Journal of Nanotechnology

Journal of Nanotechnology / 2011 / Article

Research Article | Open Access

Volume 2011 |Article ID 408151 |

Jason Maley, Gabriele Schatte, Jian Yang, R. Sammynaiken, "Spontaneous Ag-Nanoparticle Growth at Single-Walled Carbon Nanotube Defect Sites: A Tool for In Situ Generation of SERS Substrate", Journal of Nanotechnology, vol. 2011, Article ID 408151, 7 pages, 2011.

Spontaneous Ag-Nanoparticle Growth at Single-Walled Carbon Nanotube Defect Sites: A Tool for In Situ Generation of SERS Substrate

Academic Editor: A. M. Rao
Received31 Mar 2011
Accepted04 Jul 2011
Published27 Sep 2011


Silver nanoparticles were spontaneously formed on pristine and oxidized single-wall nanotubes. Nanoparticles were observed on carbon nanotubes with AFM, and the presence of Ag nanoparticles were confirmed by ESR experiments. Raman spectroscopy of the Ag-treated carbon nanotubes had a 4–10X enhancement of intensity compared to untreated carbon nanotubes. Ag nanoparticles formed at defect sites on the CNT surface, where free electrons located at the defect sites reduced Ag+ to Ag. A mechanism for the propagation of the nanoparticles is through a continual negative charge generation on the nanoparticle by electron transfer from doublet oxygen (O2).

1. Introduction

Since the discovery of carbon nanotubes was first published in 1991, their unique chemical and physical properties have since attracted interest in a wide spectrum of fields, including materials science, engineering, physical sciences, and medical/health sciences [15]. In its simplest form, single-walled carbon nanotubes (SWCNTs) are composed of a single graphene layer rolled into a cylindrical shape, having dimensions of 0.4–1 nm diameter and lengths on the order of 103 nm. Multi walled carbon nanotubes (MWCNTs), on the other hand, are composed of an array of concentric cylinders with diameters up to 50 nm. In addition, the orientation of the graphitic rings along the tubular surface result in the CNTs exhibiting metallic or semiconducting properties [6].

Similar to CNTs, metal nanoparticles have also generated interest, especially in regards to sensors, catalysis, and fuel cell research. Integrating nanoparticles with CNTs is an attractive feature that has potential application in catalysis, sensors, and fuel cells due to the enhanced dispersion and performance [79]. There are many strategies for incorporating metal nanoparticles onto CNT surfaces. One of the most straight forward methods is vapor deposition of a metal layer onto the CNT surface [10]. However, this method requires the deposition of the CNTs onto a substrate, followed by depositing a metal film under vacuum. Electrodepositing Ag through electrolysis reduction [11, 12], or through a η2-coordination, where a Sn2+-activated surface reduces Ag+ onto the CNT surface [13]. Irradiating CNTs with γ-rays in the presence of Ag+ as well as some type of hydrophilic polymer has also produced Ag-decorated CNTs, presumably through the attachment of the polymer onto the CNT surface [1416].

Here, we report the spontaneous formation of Ag nanoparticles onto freshly sonicated SWCNT surfaces. Raman spectroscopy measurements revealed signal enhancement caused by CNT/Ag nanoparticle interaction, and the presence of Ag nanoparticles on the SWCNT surface is supported by atomic force microscopy (AFM) measurements as well as electron spin resonance (ESR) spectroscopy. A mechanism for the formation of Ag nanoparticles on SWCNT defect sites is proposed.

2. Experimental

2.1. Chemicals

Unless otherwise stated, all chemicals were reagent grade and used as received. SWCNT and were purchased from Cheap Tubes (Brattleboro, VT). All water used in experiments was Millipore grade (18.2 MΩ cm).

2.2. Raman Spectroscopy

Raman spectroscopy measurements were carried out on a Renishaw InVia Reflex Raman microscope using a solid state laser diode (Renishaw) operating at 785 nm, and a 1200 lines/mm grating, or a Ar+ laser (Spectra Physics Model 153-M42-010) operating at 514.5 nm and a 1800 line/mm grating. The microscope was focused onto the sample using a Leica 50X N PLAN objective (), and the backscattered Raman signals were collected with a Peltier-cooled CCD detector. The instrument was operated in the line focus mode with a 10 s detector exposure time. The instrument calibration was verified using an internal Si sample, which was measured at 520 cm−1.

2.3. Atomic Force Microscopy

AFM measurements were carried out on an Agilent 4500 AFM (Agilent Technologies, Chandler, Ariz USA) operating in intermittent contact mode. A silicon cantilever (Nanoscience Instruments Inc., Tempe, Az) with a curvature radius of approximately 10 nm was used for AFM measurements. Its specifications include a force constant of approximately 48 N/m, and a resonant frequency of approximately 190 kHz. All measurements were taken with the ratio of the set-point oscillation amplitude to free air oscillation amplitude of 0.80 and a resonance amplitude in the range of 1–1.5 V. In addition, all measurements were performed at ambient conditions with the instrument mounted in a vibration isolation system. The scan rate was 0.5–1 Hz (256 pixels per line) for all images. Height and width measurements from resulting were obtained using SPIP V5.1.5. (Image Metrology, Denmark).

CNT samples were prepared by dissolving the samples in EtOH to a concentration in the range of 102μg/mL, and sonicated for approximately 1 min. Approximately 25 μL of solution was dropped onto freshly cleaved mica, incubated for 5 min, and gently dried with nitrogen gas.

2.4. Electron Spin Resonance Spectroscopy

ESR spectra were recorded on a Bruker EMX ESR spectrometer equipped with an Oxford cryostat ESR900 operating at 6 K. Typical operating parameters were as follows: microwave frequency 9.388 GHz, microwave power 2.00 mW, centre field 3349.88 G, sweep widths of 6000.0 and 200.0 G, conversion time 163.84 ms, time constant 81.92 ms, sweep time 167.77 s, modulation frequency 100 kHz, modulation amplitude 1.0 G, receiver gain .

3. Results and Discussion

Raman spectroscopy provides rich information for CNT characterization. Structural and electronic properties of CNTs can be evaluated by careful interpretation of the Raman spectrum [6]. The Raman spectra of both pristine SWCNT powder are shown in Figure 1. The bands associated with the radial breathing mode transitions are located at low frequencies, and a useful equation can be used to estimate the diameter () of the CNTs where is the RBM band for the nanotube in resonance with the excitation laser line, and are constants determined experimentally. For SWCNT bundles, and values of 234 nm cm−1 and 10 cm−1 nm, respectively, have been determined [17]. By using (1), for the SWCNT used in this study ranged from 0.8 to 1.5 nm.

The lineshape of the G band located at approximately 1590cm−1 indicates that the SWCNTs used in this study are semiconducting SWCNTs [6]. The G band is composed of 2 main bands: (1) G+ band located around 1590 cm−1 and associated with C atom vibrations along the nanotube axis and (2) band located at approximately 1560 cm−1 and associated with C atom vibrations along the circumferential direction. The lineshape of the band for metallic SWCNTs has a Breit-Wigner-Fano lineshape, and its intensity is similar to the G+ band [18]. The D band is a 2nd order phonon mode that is sensitive to disorder-induced effects on the nanotube sidewall, and the 2D band is an overtone of the D band.

Sonication and refluxing the SWCNTs are known to break the CNTs, thus increasing the number of defects on the CNT [19]. Freshly sonicated SWCNTs were exposed to 1 mM solution of AgNO3, centrifuged, and dried. The corresponding Raman spectra of the Ag-treated SWCNT and untreated SWCNT are shown in Figure 2 and fitting results of the more notable bands are summarized in Table 1. In general, there are a few differences associated with the Ag-treated SWCNT compared to the SWCNT. In Figure 2(a), the ratio increased from about 10.1 for SWCNT to approximately 30.4 for Ag-treated SWCNT. Similarly, approximately 3 times decrease in the D-band intensity (Figure 2(b)) was also observed for Raman data acquired with a 1.58 eV laser excitation line. Intercalation of acceptor/donor groups typically increases the intensity and linewidth of the D band, as well as an upshift/downshift of the G+ band [20, 21]. The observed decrease in the D-band intensity and the essentially constant position of the G+ band indicate that the Ag treatment induces any substitutional effects along the CNT surface. In addition to a slight downshift (3 cm−1) and decrease in peak width (47 cm−1 for SWCNT to 40 cm−1) for Ag-treated SWCNT compared to the SWCNT, the decrease in D-band intensity and lineshape, as well as the slight downshift upon Ag-treatment indicates some type of interaction occurring between the Ag and disorder regions located on the SWCNT surface. Also, the peak upshifts by approximately 10 cm−1. It has been previously reported that induced strain to SWCNT bundles causes an upshift in the band [22].

Raman bandUntreated SWCNTAg-treated SWCNT
Raman shift (cm−1)Peak width (cm−1)IntensityRaman shift (cm−1)Peak width (cm−1)Intensity


The most significant feature observed was the 5–10 times increase in Raman intensity within several spots of the Ag-treated SWCNT. This increase in Raman intensity indicates the presence of Ag nanoparticles creating a Surface Enhanced Raman Spectroscopy (SERS) hot spot, where the differences in the Raman spectra are due to a Ag-nanoparticle interaction with the SWCNT. Ag-nanoparticles on the surface of SWCNT induce strain on the attachment point with a possible small charge transfer to the SWCNT. Signal enhancement from Ag nanoparticle in contact with CNT surfaces has been well documented. For instance, Kumar and coworkers measured Raman spectra individual SWCNT grown on Si both before and after Ag deposition and found that the signal intensity increased 9–335 times (corresponding to SERS enhancement factors in the range of 3340–134 000) [10]. Chen and co-workers electrodeposited Ag onto SWCNTs, and found the relative intensity of the G band to increase on the order of 2–14 times for 514.5 and 785 nm laser excitation sources [11].

It is well known that Ag nanoparticles can be formed by thermal decomposition, or the addition of a reducing agent as shown in the following equations However, this is simply not the case here, as there was no reducing agent present in solution, and the laser power on the Raman spectrometer was quite low. Also, the laser excitation was not high enough to induce thermal decomposition of any residual Ag salt.

Figure 3 shows AFM topography images of SWCNT and Ag-treated SWCNT. The SWCNT topography image shows isolated SWCNT with heights in the range of 0.8–1.0 nm, as well as SWCNT in a bundled form (>2 nm height). On the other hand, there are instances of the appearance of nanoparticles attached to SWCNTs for the Ag-treated samples. The nanoparticles attached to both individual and bundled SWCNTs (Figures 3(b)–3(d)) and appeared at mainly the end and along the middle of the CNT walls, presumably at defect sites. The nanoparticle heights were typically in the range of 5-6 nm.

Ag nanoclusters that are not large enough to form conduction bands are still paramagnetic. ESR spectroscopy is extremely sensitive to paramagnetic species and is ideal for detecting disperse and dilute quantities of paramagnetic species. It is ideal to verify that the particles observed in the AFM are not amorphous carbon materials but that they are Ag nanoparticles. Figure 4 shows the ESR spectrum of Ag nanoparticles at 6 K. It is a line centered around 3350 Gauss or . The value is the same as reported for Ag-nanoparticles by Mitrikas and co-workers, but the line width is significantly larger. Mitrikas observed quantum effects and a decrease in line width as the size of particles increase within the range of 3–10 nm [23]. The observed linewidth of 40 Gauss and no power saturation at several milliwatts are different from other ESR studies. The observed SERS is a clear indication that there is interaction between the SWCNT and the Ag nanoparticle. The interaction allows for faster relaxation, thus accounting for the increased linewidth and lack of power saturation. Noninteracting or isolated Ag nanoparticles would be expected to powersaturate very easily due to long relaxation and resulting sharp lines [23, 24].

Formation of Ag nanoparticles in situ has been accomplished by other methods, including γ-irradiation, sonochemistry, and electroless reduction mechanisms. It is well known that γ-irradiation of water produces solvated electrons (), as well as and OH radicals. Metal ions will be reduced by , and the addition of polymers such as PVA will be oxidized, and the corresponding polymer radical have been reported to interact with the CNT surface. The PVA radical has been shown to also reduce Ag+ to form nanoclusters of Ag on the surface of MWCNTs [25]. Sonicating water also produces H and OH radicals, which again can reduce Ag+ to nanoclusters [26]. In a previous study, we reported spontaneous Ag nanoclusters deposit onto porous Si by both a hydride and a negative charge mechanism through unpaired electrons located on the surface of porous Si [27, 28]. With the exception of the hydride, we propose a similar mechanism for the formation of Ag nanoparticles on the surface of SWCNT. Freshly created defects are created by sonication of the SWCNTs. These defects have an affinity for free surface electrons which can reduce aqueous Ag+ onto the surface of the CNT. Propagation of the Ag nanoparticle is then achieved by a series of steps The silver cluster is not floating in solution. It is anchored to the CNT: and builds with time and concentration of Ag+ The key to forming silver nanoparticles on the CNT surface relies on the continual regeneration of negative charge on the silver cluster through the formation of doublet oxygen (O2) by charge transfer from a hydroxide ion to dissolved triplet oxygen (O2). The formation of anionic Ag clusters and dioxygen species has been previously reported in gas phase reactions [29]. Evidence for the generation of the doublet state oxygen has been conducted using nanomaterial and the spin trap DMPO in the presence of oxygen [30]. A single negative charge on the defect site will only result in the deposition of a single silver atom. However, replenishing the negative charge on the Ag surface allows for larger clusters to be formed. The size of clusters depends on the concentration of AgNO3 used [27].

SERS requires materials to be in physical contact with SERS active metals, like Ag. In addition, signal enhancement will be controlled by size and shape of the Ag nanoparticles. Other metal deposition strategies onto CNT surfaces have been reported with SERS enhancement [10, 11]. The SERS enhancement we observed was not uniform throughout the sample, and we found local “hot spots” within the CNT sample. However, the possibility of using this method for an in situ signal enhancement for not only CNTs reported here, but for other nanomaterials in very intriguing.

4. Conclusions

Aqueous Ag+ is reduced by the negative charge of the surface defect of SWCNT, and the process is propagated by the generation of doublet state oxygen anion. A simple novel method for spontaneous and in situ Ag-nanoparticle formation has been described. This method has potential application for spontaneous creation of hot spots for Raman signal enhancement in materials and health science.


Raman microscopy, AFM, and ESR experiments were conducted at the Saskatchewan Structural Sciences Centre which is supported by the University of Saskatchewan. The authors also thank the Canadian Breast Cancer Foundation for support.


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Copyright © 2011 Jason Maley 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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