Catalytic iron nanoparticles generated by spark discharge were used to site-selectively grow carbon nanotubes (CNTs) and control their density. The generated aerosol nanoparticles were deposited on a cooled substrate by thermophoresis. The shadow mask on top of the cooled substrate enabled patterning of the catalytic nanoparticles and, thereby, patterning of CNTs synthesized by chemical vapor deposition. The density of CNTs could be controlled by varying the catalytic nanoparticle deposition time. It was also demonstrated that the density could be adjusted by changing the gap between the shadow mask and the substrate, taking advantage of the blurring effect of the deposited nanoparticles, for an identical deposition time. As all the processing steps for the patterned growth and density control of CNTs can be performed under dry conditions, we also demonstrated the integration of CNTs on fully processed, movable silicon microelectromechanical system (MEMS) structures.
Carbon nanotubes (CNTs) have attracted an enormous amount of attention from many researchers, who have found numerous device applications [1–3] taking advantage of their unique properties. Integrating CNTs into devices inevitably requires control of their location and/or density [4, 5]. Controlling the synthetic location has been achieved mainly by depositing the metal catalysts in a controlled and patterned way for the following chemical vapor deposition (CVD) process.
Typically, patterning catalytic metals has been achieved using the lift-off technique, which consists of a conventional photolithography process and thin film deposition . Alternative patterning methods such as soft lithography  or depositing catalytic thin films through shadow masks  have also been introduced. In these methods, however, either the catalytic film deposition requires a high-vacuum system [6, 8] or the number of process repetitions is limited by the low durability of the stamp . Although electroplating or electroless plating techniques [9–11] can be used to grow CNTs site-selectively and to control the density of the CNTs, these wet process approaches are not suitable for fully processed, movable silicon microelectromechanical system (MEMS) structures.
In this study, we used the spark discharge method to generate catalytic aerosol nanoparticles for CNT synthesis and patterned the particle-deposited area using a shadow mask and the thermophoresis effect [12, 13]. With the patterned nanoparticles, site-specific growth of CNTs was demonstrated. Moreover, the blurring effect caused by adjusting the gap distance between the shadow mask and the substrate allowed us to deposit the catalytic nanoparticles with adjustable and location-specific densities so that the density of synthesized CNTs could be controlled differently on a single substrate. The spark discharge technique is performed using simple equipment without any high-vacuum system, and it generates and deposits the catalytic nanoparticles under dry conditions and atmospheric pressure. In addition, the shadow mask can be used repeatedly without clogging or chemical damage, and all the fabrication steps including thermophoresis are scalable to wafer scale. Furthermore, it is possible to integrate CNTs directly onto microstructures with high aspect ratios utilizing the shadow masking technique, which is difficult with conventional photolithographic patterning of a catalytic layer.
The exemplary applications of the suggested process could be field emission devices and gas sensors. Many of field emitters adopt CNTs for their electron emission tips, and the density of CNTs in this case is directly related to the current density of the device. Hence, it is important to adjust the density of CNTs which enables the device to get the desired field emission performance [14, 15]. So the suggested process which can control the density of CNTs may be used as in this application. In addition, a gas sensor is usually fabricated as resistor type where the target gas is absorbed onto CNTs and changes the resistance of CNTs connecting the electrodes. Because the sensitivity of the sensor and the density of CNTs are closely related, it is needed to adjust the density of CNTs ; thus, this process could be also used to fabricate the gas sensor with enhanced sensitivity.
Figure 1 shows schematic diagrams of the spark discharge process, selective deposition of aerosol nanoparticles, and the resultant site-specific growth of CNTs. As shown in Figure 1a, the nanoparticle generation system consists of two separated iron rods for the spark discharge and a Peltier cooler for the thermophoretic deposition of nanoparticles. When the potential difference between the isolated anode and cathode (two iron rods) was high enough, the accumulated charges were discharged through electrical breakdown in the form of a spark, vaporizing the electrodes and nucleating primary particles of a few nanometers in diameter (before agglomeration). These nanoparticles were carried by a flow of nitrogen gas and grew in size up to tens of nanometers to 100 nm by coalescence depending on the kind of metals [12, 13]. Then, the aerosol nanoparticles were deposited on a silicon dioxide (SiO2) substrate through the patterned holes in the shadow mask because of the thermophoresis effect, in which the particles move from a high-temperature to a low-temperature area along the temperature gradient between the room-temperature aerosol nanoparticles and the bottom of the SiO2 substrate cooled to near 0°C by the Peltier cooler. It is known that during this thermophoretic process, smaller nanoparticles are more easily affected and moved by the temperature gradient [12, 13], and thus, the majority of the nanoparticles on the patterns would be less than 100 nm in diameter. Then, the nanoparticles generated from the spark discharge were used as seed catalytic nanoparticles for CNT synthesis.
We were able to analyze the size distribution of the nanoparticles before deposition through a scanning mobility particle sizer (SMPS). The aerosol that flowed into SMPS through nitrogen at 500 sccm was analyzed for 150 s to measure the size and number of the nanoparticles, and the measurement was repeated five times to calculate the average value. Through this analysis, we were able to find the size distribution of nanoparticles in the aerosol; the diameter of the nanoparticles was distributed from 4.5 to 165.5 nm, and the mean diameter was 40.8 nm.
CNTs were synthesized by thermal CVD in a furnace. The SiO2 substrate was separated from the shadow mask and loaded into the quartz tube of the furnace for thermal CVD at a pressure of several millitorr. Nitrogen gas was passed through the quartz tube to prevent the oxidation of the iron catalyst and to clean the inside while the temperature was increasing up to 700°C. When the temperature stabilized, the carrier gas was replaced with a mixture of ammonia gas and acetylene gas for 10 min. In order to grow CNTs vertically, a mixture ratio of 3:1 was used, i.e., 90 sccm of ammonia gas and 30 sccm of acetylene gas .
Results and discussion
Scanning electron microscope (SEM) images of a patterned CNT line are shown in Figure 2. To confirm that a clear pattern of densely grown CNTs could be formed, we deposited the catalyst for 1 h and synthesized CNTs by supplying the mixture of ammonia gas and acetylene gas for 10 min. As shown in Figure 2b,c, clearly patterned and aligned CNTs were synthesized. The 100-μm-thick stainless steel shadow mask was laser-cut to form continuous line patterns of 100 μm in width. However, the CNTs patterned through these 100-μm-wide line patterns were about 43 μm in width, as shown in Figure 2. This reduction in the line width was caused by the temperature gradient induced by the Peltier cooler, as described in previous work [12, 13]. As the center of the patterns is at a lower temperature than the edge during the cooling, the majority of the nanoparticles deposited by thermophoresis will be accumulated in the narrower central region of each pattern. The average diameter of the individual CNTs shown in Figure 2d was estimated to be 30 to 50 nm.
We first varied the catalytic nanoparticle deposition time to observe its effect on the density of the grown CNTs. Figure 3a shows the nanoparticles deposited through the shadow mask for 1 h. The patterned line width is about 30 μm for a shadow mask width of 100 μm. The insets are close-up views for each panel, and the scale bar is 2 μm. Figure 3b,c,d shows the CNTs synthesized with different catalytic nanoparticle deposition times: 5, 10, and 40 min, respectively. Randomly oriented and tangled CNTs grew with a low density around the low-density catalytic nanoparticles deposited for 5 min, as shown in Figure 3b. Figure 3c,d shows the growth around the nanoparticles deposited for 10 and 40 min, respectively, where the CNTs were synthesized with a higher density and the pattern boundary was clear. The CNT line patterns had a consistent width of about 30 μm for all deposition times tested up to 40 min. From these results, we conclude that vertically aligned CNTs can grow on nanoparticles deposited for 10 min or longer. This observation matches well with the previously reported finding that the catalytic particles must have sufficient density to achieve vertical growth of CNTs .
As shown in Figure 3b, there were CNTs of low density with an unclear pattern when the deposition time was less than 10 min. However, with over 10 min of catalytic nanoparticle deposition time, vertically aligned CNTs were grown with high density forming a clear line pattern. Moreover, we found that the density of CNTs decreased and pattern fidelity deteriorated due to CNTs grown outside the pattern as shown in Figure 3d when the catalytic nanoparticle deposition time was over 40 min. In conventional synthesis result using Fe thin film catalyst, when the Fe thin film deposited is too thin or thick, the quality of CNTs such as density, directionality, and length becomes worse . For a similar reason, it is considered that the density of CNTs is decreased by depositing an excessive amount of catalytic Fe nanoparticles through the spark discharge method. The longer deposition time may also cause an excessive blurring effect of line patterns, increasing the number of CNTs grown outside the pattern and making the pattern fidelity worse. It is concluded from this experiment that there would be an optimized deposition time for clear pattern boundaries and high density of CNTs in the proposed method, and the excessive deposition of catalytic particles resulted in blurred boundary of CNT pattern and reduced density of the CNTs grown.
The gap distance between the substrate and the shadow mask also influenced the density of the deposited catalyst. The nanoparticles spread out when they pass through the patterns of the shadow mask, and the larger the gap is, the more spreading is observed, resulting in a reduction in the density of the particles on the deposited region. To utilize this blurring effect to adjust the density of the grown CNTs, we tilted the shadow mask such that the gap distance between the shadow mask and the substrate changed linearly, as shown in Figure 4a. For this experiment, we used a shadow mask tilted at an angle of 4.76° with respect to the substrate surface, and the gap distance varied linearly from 0 to 4 mm. Figure 4b shows the schematic of the shadow mask pattern used for the CNT line pattern of SEM images shown in Figure 4c. The stainless steel mask is the same as the one used in other experiments and has a length and width of 48 mm × 22 mm and 100 μm of thickness. The width of the laser-cut line pattern is 100 μm. Figure 4d,e,f shows the different site densities of CNTs at the positions illustrated in Figure 4c, where the heights of the shadow mask from the substrate were 1.58, 2.08, and 2.16 mm, respectively. As expected, when the distance between the shadow mask and the substrate was increased, the density of CNTs progressively decreased and the line became wider because of the blurring. The CNT line pattern looks broken when viewing the location of (f) in Figure 4c. The reason for the unclear pattern on the left side of (f) is a reduction of the density of CNTs due to an increase of the blurring effect caused by the receded gap distance between the substrate and the shadow mask. Using this approach, we could gradually vary the density of catalytic nanoparticles and thus gradually change the density of CNTs on a single substrate with a single run of the synthetic process.
We also demonstrated that this method could be applied to the growth of CNTs on a designated area of released micromechanical structures. Typically, released and movable microstructures fail by stiction when the structures are exposed to a liquid, and thus, this demonstration was only possible because no wet process was involved in our proposed method. Figure 5 shows the CNTs synthesized on the released comb structures formed on a device layer of a silicon-on-insulator (SOI) wafer. In Figure 5a, the CNTs were grown on a desired comb only, while the CNTs were grown in a band across multiple combs in Figure 5b. The insets in each figure are the close-up views of CNTs in red squares.
In conclusion, we demonstrated for the first time that the nanoparticles generated using the spark discharge method can be used successfully as catalysts for the growth of CNTs. The nanoparticles were transferred onto the desired area on a substrate by thermophoresis and were patterned using a shadow mask to realize patterned growth of CNTs. The nanoparticle deposition time determines the final density of the grown CNTs, and vertically aligned growth of CNTs was achieved after 10 min of nanoparticle deposition in our experiment. An alternative approach to changing the density of CNTs was to change the gap between the shadow mask and the substrate, and a patterned line of CNTs with gradually varying density along the line could be formed by tilting the shadow mask. The proposed all-dry process could also be applied to completely fabricated micromechanical structures, as demonstrated by site-specifically growing the CNTs on the released high-aspect-ratio microstructures.
Chemical vapor deposition
Scanning electron microscopy
This work was supported by the National Research Foundation of Korea Grant funded by the Korean Government (MEST) (grant no. NRF-2011-0030206) and the Basic Science Research Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Education, Science and Technology (2012R1A1A2043661).
School of Mechanical Engineering, Yonsei University
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