Journal of Nanomaterials

Journal of Nanomaterials / 2010 / Article

Research Article | Open Access

Volume 2010 |Article ID 189214 | https://doi.org/10.1155/2010/189214

Francisco Márquez, Vicente López, Carmen Morant, Rolando Roque-Malherbe, Concepción Domingo, Eduardo Elizalde, Félix Zamora, "Structure and Characterization of Vertically Aligned Single-Walled Carbon Nanotube Bundles", Journal of Nanomaterials, vol. 2010, Article ID 189214, 7 pages, 2010. https://doi.org/10.1155/2010/189214

Structure and Characterization of Vertically Aligned Single-Walled Carbon Nanotube Bundles

Academic Editor: Donglu Shi
Received09 Aug 2010
Accepted02 Sep 2010
Published22 Sep 2010

Abstract

Arrays of vertically aligned single-walled carbon nanotube bundles, SWCNTs, have been synthesized by simple alcohol catalytic chemical vapor deposition process, carried out at 800 . The formed SWCNTs are organized in small groups perpendicularly aligned and attached to the substrate. These small bundles show a constant diameter of ca. 30 nm and are formed by the adhesion of no more than twenty individual SWCNTs perfectly aligned along their length.

1. Introduction

Since the landmark paper on carbon nanotubes (CNTs) in 1991 by Iijima [1, 2], there have been relevant research efforts on this new material. This great interest has been due to their unique mechanical [3], electronic [4, 5], and chemical properties [6] and their potential applications as field emitters [79], development of new composites, and conductive coatings [10], in energy storage [11], thermal materials [12], catalyst supports [13], and many other applications in nanometer scale engineering. However, the growth of aligned CNTs is paramount, for many of these applications are fully exploited. That is the reason why during the last few years many research groups have been focused on the design of new methods for controlling the CNT morphology [1416]. In fact until a few years ago, alignment of single-walled carbon nanotubes (SWCNTs) was achieved by using strong electromagnetic fields [1719]. Hata et al. described the attractive synthesis of highly aligned SWCNTs of millimetric dimensions by chemical vapor deposition (CVD) in presence of water vapor [20]. At present, two different fabrication methods for obtaining vertically aligned CNTs are used: (i) the direct growth by thermal catalytic chemical vapor deposition (CCVD) [21] and (ii) the screen printing technology from a paste mixture of CNTs [22]. Nevertheless, these approaches have clear limitations, and, in the case of the screen-printing process, the use of organic additives is a serious problem for their application in opto-electronic technology.

One of the most promising alternative procedures for obtaining aligned SWCNTs is that reported by Maruyama et al. [2325], in which a mixture of and salts is used as catalyst precursor and the growth is achieved by CVD using alcohol as carbon source. In this case, even though the uniformity and homogeneity achieved by this procedure have been sufficiently proven, the vertical alignment of SWCNTs is partially obtained when CNTs are high enough.

In this paper we report a method for the synthesis of vertically aligned SWCNTs, with high linearity and high density, based on the CCVD on silicon and quartz surfaces. Surprisingly the obtained SWCNTs are grouped in small bundles of ca. 20 SWCNTs.

2. Experimental Section

2.1. Preparation of Supported Catalysts

The preparation procedure for supporting the catalyst precursor has been described elsewhere [25]. In this method Co-Mo acetate solutions are deposited on the substrates by dip coating following the next procedure: Co(CH3 COO) 2 4H2 O and diluted solutions in absolute ethanol was used as catalyst sources. Typically for preparing 100 mL of the corresponding acetate solution 0.02 g of the salt or of the salt were used. Both solutions were sonicated for 30 min and stirred for 2 h. Acetate solutions were kept in the dark to prevent photodecomposition. Silicon wafers (100) from El-CAT Inc. and fused quartz with both sides optically polished from SPI Supplies (quartz slide mm super smooth) were used as substrates. Substrates were cleaned with isopropyl alcohol and next dried in an oven at before use. The dip-coating was made in two steps in which the substrates are immersed into the acetate solutions and maintained there about 10 sec. In first step the substrates are immersed into the acetate solution and subsequently calcined in an oven in air at about 673 K for 20 min. After that the substrates are cooled to room temperature and the dip-coating process is repeated by using the acetate solution. Next, the substrates are calcined again in an oven at 673 K for 20 min. As a result, organics are removed from the surfaces and the metals are oxidized. In the case of Mo, this metal forms an oxide layer that is expected to prevent the aggregation of the metallic Co particles formed during the CVD treatment that are the responsible for the growth of SWCNTs.

2.2. CVD Growth of SWCNTs

We have used a home-made thermal CVD system, composed by a three-entry system (Figure 1). A cylindrical quartz reactor with an inner diameter of 25 mm and a length of 1 m was installed inside a tubular furnace. Substrates in a ceramic boat were introduced within the quartz reactor. Next, the system was closed and evacuated to Pa, by using a mechanical pump. After 15 min the mechanical pump was stopped and a mixture of 90%  and 10%  gas was incorporated into the reactor (flow rate of 300 sccm). Simultaneously, the reactor was heated up to 1073 K (10 K min ). Once reaching the synthesis temperature, the - flow was stopped and a mixture of 10%  and 90%  with ethanol (99.5%) vaporized into the nitrogen stream was introduced into the chamber at a flow rate of 200 sccm. The growth time was typically 5 min and apparently no changes were observed for longer times. The growth was typically terminated by switching the gas to (300 sccm) and cooling down the furnace.

2.3. Characterization Methods

Field emission scanning electron microscopy (FESEM, JEOL JM6400) and high-resolution transmission electron microscopy (HRTEM, JEOL JEM-3000F) were used to study the morphology, alignment, and main characteristics of the as-synthesized and purified CNTs. Raman spectra were also recorded using a Confocal Raman Microscope (Renishaw RM2000) equipped with laser sources at 514 nm, 633 nm, and 785 nm, a Leica microscope, and an electrically refrigerated CCD camera. The spectral resolution was set at 4  , laser power employed was less than 10 mW, and acquisition time of each spectrum was around 50 sec.

HRTEM samples were prepared by dispersing the synthesized SWCNTs in ethanol followed by homogenization and then placing 5  L of this solution onto a copper grid coated with a lacy carbon film.

The synthesized SWCNTs were studied with the help of a TQ500 Thermogravimetric Analyzer (TGA). The sample was thermostatized at C, in a flow of nitrogen ( ), and after that the temperature was linearly scanned, at a heating rate of /min, up to . The data collection, the temperature control, the programmed heating rate, and the gas switching were electronically controlled by the instrument. The TGA data were collected as (wt.%) versus ( ) profile, where is the loss of mass. The gas used in the TGA characterization was pure (99.9999% purity).

The specific surface area of the as-synthesized SWCNTs was determined by using the BET method [2629]. The determination of the micropore volume was carried out with the Dubinin plot method [30] and the Langmuir- type isotherm equation for micropore volume filling plot methodology [29, 31]. The Saito-Foley Method was used for determining the micropore size distribution [3234], and the Non local Density-Functional Method for determining the whole pore size distribution [29, 35]. These methodologies were applied to experimental nitrogen adsorption isotherms at 77 K, obtained for the SWCNTs using an Accelerated Surface Area and Porosimetry System, Autosorb-1, provided by Quantachrome Instruments. The equipment was previously calibrated with a zeolite A provided by Quantachrome Instruments as a standard.

3. Results and Discussion

The method used to produce the CNTs is based on that previously published by Murakami et al. [25] however, our approach simplifies the synthetic conditions previously required since in the procedure vacuum the quartz tube reactor was not used and the control of the gas mixture pressure during the process was unnecessary (Figure 1).

Figure 2 shows the field emission scanning electron microscopy (FESEM) image of the “as grown” SWCNTs from ethanol as carbon source at 1073 K on quartz substrates. As can be seen there, CNTs are vertically aligned on the substrate surfaces. The CNTs show a very high density and an averaged diameter of ca. 30 nm. The length of the nanotubes is of ca. 5  m for 5 min of growth even though previous results confirm that it depends on the synthesis procedure (flow of -ethanol, temperature, and catalyst). High-resolution transmission electron microscopy, HRTEM, revealed exclusively the presence of small packets of SWCNTs without any double-walled or multiwalled carbon nanotubes. These SWCNTs were grown longitudinally aligned, showing a homogeneous diameter of ca. 1.2 nm (see the magnification of Figure 3(a)). These bundles of SWCNT are formed by association of a constant number of them (ca. 20). Similar results were observed by E. Einarsson et al. [36] during the synthesis of carbon nanotubes on quartz substrates under vacuum conditions. In that study, bundles were formed by no more than 10 SWCNTs adhered along the whole length of the nanotube. This association is expected to be due to the presence of a carbon coating, as confirmed by the HRTEM micrographs shown in Figure 3(a). This amorphous carbon can be easily removed by a mild sonication treatment in a mixture of ethanol-isopropyl alcohol (4 : 1). Figure 3(b) shows the SWCNTs released from the former bundles after sonication.

The presence of impurities in the as-synthesized materials (i.e., amorphous carbon) was also studied by thermogravimetry, TGA. Figure 4 shows the thermogravimetric profile of the as-synthesized SWCNTs. The weight loss is very low in a wide range of temperatures (373 to 1023 K) indicating that a very low amount of amorphous carbon is present, as observed by HRTEM.

Dimensions of the as-synthesized SWCNTs were also evaluated from the nitrogen adsorption isotherms BET at 77 K. The representative adsorption isotherm, which is the average of two experimental isotherms, is shown in Figure 5. In order to apply to real adsorption data the BET isotherm equation, it is habitual to use the BET equation in linear form in the region of the isotherm, where is the relation between the adsorption equilibrium pressure,  , and the adsorbate vapor pressure, [29]. The specific surface area was calculated by means of the linear BET plot, which made possible the computation of the BET surface area, that is, (see Table 1) [26, 27, 29].


Sample 𝑆 B E T [ m 2 / g ] 𝑊 D u b i n i n M P [ c m 3 / g ] 𝑊 L T M P [ c m 3 / g ] 𝐷 S F m o d e [ n m ] 𝐷 N L D F T m o d 𝑒 [ n m ]

SWCNTs (as-synthesized)5300.220.201.31.4

Adsorption in the micropores is the main method applied for the measurement of the microporous volume, by means of the Dubinin linear plot, the t-plot method [27, 29, 30] and, the linear plot of the Langmuir- type isotherm for volume filling [29, 31]. In the present case the Dubinin and Langmuir type linear plots to adsorption data taken from the isotherm in the range were applied. Thereafter, the Gurvich rule was applied for the calculation of the Dubinin micropore volume [29, 30] and the Langmuir- type equation micropore volume (see Table 1).

The Saito-Foley pore size distribution (SF-PSD) of the synthesized SWCNTs is shown in Figure 6. The mode of the SF-PSD distribution is reported in Table 1.

The pore size distribution of the synthesized SWCNTs, corresponding to the Non local Density Functional Theory, is shown in Figure 7. The mode of the DFT-PSD distribution is reported in Table 1.

The adsorption data displayed in Table 1 demonstrates that the analiyzed SWCNTs exhibit a relatively large specific surface area. In addition, the calculated micropore volume was . Besides, the calculated pore size distributions indicate that the synthesized SWCNTs have a slightly heterogeneous distribution of pores with a clear, and highly populated, maximum at ca. 1.35 nm. The above results unambiguously show the absence of mesoporosity in the sample.

Consequently, the adsorption data indicates that the adsorption of the obtained SWCNTs is completely restricted to the micropore region, exhibiting a relatively high micropore volume.

Raman measurements reported here were performed by using the 785 nm diode laser, as the corresponding spectra recorded with 633 and 514 nm showed very poor spectra in the Raman shift region below 300  where Radial Breathing Modes (RBMs) of SWCNTs appear. This indicates that the CNTs grown by the method here reported are resonantly excited by the 1.58 eV (785 nm) laser. Figure 8(a) shows the Raman spectrum from the “as-synthesized” SWCNTs grown on Si. Typical bands of Raman spectra of SWCNTs excited by the 1.58 eV (785 nm) laser (G-band at 1594  , D-band at 1296  , -band at 2580  , and RBM modes in the low Raman shift region) are marked. The high intensity ratio G/D unambiguously indicates the high purity of SWCNTs. The Raman shift of the different RBMs can be correlated with the diameter of the SWCNT, by using an empirical formula [37], , where “ ” is the corresponding wavenumber ( ) and “ is the diameter of the SWCNT (nm). The diameter determined by this approximation shows a narrow distribution ranging from 0.9 to 1.2 nm that agrees with the dimensions measured by HRTEM and nitrogen adsorption. On the other hand, the resonance observed in the RBM region can be correlated with the presence of small bundles formed by an apparently constant number of SWCNTs, as observed by HRTEM. In such a way, the contact among SWCNTs could be responsible for the attenuation of the Raman breathing modes and so for the resonance observed in the RBM region.

Figures 8(b) and 8(c) show the Raman spectra of SWCNTs grown on quartz and , respectively, but after a dispersion treatment and posterior deposition on Si (8(b)) and glass (Figure 8(c)) surfaces. The variations observed in the RBM region with respect to the “as-synthesized” can be attributed to the different degree of aggregation of the SWCNTs. In particular, it has been reported that the intensity of the band centered around 269  can be used to probe nanotube aggregation. The fact is that this characteristic band is almost absent for dispersed SWCNTs and increases, in relation to those appearing at lower frequency values, when the aggregation level increases [38]. In the inset of Figure 8 it is clearly shown how the intensity of such a band decreases drastically in the case of dispersed nanotubes. The profile of the RBM region is similar in (b) and (c), indicating similar population distribution of diameters in the dispersed CNTs. Nevertheless, the whole RBM region in the case of CNTs deposited on glass is more intense than when deposited on Si, for an equal G-band intensity of both spectra. Due to the singular “resonant” origin of the RBM modes (optical transitions of the SWCNTs with the energy of the excitation laser), the large global intensity of the RBM region in the (c) case could be attributed either to better “resonance” conditions in this last case or to a larger amount of CNTs present in the laser spot.

4. Conclusions

Vertically aligned single-wall carbon nanotubes have been obtained by using alcohol chemical vapor deposition process. Simplification of ACCVD setup experimental conditions is of interest toward a low-cost, up-scalable synthesis of high-quality SWCNTs. Surprisingly these nanotubes are organized in narrow and homogeneous bundles of ca. 30 nm diameter that are formed by association of no more than 20 SWCNTs. This association of nanotubes has been evidenced by HRTEM and Raman spectroscopy and represents a new CNT material opening up new perspectives in the field of nanoelectronics and optics.

Acknowledgments

The authors gratefully recognize the financial support provided by MEC through Grants MAT2006-08158, MAT2007-66476-C02-02, and European Community FP6-029192. Financial support from US Department of Energy through the Massey Chair Project at University of Turabo is also acknowledged. The “Servicio Interdepartamental de Investigación (SIdI)” from Universidad Autónoma de Madrid and “Centro de Microscopia Luis Bru” from Universidad Complutense de Madrid are acknowledged for the use of the HRTEM and FESEM facilities.

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Copyright © 2010 Francisco Márquez et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


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