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ISRN Nanotechnology

Volume 2012 (2012), Article ID 234216, 16 pages

http://dx.doi.org/10.5402/2012/234216

## Raman Spectroscopy in Graphene-Based Systems: Prototypes for Nanoscience and Nanometrology

Departamento de Física, Universidade Federal de Minas Gerais, 30123-970 Belo Horizonte, MG, Brazil

Received 26 August 2012; Accepted 16 September 2012

Academic Editors: W. Lu and M. Tommasini

Copyright © 2012 Ado Jorio. 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

Raman spectroscopy is a powerful tool to characterize the different types of sp^{2} carbon nanostructures, including two-dimensional graphene, one-dimensional nanotubes, and the effect of disorder in their structures. This work discusses why sp^{2} nanocarbons can be considered as prototype materials for the development of nanoscience and nanometrology. The sp^{2} nanocarbon structures are quickly introduced, followed by a discussion on how this field evolved in the past decades. In sequence, their rather rich Raman spectra composed of many peaks induced by single- and multiple-resonance effects are introduced. The properties of the main Raman peaks are then described, including their dependence on both materials structure and external factors, like temperature, pressure, doping, and environmental effects. Recent applications that are pushing the technique limits, such as multitechnique approach and *in situ* nanomanipulation, are highlighted, ending with some challenges for new developments in this field.

#### 1. Introduction

Raman spectroscopy is the inelastic scattering of light by matter, from molecules to crystals [1]. The effect is highly sensitive to the physical and chemical properties of the scattering material, as well as to any environmental effect that may change these properties. For this reason, the Raman spectroscopy is evolving into one of the most useful tools for the development of nanoscience and nanometrology. Raman spectrometers are widely available; the technique is relatively simple to perform, possible to carry out at room temperature and under ambient pressure, and requiring relatively simple or no specific sample preparation. Optical techniques (if not using high-energy photons) are nondestructive and noninvasive, as they use a massless and chargeless particle, the photon, as a probe, which is especially important for nanoscience due to the large surface-to-volume ratio in nanomaterials.

Two-dimensional graphene, one-dimensional carbon nanotubes, and the related disordered materials, here all referred to as sp^{2} nanocarbons, are selected as the prototype materials to be discussed, first due to their importance to nanoscience and nanotechnology, second because their Raman spectra have been extremely useful in advancing our knowledge about these nanostructures.

Nature shows that it is possible to manipulate matter and energy by assembling complex self-replicating carbon-based structures that are able to sustain life. On the other hand, carbon is the upstairs neighbor to silicon in the periodic table, with carbon having more flexible bonding and having unique physical, chemical, and biological properties, holding promise for a revolution in electronics at some future time. Three important factors make sp^{2} nanocarbons special.(1)The unusually strong covalent bonding between neighboring carbon atoms. This strength is advantageous for sp^{2} nanocarbons as a prototype material for the development of nanoscience and nanotechnology, since different interesting nanostructures (sheets, ribbons, tubes, horns, cages, etc.) are stable and strong enough for exposure to many different types of characterization and processing steps. (2)The sp^{2} nanocarbons, which include graphene and carbon nanotubes, fullerenes, and other carbonaceous materials, are also called electron materials due to the extended electron clouds. The delocalized electronic states in monolayer graphene are highly unusual, because they behave like relativistic Dirac Fermions, that is, these states exhibit a massless-like linear energy momentum relation, and are responsible for unique transport (both thermal and electronic) properties at sufficiently small energy and momentum values. This unusual electronic structure is also responsible for unique optical phenomena.(3)The simplicity of the sp^{2} nanocarbon systems, which are systems formed by only one type of atom in a periodic hexagonal structure. Therefore, different from most materials, sp^{2} nanocarbons allow us to easily access their special properties using both experimental and theoretical approaches, enabling us to model the structure for the development of our methodologies and knowledge.

Finally, it is very advantageous that with a common Raman spectroscopy apparatus, one can observe the Raman scattering response from one single graphene sheet, as well as from one isolated single-wall carbon nanotube (SWNT). The similarities and differences in the Raman spectra for the different sp^{2} nanocarbons pave the route for understanding the potential of Raman spectroscopy in nanoscience and nanometrology [2].

This paper is organized as follows: Section 2 quickly introduces the atomic structure of the sp^{2} nanocarbons. Section 3 describes the historical development of Raman spectroscopy applied to sp^{2} nanocarbons. Section 4 discusses the general aspect of the sp^{2} nanocarbons Raman spectra, related to both first and higher-order scattering events, mostly induced by resonance effects. The momentum-selective resonance mechanisms in the sp^{2} nanocarbon Raman spectroscopy are discussed in Section 5. Section 6 describes the detailed behavior of the most intense features, named D, G, G^{'}, and RBM bands. Section 7 describes the new achievements that are pushing the limits of Raman spectroscopy on sp^{2} nanocarbons, such as multitechnique approach and *in situ* nanomanipulation, including also the applications to cross-related fields like biotechnology and soil science. Section 8 closes the paper with conclusions and pointing some challenges for further developments.

#### 2. The sp^{2} Nanocarbons Structure

The fundamental crystal that constitutes the basis of sp^{2} nanocarbons is graphene, a two-dimensional (2D) planar structure composed by packing hexagons (see Figure 1, left). The carbon atoms are located at the vertices of the hexagons, and a two C atoms unit cell can be used to reproduce the entire structure by applying the appropriated translation operations. When many graphene layers are put on top of each other, the resulting material is graphite.

By cutting a graphene layer, a graphene nanoribbon can be constructed. By rolling such a ribbon into a cylinder, one generates a carbon nanotube (see Figure 1, right). The carbon nanotube can be achiral, like the one shown in Figure 1, or chiral (not shown), where the carbon bonds exhibit a helical structure around the SWNT axis direction.

Other sp^{2} nanocarbons, like fullerenes, nanocones, and nanohorns, require the introduction of defects in the hexagonal structure to break the planar structure. The most common is the replacement of a hexagon by a pentagon. A fullerene is composed of 12 hexagons to fully close the structure in a “football-like” cage structure (“soccer-like” for North Americans). The number of hexagons can start from zero and increase indefinitely, making larger and larger carbon cages. The football-like structure is composed by a total of 60 atoms, thus being named the C_{60}. Strictly speaking, the C–C bonds in such structures have a mixing of the and bonds, the degree of mixing depending on the degree of planar deformation.

#### 3. Historical Development of Raman Spectroscopy Applied to sp^{2} Nanocarbons

Raman spectroscopy has been used to study carbon structures since its discovery [1]. However, when applied to sp^{2} nanocarbons, there is a milestone in the early seventies, in the field of nanographite and amorphous carbons [3], followed by many important works in that decade (e.g., [4, 5]). The technique has encountered important applications in the field of ion implantation and graphite intercalation compounds [6], and its success on this field kept increasing with applications to fullerenes [7], carbon nanotubes [8], and finally the mother material graphene [9]. While the main route of the solid-state physics approach has provided the framework for the great majority of the studies in this field, quantum chemical studies of polyaromatic compounds were crucial for understanding different uncommon aspects related to the Raman spectra of sp^{2} nanocarbons [10].

Important developments in our understanding of the Raman spectroscopy applied to graphene-based systems happened in the early 21st century. In 2000, Ferrari and Robertson [11] described qualitatively the amorphization trajectory from graphite to tetrahedral amorphous carbon. They proposed a three-stage classification of disorder: stage 1, from graphite to nanocrystalline graphite; stage 2, from nanocrystalline graphite to low sp^{3} amorphous carbon; stage 3, from low to high sp^{3} (tetrahedral) amorphous carbon.

In the same year, Thomsen and Reich [12] introduced the double-resonance mechanism to explain the observation and dispersive behaviour of the disorder-induced D band in defective graphite, appearing near 1350 cm^{−1} for excitation with a 514 nm wavelength laser. This solid-state physics approach was shown to be consistent with quantum chemical studies of polyaromatic compounds to explain the D band [10]. While the two approaches are complementary to understand the phenomena, the solid-state physics approach can be made analytical, allowing further advances. For example, Saito et al. [13] extended the double-resonance model, including intravalley and intervalley electron-phonon scattering mechanisms and application to all phonon branches in different sp^{2} carbons.

Still in 2000, Rao et al. [14] were the first to explore one-dimensional selection rules in the Raman spectra of multiwall carbon nanotubes (MWNTs), and this study was further clarified performing experiments on SWNTs and using group theory [15–17].

A breakthrough in the field came with the launch of single-nanotube spectroscopy in 2001 [18], showing that carbon nanotubes could be studied at the isolated tube level. Each SWNT species was shown to present specificities in the Raman scattering processes, thus starting the single-nanotube spectroscopy rush. Realization of single graphene nanoribbon spectroscopy came a few years later [19].

Based on the double-resonance mechanics, in 2002, Souza Filho et al. [20] demonstrated how the second-order Raman spectra could be used to provide information about changes in the electronic structure of different () SWNTs. A few years later, in 2006, Ferrari et al. [21] used the same concept to show that Raman spectroscopy could be applied as a very simple and straightforward method to determine the number of layers in a graphene sample. Similar results were obtained simultaneously by Gupta et al. [22].

In 2003, two different groups, Hartschuh et al. [23] and Hayazawa et al. [24], observed, for the first time, the tip-enhanced Raman spectroscopy (TERS) from carbon nanotubes. Due to their low dimensionality and huge optical response, carbons nanotubes started to be widely used as a prototype for the development of TERS. Some results achieved in carbon nanotubes were nanoscale vibrational analysis [25], nanoscale optical imaging of excitons [26], TERS polarization measurements [27], imaging of nanotube chirality changes [28], spectral determination of single-charged defects [29], and local optical response of semiconducting nanotubes to DNA wrapping [30], among others. A comprehensible review for TERS in carbon nanotubes can be found in [31]. In the case of graphene, a few results are appearing in the literature [32–35], including the imaging of defects and contaminants [36].

In 2004, Cançado et al. [37] showed that the disorder-induced D band intensity in graphite edges depends on the edge atomic structure, differentiating the zigzag from the armchair edge. A few years later, in 2009, Casiraghi et al. [38] showed that the same effect could be observed in graphene. In the same year, the quantum chemical calculations approach was shown to be consistent with the solid-state physics predictions for the zigzag versus armchair edge response [39].

High-level doping effects could also be assessed in carbon nanotubes, as summarized in 2003 for chemical doping by Filho et al. [40], and in 2004 for electrochemical doping by Corio et al. [41]. As demonstrated later, understanding low-doping effects had to wait for the introduction of new concepts.

The different Raman scattering phenomena—1st and multiple-order, single, and multiple resonances—responsible for the Raman features were established, but quantitative accurate description of the main features was restricted to empirical models [42, 43]. Despite so many studies, the phonon dispersion for the optical modes near the high-symmetry and K points was not accurately described theoretically, leading to the development of different and unsuccessful models. A very important conceptual change was then proposed by Piscanec et al. [44] in 2004, with the introduction of the Kohn anomaly physics in the graphite phonon dispersion. This new concept was applied successfully to describe the phonon dispersion of graphite near the high-symmetry points in the Brillouin zone and to understand and characterize low doping levels in both graphene [45] and carbon nanotubes [46, 47]. The Raman frequencies, including their dependence on strain and doping, were understood [48, 49], and the overall consistency with quantum chemistry calculations was established [50].

Starting from 2004, resonance Raman spectroscopy with many excitation laser lines was extensively applied for the determination of the optical transitions () in SWNTs by Fantini et al. [51], Telg et al. [52], Araujo et al. [53], and Doorn et al. [54], among others, and in double-wall carbon nanotubes (DWNTs) by Pfeiffer et al. [55]. All this development came together with the introduction of many-body physics (electron-electron and electron-hole interactions) for accurate description of and the Raman matrix elements in SWNTs, by Jiang et al. [56, 57].

Finally, the introduction of environmental effects in both vibrational [58] and electronic properties [59] of SWNTs was largely studied, staring in 2008 by Araujo et al. [58, 59]. The effect of the dielectric constant in SWNTs was shown to depend on the SWNT diameter due to the presence of electric field inside the *quasi*-one-dimensional tube [59, 60].

#### 4. General Aspect of the sp^{2} Nanocarbons Raman Spectra

Different aspects have to be considered to understand why the Raman spectroscopy has played a very important role in the development of the science related to sp^{2} nanocarbons: (1) vibrations in carbon nanostructures strongly modulate the Raman polarizability tensor, and the scattering processes are resonant because of the electrons, guaranteeing a strong response; (2) the Raman spectra exhibit peaks with relatively high frequencies because of the high stiffness of the C–C bonds, and any small frequency change (less than 1%) is easily detectable with broadly available spectrometers; (3) the resonance effects make it possible to study both phonons and electrons, and multiple resonances enhance special scattering processes probing phonons in the interior of the Brillouin zone.

The Raman spectra from sp^{2} nanocarbons are composed of many peaks coming from first-order and higher-order scattering processes (see Figure 2). The Raman features can all be related to phonons in graphene, not only at the Brillouin zone center, but also from the interior of the Brillouin zone. The modes associated with interior points are activated either by higher-order (combination modes and overtones) processes or by defects which break the momentum selection rule [2, 12] (see Section 5). The modes from the interior of the Brillouin zone can be dispersive (frequency changes with changing the excitation laser energy ), and therefore, they can be used for measuring the electron and phonon dispersion based on the double-resonance model. However, according to the multiple-resonance model, the Raman features are composed of averages of phonons around the high-symmetry points and lose well-defined momentum information. Table 1 provides a summary of the assignments of many of these features in the Raman spectra [2]. The results give average values that usually exhibit small deviations depending on the sp^{2} nanocarbon structure and on the ambient conditions.

#### 5. Momentum-Selective Resonance Mechanisms in sp^{2} Nanocarbon Raman Spectroscopy

As pointed in Section 4, the scattering processes are resonant because of the electrons. In a perfectly crystalline structure, translational symmetry guarantees momentum conservation, so that only point phonons () can be Raman active in a one-phonon (first-order) scattering process. In grapheme-related systems, this resonance process gives rise to the G band peak, and the respective resonance process is displayed in Figure 3. The red circle in the graphene phonon dispersion (left part of Figure 3) shows the G band momentum and frequency. On the right part of Figure 3, the G band eigenvector is shown (top), as well as the electronic transitions induced by the incoming photon (green), by the G band phonon (black) and generating the outgoing photon (red). The point phonon near 870 cm^{−1} is not Raman active, but it can be seen by infrared absorption experiments.

When higher-order scattering events are considered, for example, two-phonon scattering with and momentum transfer, or when defects in the lattice break the crystal translational symmetry, phonons with momentum are Raman allowed [12, 13]. In these cases, specific phonons will be selected in the sp^{2} nanocarbons Raman spectra, due to higher-order resonance effects, as displayed in Figure 4. Both electron-photon (upwards green arrow) and electron-phonon (diagonal black solid arrows) scattering processes are resonant. After the electronic transition induced by absorbing the incoming photon (green vertical arrow), the electron in the valence band can be scattered by a momentum phonon resonantly, considering that the phonon energy and momentum will connect two real electronic states, as indicated by the black diagonal solid arrows indicated by D and in Figure 4. The diagonal black-dashed arrow indicates a nonresonant scattering. These special D and phonons can be mapped back into the graphene phonon dispersion, and they lye either near the (intra-valley scattering) or near the K (inter-valley scattering) point in the Brillouin zone (see Figure 4, top right). For the D band phonon, there are two optical branches close in energy, the in-plane transversal optical (iTO) and the in-plane longitudinal optical (iLO). The D band, as well as the second-order (or 2D) band, comes from the TO mode (red branch in Figure 3) because the electron-phonon coupling near K is much stronger for the TO phonon than for the LO phonon. However, as described in Section 4, all phonon branches can generate the multiple-resonance Raman scattering processes, thus generating a large number of peaks in the Raman spectra from sp^{2} nanocarbons [13], as shown in Figure 2. Most of these peaks exhibit relatively low intensity due to the weak electron-phonon coupling.

#### 6. Detailed Behaviour of the Main Features

Although the Raman spectra of graphitic materials consist of a large number of peaks, as discussed in the previous sections, most of them are relatively weak. The most intense peaks and broadly used to study and characterize these materials are the G and D bands, appearing around 1585 cm^{−1} and 1350 cm^{−1}, respectively. The G peak corresponds to the first-order Raman-allowed phonon at the Brillouin zone centre (see eigenvector schematics in Figure 3—top-right). The D peak is related to the breathing modes of the six-atom rings (see K point eigenvector schematics in Figure 4—bottom-right) and requires a defect for its activation. The peak, related to the second order of the D peak, is also strong and important for sp^{2} nanocarbon characterization. Finally, the radial breathing mode (RBM), present only in SWNTs, is the key feature for SWNT studies. The characteristics for these most intense Raman features are presented in Figure 5 for different sp^{2} nanocarbons, and a summary of how they are used to characterize sp^{2} nanocarbons is discussed here.

##### 6.1. The G Band

The G band, related to the C–C bond stretching (see eigenvector in Figure 3), is the main Raman signature for all sp^{2} carbons, and it is observed as a peak (or a multipeak feature) at around 1585 cm^{−1} (see Figure 5). The G band properties can be summarized as follows.(i)Hydrostatic pressure on graphene shifts its frequency . (ii)Uniaxial stretching of graphene splits the G peak into and , which are, respectively, related to atomic motion along and perpendicular to the stretching direction. Increasing the stretching redshifts both and .(iii)Doping graphene blueshifts for weak doping (changes in the Fermi level near the K point). Higher doping levels can cause blue (red) shift for () doping. (iv)Increasing temperature () generally redshifts . Different effects take place, such as changes in the electron-phonon renormalization, phonon-phonon coupling, and shifts due to thermal expansion-induced volume changes.(v)When choosing light polarized in the graphene plane (propagation perpendicular to the sheet), then rotating the polarization is irrelevant for unstrained or homogeneously strained graphene. If graphene is inhomogeneously strained, then the relative intensity between the G^{+} and G^{−} peaks / will give the strain direction.(vi)The linewidth for the G peak is usually in the range of 10–15 cm^{−1}, although it changes with strain, temperature, and doping.(vii)Bending the graphene sheet splits the G band into and , which have their atomic vibrations preferentially along and perpendicular to the folding axis, respectively.(viii)Rolling up the graphene sheet into a seamless tube (SWNT) causes the following effects: (1) bending splits the G band into and , which are preferentially along (LO) and perpendicular (TO) to the tube (folding) axis, respectively, for semiconducting SWNTs. For metallic tubes, electron-phonon coupling softens the LO modes, so that and are actually associated with TO and LO, respectively. (2) Quantum confinement generates up to 6 Raman-allowed G band peaks, three of each exhibiting LO- or TO-like vibrations, two totally symmetric A1 modes, two E1 modes, and two E2 symmetry modes. Due to the depolarization effect and special resonance conditions, the A1 modes usually dominate the G band spectra.(ix)Decreasing the SWNT diameter increases the bending and shifts mostly . The shift can be used to measure the SWNT diameter.(x)Changing the SWNT chiral angle changes the intensity ratio between LO- and TO-like modes.(xi)Hydrostatic pressure on SWNT bundles shifts .(xii)Strain on isolated SWNTs under hydrostatic and uniaxial deformation, torsion, bending, and so forth, changes G^{−} and G^{+}, depending on the tube structure, as defined by the chiral indices (). (xiii)Doping SWNTs changes , mainly for metallic SWNTs. There is a rich doping dependence on (), but a strong effect is felt mostly on the broad and downshifted G^{−} peak in metallic SWNTs, with doping usually causing an upshift and sharpening of the G^{−} feature.(xiv)Temperature change generates similar effects in SWNTs and graphene. Increasing T softens and broadens the G band peaks in SWNTs.(xv)Polarization analysis in SWNTs can be used to assign the G band mode symmetries.

##### 6.2. The G′ Band

The band is the second-order sp^{2} Raman signature, observed for all sp^{2} carbons as a peak (or a multipeak feature) in the range of 2500–2800 cm^{−1} (see Figure 5), changing with . The band properties can be summarized as follows.(i)The frequency appears at 2700 cm^{−1} for eV, but its frequency changes by changing . Its dispersion is (/) 90 cm^{−1}/eV for monolayer graphene, and this dispersion changes slightly by changing the sp^{2} nanocarbon structure. The sensitivity of to the detailed sp^{2} structure makes this band a powerful tool for quantifying the number of graphene layers and the stacking order in few-layer graphenes and graphite, and for characterizing SWNTs by the diameter and chiral angle dependence of and the band intensity.(ii)The band depends on the number of graphene layers: one-layer graphene (1LG) exhibits a single Lorentzian peak in the band, and the intensity of the band is larger (24 times) than that of the G band in 1LG. In contrast, 2LG with AB Bernal stacking exhibits four Lorentzian peaks in the band, and the intensity of the band with respect to the G band is strongly reduced (same magnitude or smaller). For 3LG with AB Bernal stacking, 15 scattering processes are possible for the band, but the 15 peaks occur close in frequency and cannot all be distinguished from each other. Usually the band from 3LG is fitted with 6 peaks. Highly oriented pyrolytic graphite (HOPG) exhibits two peaks. Turbostratic graphite exhibits only a single peak, and care should be taken when assigning the number of layers based on the feature. The single peak in turbostratic graphite is slightly blueshifted (~8 cm^{−1}) from the peak in 1LG.(iii)While HOPG (considered as a three-dimensional structure) exhibits a two-peak G′ feature, turbostratic graphite (no AB Bernal stacking order and considered as a two-dimensional structure) exhibits a single Lorentzian line. Therefore, the single- versus double-peak G′ structure can be used to assign the amount of stacking order present in actual graphite samples.(iv)By changing , it is possible to probe different electrons and phonons in the interior of the Brillouin zone, according to the double-resonance model. The band probes the iTO phonons near the K point, where the strongest electron-phonon coupling occurs.(v)The feature can be used to assign and type doping in graphene and SWNTs. A blueshift (redshift) is observed for () doping. The magnitude of the shift depends also on the specific type of doping atom, while the relative intensity between doped and undoped pristine band peaks can be used to obtain the dopant concentration.(vi)Carbon nanotubes show a very special band feature, where the number of peaks and their frequencies depend on () due to both curvature-induced strain and the quantum confinement of their electronic and vibrational structures. The resonance condition is restricted to , and this fact gives rise to a dependence on the SWNT diameter and chiral angle.

##### 6.3. The D Band

The D band is the dominant sp^{2} Raman signature of disorder (or defects). It is observed as a peak in the range of 1250–1400 cm^{−1} (see Figure 5), and it is related to the breathing of the carbon hexagons (see eigenvector in Figure 4). The D band properties can be summarized as follows.(i)The D band frequency appears at 1350 cm^{−1} for eV, but its frequency changes by changing . Its dispersion is cm^{−1}/eV for monolayer graphene, and it changes slightly by changing the sp^{2} nanocarbon structure. For SWNTs, the frequency depends on the nanotube diameter as well.(ii)The D band intensity can be used to quantify disorder. The effect of nanocrystallite size and Ar^{+} bombardment dose has been used to characterize the disorder in both SWNTs and graphene, and a phenomenological model has been developed for explaining the D band intensity evolution with the amount of disorder.(iii)Being disorder related, the D band linewidth can change from 7 cm^{−1} (observed for isolated SWNTs) to a hundred wavenumbers (for very defective carbon materials).(iv)The D band scattering is forbidden at edges with zigzag structure. This property can be used to analyze the edge structure and to distinguish zigzag from armchair edges.(v)Because absolute intensity measurement is a difficult task in Raman spectroscopy, the normalized intensity ratio is largely used to measure the amount of disorder. This ratio depends not only on the amount of disorder, but also on the excitation laser energy, since , while I_{D} is independent (when measured in the 1.9–2.7 eV range).(vi)Since the D band is activated by defects, it can only be observed near the defect within a coherence length . The D band was used to obtain nm for ion-bombarded graphene measured with = 2.41 eV.

##### 6.4. The Radial Breathing Mode (RBM)

The radial breathing mode (RBM) is the Raman signature for the presence of carbon nanotubes, related to the “tube-breathing-like” motion. The RBM is observed as a peak (or a multipeak feature) in the 50–760 cm^{−1} range (see Figure 5). The RBM properties can be summarized as follows.(i)The depends on diameter (), according to , where (nm^{−2}) probes the effect of the environment on .(ii)The is predicted to depend on SWNT diameter and , while the dependence of on the chiral angle is rather weak, even for SWNTs with nm, where the dependence of reaches a few wave numbers.(iii)For a given SWNT, the RBM peak intensity I () is a function of due to resonance effects with the one-dimensional van Hove singularities. The RBM is intense when the incident light () or the scattered light () is in resonance with the SWNT optical transition energies .(iv)The optical transition energies can be obtained using resonance Raman spectroscopy. The theoretical description depends on an accurate analysis of the nanotube structure, exciton effects, and dielectric screening.(v)The electron-photon and electron-phonon matrix elements for the RBM intensity, as well as the resonance broadening factor , strongly depend on ().(vi)The RBM is a totally symmetric mode. The polarization dependence is dominated by the antenna effect, where a strong Raman signal is observed when both the incident and scattered lights are chosen along the tube axis.(vii)The same inner () tube within a double wall-carbon nanotube (DWNT) can exhibit different values if surrounded by different outer () tubes.(viii)Usually in the RBM, linewidth is in the range of 3 cm^{−1}, although it can reach much larger values (by one order of magnitude) due to environmental effects, or smaller (also by as much as one order of magnitude) when measured for the inner tube of a DWNT and at low temperature.(ix)Due to the relatively low RBM frequency, changes in with temperature, doping, strain, and other such effects are less pronounced in the RBM than in the from the G band. However, the RBM becomes important when looking for the effects on one single () specie among many SWNTs, since the RBM feature is unique for each () ( depends strongly on tube diameter), while the G band appears within the same frequency range for most SWNTs (weak dependence).(x)As discussed above, changes in temperature, pressure or the dielectric constant of the environment do not change significantly. However, these factors do change , and changing the resonance condition changes the RBM intensity. Therefore, the RBM can be used to probe resonance effects sensitively, and for understanding the importance of excitonic effects for a theoretical description of the observed Raman spectra. Increasing the temperature decreases , and the temperature-dependent change in also depends on (). Increasing the pressure changes , and the pressure-dependent changes in also depend on (). Here a change in can be positive or negative, depending on and on the type. Increasing the dielectric constant of an SWNT-wrapping agent decreases .(xi)The Stokes versus anti-Stokes (S/aS) intensity ratio for the RBM features is strongly sensitive to the energy displacement of with respect to .

#### 7. Pushing the Limits of Raman Spectroscopy Applications on sp^{2} Nanocarbons

The state-of-the-art experiments are pushing the limits of Raman spectroscopy and its applications to carbon nanoscience.

The ability to perform nanomanipulation and Raman spectroscopy is important for a well-controlled study of intrinsic and extrinsic properties of nanostructures. Superlattice graphene structures can be generated in bilayer graphene, by inducing a mismatch angle between the top and bottom layers [62–66] (see the left part of Figure 6). Such graphene superlattices can be formed by nanomanipulation, for example, by folding graphene into itself with an atomic force microscopy (AFM) tip [67].

The superlattice formation was recently shown to activate new Raman modes from the interior of the graphene phonon Brillouin zone [67–70], as a new type of multiple-resonance phenomena in sp^{2} nanocarbons. Different from what was discussed in Section 5, here the modulation in the superlattice, which is characterized by a momentum (see right part of Figure 6), will generate the momentum required for momentum conservation in the multiple-resonance scattering mechanism [67]. Alternatively one could say that in the superstructure, the interior of the Brillouin zone is folded into the point, which is equivalent. Specific generates specific Raman frequencies that will appear resonantly in the Raman spectra when the right is used. These new features have been called R′ (from “rotation”) when related to a double-resonance intra-valley process (, like in Figure 6), appearing above the G band frequency, and when related to a double-resonance inter-valley process (, not shown here), appearing below the G band frequency [67].

Furthermore, the G band intensity in graphene superlattices was shown to exhibit a large intensity enhancement for specific combined values of and excitation laser energy [71–73]. This effect happens due to resonance achieved with the new van Hove singularity (vHS) that appears in the electronic joint density of states due to the superstructure formation. In this case, the unusual enhancement is not due to multiple-resonance effects, but rather due to achieving resonance with a specific energy where the density of electronic states is unusually large (the vHS). This new result shows that Raman spectroscopy can probe the changes in the electronic structure due to the superlattice formation.

Another example of recent experiments where nanomanipulation has been combined with Raman spectroscopy was developed in carbon nanotubes. Raman spectroscopy has been broadly used to study effects caused by strain, majorly focusing on the G band behaviour on SWNT bundles [74–80]. Combination of AFM with confocal Raman spectroscopy was made to follow, *in situ*, the evolution of the SWNT structure with transversal pressure applied to the tube. The G band feature in isolated SWNTs deposited on a substrate was monitored while pressing the tube with the AFM tip [81].

The G band, which is related to two phonon branches degenerated at the point (see phonon dispersion in Figure 3), splits in SWNTs due to the tube curvature (see G^{+} and G^{−} in Figure 5). In achiral SWNTs, the G band splits into LO and TO modes, where longitudinal and transversal here stand for parallel and perpendicular to the tube axis. The experiments performed on isolated SWNTs [81] evidenced a previously elusive and fundamental symmetry-breaking effect for the totally symmetric TO G-band mode, which exhibited two distinct Raman-active features with increasing applied pressure. One of the features is related to atomic motion localized at the flattened regions, while the other feature is related to atomic motion localized at the curved regions of the ovalized SWNT.

However, different SWNTs showed different G^{+} and G^{−} band behaviours. For example, in one case, rather than the TO (G^{-}) splitting discussed in the previous paragraph, the observed effect was the increase in the splitting between the G^{+} and G^{−} modes in SWNTs, indicating in that case that the LO versus TO nature was not identified. This result is expected for chiral SWNTs, where the C–C bonds exhibit a helical structure, and the LO versus TO nature for the two G band peaks is indeed not expected. These results showed the richness of transversal deformation at the isolated SWNT level [81], which are averaged out on SWNT bundle measurements.

Besides the ability to perform nanomanipulation and Raman spectroscopy experiments to perform detailed studies, another advance is the multitechnique approach, which is important for the development of nanometrology. Generally speaking, for the development of accurate Raman-based analysis, systematic calibration procedures are necessary. One way is making use of a microscopy technique to independently quantify any specific effect that will be further probed with Raman spectroscopy.

Combined Raman spectroscopy, ion bombardment, and scanning tunnelling microscopy (STM) were applied to study the evolution of peak frequencies, intensities, linewidths, and integrated areas of the main Raman bands of graphene, as a function of ion bombardment dose [82, 83]. The main effects are displayed in Figure 7. On the left side of Figure 7, one sees three STM images of the sp^{2} carbon surfaces before ion bombardment (pristine), after 10^{11} Ar^{+}/cm^{2} ion dose, and after 10^{14} Ar^{+}/cm^{2}. Point defects appear for the low ion dose, and amorphization of the graphene surface takes place for the larger ion dose. On the right side of Figure 7, the respective Raman spectra for the graphene samples at the same ion bombardment levels are shown. For pristine graphene, only the G band is observed. For defective graphene, the D and peaks appear. Large bombardment ion dose generates high level of disorder, and the respective Raman spectrum becomes typical of amorphous carbon, marked by broad bands (compare with the bottom spectrum in Figure 5).

Systematic work was developed for calibrating the intensity ratio between the D and G peaks (I_{D}/I_{G}) in graphene as a function of ion dose, and this is reported in [82, 83]. The Raman relaxation length for the disorder-induced Raman scattering process in graphene was also established in these experiments, and 2 nm [82] was found, a value that is at least 10 times more accurate than the values previously published in the literature [84, 85]. This work was extended to study the effect of low-energy (90 eV) Ar^{+} ion bombardment in graphene samples as a function of the number of layers [86, 87]. In sequence, the dependence on the excitation laser energy , already established for nanographite [88, 89], was extended to point defects in graphene [90], thus providing a formula for quantifying the amount of defects in graphene for any excitation laser energy.

The multitechnique approach has also been used in the development of nanometrology on single-wall carbon nanotubes (SWNTs). The Raman spectra from the radial breathing modes (RBMs) have been largely used to give information about the diameter distribution in the samples [2, 9]. However, it is known that the Raman cross-section itself depends strongly on the tube diameter, mostly due to the diameter dependence on the excitonic effects [57]. Pesce et al. [91] used a high-resolution transmission electron microscopy (HRTEM) protocol to measure the SWNT diameter distribution in a bundles sample and compared the results with the RBM resonance Raman map. This procedure was used to calibrate the diameter dependence of the RBM Raman cross-section, thus establishing a method for accurate determination of the diameter distribution in an SWNT sample using Raman spectroscopy [91].

As can be seen here, the nanoscience and nanometrology of Raman spectroscopy applied to sp^{2} nanocarbons are maturing. Consequently, the Raman spectroscopy is now being applied to develop cross-related fields. Basically, wherever sp^{2} carbon nanostructures are used, the Raman scattering can help detecting and characterizing. Spectral imaging can be used to detect and locate the sp^{2} nanocarbons inside biological materials, for example, while Raman frequency shifts indicate and quantify carbon-environment interactions.

One example of application in biotechnology: different studies have evaluated the ability of SWNTs and multiwall carbon nanotubes (MWNTs) as transfection agents to deliver gene materials [92–95]. Ladeira et al. [96] demonstrated highly efficient RNA delivery system into human and murine cells using MWNTs. They applied a G band MWNT confocal imaging to demonstrate the presence of MWNTs inside neonatal cardiomyocytes, confirming the ability of MWNTs to enter this cell.

Another example is the study of soil sciences: the carbon materials found in specific sites in the Amazonian forest, where Indians subsisted on agriculture in addition to hunting, fishing, and gathering activities [97]. Their way of life generated areas of highly fertile soils, rich in plant nutrients, known as “*Terra Preta de Índio*” (Amazonian Dark Earth) [98–103]. This phenomenon is more frequent in the Amazon, but it can also be found in other regions of South America and Africa [104, 105]. The soil recalcitrance is known to be due to a large amount of stable carbons in these soils, which are responsible for their black colour.

In sp^{2} nanocarbons, Raman spectroscopy has been used to measure the nanocrystallite graphite dimensions, which are defined by the in-plane crystallite size () [11, 88, 89, 106, 107]. One way of doing it is to correlate the G band linewidth with , as accurately developed by Cançado et al. [88, 89]. This protocol was used to elucidate the nanostructure of the stable carbon materials found in the “*Terra Preta do Índio*,” which were shown to be majorly sp^{2} nanocarbons [108]. The results were then compared with results obtained in charcoal samples, which are being used in attempts to reproduce the “*Terra Preta do Índio*” soil. Under the Raman spectroscopy analysis, the crystallite size distribution was found to be in the 3–8 nm range in the “*Terra Preta do Índio*” sp^{2} nanocarbons, while in commonly produced charcoal, it was found as typically between 8 and 12 nm. This provides imputes from nanotechnology, based on Raman spectroscopy [108], for the development of new routes to generate a nanocarbon structure that would be suitable for the generation of stable and highly productive soils in the humid tropics, similar to the “*Terra Preta do Índio*.”

#### 8. Conclusion

In conclusion, Raman spectroscopy is already established as a powerful tool to characterize the different types of sp^{2} carbon nanostructures, for the development of nanoscience and nanometrology. Here, the rather rich Raman spectra of sp^{2} nanocarbons, composed by many peaks induced by single- and multiple-resonance effects, were discussed in depth. The properties of the main Raman peaks were described, including their dependence on both materials structure and external factors, like temperature, pressure, doping, and the environment.

This knowledge can be used as a guide for the use of Raman spectroscopy to characterize sp^{2} nanocarbons, and recent applications are already pushing the limits of the technique, in graphene superlattices, for example, but also connecting Raman spectroscopy to other fields where the sp^{2} nanocarbons are being utilized, like biotechnology and soil science.

Furthermore, the study of new materials is always a challenge that promises important new findings. New carbon nanostructures, like nanocones, which hold strong promises of several interesting mechanical, thermal, and electronic properties, have been addressed mostly theoretically [109–112]. Carbon nanocones are likely to find in Raman spectroscopy a key development technique starting point. Another route is using the knowledge on graphene to study other few layer materials, like MoS_{2} and BN [113–115]. Raman spectroscopy is likely to play an important role in such explorations as well.

A challenge for a big step forward on the potential of Raman spectroscopy for developing even further nanoscience and nanometrology lies in the tip-enhanced Raman spectroscopy (TERS) technique. However, the high resolution (~10 nm) instrumental setups are still at the home-built development stage, and severe instrumental work is still needed for achieving reliable results. The main challenge for TERS is the development of new and robust instrumentation for achieving a ready-to-use system. TERS in sp^{2} nanocarbons started focusing on experimental work [23–30], but recently theoretical studies are appearing in both one-dimensional (SWNTs) [116] and two-dimensional (graphene) [117] materials, thus guiding the way for future developments.

#### Acknowledgments

The author acknowledges many colleagues and students who have been working on the Raman spectroscopy of sp^{2} nanocarbons. This work has been supported by CNPq (under *Rede Brasileira de Pesquisa e Instrumentação em NanoEspectroscopia Óptica* and *Universal* grants) and by FAPEMIG (under *Núcleo de Pesquisa em Aplicações Biotecnológicas de Nanomateriais de Carbono* and *Programa Pesquisador Mineiro* grants).

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