Journal of Nanomaterials

Volume 2014 (2014), Article ID 327398, 5 pages

http://dx.doi.org/10.1155/2014/327398

Research Article

Synthesis of Vertically Aligned Carbon Nanotubes on Silicalite-1 Monolayer-Supported Substrate

Wei Zhao,¹ Bijay Basnet,² Sukyoung Kim,¹ and Ik Jin Kim²

¹School of Materials Science & Engineering, Yeungnam University, Gyeongsan City, Gyeongbuk 712-749, Republic of Korea

²Department of Materials Science and Engineering, Institute of Processing and Application of Inorganic Materials, Hanseo University, Seosan City, Chungnam 356-706, Republic of Korea

Received 19 October 2013; Accepted 23 December 2013; Published 10 February 2014

Academic Editor: Alireza Talebitaher

Copyright © 2014 Wei Zhao 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.

Abstract.

Monodisperse magnetic nanoparticles (NPs) with the size of ca. 3.5 nm were prepared and used as the catalysts for the synthesis of vertically aligned carbon nanotube (VACNT) arrays. A silicalite-1 microcrystal monolayer was used as the support layer between catalyst NPs and the silicon substrate. Compared to our previous report which used radio-frequency- (rf-) sputtered film as the catalyst, NPs that were synthesized by wet chemical method showed an improved catalytic ability with less agglomeration. The silicalite-1 crystal monolayer acted as an effective “buffer” layer to prevent the catalyst NPs from agglomerating during the reaction process. It is believed that this is the first report that realizes the vertical alignment of CNTs over the zeolite monolayer, namely, silicalite-1 microcrystal monolayer, instead of using the intermediate anodic aluminum oxide (AAO) scaffold to regulate the growth direction of CNT products.

1. Introduction

Carbon nanotubes (CNTs) have become the target of intense study owing to their unique nanostructure-dependent physical and chemical properties [1]. These distinctive characteristics arise from their different atomic structures and sizes. For example, CNTs can be either metallic or semiconducting according to their helicity and diameter [2]. The latter can also influence their mechanical properties, which can have a significant impact on their promising applications in many potential fields, such as nanoelectronic devices [3], composite materials [4], hydrogen storage media [5], and field emission devices [6].

Although not all the reported applications will require large scale CNT use, there are still some where the mass production of CNTs is strongly in demand. As a result, there is a need for facile and inexpensive approaches for the large scale production of CNTs. For some applications, such as scanning probes [7] and sensors [8] and field emitters in nanoelectronics [9], vertically aligned CNT (VACNT) arrays are particularly required through control and optimization of the diameter, wall structure, and areal density of CNTs.

A range of techniques have been developed for VACNT synthesis, such as HiPco [10], fluidized bed [11], and chemical vapor deposition (CVD) [12], and CVD has proven to be the most effective one. Although the growth of VACNT reduces or eliminates the necessity of postprocessing the as-produced CNTs, it is still dependent on the use of expensive substrate materials and deposition equipment, such as electron beam evaporation, which reduces the potential for scaling-up CNT production.

An important issue impeding such growth is the limited thermal stability of nanoparticles (NPs), because they tend to agglomerate into larger ones at elevated temperatures through atomic interdiffusion, also known as “Ostwald ripening” [13]. This will result in catalyst clusters without monodisperse diameters and quantifiable areal densities so that it is hardly to achieve self-oriented CNTs perpendicular to the substrate. Therefore, an efficient substrate that can stabilize catalyst NPs at high temperatures is necessary. Many templates, such as porous anodic aluminum oxide (AAO) [14] and block copolymer micelles [15], have been used.

In this study, we reported a simple approach that used premade monodisperse Fe₃O₄ nanoparticles (NPs), ~3.5 nm in size, as the catalysts and self-assembled silicalite-1 monolayer as the support layer to synthesize VACNT arrays by catalytic CVD (CCVD). The difference of this study from others is that the silicalite-1 microcrystals were self-assembled on the silicon (Si) wafers in the form of a monolayer to be used as a “buffer” layer, instead of AAO scaffold [16] or Al₂O₃ layer [17], to support Fe₃O₄ catalyst NPs. As far as we know, this is the first report on the synthesis of VACNTs using well-oriented zeolite monolayer to replace other commonly-used templates mentioned above as the support layer.

2. Experimental

2.1. Preparation of Fe₃O₄ NPs

Monodisperse Fe₃O₄ NPs were prepared using the method reported elsewhere [18]. Briefly, 1 mmol Fe(acac)₃, 5 mmol 1,2-hexadecanediol (HDD), 4.5 mmol oleic acid (OA), 3 mmol oleylamine (OAm), and 10 mL phenyl ether (PE) were mixed and heated under reflux for 30 min with vigorous stirring under a mild nitrogen (N₂) flow. Subsequently, the black mixture was cooled to room temperature by removing the heat source. The product was then precipitated with ethanol, centrifuged, and redispersed several times in hexane, resulting in a fine hexane dispersion of Fe₃O₄ NPs.

2.2. Self-Assembly of Silicalite-1 Monolayer onto the Si Wafer

A silicalite-1 microcrystal monolayer was simply assembled using a previously reported procedure [19]. Briefly, Si wafers (1 cm × 1 cm) were cleaned thoroughly, and immersed in a diluted hydrofluoric acid solution to eliminate the oxidized surface. They were then rinsed with distilled (DI) water and dried in a high-purity N₂ steam. To self-assemble the silicalite-1 microcrystals on the Si wafer, an ethanol solution of poly(ethylenimine) (PEI) was first spin-coated on the substrate. Approximately 5 mg of silicalite-1 microcrystals was gently rubbed on the wafer by a finger for 30 s to form a monolayer. Mild sonication of the coated wafer for several seconds in DI water is essential for removing the crystals physically-adsorbed on the monolayer. Subsequently, the silicalite-1-assembled Si wafers were dried by N₂, and they are signified as Z/Si.

2.3. Synthesis of VACNT Arrays by CCVD

To prepare the catalyst-supported substrate, one drop of a hexane dispersion of Fe₃O₄ NPs was dropped onto Z/Si. The substrate is designated Fe₃O₄/Z/Si. After being dried in air for a short time, the substrate was inserted into a horizontal electric tubular furnace. Under an Ar/H₂ atmosphere, the substrates were heated from room temperature to 973 K. After pretreatment for 10 min, C₂H₂ (10 sccm) was fed into the furnace with an Ar/H₂ (200 sccm) flow at this temperature for CNT synthesis and growth. C₂H₂ was then cut off and the reactor was cooled to room temperature under an Ar/H₂ flow. Figure 1 shows the process for synthesizing the VACNT arrays.

Figure 1: Synthesis of VACNT arrays on a silicalite-1 monolayer-assembled Si wafer using the synthesized Fe₃O₄ NPs as the catalysts.

3. Characterization

Powder X-ray diffraction (XRD, Rigaku D/max 2500 VL/PC) was performed using a Cu Kα radiation (40 kV, 40 mA,  Å). The patterns were recorded from 10 to 80° 2θ in 0.04° steps with a counting time of 2 s per step. Field emission scanning electron microscopy (FESEM) images were collected on a SEM LEO 1530 VP microscope. High resolution transmission electron microscopy (HRTEM, JEOL JEM-3011) was carried out at an accelerating voltage of 200 kV. The samples were prepared by evaporating drops of a sonicated ethanol suspension onto a carbon-coated lacy film supported on a 3 mm diameter, 300-mesh copper grid.

4. Results and Discussion

The synthesized Fe₃O₄ NPs were characterized by TEM, as shown in Figure 2. Figures 2(a) and 2(c) showed low and high magnification HRTEM images of the as-produced Fe₃O₄ NPs without further size-sorting, respectively. Clear lattice fringes were observed (Figure 2(c)), indicating a single crystalline structure [20]. The distance between the two adjacent planes was ~2.52 Å, which corresponds to the (311) plane of the FCC structured Fe₃O₄.

(a)

(b)

(c)

Figure 2: (a) Low magnification TEM image, (b) selected area electron diffraction pattern, and (c) high magnification TEM image of synthesized Fe₃O₄ NPs (inset: a single Fe₃O₄ NP).

The selected area electron diffraction (SAED) patterns revealed six distinct rings, and the calculated d-spacings matched well with the interplanar distances of face-centered cubic (FCC) Fe₃O₄, as shown in Figure 2(b).

More than 100 NPs were measured to obtain the size distribution, which is shown in Figure 3. The particles were monodisperse with a size of approximately 3.5 nm, which is also in accordance with the TEM results shown above.

Figure 3: Size distribution of the synthesized Fe₃O₄ NPs.

According to a previous report [19], the silicalite-1 crystals with a mean size of 1.5 × 1.1 × 0.6 μm³ were assembled onto a Si wafer in the form of a monolayer by finger rubbing, as shown in Figures 4(a) and 4(b). Compared to the random orientation of pristine silicalite-1 crystals shown in the inset of Figure 4(a), Figures 4(a) and 4(b) show crystals all with b-axes perpendicular to the Si wafer surface, which was confirmed by the cross-sectional view, as shown in Figure 4(c). In addition, almost the entire Si surface was covered with the crystals. The same results were verified by XRD patterns of monolayer-assembled and pristine silicalite-1 crystals, as shown in Figure 4(d) and its inset, respectively. A comparison between the two patterns revealed that only five (0 k 0) reflection planes (k = 2, 4, 6, 8, and 10) at 8.9, 17.8, 26.8, 36.0, and 45.5° 2θ were shown after the assembling of the silicalite-1 crystal monolayer, as shown in Figure 4(d), indicating the uniform orientation of the microcrystals on the Si wafer. This is obviously different from that of the pristine random crystals, shown by the XRD pattern in the inset of Figure 4(d).

(a)

(b)

(c)

(d)

Figure 4: (a) Low magnification SEM image of the Z/Si substrate (vertical view) and as-synthesized silicalite-1 crystals (inset), (b) high magnification SEM image of uniformly oriented Z/Si substrate (vertical view) and the pore structure on the (100) sheet (inset), (c) SEM image of uniformly-oriented Z/Si substrate (sectional view), and (d) XRD pattern of uniformly-oriented silicalite-1 monolayer-assembled Si wafer and as-synthesized silicalite-1 crystals (inset).

VACNT arrays on the Z/Si were synthesized according to the experimental procedures described above. Figure 5 shows representative FESEM images of the samples. As shown in Figure 5(a), a CNT “carpet” formed on top of the Z/Si. From the view of the locally enlarged area, as presented in Figure 5(b), the CNTs exhibited a vertical orientation to a large extent. In addition, the CNTs synthesized were typically multiwalled CNTs, and their mean inner and outer diameters were estimated to be 7.5 and 17.5 nm, respectively, as shown in the inset of Figure 5(b). Compared with our previous study [19] that used radio-frequency- (rf-) sputtered Fe₂O₃ film as the catalysts, the CNTs synthesized in this study showed a great improvement. As shown in Figure S1(a) in the Supplementary Material available online at http://dx.doi.org/10.1155/2014/327398, CNTs synthesized from rf-sputtered Fe₂O₃ film showed random growth directions and distinct diameter distribution. Quite a number of CNTs grew directly on the Si wafer surface between silicalite-1 crystals, and even those grown on the silicalite-1 crystals could hardly keep vertical-alignment tendency, as shown in Figure S1(b). Moreover, some fiber-like thick products were observed, as shown in Figure S1(a), indicating the formation of more defects and broad diameter distribution. One explanation for this phenomenon is the serious agglomeration of catalyst NPs [19], which could be observed from Figure S2. In Figure S2(a), the continuous Fe₂O₃ film showed domains of Fe₂O₃, with the size being approximately 15~18 nm, which seemed enough for CNT synthesis. However, in Figure S2(b), the Fe₂O₃ particles showed a strong agglomeration, leading to even large clusters. As a result, it not only led to a lower catalytic ability for CNT formation but also shrank areal density of catalyst NPs, which could compromise their initial crowding and continuous growing upward [21]. In addition, when the catalyst clusters were too large, the role of silicalite-1crystal layer became insignificant because the pore size of the silicalite-1 crystals is just a few Angstroms. In contrast, in this study, monodisperse Fe₃O₄ NPs with the 3.5 nm size were used, aiming at increasing the areal density [22] of the catalyst NPs on the substrate. Moreover, H₂ used in this study reduced Fe₃O₄ NPs to discrete Fe NPs, preventing them from agglomeration [23] and also reduced the rate of carbon production by dehydrogenation [24] so that the more ordered and thermodynamically stable CNTs can be produced rather than the less ordered and unstable soot and carbon fibers obtained in our previous study. As shown in Figure 5, it is confirmed that main products were MWCNTs without thicker carbon fibers, and synthesized CNTs showed a uniform vertical-alignment tendency, indicating the advantage of using smaller monodisperse catalyst NPs over rf-sputtered ones and that of adding H₂.

(a)

(b)

Figure 5: Cross-sectional SEM images of vertically aligned carbon nanotube arrays synthesized from Fe₃O₄/Z/Si. (a) Macroscale view and (b) enlarged view of the selected area (inset: synthesized MWCNT along with the mean diameter).

The mean diameter of the synthesized CNTs was several times larger than the original NP size, which can be explained by unavoidable coalescence during the heat-treatment. Despite this, the relatively thinner diameters compared to the previous results suggest that silicalite-1 crystals played a significant role in stabilizing and isolating the catalyst NPs to prevent them from coalescing under elevated temperatures. Therefore, the high density of NPs on the substrate could be retained to guarantee the synthesis of VACNT arrays with thinner diameters.

5. Conclusions

In this study, we reported the synthesis of vertically-aligned carbon nanotube (VACNT) arrays by using monodisperse magnetic Fe₃O₄ NPs with the size of ca. 3.5 nm as the catalysts and a silicalite-1 microcrystal monolayer as the “buffer” layer between catalyst NPs and the silicon substrate. As far as we know, this is the first report succeeding in VACNT synthesis using the assembled silicalite-1 monolayer as the support layer rather than intermediate AAO scaffold and others. Fe₃O₄ NPs of 3.5 nm size that were synthesized by wet chemical method showed an improved catalytic ability and provided a large catalyst surface density. And the silicalite-1 crystal monolayer acted as an effective “buffer” layer to stabilize the catalyst NPs from agglomerating during the reaction process. An ensemble of VACNT arrays was obtained despite some disturbance of a small number of random CNTs catalyzed from the NPs deposited directly on the Si wafer between the gaps of the silicalite-1 crystals.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

This study was supported by a grant from the 2012 Fundamental R&D Program of Hanseo University, Korea, and by the National Research Foundation of Korea (NRF) grant funded by the Korean government (MEST).

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