Facile Synthesis of Highly Aligned Multiwalled Carbon Nanotubes from Polymer Precursors
We report a facile one-step approach which involves no flammable gas, no catalyst, and no in situ polymerization for the preparation of well-aligned carbon nanotube array. A polymer precursor is placed on top of an anodized aluminum oxide (AAO) membrane containing regular nanopore arrays, and slow heating under Ar flow allows the molten polymer to wet the template through adhesive force. The polymer spread into the nanopores of the template to form polymer nanotubes. Upon carbonization the resulting multi-walled carbon nanotubes duplicate the nanopores morphology precisely. The process is demonstrated for 230, 50, and 20 nm pore membranes. The synthesized carbon nanotubes are characterized with scanning/transmission electron microscopies, Raman spectroscopy, and resistive measurements. Convenient functionalization of the nanotubes with this method is demonstrated through premixing CoPt nanoparticles in the polymer precursors.
The discovery of carbon nanotubes (CNTs) by Iijima in 1991 opened up a brand new era in materials science and nanotechnology . The intrinsic electronic properties of single-walled carbon nanotubes are such that they may be metallic or semiconductive depending on their diameter and the graphitic ring arrangement around the tube wall . Furthermore, CNTs show exceptionally good thermal and mechanical properties. It is expected that CNTs could solve the thermal dissipation problem of nanodevices due to their high thermal conductivity. CNTs can transport significant amount of electric current without doping problem encountered in Si-based FETs (field effect transistors) because of the graphitic nature, and the covalent bonds among carbon atoms are much stronger. CNTs are among the most promising materials anticipated to impact future nanotechnology due to their unique structural and electronic properties, which have generated great interest for application in a broad range of potential nanodevices. The unique properties of CNTs have led to the study of their use in areas as diverse as sensors , electrochemical actuators , nanoelectronics , field-emitting flat panel displays , battery , scanning probe microscopy tips [8–10], FETs [11, 12], gas storages , and so forth.
Extensive efforts have been made to control the growth and properties of CNT since their discovery in 1991 . Large quantities of carbon nanotubes can now be produced by arc discharge , laser ablation , chemical vapor deposition methods [16–20], or flame synthesis [21–24]. However, the applications of CNTs have been limited because of problems in catalyst residues, difficulty with the alignment, diameter uniformity of the nanotubes mixed metallic and semiconductive properties, and so forth . One of the most efficient approaches to the production of large areas of highly ordered, isolated long CNTs with monodispersed tube diameter and length is based on template-confined growth of CNTs. The diameter, length, and packing density of CNTs can be ideally controlled when the nanotube arrays are fabricated in porous anodic aluminum oxide (AAO) templates [16, 25–27]. Furthermore, porous AAO templates with well-controlled 3D channel structures such as dumbbell shaped , linearly joined [29, 30], Y-branched  as well as novel dendriform have been prepared and used to grow well-aligned arrays of CNTs through the chemical vapor deposition method . Pyrolysis of gaseous hydrocarbons such as , , and in templates can be achieved with or without catalyst, but both processes require specialized reaction chamber, various gas supply, careful control of gas flow, pyrolyzing temperature higher than , and costly safety equipments for highly flammable gases.
Graphitic nanotubes have also been synthesized by carbonization of the polyacrylonitrile  and poly(furfuryl alcohol) [34, 35] within the pores of AAO membranes at 600 and 900, respectively. The synthesis is achieved by carbonization of polymers through a three-step approach: (1) monomers and initiators are infiltrated into the pores of AAO template, (2) the polymers are produced inside the pores of AAO template through polymerization, and (3) The CNTs are produced through carbonization of the polymers prepared in step (2). The whole process requires carefully controlled polymerization initiation and it is tedious and time consuming. No detailed structural characterization was reported in the first case , and bamboo and bubble structure were obtained for the latter .
Herein we report a convenient one-step approach for the preparation of well aligned carbon nanotube array. Commercially available polymers are used for the study. No catalyst and no monomer initiator are required. Comparing to pyrolysis of highly combustible gases, this method is simple and avoids many safety concerns. In addition, the as-prepared aligned CNTs contain open pores that are ready for functionalization or filling with nanoparticles. Polymer nanotubes prepared with templates through melt-wetting in the 300 to 900 nm pore diameter region have been reported . Due to the high viscosity nature of the polymers in general, whether the melt-wetting method works for much smaller pores has not been addressed. In this work, we explore templates with pore diameters between 230 and 20 nm with melt-wetting, and through carbonization at a moderate temperature we report good quality multi-walled carbon nanotubes (MWNTs) formation. Aligned CNTs with both ends open or with one end open and one end closed are presented here.
All chemicals and polymers are reagent grade from Aldrich Chemicals except the five-minutes epoxy (Devcon Corp.). Three types of porous anodic aluminum oxide (AAO) membranes are used as templates in this work. One is a commercially available membrane with 60 μm thickness and 230 nm pore diameter (Whatman Ltd. , Anodisc 13 mm) . The other two are prepared by anodic oxidation of high purity aluminum plate (Alfa Aesar, 99.99%, 0.25 mm thick) through a two-step anodization process that has been reported in literature [38, 39]. The membranes are 60 μm thick, and the pore diameters are 50 and 20 nm, respectively. A typical procedure for polymer carbonization in AAO membrane is described here. Either solid or liquid polymers are placed on top of AAO templates (25–30 mg polymer per disk). The polymer over AAO template in an alumina boat is placed in a tube furnace (Lindberg). Ar is purged for 30 minutes. Then the temperature is slowly increased at a rate of about 2/min from ambient to the desired temperature (typically 600). The temperature is kept constant for 3 hours under Ar flow to fully carbonize the polymer. The polymer slowly melts and spreads into the nanopores of the AAO template to form polymer nanotubes. Starting at a very low temperature of 400, the polymers are carbonized, and graphitic nanotubes are generated. Thermal decomposition of small molecules and polymers is a complex reaction. We observe good Raman signals and the presence of MWNT with SEM from all blackened areas on AAO (vide infra). Therefore, we estimated the MWNT yield based on the starting reagent weight and the final weight gain on the AAO template. Typical yield is about 1% by weight.
The Raman measurements are carried out at room temperature with the use of a Raman microscope spectrometer (Renishaw, Ltd.) equipped with a HeNe laser (632.8 nm). A reflective geometry with the analyzer polarization parallel to the incident laser beam polarization is adopted. The spectrum is calibrated against a Si wafer standard (520 ). The spectrum analysis is done with the use of Origin software. The UV-Raman measurement is carried out with the use of a frequency-doubled argon ion laser with excitation at 244 nm. Typical spectrum is averaged over 10 scans. Field-emission scanning electron microscopy (FESEM) images are obtained on Hitachi S-4700-II field emission SEM operating with an accelerating voltage of 10 kV. Transmission electron micrographs (TEM) and electron diffraction patterns are obtained on a Philips CM30T at 200 kV.
3. Results and Discussion
A range of polymers from very low molecular weight of a few hundred to medium size ones of ~450 k (g/mol) has been applied in this study (Table 1). Regardless whether the polymer is solid or viscous liquid, upon heating all polymers melt at higher temperatures and the wetting phenomena between the polymers and AAO templates occur. The melts wet the membranes very well, and this is likely due to the fact that the cohesive force for complete filling of the nanopores is not as strong as the adhesive force for wetting the walls of the nanopores . This wetting process leads to AAO membranes that are completely covered with polymers, and upon carbonization at temperature beyond 400, the entire membrane is blackened. However, the faster rate of adhesive force must be properly balanced with a slower sample heating rate in order to allow sufficient flow and maximize the carbon nanotube formation. Typical sample heating rate in this study is 2/min. When higher heating rate such as 5/min is used, the AAO membrane shows inhomogeneously darkened areas due to fast thermal decomposition of the melts. The blackened AAO membranes are subject to Raman, SEM, TEM, and conductivity measurements. Control experiment with use of polymers on flat substrate (nonporous alumina) upon carbonization fails to yield any CNTs. Sample characterization, the effects of different starting polymers, and preliminary results on incorporation of nanoparticles are presented below.
3.1. Raman Characterization
Raman spectroscopy has been used extensively for the characterization of multi-walled (MWNTs) and single-walled carbon nanotubes (SWNTs). The polymer/AAO membrane (230 nm) after carbonization at 600 has been subjected to Raman studies (typical polymer, e.g., is bisphenol A ethoxylate dimethacrylate with Mn ~1700). After carbonization at 600 under Ar over three hours, the AAO membrane is completely black with slight shiny luster. The Raman spectrum is shown in Figure 1. The first-order (below 2000 ) and second-order (2000–4000 ) Raman scattering peaks are clearly visible with the third-order peak (above 4000 ) noticeable. The very broad background over the entire measurement range is due to luminescence from the AAO membrane as indicated in the AAO Raman spectrum in Figure 1. Upon background subtraction, the analyzed Raman spectrum is shown in Figure 2. The black dots are the experimental Raman data, and the red trace is the overall fitting with 7 Lorentzian peaks as indicated individually in blue traces. The strongest peaks are D- and G-lines at 1341 and 1593 , respectively. The D-line is due to the disordered hybridized carbon, and the G-line is associated with the tangential stretching mode () of highly ordered pyrolytic graphite (HOPG) and indicates the presence of crystalline graphitic carbon in the MWNTs [40, 41]. The second-order Raman peaks corresponded to (overtone), and D + G (combination) have also been observed. The complete observed Raman peaks and their assignments compared to literature values are listed in Table 2. It is worth noting that a diameter-independent nanotube mode at 430 is also consistently observed in our samples . All observed Raman modes are in reasonably good agreement with literature values for MWNTs. The D-line and associated higher-order modes are lower than reported values in literature measured with different laser excitation (Table 2). This is likely due to the fact that the D-line is dispersive and its frequency is linearly laser excitation energy dependent. We have also carried out UV-Raman measurements (244 nm laser excitation) on these samples, and the results are shown in Figure 3. With UV excitation, the D-line is very broad and shifts to higher frequency (>1400 ). Based on the large D/G ratio observed with the visible laser excitation, the template confined carbonization of polymers also produces significant amount of disorder in the MWNTs as compared to those from the CVD method. Another observation worth noting is that when the MWNTs/AAO sample is cut, Raman measurements are carried out on the cross-section and the laser polarization is applied parallel and perpendicular to the expected MWNT axis direction, the perpendicular direction consistently gives ~10% higher Raman peak intensity. This anisotropy strongly suggests the presence of aligned MWNTs and not disordered graphite.
3.2. SEM Characterization
The formation of polymer nanotubes and carbon nanotubes upon carbonization is directly studied with the use of field emission scanning electron microscopy. A five-minute epoxy polymer is used for the initial study. There are two components, the epoxy and curing agent, after the two components are mixed a drop of polymer is placed on a 230 nm AAO disk that is glued onto a Cu plate. The sample is heated at 140 for 1 hour. After the polymer is fully cured, the template is removed by soaking and washing with NaOH solution, and the SEM image of the remaining polymer is shown in Figure 4(a). As revealed in the image, the epoxy polymer flows into the 230 nm pores very well. From this study also consistent with that reported in , majority of the observed nanoscale objects are polymer nanotubes. This is likely due to the stronger adhesive force than the cohesive force. Since the major component of the five-minute epoxy is bisphenol A, a few well-defined small molecular weight bisphenol A related polymers are used for the polymer nanotube carbonization study (Table 1). The epoxy coated AAO disk is heat treated at 2/min to 500, after template removal, the CNT bundle is shown in Figure 4(b). The top view and the close-in side view of these CNTs are shown in Figures 4(c) and 4(d), respectively. To explore whether the molten wetting procedure works for much smaller nanopores, we apply the same epoxy to home-made AAO membranes with 50 and 20 nm pore diameters. With the same heating rate at 2/min, the samples are heated to 600 and hold for 3 hours. The results as shown in Figures 4(e) and 4(f) indicate that the method indeed works well for small nanopores.
For the commercial 230 nm pore diameter AAO disk, both ends of the nanopores are open. For the home-made AAO membranes, before the barrier layer is removed, one end is open and the other end is closed for all the nanopores . Since open or closed ends play a crucial role for additional nanotube functionalization and/or tube filling, we look into the nature of the MWNTs prepared with our home-made AAO membranes in more details. The side view SEM images in Figures 4(e) and 4(f) of the MWNTs released from the templates do not provide conclusive answer. Therefore we remove the barrier layer by slow etching and image the back side directly. We use one piece of the MWNTs/AAO sample and glue the polymer filling side (open-end side) to a Cu foil. The sample is soaked in a 1 M NaOH solution at room temperature, and the sample is studied with the use of SEM at a fixed time increment. After 10 minutes etching, the barrier layer starts to open. The SEM image (Figure 5(a)) shows a large area view of AAO barrier side with imbedded MWNTs. After 15 minutes etching, the alumina barrier layer is removed. However, the end of each MWNT is still capped (Figure 5(b)). This is indicative of the materials at the end of the MWNT being etched at a much slower rate compared to that of the alumina barrier layer. Additional etching beyond 20 minutes only widens the nanopores, and individual MWNTs are standing in each pore and leaning toward each other (Figures 5(c) and 5(d)). As shown in Figure 5(d) the end of each MWNT is darker in the middle and brighter around the edge and does not appear to be a solid rod. Our result supports that during the melt-wetting process, the melts driven by adhesive force reach the bottom of the nanopores and form a conformal layer that upon carbonization leads to MWNTs with one end closed.
3.3. TEM Characterization
Additional sample characterization is carried out using transmission electron microscopy. Figure 6(a) shows a TEM image of a 230 nm carbon nanotube bundle which resulted from completely dissolving the AAO template. Electron diffraction patterns of all nanotubes were not of high quality. Many amorphous domains are observed but occasionally some graphitic characteristics are revealed in some diffraction patterns: the brightest ring corresponds to the 002 reflection of hexagonal graphite and the next continuous ring seen in the diffraction pattern corresponds to the 110 reflection of hexagonal graphite. There is no difference in the intensity in this particular diffracted ring, which suggests that there is no preferred orientation along the - or -axes . A high-magnification TEM image of a 20 nm CNT prepared from AAO template with slow heating to 600 is shown in Figure 6(b). The tube wall thickness between 4 and 5 nm is visible from the image. Based on the interplanar separation in graphite ( = 3.35 Å), such tube wall thicknesses could accommodate approximately 12–15 graphitic shells .
Another advantage of the current process is that it can be easily extended to prepare functionalized nanotubes by premixing any type of nanospecies such as nanoparticles or nanofibers with the polymer precursor, and then let the wetting process bring these nanospecies into the template channel to form various functional nanotubes. For example, CoPt nanoparticles with 6 nm diameter  are successfully incorporated into carbon nanotubes with diameters at 230 and 50 nm by this method (Figures 7(a) and 7(b)). Some aggregation is noticed as the incorporated nanoparticles appear to be slightly larger than 6 nm; however, we demonstrate that this procedure brings nanoparticles into nanopores successfully without major aggregation of the nanoparticles upon heating, and this is a simple one-step method for such a complicated nanostructure. Apparently, the polymer matrix, viscosity, and low loading all help to avoid nanoparticle aggregation. Previously nanoparticles may have been loaded by multistep impregnation followed with reduction to prepare such functionalized nanostructure .
3.4. Nature and Effect of Polymer Precursors
When a polymer melt or solution is placed on a substrate with high surface energy, it will spread to form a thin film. Similar wetting phenomena occur if porous templates are brought into contact with polymer melts or solutions. A nanotube structure can be preserved if the wetting process is quenched at the initial stage since the wall wetting and complete filling of the pores take place at different time scales [36, 44]. In our experiments, wetting of template wall happens on a time-scale of a few minutes when any liquid-form epoxy (e.g., a 5-minute epoxy) is used as starting materials. The fully crosslinked epoxy nanotubes are released from the AAO template by dissolving the alumina (Figure 4(a)). The epoxy tubes are of uniform diameter and length, with wall thickness of several tens of nanometers. It is found that the topography of the epoxy tubes matches the shape of their hosting pore channels so well that they can be used to duplicate the internal pore structure faithfully. Further carbonization process does not change the morphology of the epoxy nanotubes and their examination by electron microscopy technique can thus give a more reliable approach to study the pore structure since the carbonized nanotubes become conducting enough so that no additional carbon or metal coating is needed for imaging (Figure 8(a)). Since AAO membrane has recently attracted much attention for its application in nanotechnology, it is important to know the actual internal pore structure. AAO templates with pore diameter as small as 20 nm are also used for CNTs growth successfully (Figure 4(f)). The pore diameters can be increased or reduced by wet chemical etching  and atomic layer deposition method [45–48], respectively. The CNTs grown in the AAO template are very flexible and they can be bent at large angle () without being broken. The CNTs are of uniform length and the open-ended structure will facilitate their use in sensing applications as well as tube filling (Figure 8(b)) [3, 49–52].
All CNTs are of equal height and there is no overgrown problem normally happening in CVD growth. The nanotubes are parallel to each other, perpendicular to the template, and well-ordered to form a periodic triangular close-packed array without extra processing steps. The tube density, estimated from the pore density, can be as high as pores/. The tube diameter distribution throughout the array is narrow, typically 10% of the main diameter—much narrower than heretofore reported using other methods of nanotube array synthesis. This CNT preparation process works for a large number of polymers we have tried (Table 1), except for polystyrene and polybisphenol A carbonate that decompose into styrene and bisphenol A, respectively [53, 54]. These small molecules evaporate completely and nothing is left after the carbonization process. It is found that carbon nanospecies with different morphology and/or structure can be produced when different polymer precursors are carbonized under the same reaction condition. For example, polystyrene-co-polymethyl mathacrylate resulted in carbon nanotubes with many bubbles and sponge-like features (Figure 8(c)) and polystyrene-block-polybutadiene generated CNTs with very thin walls, so that they appear collapsed (Figure 8(d)). Fully collapsed carbon nanotubes have been reported in literature. For certain range of tube parameters, a completely collapsed nanotube is energetically more favorable . A more recent article reported collapsed nanotubes due to poisoned metal catalyst that led to uneven carbon concentration and precipitation . Since no catalyst is used in our study, the collapsed nanotubes may be related to the loss of styrene, a decomposed product from the block copolymers used that also leads to uneven carbon generation during carbonization. While there are remaining questions regarding the collapsed nanotubes formation from other polymers such as poly(acrylic acid), all observations of MWNTs and other morphology formation from various polymer precursors are summarized in Table 1.
The transport measurements made on a 50 nm CNT array imbedded in AAO template by a two probe method show the characteristic of a semiconductor (Figure 9). Even though CNTs can be made at temperatures as low as 400, semiconductive behavior is observed only in samples made at temperatures above 600. The resistance of MWNTs imbedded in 230 nm AAO membranes prepared at 600 from different polymer precursors is measured with a two-probe method across the membranes and ranges between 6 and 40 KΩ. Not well formed and collapsed carbon tubes give much higher resistance values between 300 KΩ and 7 MΩ. The results are also listed in Table 1.
We report a simple, fast, one-step approach for the preparation of well aligned carbon nanotube array. Starting at very low temperature, ~400, the polymers are carbonized and graphitic nanotubes are generated. There is no flammable gas and catalyst involved, no monomer or polymer initiator is needed. The MWNTs duplicate the membrane nanopores precisely. For membranes with open ends on both sides, the resulting MWNTs contain the same open ends. For AAO membrane with closed barrier at one side, the resulting MWNTs contain one closed end. The open or closed ends of the MWNTs have strong implication for additional nanotube functionalization and/or filling. The template imbedded MWNTs of the same height are also ideal for nanoparticles filling. We demonstrated that CoPt nanoparticles can be filled along with the polymer nanotube precursor that can not be done with the CVD process. This method also allows post-synthesis nanoparticle filling. The MWNT and functionalized MWNT imbedded AAO membranes may find applications in catalysis reactions or catalyst support. The released MWNTs with combined semiconductive property and mechanical strength may be useful toward sensors and actuators. Finally, this method of MWNT array synthesis is not inherently area limited and can be scaled up with proper templates.
The work at Argonne National Laboratory and the electron microscopy accomplished at the Electron Microscopy Center for Materials Research are supported by UChicago Argonne, LLC, Operator of Argonne National Laboratory (“Argonne”). Argonne, a U.S. Department of Energy Office of Science laboratory, is operated under Contract no. DE-AC02-06CH11357.
M. S. Dresselhaus, G. Dresselhaus, and P. C. Eklund, Science of Fullerenes and Carbon Nanotubes, Academic Press, San Diego, Calif, USA, 1996.
W. B. Choi, W. Park, E. J. Bae et al., “Aligned carbon nanotubes for Nanoelectronics,” Nanotechnology, vol. 15, pp. 512–516, 2004.View at: Google Scholar
K. Saito, F. A. Williams, and A. S. Gordon, “Structure of laminar coflow methane-air diffusion flames,” Journal of Heat Transfer, vol. 108, no. 3, pp. 640–648, 1986.View at: Google Scholar
J. Li, C. Papadopoulos, and J. Xu, “Growing Y-junction carbon nanotubes,” Nature, vol. 402, no. 6759, pp. 253–254, 1999.View at: Google Scholar
P. G. Collins, K. Bradley, M. Ishigami, and A. Zettl, “Extreme oxygen sensitivity of electronic properties of carbon nanotubes,” Science, vol. 287, no. 5459, pp. 1801–1804, 2000.View at: Google Scholar
A. V. Bazilevsky, K. Sun, A. L. Yarin, and C. M. Megaridis, “Room-temperature, open-air, wet intercalation of liquids, surfactants, polymers and nanoparticles within nanotubes and microchannels,” Journal of Materials Chemistry, vol. 18, no. 6, pp. 696–702, 2008.View at: Publisher Site | Google Scholar