Journal of NanomaterialsVolume 2011 (2011), Article ID 125846, 7 pagesdoi:10.1155/2011/125846

Research Article

Physical and Electrical Characteristics of Carbon Nanotube Network Field-Effect Transistors Synthesized by Alcohol Catalytic Chemical Vapor Deposition

Chin-Lung Cheng,¹ Chien-Wei Liu,² Bau-Tong Dai,³ and Ming-Yen Lee⁴

¹Department of Electro-Optical Engineering, National Formosa University, Yunlin 63201, Taiwan²Department of Mechanical Engineering, National Yunlin University of Science and Technology, Yunlin 64054, Taiwan³National Nano Device Laboratories, National Applied Research Laboratories, Hsinchu 30078, Taiwan⁴Institute of Materials Science and Green Energy Engineering, National Formosa University, Yunlin 63201, Taiwan

Received 15 March 2011; Revised 2 May 2011; Accepted 12 May 2011

Academic Editor: Gong Ru Lin

Copyright © 2011 Chin-Lung Cheng 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.

Carbon nanotubes (CNTs) have been explored in nanoelectronics to realize desirable device performances. Thus, carbon nanotube network field-effect transistors (CNTNFETs) have been developed directly by means of alcohol catalytic chemical vapor deposition (ACCVD) method using Co-Mo catalysts in this work. Various treated temperatures, growth time, and Co/Mo catalysts were employed to explore various surface morphologies of carbon nanotube networks (CNTNs) formed on the SiO₂/n-type Si(100) stacked substrate. Experimental results show that most semiconducting single-walled carbon nanotube networks with 5–7 nm in diameter and low disorder-induced mode (-band) were grown. A bipolar property of CNTNFETs synthesized by ACCVD and using HfO₂ as top-gate dielectric was demonstrated. Various electrical characteristics, including drain current versus drain voltage , drain current versus gate voltage , mobility, subthreshold slope (SS), and transconductance , were obtained.

1. Introduction

Carbon nanotube field-effect transistors (CNTFETs) have been explored in nanoelectronics to realize desirable device characteristics [1–11]. Both n-type and p-type single-walled carbon nanotube (SWCNT) field-effect transistors (FETs) with top-gate electrodes in the conventional metal-oxide-semiconductor field-effect transistor (MOSFET) structures were demonstrated [1]. Two methods, including conventional doping and annealing metal/carbon nanotubes (CNTs) contact in vacuum, were used for the CNTFETs conversion from p- to n-type devices [2]. Moreover, the fabrication of the n-type CNTFET by Al-doped CNTs as channel was also achieved [12]. The primary potential advantage of CNTs is their very high carrier mobility ( cm²/V-s) [13]. However, one of challenges of CNTs to be viable in high-performance FETs is the requirement for processes that provide each CNTs placed in a desired location and direction [14]. Recently, an architecture based on the assembly of two- and three-dimensional networks of SWNTs using chemical vapor deposition (CVD) was demonstrated [15]. The field-effect mobility of random networks of SWCNT as thin-film transistor can exceed 100 cm²/V-s [16]. SWCNT random network thin film transistor with a 10⁵ of on/off ratio and a ~8 cm²/C-s of field-effect mobility was demonstrated using water-assisted plasma-enhanced CVD (PECVD) [17]. Although various methods were used to synthesize the carbon nanotube networks (CNTNs), some electrical characteristics of CNTNs fabricated by alcohol catalytic CVD (ACCVD) remain not totally understood. We, therefore, attempt to explore some characteristics to gain better physical and electrical insights into the properties of CNTN field-effect transistors (CNTNFETs).

2. Experimental Methods

CNTNFETs with top-gated structures were fabricated on (100-) oriented n-type silicon wafers. The substrate consists of a highly doped n-type Si(100) wafer with an arsenic doping concentration of  cm⁻³. Prior to SiO₂ growth, all wafers were cleaned through a wet cleaning process (APM/HPM/DHF), using an NH₄OH/H₂O₂/H₂O mixture (APM) in a ratio of 1 : 4 : 20 (volume) at 75°C and an HCl/H₂O₂/H₂O mixture (HPM) in a ratio of 1 : 1 : 6 (volume) at 75°C, to remove residues and contaminants. The dipping time in all processes was 10 min. Diluted HF (DHF), with an HF : H₂O ratio of 1 : 100 (volume), was used to remove native oxide. Following the wet processes, all of the samples were rinsed in deionized water for 10 min. Then, the SiO₂ layers with 100 nm thicknesses measured by the spectroscopic ellipsometry were thermally grown on the cleaned wafers. The SiO₂ layers were prepared by the dry thermal oxidation in O₂ at 925°C. To obtain a hydrophilic surface, all SiO₂/n-Si(100) stacked substrates were treated through a wet cleaning process (APM/HPM). Next, a Co acetate [(CH₃CO₂)₂Co-4H₂O] and a Mo acetate [(CH₃COOH)₂Mo] were premixed at (a) Co : Mo = 0.1 : 0.1 wt%, (b) Co : Mo = 0.05 : 0.05 wt%, and (c) Co : Mo = 0.02 : 0.02 wt%, as well as dissolved in ethanol with sonication for 8 hours and then the Co/Mo catalysts were dip-coated on the SiO₂ surface. After drying at the room temperature, all samples were put into ACCVD chamber and were calcined from the room temperature to 400°C for 10 min. Then, the temperature was risen from 400 to (a) 650, (b) 700, and (c) 750°C for 30 min with a mixed Ar/NH₃ gases flow of 200/30 SCCM (SCCM denotes cubic centimeter per minute at STP), and a pressure is about 10–15 torr. Under the process temperature of (a) 650, (b) 700, and (c) 750°C, the Ar/NH₃ mixed gases were stopped, and the heated alcohol vapor was supplied into the quartz tube with a process pressure of 10 Torr for (a) 5, (b) 10, (c) 15, and (d) 20 min, respectively. After active region (AR) definition lithography, outer CNTN of AR was etched by an SF₆ = 50 sccm ambient with a radio frequency (RF) power of 50 W and following photoresist (PR) removal. Then, the source/drain electrodes using Au (bottom)/Al (top) stacked films of 20/300 nm thick were deposited via sputtering and were patterned by lift-off technique. Then, the HfO₂ layers with 30.0 nm thicknesses measured by the deposited sensor were deposited using reactive dc magnetron sputtering of 99.95% pure Hf targets in an Ar = 24 sccm ambient with a power of Hf target at RF power of 30 W. Subsequently, postdeposition annealing (PDA) using furnace annealing was performed in O₂ gas for 30 min at 450°C. A metal gate electrode with a 500 nm Al film was deposited via sputtering and was patterned by the lithography. Various physical properties of CNTNs were analyzed by Raman spectrometry, scanning electron microscope (SEM), and high-resolution transmission electron microscope (HRTEM), respectively. Various electrical characteristics of CNTNFETs were evaluated by the HP 5270B instrument.

3. Results and Discussion

Various treated temperatures, growth time, and Co/Mo catalysts were employed to explore various surface morphologies of CNTNs formed on the SiO₂/n-type Si(100) stacked substrate. The substrate consists of a highly doped n-type Si(100) wafer with an arsenic doping concentration of  cm⁻³. Various SEM plane views of CNTNs formed on the SiO₂/n-type Si(100) stacked substrates were shown in Figures 1–3. The growth conditions were carried out at 750°C in the alcohol ambient for (a) 5, (b) 10, (c) 15, and (d) 20 min; respectively, and the partial pressure was achieved in 10 Torr as shown in Figure 1. A Co/Mo acetate was premixed at Co : Mo = 0.1 : 0.1 wt% and dissolved in ethanol with sonication for 8 hours. It can be seen that dispersed CNTNs were formed on the SiO₂/n-type Si(100) stacked substrate resulting from short growth time as shown in Figure 1(a). On the contrary, the dense CNTNs were demonstrated using long growth time as shown in Figure 1(d). Thus, the results suggest that the densities of CNTNs increase with increasing time of growth.

(a)

(b)

(c)

(d)

Figure 1: Plane view of SEM morphology of random carbon nanotube networks (CNTNs) formed on the SiO₂/n-type Si(100) stacked substrate. The substrate consists of a highly doped n-type Si(100) wafer with an arsenic doping concentration of  cm⁻³. The growth conditions were carried out at 750°C in the alcohol ambient for (a) 5, (b) 10, (c) 15, and (d) 20 min; respectively, and the partial pressure was achieved in 10 Torr. A Co/Mo acetate was premixed at Co : Mo = 0.1 : 0.1 wt% and dissolved in ethanol with sonication for 8 hour.

(a)

(b)

(c)

Figure 2: Plane view of SEM morphology of CNTNs formed on the SiO₂/n-type Si(100) stacked substrate. The growth conditions were carried out at 750°C in the alcohol ambient for 10 min, and the partial pressure was achieved in 10 Torr. Various Co/Mo acetate were premixed at (a) Co : Mo = 0.1 : 0.1 wt%, (b) Co : Mo = 0.05 : 0.05 wt%, and (c) Co : Mo = 0.02 : 0.02 wt%, respectively. Then, all Co/Mo catalysts were dissolved in ethanol with sonication for 8 hours.

(a)

(b)

(c)

Figure 3: Cross-sectional view of SEM morphology of CNTNs formed on the SiO₂/n-type Si(100) stacked substrate. Various plane views were also shown in the inset of figure. The growth conditions were carried out at (a) 750, (b) 700, and (c) 650°C in the alcohol ambient for 10 min, and the partial pressure was achieved in 10 Torr. A Co/Mo acetate was premixed at Co : Mo = 0.1 : 0.1 wt% and dissolved in ethanol with sonication for 8 hours.

To scrutinize the effects of various wt% of Co/Mo catalysts on characteristics of CNTNs, various Co/Mo acetates were premixed at (a) Co : Mo = 0.1 : 0.1 wt%, (b) Co : Mo = 0.05 : 0.05 wt%, and (c) Co : Mo = 0.02 : 0.02 wt%, respectively, as shown in Figure 2. The growth conditions were carried out at 750°C in the alcohol ambient for 10 min. Compared with high concentration of the Co/Mo catalysts, the dispersed CNTNs were formed by the Co/Mo catalysts with low concentration. This could be due to the dispersion of the Co/Mo catalysts with low concentration. Therefore, the results indicate that the densities of CNTNs decrease with decreasing wt%. Moreover, the effects of various treated temperatures on the densities of CNTNs are important issues. Thus, the growth conditions were performed at (a) 750, (b) 700, and (c) 650°C, respectively, in the alcohol ambient for 10 min and shown in Figure 3. A Co/Mo acetate was premixed at Co : Mo = 0.1 : 0.1 wt%. The experimental results demonstrate that the densities of CNTNs increase with increasing growth temperature.

To probe diameter of CNTNs, the TEM analysis was adopted. According to the top morphology of TEM analysis, a single-walled CNTN with 5–7 nm in diameter was grown as shown in Figure 4. Experimental results show that CNTs with various diameters were crisscrossed through another one densely. Thus, according to the results of Figures 1–4, the CNTNs synthesized at 750°C in the alcohol ambient for 10 min under the Co : Mo = 0.1 : 0.1wt% were used to prepare the CNTNFET.

Figure 4: Plane view of TEM morphology of CNTNs was formed on the SiO₂/n-type Si(100) stacked substrate. The growth conditions were carried out at 750°C in the alcohol ambient for 10 min, and the partial pressure was achieved in 10 Torr. A Co/Mo acetate was premixed at Co : Mo = 0.1 : 0.1 wt% and dissolved in ethanol with sonication for 8 hours.

To demonstrate various physical characteristics of as-grown CNTNs, Raman spectra of as-grown CNTNs deposited on the SiO₂/n-type Si(100) substrate measured with 633 nm excitation and energy of 1.96 eV were shown in Figure 5. For isolated semiconducting SWNT, the Raman-allowed tangential modes ( mode) are labeled and at Raman frequency () of 1592 () and 1570 () cm⁻¹, respectively [18]. Thus, the results suggest that as-grown CNTNs synthesized by ACCVD are semiconducting SWNTs. This is further demonstrated by using the low-frequency peak measurement. The low-frequency peak is given by , where is the diameter of CNT, with being different for metallic ( cm⁻¹ nm²) and semiconducting ( cm⁻¹ nm²) SWNTs [19]. Since the results show that the value of CNTNs synthesized by ACCVD is to be around 57 cm⁻¹ nm², most semiconducting CNTNs were demonstrated. A little metallic nanotubes could be included in the CNTNs synthesized by ACCVD. Moreover, it has been reported that the intensity ratio between the two most intense features is in the range for most of the isolated SWNTs (90%) [19]. In this work, the value of is to be around 0.214, indicating that the CNTNs with 90% SWNTs were demonstrated. Furthermore, the defects in CNTs are characterized by , where is the intensity of mode, is the intensity of disorder-induced mode (D band). The value of is estimated to be around 0.92, indicating that the CNTNs with low defects were synthesized by ACCVD.

Figure 5: Raman spectra of as-grown CNTNs deposited on the SiO₂/n-type Si(100) substrate measured with 633 nm excitation and energy of 1.96 eV.

Figure 6 shows the output characteristics, drain current versus drain voltage (-), of p-CNTNFET and n-CNTNFET consisting of an HfO₂ of 30 nm as top-gate dielectric for several values of the gate voltage. The channel length and width of CNTNFETs was 1 and 5 μm, respectively. At near 0 V, the current of devices were to be around 0, indicating that the devices were off-status. For and , the behavior of - curves were similar to that of n-MOSFET. For and , the behavior of - curves were similar to that of p-MOSFET. Thus, the bipolar property of CNTNFET synthesized by ACCVD and using HfO₂ as top-gate dielectric was demonstrated.

(a)

(b)

Figure 6: Drain current versus drain voltage (-) characteristics of (a) p-CNTNFET and (b) n-CNTNFET with HfO2 of 30 nm as gate dielectric. The channel length and width of CNTNFETs were 1 and 5 μm, respectively.

Figure 7 shows the output characteristics, drain current versus gate voltage (-), of (a) p-CNTNFET and (b) n-CNTNFET with an HfO₂ of 30 nm as gate dielectric. The results suggest that both p-CNTNFET and n-CNTNFET exhibits an on-to-off ratio of ~10⁶ and a threshold voltage of −3 and 2.6 V, respectively. To estimate the effective hole and electron mobility in p-CNTNFET and n-CNTNFET, respectively, the following formula is adopted [16]: where is the equivalent oxide thickness (EOT) of HfO₂-gate, dielectric and is the permittivity of the silicon dioxide. and are the channel length and the channel width of CNTNFETs. For these networks, the effective hole mobility of  cm²/V-s for the p-CNTNFET and the effective electron mobility of  cm²/V-s for the n-CNTNFET were extracted, respectively. To estimate the subthreshold slope (SS) in both p-CNTNFET and n-CNTNFET, the following formula is adopted [20]: The results show that the of 6 mV/decade for the p-CNTNFET and the of 18 mV/decade for the n-CNTNFET were extracted, respectively. In general, the SS characteristics of the conventional silicon-based MOSFET is to be around 70–100 mV/decade [20]. Thus, the characteristics of CNTNFETs synthesized by ACCVD is better than that of the silicon-based MOSFET one. To demonstrate the amplifier characteristics, the transconductance output characteristics () of HfO₂-gated p-CNTNFET and n-CNTNFET were shown in Figure 8. The results show that the of 1.93 A/V for the p-CNTNFET and the of 0.095 A/V for the n-CNTNFET were extracted, indicating that the amplifier characteristics of p-CNTNFET is better than that of n-CNTNFET one.

(a)

(b)

Figure 7: Drain current versus gate voltage (-) characteristics of (a) p-CNTNFET and (b) n-CNTNFET with an HfO₂ of 30 nm as gate dielectric. The channel length and width of CNTNFETs were 1 and 5 μm, respectively.

(a)

(b)

Figure 8: The output characteristic transconductance () of HfO₂-gated (a) p-CNTNFET and (b) n-CNTNFET.

4. Conclusions

The present study gives an important message that the bipolar property of semiconducting single-walled CNTNFET synthesized by ACCVD and using HfO₂ as top-gate dielectric was demonstrated. The densities of CNTNs increase with increasing process temperature, treated time, and Co/Mo catalysts concentrations. Experimental results indicate that the random networks of SWNTs with higher effective hole/electron mobility, smaller subthreshold slope, are the promising candidate for the development of the nano-electronic devices.

Acknowledgments

The authors would like to thank the National Science Council of Taiwan for the financial support under Contract no. NSC 99-2221-E-224-020 and NSC 99-2622-E-150-032-CC3. Technical support from National Nano Device Laboratories (NDL) of Taiwan and common Laboratories for Micro/Nano Science and Technology of National Formosa University are also acknowledged.

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