One-dimensional (1D) nanostructures such as nanotubes, nanowires, and nanobelts have been the focus of much recent attention, owing to the novel electronic and optical properties intrinsically associated with their low dimensionality and the quantum confinement effect. Such 1D nanostructures have potential applications in nanoelectronics, advanced composites, field emission devices, sensors, probes, optics and optoelectronics (Baughman et al., 2002, Agarwal & Lieber, 2006). Silicon nanowires have been preferentially studied since Si is of great technological importance in microelectronics (Morales & Lieber, 1998). Silicon nanowires exhibit significant differences in physical (Cui & Lieber 2001,. Ma, et al 2003, Sun et al., 2001) and chemical properties (Sun et al., 2003, Chen et al., 2005) from bulk Si, which have been exploited to fabricate nanoelectronic devices such as logic circuits (Huang et al., 2001), field effect transistors (Lieber, 2003), and sensors (Cui et al., 2001). Compared to Si, Ge nanostructures are of particular interest, since the exciton Bohr radius of bulk Ge (24.3 nm) (Maeda et al., 1991) is larger than that of Si (4.9 nm) (Cullis et al., 1997), resulting in more prominent quantum confinement effects. Ge also offers the advantage of lower processing temperatures with easier integration into conventional devices. Furthermore, Ge has much higher electron and hole mobility than Si (Sze, 1981), which is especially required when electronic devices are scaled down to the sub-100 nm regime.
Several growth methods have been developed for the synthesis of Ge nanowires, including laser ablation (Morales & Lieber, 1998, Zhang et al., 2000), thermal evaporation (Gu et al., 2001, Nguyen et al., 2005, Sun et al., 2006, Das et al., 2007, Sutter et al., 2008), supercritical-fluid synthesis (Ryan et al., 2003, Polyakov et al., 2006, Ziegler et al., 2004, Erts et al., 2006), liquid-state synthesis (Heath & LeGoues, 1993, Song et al., 2009), molecular beam epitaxy (Omi & Ogino, 1997), and chemical vapor deposition (CVD) (Kodambaka et al., 2007, Ryan et al., 2003). CVD has been the most widely employed of these synthesis methods, with the aim of synthesizing Ge nanowires in a controllable way via the selection of suitable Ge precursors and catalysts. To date a number of Ge-containing precursors have been used to grow Ge nanowires, including GeH4 (Kamins et al., 2004, Wang & Dai, 2002, Jin et al., 2006, Kang et al., 2008, Wang & Dai, 2006), Ge2H6 (Kodambaka et al., 2007), Ge(C5H5)2 (Mathur et al., 2004; Mathur & Barth, 2008), C12H12Ge (diphenyl germane) (Ryan et al., 2003, Hanrath & Korgel, 2002, Polyakov et al., 2006, Ziegler et al., 2004, Erts et al., 2006), Ge-GeO2 (Yin et al., 2007), and Ge-GeI4 (Wu & Yang, 2000). In most CVD methods, as well as methods employing thermal evaporation of Ge powders (Gu et al., 2001, Nguyen et al., 2005, Sun et al., 2006, Das et al., 2007, Sutter et al., 2008), Au nanoparticles have been typically selected as the catalyst for Ge nanowire growth via the vapour–liquid–solid (VLS) mechanism (Wagner & Ellis, 1964) due to the low eutectic temperature of the Ge–Au alloy (360 C). Other low melting point metals/alloys that have been employed as the catalyst include Al (Wang et al., 2006), Cu (Yao & Fan, 2007), Cu-Ni (Kang et al., 2008) and Fe(Ge) (Mathur, et al., 2004). Recently, the vapor-solid-solid (VSS) mechanism (Kamins et al. 2001, Bootsma & Gassen, 1971) has also been implicated, based on experimental observations that the catalyst state can be either liquid or solid depending on the thermal history, Ge2H6 pressure, and temperature. The supersaturation of Ge in the alloy catalyst caused by the growth process appears to be essential in stabilizing the liquid below the eutectic temperature; therefore, Ge nanowires can grow by both the VLS and VSS mechanisms, although at different rates (Kodambaka et al., 2007).
Although highly ordered metallic and semiconductor nanowires can be used in electronic devices, in many cases these nanowires are sensitive to oxygen and water vapor, resulting in degradation of the nanodevice performance (Zhang et al., 2007). Consequently, in some cases it is necessary to avoid any contact of these materials with the external environment. This is particularly important for Ge, which forms oxide coatings possessing unfavorable electronic properties. Untreated Ge nanowires are reported to oxidize upon exposure to ambient conditions to form a 1-2 nm thick GeO2-
Carbon-encapsulated Ge nanowires have previously been prepared using a chemical vapor deposition (CVD) technique (Sutter & Sutter, 2006). A supported Au catalyst was employed to catalyze the growth of Ge nanowires, which were then dispersed on an amorphous carbon film and annealed, resulting in the encapsulation of the nanowires by well defined, curved graphene sheets. The presence of gold nanoparticles (residual catalyst) on the surface of the nanowires was indicated as being instrumental in initiating graphene sheet formation. Other methods which have been employed for the preparation of Ge/C core-sheath nanostructures include the arc discharge synthesis of CNTs in the presence of Ge metal (Dai et al., 1996; Loiseau et al., 2000), and the deposition of graphitic coatings on pre-formed Ge nanowires by their treatment with organic vapors at 700-900 C (Wu & Yang, 2000).
For practical circuit device fabrication, e.g., for photoresistors (Polyakov et al., 2006), photoluminescence devices (Ryan et al., 2003) and gas sensors (Rajaputra et al., 2008), ordered nanowire arrays are required. To this end, Holmes’s research group has employed ordered mesoporous aluminosilicate thin films (Ryan et al., 2003, Ziegler et al., 2004) and AAO membranes (Polyakov et al., 2006, Erts et al., 2006) as templates to grow Ge nanowire arrays by the degradation of diphenylgermane (C12H12Ge) in supercritical CO2. The experimental protocol involved placing the ordered porous films or AAO membranes inside a 25 mL high-pressure reaction cell with diphenylgermane placed inside an open top quartz glass boat adjacent to the membranes under an inert atmosphere. A typical synthesis at 600 C under 37.5 MPa for 30 min resulted in conductive Ge nanowires which filled the template pores (Ziegler et al., 2004).
To meet the demands for practical device fabrication, we have studied the synthesis of Ge nanowires protected through encapsulation in multi-walled carbon nanotubes (MWCNTs) using a simple one-step synthesis method (Pandurangan et al., 2009). In this approach, a CVD method employing neat phenyltrimethylgermane (PTMG, boiling point of b.p. 183 C) was used, the PTMG functioning as both the Ge and C source. Although transition metal catalysts have typically been employed for the synthesis of CNTs, it has recently been shown that semiconductor nanoparticles of SiC, Ge and Si can act as templates for the production of single-walled and double-walled carbon nanotubes during CVD synthesis with ethanol (Takagi et al., 2007). In this study, pure PTMG acts as a precursor for the formation of Ge nanoparticles which act as templates for the formation of MWCNT-encapsulated Ge nanowires. The effect of employing a floating Fe catalyst, using ferrocene as a precursor, has also been investigated. To tailor the derived Ge nanowire diameter and orientation, the use of anodized aluminum oxide (AAO) templates has also been evaluated.
2. Synthesis of Ge nanowires encapsulated within multiwalled carbon nanotubes
Previous work in our laboratory (Andrews et al., 1999) and others (Öncel & Yürüm, 2006) has established chemical vapor deposition (CVD) as an efficient means of preparing multiwalled carbon nanotubes (MWCNTs). In addition to the relatively simple equipment required, the use of CVD enables the process to be readily scaled, such that MWCNTs can be produced in quantities ranging from milligrams to kilograms. Consequently, to prepare MWCNT-encapsulated Ge nanowires, we elected to employ the same basic CVD technique. However, rather than using a floating catalyst such as ferrocene (required to catalyze MWCNT growth) dissolved in a carbon precursor such as xylene, we elected to employ neat PTMG as both the Ge and C source. In effect, PTMG acts as a precursor for the formation of Ge nanoparticles which, in turn, function as templates for the formation of MWCNT-encapsulated Ge nanowires (Pandurangan et al., 2009).
The two-zone furnace employed for the CVD preparation was similar to that described previously for the growth of pristine MWCNTs, and consisted of a quartz tube reactor with a flat quartz slide inserted at the reaction zone for additional deposition surface (Andrews et al., 1999). Neat PTMG was injected into the preheat zone of the reactor at a rate of 1 ml/h. After volatilization in the preheat zone (~250 C), the PTMG was carried into the reaction zone of the furnace, maintained at 800 C, by a 10% H2/Ar sweep gas. The entire system was maintained at a slight positive pressure (~0.75 kPa) versus atmospheric pressure. Typical CVD runs were of 2 h duration, after which the material deposited on the quartz slide was collected for analysis.
Representative scanning electron micrographs of the material prepared at 800 C are shown in Fig. 1. These show the sample to consist mainly of nanowires, possessing diameters of less than 500 nm (see Fig. 1b). The nanowires appear smooth, with little evidence of metal cluster formation. Furthermore, from Fig. 1 and other micrographs, it is apparent that the as-synthesized nanowires are largely free from amorphous carbon and possess large aspect ratios, the typical length being in the order of 10 µm. In contrast, at 700 C decomposition of the precursor appears to be incomplete; consequently, only a few short wires are formed. Increase of the temperature above 800 C results in the formation of amorphous carbon, with Ge nanoparticle formation being favored over the formation of nanowires.
As revealed by TEM, the product obtained at 800 C (hereafter denoted as Ge@MWCNT/800) consists of crystalline Ge nanowires, encapsulated in a thin MWCNT sheath. Typical TEM images at low magnification (see Fig. 2a) reveal a pin-like morphology. TEM images at higher magnification (Fig. 2b-d) show that the Ge nanowires consist of well crystallized Ge cores which are completely encapsulated by the sheath-like MWCNTs possessing a thickness of 5-10 nm. Ge incorporation within the graphene sheets of the MWCNTs is not observed according to EDS analysis under STEM mode. Quantitative EDS analysis of the tube cores indicates a composition of 95% Ge and 5% C (atom %). Given the existence of 5-10 nm thick of graphene (C) layers covering the Ge core at the analytical probe position, it can be concluded that the core consists of pure Ge, as supported by HRTEM observations that show clear fringes corresponding to single crystal Ge (see Fig. 2c, 2d). Furthermore, EDS analysis confirmed that the near spherical heads of the nanowires consist of over 97 atom % Ge (the balance being C).
Powder X-ray diffraction data confirm the crystalline nature of the nanowires (Fig. 3a). The positions of the observed diffraction peaks (2θ = 27.43, 45.45, 53.83, 66.13, 73.11, 83.79) are in good agreement with literature values (Miikin, 1961) for the crystalline face centered cubic phase of Ge with lattice parameter
As shown in Fig. 3b, the X-ray photoelectron spectrum of Ge@MWCNT/800 contains two Ge 3d photoelectron lines. The signal corresponding to a binding energy of 29.7 eV can be assigned to Ge metal, albeit that it is slightly shifted (~0.3 eV) compared to 3d binding energies typically observed for bulk Ge. The other signal at 32.5 eV is characteristic of GeO2. Deconvolution of the signals and integration indicates a Ge(0):Ge(IV) atomic ratio of 78:22, suggesting that the Ge nanowires are largely, although not completely, protected from oxidation. Additionally, it is likely that amorphous, partially oxidized Ge is present, which contributes to the GeO2 signal. While SEM analysis of Ge@MWCNT/800 suggests that nanowires constitute at least 80% of the sample, the presence of irregularly shaped Ge particles can be observed in some SEM images (as shown in Fig. 5c below).
The results of thermogravimetric analysis performed on Ge@MWCNT/800 in air are shown in Fig. 4a. Noteworthy is the observation that a pronounced increase in sample weight commences at around 550 C, consistent with the oxidation of Ge to GeO2. This temperature corresponds to the initiation of MWCNT combustion (Bom et al., 2002), suggesting that Ge oxidation proceeds as the nanowires’ outer carbon shells are oxidized and the Ge cores are exposed. Allowing for the initial carbon content of 3 wt.% in the sample (by elemental analysis), and assuming that all of the Ge present is oxidized to GeO2, the observed gain in sample weight (37%) corresponds to an initial molar Ge:GeO2 ratio of 86:14 (in reasonable agreement with the value determined by XPS). As shown in Fig. 4b, differential scanning calorimetry (DSC) performed under N2 gave a melting point of 934 C for the Ge nanowires.
In the absence of an external carbon source, the carbon constituting the MWCNTs derives from the phenyltrimethylgermane precursor. In principle, an atomic Ge:C ratio of 1:9 is feasible in the product if decomposition of the precursor proceeds according to: C6H5Ge(CH3)3 → Ge + 9C + 7H2. In fact, elemental analysis of the product typically showed a Ge:C ratio of
Insight into the factors controlling nanowire formation is provided by the results of CVD experiments in which the deposited solid was sampled from quartz slides placed at fixed distances from the inlet, i.e., along the length of the tube reactor. The reaction zone was again held at 800 C. SEM images of these materials are shown in Figs. 5 and 6. Images 5a-5d correspond to a CVD run performed using neat PTMG as the precursor, while images 6a-6d correspond to the product obtained using PTMG diluted to 50 wt% with xylene. For both runs, light deposits of mainly amorphous Ge particles were obtained closest to the inlet. For the run using neat PTMG, nanowires could be found in a localized region of the reactor, between 4’’ and 5’’ from the inlet. Further away from the inlet, Ge particles were obtained (Fig. 5d). Evidently, while carbon is available beginning at 4’’ from the inlet from cracking of the PTMG, the partial pressure of carbon in the atmosphere is insufficient to produce Ge-filled nanotubes along the entire length of the reactor. In contrast, when the PTMG/xylene mixture was used, not only was the total yield of Ge-filled nanotubes increased (estimated at >50% based on Ge), Ge-filled nanotubes were observed in the entire region 4”-7” from the inlet. Furthermore, the dimensions of the filled nanotubes were rather uniform, with diameters in the 200-300 nm range and lengths of 6-10 μm. These results suggest that the form of the germanium deposit obtained is regulated by the partial pressure of carbon in the atmosphere.
For the runs performed with both neat PTMG and PTMG/xylene, structures could be observed which appear to correspond to the early stages of nanotube/nanowire growth. Examples of this are shown in the circled regions of Fig. 5b. CNT growth evidently occurs
from the Ge particle (root growth mechanism) and appears to carry Ge as a nanowire away from the initial particle. Presumably, this synthesis mode is the result of wetting at the interface of the Ge and the growing carbon nanotube. This is illustrated in Fig. 2c, which shows the high degree of association between the carbon sheath and the Ge nanowire. It should be noted that the synthesis temperature used (800 C) was more than 100 C lower than the melting point of Ge. As shown in Fig. 4b, a m.p. of 934 C was measured for the Ge nanowires. While this is only slightly lower than the melting point for bulk Ge (938 C), it has been reported that smaller nanoscale metal structures can exhibit much greater melting point depression (Buffat & Borel, 1976, Couchman & Jesser, 1977). Hence, melting point depression can be expected during the initial stages of nanowire growth. This effect, together with possible capillary action (Dujardin et al., 1994), can explain the apparently low Ge viscosity and the tendency for CNT filling by Ge.
Finally, it is worth noting that initial attempts to prepare MWCNT-encapsulated Si, Sn or Bi nanowires using this approach have proved unsuccessful. In the case of silicon, this can be attributed to its high melting point (1410 ºC), such that any Si nanoparticles formed will be solid at the synthesis temperature. In the case of Sn and Bi, the melting points are much lower (232 and 271 ºC, respectively). In this case, the observation of metallic deposits in the pre-heat zone is consistent with the relatively low decomposition temperatures of the organometallic precursors used (Sn(C6H5)(CH3)3 and Bi(C6H5)3), i.e., deposition occurs in a region where the temperature is too low for carbon nanotube formation to occur. Consequently the need for precursors which are less thermally labile is indicated.
3. Synthesis of Ge-Fe nanowires encapsulated by multiwalled carbon nanotubes
Recent work has shown that the properties of nanotubes formed by assembly of metal encapsulated silicon and germanium clusters can be tailored by a suitable choice of metal atoms (Pokropivnyi, 2001). Fe-doped ferromagnetic Si nanotubes and Mn-doped Si nanotubes with nearly degenerate ferromagnetic and antiferromagnetic states have been obtained with high local magnetic moments (Singh et al., 2004), making them attractive for nanomagnetic and spintronic devices. Although Mn doping in bulk Ge has found to give rise to weak ferromagnetic behavior (Park et al., 2002, Cho et al., 2002), in low dimensional systems such as nanowires the magnetic behavior could be very rich depending upon the nanostructure and doping of metals. From this it follows that the synthesis of MWCNT-encapsulated Ge-Fe nanowires is of interest.
To prepare Ge-Fe nanowires, the same one-step CVD process was used as successfully employed for the growth of encapsulated Ge nanowires, employing PTMG, pyridine and ferrocene as precursor materials. Ferrocene (b.p. 249 oC) has been shown to be an excellent precursor for producing metallic iron catalyst particles which can seed carbon nanotube growth. Pyridine was used as the solvent and additionally functions as the primary carbon source. In a typical run 1.15g of ferrocene was dissolved in 10 g pyridine, to which 1.0 g of
PTMG was added. The homogeneous solution was injected into the preheat zone of the reactor (~250 oC) at an addition rate of 1 mL/h and the resulting vapor was swept into the reaction zone of the furnace by a 10% H2/Ar carrier gas.
After a typical CVD run of 2 h duration, the black deposit obtained was recovered and analyzed by SEM. Figure 7a-7d shows SEM images of the product formed at temperatures varying between 700 and 1000 oC. From Figure 7b and other micrographs it is apparent that the nanotube bundles obtained at 800 C are free from other carbonaceous materials and possess large aspect ratios, typical nanotube length being in the order of 10 µm. In contrast, at 700 oC only a few short MWCNTs are formed (Figure 7a). The majority of the carbon present is amorphous in form, while the metals are observed as particles which are agglomerated on the surface of the carbon. At 800 oC, carbon nanotube production improves significantly, while there is an absence of metal particles. As for Ge@MWCNTS, these findings suggest that the growth kinetics of the MWCNTs at these different temperatures significantly impact the form of the deposited metals. Further increase of the temperature results in decreased MWCNT purity and increased amounts of pyrolytic forms of carbon.
As revealed by TEM, the CVD-derived material prepared at 800 ºC (Figure 8) consists of pure MWCNTs possessing cores composed of a Ge-Fe alloy. As shown in Figures 8a and 8b, the Ge-Fe nanowires consist of a uniform single crystal core with the exception of an enlarged head and tail portion, and are completely encapsulated by the MWCNTs. Figure 8b shows a high magnification view of a completely filled MWCNT. From this and other images it is apparent that these nanowires are indeed crystalline and without an amorphous coating of any kind, as is sometimes observed for metallic nanowires (Morales & Lieber, 1998). According to TEM, the outer diameter of the Fe-Ge filled MWCNTs lies in the 20-70 nm range, with the diameter of the Ge-Fe cores falling in the range 5-15 nm. Electron energy loss spectroscopy (EELS) analysis under STEM mode shows a sharp C-K edge at 284 eV, indicating that the carbon atoms are in the sp2-hybridized state. The EDS spectrum obtained from the MWCNT-sheathed nanowires show the presence of Ge, Fe and C (Figure 8c), while XRD (Figure 8d) shows diffraction peaks which are close to those characteristic for the phase Fe1.67Ge (PDF# 00-017-0232).
Examination of Ge binary phase diagrams shows that the Ge-rich region of the Ge-Fe diagram (Mathur et al., 2004) is similar to that of the Si-Fe diagram (Morales & Lieber, 1998, Moffatt, 1976); above 838 oC the phases are FeGex(l) + Ge(s), and below this temperature they are β-FeGe2(s) + Ge(s). The mechanism of Ge-Fe nanowire formation is therefore likely to follow that proposed above for the growth of Ge nanowires, i.e., involving Ge-Fe nanoparticle formation, followed by carbon nanotube growth and nanotube filling by the mobile Ge-Fe phase. In comparison with the Ge nanowire synthesis, the elemental C:metal ratio used in the Ge-Fe nanowire synthesis is much higher, i.e., C:(Ge+Fe) = 112, as opposed to the C:Ge ratio of 24 used in the optimized Ge nanowire synthesis (employing 50 wt% PTMG in xylene). Consequently, there appears to be insufficient Ge-Fe alloy to completely fill the nanotubes, as evidenced by the TEM image in Fig. 8a. Finally, we note that these results contrast with MWCNTs grown using a simple pyridine-ferrocene feedstock via the same floating catalyst CVD method (Qian et al., 2003). In the latter case, conical Fe3C catalyst particles are observed in the product, located at each nanotube root (being consistent with a typical root growth model), without any filling of the tube cores by Fe. This supports the idea that the active catalyst in the Ge-Fe system is indeed a Ge-Fe alloy, rather than an iron carbide type catalyst.
4. Growth of MWCNT-encapsulated Ge nanowires with uniform diameters
In previous work, vertically aligned carbon nanotube arrays have been grown in the pores of AAO templates using a CVD method similar to the general method described for the synthesis of MWCNTs (Andrews et al., 1999), with the exception that pure xylene was used as the hydrocarbon source without any ferrocene catalyst precursor in the feed (Rajaputra et al., 2008). The resulting aligned MWCNT arrays have been used to fabricate gas sensors (Rajaputra et al., 2008); by monitoring the electrical resistance response, low concentrations of NH3 and NO2 can be detected by these arrays.
In this study, porous AAO templates were fabricated by a two-step anodization process of high purity aluminium tape in a 0.3 M oxalic acid medium as reported earlier (Rajaputra et al., 2008). By selecting suitable electrochemistry parameters, AAO membranes with uniform pore size of ~45 nm and thickness of 50 µm were prepared. Several pieces of these AAO templates were placed on a quartz plate that was inserted in a quartz tube (CVD reactor) at 800 C, while undiluted PTMG was fed into reactor at a rate of 1 ml/h for 2 h. After the experiment, the color of the AAO templates had changed to black, indicating the presence of deposits. Low magnification SEM shows that nanowires were deposited on the whole top surface of the AAO template (Figure 9a). HRSEM observations reveal that these nanowires have the same shape and length (10-20 µm) as those grown on flat quartz slides, but have much smaller, uniform outer diameters of less than 100 nm (Figure 9c). According to SEM, the AAO template surface is coated with an amorphous-like layer, on top of which Ge nanowires have been deposited. After intentionally removing this surface coating with a blade, the AAO internal surface can be observed and it is apparent that some of the pores have been filled with nanowires (with closed cap ends, as indicated by the arrows in Figure 9d) or nanotubes (with open tube cores, as indicated by the circles in Figure 9d).
From the cross-sectional view, it is clear that nanowires and nanotubes have grown within the AAO channels, although not along their whole length (Figure 10a and 10b). Energy dispersive spectra contain obvious Ge and C peaks (Figure 10c and 10d), consistent with the presence of MWCNT-encapsulated Ge nanowires. The Al and O peaks in the spectra derive from the AAO template, while Au derives from the SEM sample coating (applied to improve the image quality). These Ge@MWCNT nanowires present within the AAO channels have uniform outer diameter, close to the original AAO pore size of ~45nm.
Efforts to dissolve the AAO template using H3PO4 or KOH, as done previously for MWCNT/AAO arrays produced from the pyrolysis of xylene (Rajaputra et al., 2008), proved unsatisfactory. The amorphous-like coating covering the AAO surface after CVD may be responsible for slowing the acid dissolution process, which in turn suggests that reactions between the Ge clusters and Al(O) surface may have taken place during the CVD process. In this context it is pertinent to note that Al can catalyze Si nanowire growth via a vapor–solid–solid (VSS) rather than a VLS mechanism (Wang, et al., 2006). Hence, a similar process, involving a Ge-Al(O) phase, may be responsible for the growth of the amorphous-like coating. It is clear, however, that during the CVD process Ge clusters, formed from the PTMG, deposited on both the AAO top surface and the internal channels and catalyzed MWCNT nucleation and growth with incorporation of the Ge as nanowires.
5. Concluding remarks
CVD using a floating Ge catalyst represents a simple method for the preparation of carbon-encapsulated Ge nanowires. The process temperature and the partial pressure of carbon in the reactor are indicated as being critical factors for successful nanowire growth. By optimization of appropriate CVD parameters, such as the C:Ge ratio, reaction time and temperature, nanowires can be reproducibly synthesized with dimensions of 200-300 nm in diameter and 6-10 μm in length. Furthermore, by using thin AAO plates (i.e., 10-20 µm) as a template, the growth of MWCNT-encapsulated Ge nanowires with controllable diameter and orientation within AAO can be realized. Although there is a tendency for amorphous deposits to cover the AAO template, the coating can be mechanically removed by polishing to expose MWCNT-encapsulated Ge nanowire arrays which protrude out of the AAO matrix. Past work suggests that it should be possible to exploit these arrays to fabricate gas sensors and optoelectronic devices (Baughman et al., 2002, Agarwal & Lieber, 2006, Polyakov et al., 2006, Erts et al., 2006).
The authors would like to thank Drs. S. Rajaputra, R. Mangu and V.P. Singh for kindly supplying high quality AAO templates for this study. This work was supported in part by the Department of Science and Technology, Ministry of Science and Technology, Govt. of India, under young scientist programme award no. SR/BY/C-11/05. A.P. thanks the DST for the award of a BOYSCAST fellowship.