and the test tube containing the slurry. The bottom of the test tubes used, i.e., the copper cylinder, and the copper rod had identical diameters, so that the test tube could be placed on top of the copper rod. To realize directional solidification of the slurry, the sides and top of the test tube were insulated with polystyrene foam. The test tube was removed from the freezing unit after 1.5 h.
The frozen ice/CuO billets were then sublimated for 24 h in a lyophilizer under a 0.060 mbar vacuum at −83 °C. For the sintering of the resulting ice-free green bodies, a tube furnace was used with a flowing atmosphere of Ar-4% H2 to reduce the cupric oxide to metallic copper. The sample was heated at a constant heating rate of 10 °C min−1 until it reached 600 °C. The holding time was 2 h and the sample was then furnace-cooled.
One additional experiment was conducted, in which a sintered billet was broken in two pieces. One piece was re-sintered with a heating rate of 10 °C min−1 and holding time of 4 h at 800 °C, to investigate the influence of further sintering on the foam microstructure.
3.3. Microstructural Analysis
The freeze-cast and sintered billets were cut such that cross-sections parallel and perpendicular to the pore longitudinal direction could be polished and imaged. The width of twenty pores was measured on an image of the transverse cross-section using the ImageJ software.
Porosity was measured by the Archimedes method, where the samples were weighted in air and in water (after filling pores with grease in the latter case). These results were verified by means of the ImageJ software, where porosity was calculated from the digitally colored optical micrographs of the epoxy-filled sample by measuring the area occupied by the epoxy.
Copper foams with aligned, elongated macro-pores were created by directional freeze casting of aqueous slurries of cupric oxide powders followed by freeze-drying to remove ice dendrites and annealing in an Ar-4% H2 atmosphere to reduce the cupric oxide to copper and to sinter the powders. To achieve formation of aligned, elongated pores, sufficient solids loading and stability of the suspension during the freezing stage are required. Cupric oxide nanoparticle suspensions can be successfully stabilized by adjusting the pH of the suspension to 10 though addition of KOH. Three populations of pores are present in the foam microstructure: aligned, elongated pores (replicating ice dendrites), cracks in the copper walls (probably due to shrinkage during reduction) and micro-porosity within the copper walls (from incomplete sintering). The amount of micro-porosity is significantly reduced by increasing sintering time and temperature. Finally, density and porosity measurements have shown that total porosity of the sintered copper foams is about 80% for initial solids loading of 15 vol % in the slurry, and pore diameter is about 91 μm.
We thank C.A. Mirkin for the use of his lyophilizer, D.N. Seidman for the use of his tube furnace, and D. Isheim for helpful instructions about tube furnace operation.
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