ISRN Physical Chemistry

Volume 2013, Article ID 487485, 11 pages

http://dx.doi.org/10.1155/2013/487485

## Structure of Carbonic Layer in Ohmic Contacts: Comparison of Silicon Carbide/Carbon and Carbon/Silicide Interfaces

^{1}Department of Characterisation of Nanoelectronic Structures, Institute of Electron Technology, Al. Lotników 32/46, 02-668 Warsaw, Poland^{2}Department of Photochemistry and Spectroscopy, Institute of Physical Chemistry, Polish Academy of Sciences, Kasprzaka 44/52, 01-224 Warsaw, Poland^{3}Diagnostic Center, V. Lashkaryov Institute of Semiconductor Physics, NAS of Ukraine, Pr. Nauky 45, 03028 Kiev, Ukraine^{4}Laboratory of Growth and Physics of Low Dimensional Crystals, Institute of Physics, Polish Academy of Sciences, Al. Lotników 32/46, 02-668 Warsaw, Poland^{5}Department of Micro- and Nanotechnology of Wide Bandgap Semiconductors, Institute of Electron Technology, Al. Lotników 32/46, 02-668 Warsaw, Poland

Received 28 October 2012; Accepted 3 December 2012

Academic Editors: J. G. Han and S. Yang

Copyright © 2013 Paweł Borowicz 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

The structure of carbonic layer in three samples composed of 4H polytype of silicon carbide and the following sequence of layers: carbon/nickel/silicon/nickel/silicon was investigated with Raman spectroscopy. Different thermal treatment of the samples led to differences in the structure of carbonic layer. Raman measurements were performed with visible excitation focused on two interfaces: silicon carbide/carbon and carbon/silicide. The results showed differences in the structure across carbon film although its thickness corresponds to 8/10 graphene layers.

#### 1. Introduction

Silicon carbide (SiC) is known as an excellent material for fabrication high-power, high-frequency, and high-temperature electronic devices due to its properties like: good thermal conductivity, high critical electric field, and simple method of dielectric layer fabrication [1, 2]. Formation of ohmic contacts with low specific resistance is an important aspect in application of silicon carbide [3]. This fabrication is realized by deposition of metallic layer on the substrate surface followed by thermal treatment at high temperature [4, 5]. Nickel is probably the most popular metal used in technology of ohmic contact formation, because the contacts formed with its application have specific contact resistance equal to ~10^{−6} Ω cm^{2} [4]. The interaction of carbonic structures with the SiC substrate was investigated with X-ray photoelectron spectroscopy and Raman scattering [6]. The properties of the ohmic contact are determined by concentration of graphitic nanoflakes formed during the annealing procedure. The initial structure of carbon film has no impact on properties of the formed contact [6, 7]. In previous work, structural and electrical properties of different Ni- and Ni/Si-based contacts to silicon carbide were investigated [8]. Reported structural data obtained by various experimental techniques like X-ray diffraction (XRD), Rutherford Backscattering Spectrometry (RBS), and Secondary Ion Mass Spectrometry (SIMS) showed that optimal metallization sequence for manufacturing ohmic contacts is Ni/Si/Ni/Si. The thicknesses of each layer should provide optimal conditions for creation of Ni_{2}Si silicides.

This paper focuses the attention on structural properties on different sides of thin carbon film introduced between SiC substrate and nickel/silicon/nickel/silicon sequence of layer. Since thermal treatment at high temperature results in SiC decomposition, new carbon atoms appear at the interface between silicon carbide substrate and deposited carbonic layer. Decomposition of silicon carbide leads up to creation of carbon structures with preferred ABC stocking order [9]. Annealing above 800°C results in structural changes in carbon structure and migration of carbon atoms towards free silicide surface.

The main topic discussed in this work is the comparison of the structure observed for carbon layer at different sides: SiC/C interface and C/Ni_{2}Si interface. As an experimental technique, Raman spectroscopy was chosen. Due to large penetration depth of visible light into silicide layer and silicon carbide substrate, it was possible to observe Raman spectra excited from both sides of carbon film introduced between Ni/Si/Ni/Si sequence and SiC substrate.

#### 2. Experimental

##### 2.1. Samples

The preparation of the samples was already described in the paper concerning visible and ultraviolet Raman study of carbon properties in ohmic contacts [10].

The samples will be called hereafter *nsc1_2* (temperature of the second annealing step 800°C), *nsc1_3* (temperature of the second annealing step 950°C), and *nsc1_1* (temperature of the second annealing step 1000°C).

##### 2.2. Apparatus and Experimental Conditions

Raman scattering was measured with MonoVista 2750i micro-Raman confocal spectrometer (Spectroscopy and Imaging GmbH, Germany). The microscopic part was based on Olympus BX51 microscope. The images from microscope were recorded with TM 2040GE imaging camera (JAI, Japan). Motorized stage (Märzhauser GmbH, Germany) allowed sample positioning with accuracy equal to 100 nm in , , and directions. The positioning mechanism worked in feedback loop in order to stabilize the position of the stage. Spectral part of the MonoVista was based on Princeton Instruments spectral devices: spectrograph SpectraPro 2750i (focal length 750 mm) and spectral nitrogen-cooled CCD camera LN/2048 × 512B/I UVAR, Spec-10 System with maximum efficiency at 250 nm.

As an excitation light, the Ar^{+} laser INNOVA 90C (Coherent, USA) line ( nm) was used. The power of laser light on the sample was below 1 mW in order to avoid thermal effects caused by focused laser light. The grating with 1800 lines/mm and blazed for visible spectral range was used to measure Raman spectra. Two types of excitations were used: through the silicide layer, hereafter called also *top* excitation, and through SiC substrate, hereafter called also *bottom* excitation. Although confocal configuration strongly reduced signal generated outside the focal plane *bottom*, excitation introduces strong component of two-phonon scattering from 4H-SiC. Huge difference between thickness of SiC substrate and carbon film (~1 mm versus 3 nm) caused large signal from 4H-SiC substrate placed outside focal plane. In order to separate Raman scattering generated by carbon layer from two-phonon SiC background, two measurements were necessary to get “pure” spectrum of carbon layer. The first measurement was taken from the area covered with carbon layer and the second one outside of this area. The “pure” carbon spectrum was calculated by subtraction of two-phonon SiC spectrum measured outside of the covered area from the spectrum collected from area covered with carbon and silicide layers. In order to obtain good signal-to-noise ratio, long irradiation time, about 1 hour, was applied for measurement of single spectrum.

##### 2.3. Spectra Analysis

The spectra were mathematically processed before analysis and interpretation. Mathematical treatment included offset removal, baseline correction, smoothing, and normalization. Measured spectra were normalized to unity. The procedure used to calculate pure carbon spectra from *bottom* excitation measurements was similar to the procedure used in the study of carbon inclusions at SiC/SiO_{2} interface [11].

#### 3. Results

Raman spectra measured with visible excitation ( nm) and irradiation through the silicide layer are presented in: Figure 1(a)—data obtained for *nsc1_2*, Figure 1(b)—for *nsc1_3*, Figure 1(c)—*nsc1_1*.

The main plot of each panel shows the experimental data together with fitted Gaussian profiles. The upper inset in each panel compares experimental points with fitted function (the sum of Gaussian profiles used to reconstruct the experimental data). The lower inset presents autocorrelation function which attests to quality of fitting procedure. The maxima of Gaussian profiles fitted to experimental data are given in the main plot of each panel. Random distribution of points around zero level in autocorrelation function bears testimony to the quality of fitting procedure. Qualitative description of the spectra measured for *top* excitation was already presented in the paper comparing visible and deep-ultraviolet Raman investigation of these samples, and it will be not repeated here in details [10]. The main difference between the results presented here and in [10] is the number of profiles necessary for reconstruction and bands in the case of samples *nsc1_3* and *nsc1_1*. In [10], one Lorentzian component was sufficient to reconstruct each band, whereas, here, two Gaussian profiles are necessary. The detailed description of the results obtained from mathematical analysis performed in this work will be reported in the part *Discussion*.

Subtracted spectra obtained from *bottom* excitation are presented in Figure 2. The data in Figure 2 are presented in the same way as in Figure 1. It means that the main plot of each panel shows experimental points and Gaussian profiles used in fitted function, upper inset compares the whole fitted function with experimental data, and lower inset presents the autocorrelation function. The maxima of Gaussian profiles are given in the main plot of each panel. In the case of each sample, different numbers of Gaussian profiles are necessary to reconstruct the course of experimental points. Four profiles are necessary to reproduce the shape of the subtracted spectrum in the case of *nsc1_2*, for *nsc1_3*, as many as seven profiles are necessary and for *nsc1_1*, six. The detailed discussion of the mathematical analysis will be presented in next the part of this paper. In this chapter, the description of the spectra is limited to qualitative discussion of its main features. Two strong bands are present in the spectrum of each sample. The maximum of the first one is placed between about 1520 cm^{−1} and about 1540 cm^{−1}. The maximum of the second band appears between 1580 cm^{−1} and 1610 cm^{−1}. Maximum position of the first band is correlated with amorphous carbon (*a*-C) [12, 13]. The position of the second observed band is typical for band reported for different types of graphite. Maximum placed slightly above 1600 cm^{−1} and obtained here for *nsc1_2* and *nsc1_3* subtracted spectra is a typical trace of nanocrystalline graphite [12, 13]. The maximum shifted to lower values of Raman shift and placed between 1580 cm^{−1} and 1590 cm^{−1} in the case of *nsc1_1* is reported in the literature for graphite in crystalline form [12, 13]. To sum up, for the first look, Raman spectra of carbon layer observed from the side of silicon carbide substrate can be assigned to the mixture of *a*-C with different forms of graphite. The type of graphite component seems to be dependent on the temperature applied in the second step of thermal treatment.

The spectra measured for band are presented in Figure 3(a) showing data obtained for *nsc1_3*, Figure 3(b) and for *nsc1_1*. In the case of *nsc1_2* sample, the signal in this range of Raman shift was too small to distinguish unequivocally band [10]. The convention used in Figure 3 is the same as in Figures 1 and 2. The main plot of each panel presents experimental points together with fitted Gaussian profiles. The maxima of the profiles are given in the plot. Upper inset compares experimental points with fitted function, and lower inset presents autocorrelation function as a certificate of fitting quality. The qualitative description of the spectra was presented earlier [10], and it will be not repeated here in detail. Briefly, band observed for *nsc1_3* has slightly larger FWHM than the band recorded for *nsc1_1*. The band observed for *nsc1_1* has the red side slightly shifted towards higher frequencies. The detailed discussion of mathematical analysis will be presented in the next part.

#### 4. Discussion

The list of Raman bands found with application of mathematical analysis in spectra excited through the silicide layer is presented in Table 1. Each band is characterized by maximum position, half width FWHM, and relative intensity. The last column of the table contains proposed assignment of the band. The carbon layer in samples from *nsc1_ * series has no uniform, ideal crystal structure but is composed of graphite domains. In such a case, measured Raman spectra contain the information about structures with crystallographic parameters scattered around the main values. Reliable information about the intensity of the main crystalline structure is derived from the height of the fitted profile and not from the area under the curve [12]. Because of this, the intensities given in this work are determined from the heights of fitted Gaussian functions. In the case of each sample presented in Table 1, intensities are normalized to the height of the profile reproducing band. For samples *nsc1_1* and *nsc1_3*, for which two Gaussian functions are necessary for reconstruction of band, the profile with smaller FWHM is taken as reference.

Three Gaussian components are necessary for reconstruction of Raman spectrum measured for *nsc1_2*. The first and third ones reproduce and bands. Their maxima positions and FWHMs are close to those which were reported for the model based on Lorentzian functions [10]. The maxima positions and FWHM values are typical for nanocrystalline graphite. The intensity ratio is here slightly larger in comparison to the value reported for Lorentzian-based model [10]. In particular, the values of intensity ratio presented here and in [10] are equal to 1.29 and 1.16, respectively. The second Gaussian component of fitted function has the maximum at 1533 cm^{−1}, large FWHM equal to about 360 cm^{−1}, and the intensity much lower than band (0.16). The maximum of this component corresponds with the data reported for *a*-C. Also, the large value of FWHM is typical for this kind of carbon structure [13]. For example, fused and bands observed for carbon films deposited by supersonic cluster beam spread form about 1000 cm^{−1} to about 1650 cm^{−1} [14].

The reconstruction of band observed for samples *nsc1_3* and *nsc1_1* requires two Gaussian functions for each sample. In the case of each sample, the pair of Gaussian functions has similar properties. One component has the maximum placed at about 1355 cm^{−1} and FWHM equal to about 30 cm^{−1}. The relative intensity of this component decreases about two times from *nsc1_3* to *nsc1_1*; in particular, it is equal to 1.29 and 0.68 for *nsc1_3* and *nsc1_1*, respectively. The decrease of normalized intensity between *nsc1_3* and *nsc1_1* shows the increase of graphitization degree between the samples. The other type of Gaussian function has the maxima shifted towards larger values of Raman shift. The positions are equal to about 1363 cm^{−1} and 1361 cm^{−1} for *nsc1_3* and *nsc1_1*, respectively. The FWHM values obtained for this type of Gaussian functions are about twice larger than the corresponding parameters obtained for previously described “narrow” profiles. The values are equal to about 76 cm^{−1} and 68 cm^{−1} for *nsc1_3* and *nsc1_1*, respectively. The normalized intensities are in the case of these “broad” profiles similar and they are equal to 0.69 and 0.59 for *nsc1_3* and *nsc1_1*, respectively. The requirement to use two Gaussian function for band reconstruction can be associated with difference in the structure of carbon layer along its thickness. Comparison of Figures 1 and 2 shows differences in crystalline structure of carbon layer observed for *top* and for *bottom* excitations. It means that the crystalline structure of the layer should change across this layer. The “narrow” Gaussian component in Raman spectra recorded for samples *nsc1_3* and *nsc1_1* describes this part of the layer which has regular graphite structure. The “broad” profile corresponds to structures which have the crystalline parameters scattered around the mean values. This distribution of crystalline parameters is reflected in relatively large FWHM equal to about 70 cm^{−1}. The hypothesis that “broad” Gaussian function in band reproduces this part of Raman spectrum which is generated by structures with scattered structural parameters is supported by the reconstruction of band. In the case of samples *nsc1_3* and *nsc1_1*, three Gaussian functions are necessary for proper reconstruction of band. The third profile has the maximum at about 1622 cm^{−1} and 1620 cm^{−1} for *nsc1_3* and *nsc1_1*, respectively. The FWHM values of this band are equal to about 23 cm^{−1} and 32 cm^{−1} for *nsc1_3* and *nsc1_1*, respectively. Normalized intensities of these Gaussian functions are equal to 0.36 and 0.28 for *nsc1_3* and *nsc1_1*, respectively. This band originates mainly from structure with double C=C bonds in the case of *nsc1_3* and from nickel-graphite intercalated compounds (NiGICs) in the case of *nsc1_1*. Details of this assignment were already discussed [10]. Two remaining Gaussian functions form the pair consisting of “narrow” and “broad” components similar to the pair of functions reconstructing band. The “narrow” components have the maxima placed at about 1591 cm^{−1} and 1587 cm^{−1} for *nsc1_3* and *nsc1_1*, respectively. The corresponding values of FWHM are equal to about 40 cm^{−1} and 26 cm^{−1}. The “broad” Gaussian components have the maxima placed at about 1582 cm^{−1} and 1586 cm^{−1}, and corresponding FWHM values are equal to about 113 cm^{−1} and 78 cm^{−1} for *nsc1_3* and *nsc1_1*, respectively. The normalized intensities of “broad” components are equal to 0.70 and 0.50 for *nsc1_3* and *nsc1_1*, respectively. The FWHM observed in the case of both components (“narrow” and “broad”) is smaller for *nsc1_1* in comparison with *nsc1_3*. This decrease suggests larger homogeneity of carbon layer in the case of *nsc1_1*. Both components can be interpreted as band in particular,(i)“narrow” component can be associated with regular graphite structure;(ii)“broad” component is generated by structures with crystallographic parameters scattered around mean values.

The maxima positions obtained for “narrow” components have larger values in comparison with maxima of “broad” structures contributing to band. The maximum of band reported for ABA stacking order is shifted towards larger frequencies in comparison with the maximum of this band in the case of ABC stacking order [15]. One can expect the dominance of ABA stacking order in “narrow” component and ABC stacking order in “broad” one [10]. The carbon layer with ABC stacking order appears in the vicinity of SiC/C interface due to interaction between silicon carbide substrate and carbon layer [9]. Therefore, the structures contributing to the “broad” components of and bands should be placed near SiC substrate, and “narrow” components of and bands should be generated in the part of carbon layer placed in the vicinity of silicide layer.

The last band given in Table 1 has the maximum at about 1784 cm^{−1}, FWHM equal to about 90 cm^{−1}, and very weak intensity equal to about 6% of the intensity obtained for the “narrow” component of band. It was found in the spectrum of *nsc1_3* only. The band is placed in the range of Raman shift where out-of-plane vibrational modes of graphite are reported in the literature [16]. In particular, the best correlation of the maximum band is with the position of so-called band [17]. This band was assigned to the overtone of out-of-plane Transverse Optical (*2oTO*) mode [18]. The other reported in the literature, carbon band placed in the vicinity of 1784 cm^{−1}, is assigned to benzene-related vibrations [19, 20]. It has the maximum at about 1740 cm^{−1}. The correlation of the band centred around 1784 cm^{−1} with the combination of in-plane Transverse Acoustic (*iTA*) and Longitudinal Optical (*LO*) modes: *iTALO* band (maximum at about 1860 cm^{−1}) [21] or band reported for cumulene vibrations (maximum at about 1980 cm^{−1}) [14] is much worse.

The parameters of bands found in subtracted spectra of *nsc1_1*, *nsc1_2*, and *nsc1_3* samples (*bottom* excitation) are given in Table 2. As in Table 1, each band is characterized by maximum position, FWHM, and normalized intensity. As a reference, the intensities of bands assigned to *a*-C were chosen, because this type of band was found in subtracted spectra of all samples. The last column of Table 2 contains proposed assignment. The main common feature observed for all samples was assigned to *a-*C [22]. The maxima of this band are placed at ~1525 cm^{−1}, ~1537 cm^{−1}, and ~1518 cm^{−1} for *nsc1_2*, *nsc1_3*, and *nsc1_1*, respectively. Corresponding FWHMs are equal to about 59 cm^{−1}, 66 cm^{−1}, and 39 cm^{−1}. The *a*-C layer placed at the interface of SiC was already observed with cross-sectional transmission electron microscopy in the case of thermal decomposition of 4H-SiC [23]. The *a*-C layer observed for all samples in present study appears probably due to 20% in-plane lattice mismatch between 4H-SiC and graphite combined with 60%/ 80% in-plane expansion mismatch reported for silicon carbide and graphite at SiC/graphite interface [23].

The bands placed between 1370 cm^{−1} and 1400 cm^{−1}, in particular:(i)for *nsc1_2* maximum at ~1394 cm^{−1};(ii)for *nsc1_3* maximum at ~1397 cm^{−1};(iii)for *nsc1_1* maximum at ~1378 cm^{−1},

are assigned to type of vibration responsible band. Typical position of the band maximum is equal to about 1350 cm^{−1} [12, 24–26]. In the case of structures like carbon nanotubes, the maximum position of band is expected in the range of Raman shift between 1250 cm^{−1} and 1450 cm^{−1} [27]. In carbon films, the position of band maximum was reported as equal to about 1380 cm^{−1} [19]. The band with maximum at about 1319 cm^{−1} corresponds to the data reported for cubic diamond [28]. This kind of carbon structure is formed form graphite which has ABC stacking order. Such a type of graphite is preferentially formed in the process of thermal decomposition of silicon carbide [9]. This kind of diamond can be formed under low pressure in the presence of nickel which plays a role of catalyst in formation of cubic diamond [28]. The activation barrier of diamond formation form graphite is slightly lower for cubic form of diamond than for hexagonal type [28]. The correlation of the maximum 1319 cm^{−1} with band reported for carbon nanotubes is much worse [29]. The changes of Raman spectra recorded for *bottom* excitation for samples *nsc1_2*, *nsc1_3*, and *nsc1_1* in the range below 1400 cm^{−1} can be summarized in the following way. Thermal treatment at 800°C applied to *nsc1_2* sample results in formation of structures generating band with maximum at 1394 cm^{−1}. The maximum of the band is shifted towards higher frequencies in comparison with typical position of band equal to about 1350 cm^{−1}. The reason for this shift is probably the interaction with nitrogen used for doping of the substrate [10]. Such kind of shift resulting from interaction with nitrogen was already reported for carbon film deposited on silicon substrate [30, 31]. Increase of the temperature in second step of thermal treatment of the samples up to 950°C [10] results in formation of cubic diamond-like structures observed as a weak band with maximum at 1319 cm^{−1} in *nsc1_3* subtracted Raman spectrum. Further increase of the annealing temperature up to 1000°C causes the graphitization of the sample. The trace of this graphitization is observed for *nsc1_1*. band obtained for subtracted spectrum is shifted towards standard position in comparison with data recorded for *nsc1_2* and *nsc1_3* samples.

The other strong band observed in the spectrum of *nsc1_2* obtained for *bottom* excitation has the maximum at about 1602 cm^{−1} and FWHM equal to about 57 cm^{−1}. These values are almost the same as parameters describing band observed for the same sample in the case of *top* excitation and are typical for spectra observed in the case of nanocrystalline graphite [13, 32, 33]. The maximum of band is shifted in the case of *nsc1_3* towards higher frequencies and is placed at about 1610 cm^{−1}. This kind of shift suggests increase of the concentration of the double C=C bonds. The maximum of Raman band associated with vibration of double C=C bonds is placed at about 1620 cm^{−1} [34]. Small band with maximum placed at about 1566 cm^{−1} in subtracted spectrum of *nsc1_3* is well correlated with data reported for carbon nanotubes and known as band [27]. In the case of *nsc1_1* sample, the second important band has the maximum placed at about 1580 cm^{−1}, which is in agreement with the position of band reported for graphite [12, 24]. The band with maximum at 1644 cm^{−1} obtained for *nsc1_1* is assigned to C=C stretching vibrations. The typical reported value 1620 cm^{−1} corresponding to double bond C=C vibration can be modified by the environment. An example of such behaviour is delivered by Raman study of liquid hydrocarbons-botryococcenes. In this type of compounds, three bands, 1640 cm^{−1}, 1647 cm^{−1}, and 1670 cm^{−1}, were assigned to C=C stretching vibrations [35]. In summary, with increase the temperature of second step of annealing process band moves to the typical position reported for graphite. In each sample, large content of C=C vibration is observed. In the case of *nsc1_3* sample also, the traces of carbon nanotubes were observed in Raman spectra excited through 4-SiC substrate.

The bands placed between about 1700 cm^{−1} and 1900 cm^{−1} can be classified as one group. In the case of the sample *nsc1_2*, only one band of this type can be recognized in this range of Raman shift. It is placed around 1707 cm^{−1}. For *nsc1_3* and *nsc1_1*, two bands appear in Raman spectra in the range 1700 cm^{−1}/1900 cm^{−1}. The maxima positions of the bands are placed at 1694 cm^{−1}, and 1795 cm^{−1} for *nsc1_3*. For *nsc1_1* the corresponding values are equal to 1710 cm^{−1} and 1792 cm^{−1}. The bands placed near 1700 cm^{−1} have the best correlation with the band assigned to the infrared active *2oTO* mode [18]. This mode has two components and . The band is of great interest in the case of structural investigation of carbon nanotubes [29]. The band is dispersive, whereas the position of maximum does not change with excitation wavelength [17]. The maxima positions of band components depend on the type of carbon structure. For example, in the case single wall carbon nanotubes (SWCNTs), the maxima of and bands are placed in ranges 1732 cm^{−1}/1744 cm^{−1} and 1755 cm^{−1}/1766 cm^{−1}, respectively [18]. The maxima positions depend on the tube diameter, and they moved towards higher frequencies with the increase of this diameter. For “planar” forms of carbon, and are shifted above 1750 cm^{−1} [17]. For example, in the case of highly ordered pyrolytic graphite (HOPG), the maxima are placed at 1754 cm^{−1} and 1775 cm^{−1} [18]. There are two other possibilities of assignment. The bands 1707 cm^{−1}, 1694 cm^{−1}, and 1710 cm^{−1} can be correlated with benzene-related vibrations. The corresponding band assigned to benzene-related vibrations in carbon films is placed around 1740 cm^{−1} [19]. The other possible assignment is concerned with bands maxima at 1795 cm^{−1} and 1792 cm^{−1}. These values are not far from the maximum of vibrations assigned to *iTALO* mode. The reported maximum of *iTALO* band is placed at about 1860 cm^{−1} [21]. The correlation with band reported for cumulene chains placed around 1980 cm^{−1} is much worse [14]. To sum up, the bands 1707 cm^{−1}, 1694 cm^{−1}, and 1710 cm^{−1} can be assigned to *2oTO* modes or benzene-related vibrations and bands 1795 cm^{−1} and 1792 cm^{−1} should be correlated with *2oTO* or *iTALO* modes.

Table 3 summarizes the features of Raman spectra measured for *nsc1_3* and *nsc1_1* with *top* excitation in the range corresponding to band. Each component is characterized by maximum position, FWHM, and normalized intensity. The intensity of the most intense Gaussian profile in the spectrum of each sample, in particular, 2704.4 cm^{−1} for *nsc1_3* and 2700.4 cm^{−1} for *nsc1_1*, was normalized to unity. The last column of the table contains proposed assignment. band appears in double resonance mechanism [36] and is susceptible to the carbon structure. For example, Raman spectrum of so-called two-dimensional graphite (without stacking order) has band which can be reproduced with single Lorentzian function centred at 2707 cm^{−1} [37]. This type of structure is called turbostatic graphite. To describe band of three-dimensional graphite with mathematical model, two Lorentzian functions are necessary [37]. They have maxima at 2687 cm^{−1} and 2727 cm^{−1}. The shape of band is very sensitive to the number of layers in graphite sample especially for so-called “few-graphene layers” [22]. In the case of graphene, band can be modeled with single Lorentzian function [22]. The band splits into multiprofile structure due to splitting of electronic band structure and interaction between “graphene” layers if the number of layers increases [38]. This splitting causes four processes contributing to band. Two of them introduce components with relatively strong intensity, while two others give a rise to weaker components. The most spectacular changes of band are observed in the case of numbers of layers below ten [39]. “Graphene bilayer” requires four Lorentzian components for proper mathematical representation of band [40]. In the case of “graphene three-layer”, it is necessary to use even six Lorentzian functions to reproduce properly the band shape [16]. The analysis of band observed for samples *nsc1_1* and *nsc1_3* suggests that carbon few-layer can be divided into two sublayers: one with dominant ABC stacking order and the other with dominant ABA stacking order. Graphite with ABA stacking order (Bernal type) shows metallic-like behaviour [41]. The rhombohedral graphite shows the properties of narrow-band semiconductor [41] which has the band-gap equal to about 6 meV around point [41]. The band-gap in -“graphene”-layer depends on the number of layers and the stacking order. For example, calculated band-gap from first principle for rhombohedral graphite changes from 18 meV to 4.8 meV if sequence and number of layers change from ABC to ABCA [42]. The four-layer with stacking order ABAC should have two band-gaps: “quasidirect” equal to 8.8 meV and secondary (around point) equal to 11.5 meV [42]. Reported values of band-gap, 4.8 meV/18 meV, correspond to the range 39 cm^{−1}/145 cm^{−1}. This range of band gap corresponds to the energy of two vibrational modes in carbon structures: and [43]. vibrational mode contributes to Raman spectrum of HOPG as weak line centred around 42 cm^{−1} [43–45]. In the case of carbon nanotubes, the reported frequency of this mode is equal to 49 cm^{−1} or 58 cm^{−1} depending on the tube diameter [44]. The mode was observed in Raman spectra of HOPG as weak line with maximum at 127 cm^{−1} [43–45].

We will adopt the concept of interacting layers to explain the origin of four Gaussian components of band. Instead of “graphene” layers, we have two graphite sub-layers with ABA- and ABC-dominant stacking orders. One has to take into account that scattering accompanied by interaction between carbon sub-layers with different stacking order requires in the energy balance the quantum related to small band-gap in part of carbon layer with dominant ABC stacking order. Let us now come back to the measured Raman spectra. The components of band recorded for *nsc1_1* and centred around 2700 cm^{−1} and 2720 cm^{−1} can be assigned to overtones “narrow” and “broad” parts of band, respectively. Similar assignment can be carried out for strong components of band (maxima 2704 cm^{−1} and 2725 cm^{−1}) observed for *nsc1_3*. Weak components with frequencies 2660 cm^{−1} for *nsc1_3* and 2642 cm^{−1} for *nsc1_1* can be assigned to overtone of “narrow” component of band shifted due to energy exchange with “broad” component of the same band. Symmetrically, the components centred around 2767 cm^{−1} for *nsc1_3* and 2752 cm^{−1} for *nsc1_1* can be treated as overtone of “broad” component of band arising in scattering accompanied with energy exchange with “narrow” component of the same band. “Weak” components in Raman spectrum of band observed for *nsc1_1* are shifted towards smaller values of Raman shift in comparison with spectrum obtained for *nsc1_3*. This shift is equal to about 15 cm^{−1}/18 cm^{−1} and is due to changes in stacking caused by higher annealing temperature. An example of electronic excitation and vibrational modes joined action was reported in the case of intramolecular excited state proton transfer reaction [46]. The tautomerization mechanism of [2,2-bipyridine]-3,3′-diol was explained in [46] in terms of wavepacket evolution triggered by electronic excitation.

#### 5. Summary

Let us state at the beginning that application of Gaussian profiles significantly improved the quality of the fitting procedure in comparison with former approach based on Lorentzian functions [10]. This is probably due to complicated character of the spectra. Gaussian function is focused on the information from the vicinity of maximum of the band, whereas in case of Lorentzian profile, the tails far from the maximum play much more important role than for Gaussian function.

The part of carbon layer place at the SiC/C interface has complex structure. The existence of such amorphous component probably cannot be avoided because of lattice mismatch between silicon carbide and graphite [47] and differences between in-plane thermal expansion of silicon carbide and graphite [23]. The complicated character of Raman spectra suggests that the achieving low-resistance ohmic contacts is not only dependent on graphitization process understood as decrease of the concentration of defects in graphite lattice. It also includes more subtle processes like changes in stacking order or creation of structures like carbon nanotubes. It is especially important in the vicinity of SiC/C interface. The nanotube-like structure should have much better electric properties [48] than amorphous carbon placed on the SiC/C interface [49].

#### Acknowledgment

The research was partially supported by the European Union within European Regional Development Fund, through grant Innovative Economy (POIG.01.03.01-00-159/08 “InTechFun”).

#### References

- J. A. Cooper and A. Agarwal, “SiC power-switching devices-the second electronics revolution?”
*Proceedings of the IEEE*, vol. 90, no. 6, pp. 956–968, 2002. View at Publisher · View at Google Scholar · View at Scopus - R. C. Clarke and J. W. Palmour, “SiC microwave power technologies,”
*Proceedings of the IEEE*, vol. 90, no. 6, pp. 987–992, 2002. View at Publisher · View at Google Scholar · View at Scopus - H. Matsunami, “Current SiC technology for power electronic devices beyond Si,”
*Microelectronic Engineering*, vol. 83, no. 1, pp. 2–4, 2006. View at Publisher · View at Google Scholar · View at Scopus - J. Crofton, P. G. McMullin, J. R. Williams, and M. J. Bozack, “High-temperature ohmic contact to n-type 6H-SiC using nickel,”
*Journal of Applied Physics*, vol. 77, no. 3, pp. 1317–1319, 1995. View at Publisher · View at Google Scholar · View at Scopus - M. G. Rastegaeva, A. N. Andreev, A. A. Petrov, A. I. Babanin, M. A. Yagovkina, and I. P. Nikitina, “The influence of temperature treatment on the formation of Ni-based Schottky diodes and ohmic contacts to n-6H-SiC,”
*Materials Science and Engineering B*, vol. 46, no. 1–3, pp. 254–258, 1997. View at Google Scholar · View at Scopus - W. Lu, W. C. Mitchel, C. A. Thornton, G. R. Landis, and W. Eugene Collins, “Carbon structural transitions and ohmic contacts on 4H-SiC,”
*Journal of Electronic Materials*, vol. 32, no. 5, pp. 426–431, 2003. View at Google Scholar · View at Scopus - W. Lu, W. C. Mitchel, G. R. Landis, T. R. Crenshaw, and W. E. Collins, “Electrical contact behavior of Ni/C60/4H-SiC structures,”
*Journal Vacuum Science & Technology A*, vol. 21, no. 4, pp. 1510–1514, 2003. View at Publisher · View at Google Scholar - A. Kuchuk, V. Kladko, M. Guziewicz et al., “Fabrication and characterization of nickel silicide ohmic contacts to n-type 4H silicon carbide,”
*Journal of Physics*, vol. 100, no. 4, Article ID 042003, 2008. View at Publisher · View at Google Scholar · View at Scopus - W. Norimatsu and M. Kusunoki, “Selective formation of ABC-stacked graphene layers on SiC(0001),”
*Physical Review B*, vol. 81, no. 16, Article ID 161410, 2010. View at Publisher · View at Google Scholar · View at Scopus - P. Borowicz, A. Kuchuk, Z. Adamus et al., “Visible and deep-ultraviolet Raman spectroscopy as a tool for investigation of structural changes and redistribution of carbon in Ni-based ohmic contacts on silicon carbide,”
*ISRN Nanomaterials*, vol. 2012, Article ID 852405, 11 pages, 2012. View at Publisher · View at Google Scholar - P. Borowicz, T. Gutt, T. Małachowski, and M. Latek, “Carbonic inclusions on SiC/SiO
_{2}interface investigated with Raman Scattering,”*Diamond and Related Materials*, vol. 20, no. 5-6, pp. 665–674, 2011. View at Publisher · View at Google Scholar · View at Scopus - A. C. Ferrari and J. Robertson, “Interpretation of Raman spectra of disordered and amorphous carbon,”
*Physical Review B*, vol. 61, no. 20, pp. 14095–14107, 2000. View at Google Scholar · View at Scopus - A. C. Ferrari and J. Robertson, “Raman spectroscopy of amorphous, nanostructured, diamond-like carbon, and nanodiamond,”
*Philosophical Transactions of the Royal Society A*, vol. 362, no. 1824, pp. 2477–2512, 2004. View at Publisher · View at Google Scholar · View at Scopus - L. Ravagnan, F. Siviero, C. Lenardi et al., “Cluster-beam deposition and in situ characterization of carbyne-rich carbon films,”
*Physical Review Letters*, vol. 89, no. 28, pp. 285506/1–285506/4, 2002. View at Google Scholar · View at Scopus - C. H. Lui, Z. Li, Z. Chen, P. V. Klimov, L. E. Brus, and T. F. Heinz, “Imaging stacking order in few-layer graphene,”
*Nano Letters*, vol. 11, no. 1, pp. 164–169, 2011. View at Publisher · View at Google Scholar · View at Scopus - C. Cong, T. Yu, K. Sato et al., “Raman characterization of ABA- and ABC-stacked trilayer graphene,”
*ACS Nano*, vol. 5, no. 11, pp. 8760–8768, 2011. View at Publisher · View at Google Scholar - C. Cong, T. Yu, R. Saito, G. F. Dresselhaus, and M. S. Dresselhaus, “Second-order overtone and combination raman modes of graphene layers in the range of 1690-2150 cm-1,”
*ACS Nano*, vol. 5, no. 3, pp. 1600–1605, 2011. View at Publisher · View at Google Scholar · View at Scopus - V. W. Brar, G. G. Samsonidze, M. S. Dresselhaus et al., “Second-order harmonic and combination modes in graphite, single-wall carbon nanotube bundles, and isolated single-wall carbon nanotubes,”
*Physical Review B*, vol. 66, no. 15, Article ID 155418, pp. 1554181–15541810, 2002. View at Google Scholar · View at Scopus - N. Radić, B. Pivac, F. Meinardi, and T. Koch, “Raman study of carbon clusters in W-C thin films,”
*Materials Science and Engineering A*, vol. 396, no. 1-2, pp. 290–295, 2005. View at Publisher · View at Google Scholar · View at Scopus - Z. Y. Chen, J. P. Zhao, T. Yano, T. Ooie, M. Yoneda, and J. Sakakibara, “Observation of sp3 bonding in tetrahedral amorphous carbon using visible Raman spectroscopy,”
*Journal of Applied Physics*, vol. 88, no. 5, pp. 2305–2308, 2000. View at Google Scholar · View at Scopus - R. Rao, R. Podila, R. Tsuchikawa et al., “Effects of layer stacking on the combination raman modes in graphene,”
*ACS Nano*, vol. 5, no. 3, pp. 1594–1599, 2011. View at Publisher · View at Google Scholar · View at Scopus - A. C. Ferrari, “Raman spectroscopy of graphene and graphite: disorder, electron-phonon coupling, doping and nonadiabatic effects,”
*Solid State Communications*, vol. 143, no. 1-2, pp. 47–57, 2007. View at Publisher · View at Google Scholar · View at Scopus - R. Colby, M. L. Bolen, M. A. Capano, and E. A. Stach, “Amorphous interface layer in thin graphite films grown on the carbon face of SiC,”
*Applied Physics Letters*, vol. 99, Article ID 101904, 2011. View at Publisher · View at Google Scholar - F. Tuinstra and J. L. Koenig, “Raman spectrum of graphite,”
*Journal of Chemical Physics*, vol. 53, no. 3, pp. 1126–1130, 1970. View at Google Scholar · View at Scopus - R. J. Nemanich and S. A. Solin, “First- and second-order Raman scattering from finite-size crystals of graphite,”
*Physical Review B*, vol. 20, no. 2, pp. 392–401, 1979. View at Publisher · View at Google Scholar · View at Scopus - J. Maultzsch, S. Reich, and C. Thomsen, “Double-resonant Raman scattering in graphite: interference effects, selection rules, and phonon dispersion,”
*Physical Review B*, vol. 70, no. 15, Article ID 155403, pp. 155403–9, 2004. View at Publisher · View at Google Scholar · View at Scopus - M. S. Dresselhaus, G. Dresselhaus, A. Jorio, A. G. S. Filho, and R. Saito, “Raman spectroscopy on isolated single wall carbon nanotubes,”
*Carbon*, vol. 40, no. 12, pp. 2043–2061, 2002. View at Publisher · View at Google Scholar - M. Nishitani-Gamo, I. Sakaguchi, K. P. Loh, H. Kanda, and T. Ando, “Confocal Raman spectroscopic observation of hexagonal diamond formation from dissolved carbon in nickel under chemical vapor deposition conditions,”
*Applied Physics Letters*, vol. 73, no. 6, pp. 765–767, 1998. View at Publisher · View at Google Scholar · View at Scopus - A. M. Rao, E. Richter, S. Bandow et al., “Diameter-selective Raman scattering from vibrational modes in carbon nanotubes,”
*Science*, vol. 275, no. 5297, pp. 187–190, 1997. View at Publisher · View at Google Scholar · View at Scopus - J. R. Shi, X. Shi, Z. Sun, E. Liu, B. K. Tay, and S. P. Lau, “Ultraviolet and visible Raman studies of nitrogenated tetrahedral amorphous carbon films,”
*Thin Solid Films*, vol. 366, no. 1-2, pp. 169–174, 2000. View at Publisher · View at Google Scholar · View at Scopus - H. Riascos, G. Zambrano, E. Camps, and P. Prieto, “Influence of nitrogen gas pressure on plume-plasma and chemical bonding of carbon nitride films synthesized by pulsed laser deposition,”
*Revista Mexicana de Fisica*, vol. 53, no. 7, pp. 274–278, 2007. View at Google Scholar · View at Scopus - W. Lu, W. C. Mitchel, G. R. Landis, T. R. Crenshaw, and W. E. Collins, “Catalytic graphitization and Ohmic contact formation on 4H-SiC,”
*Journal of Applied Physics*, vol. 93, no. 9, pp. 5397–5403, 2003. View at Publisher · View at Google Scholar · View at Scopus - V. Y. Osipov, A. V. Baranov, V. A. Ermakov et al., “Raman characterization and UV optical absorption studies of surface plasmon resonance in multishell nanographite,”
*Diamond and Related Materials*, vol. 20, no. 2, pp. 205–209, 2011. View at Publisher · View at Google Scholar · View at Scopus - C. Fantini, M. A. Pimenta, and M. S. Strano, “Two-phonon combination Raman modes in covalently functionalized single-wall carbon nanotubes,”
*Journal of Physical Chemistry C*, vol. 112, no. 34, pp. 13150–13155, 2008. View at Publisher · View at Google Scholar · View at Scopus - T. L. Weiss, H. J. Chun, S. Okada et al., “Raman spectroscopy analysis of botryococcene hydrocarbons from the green microalga Botryococcus braunii,”
*Journal of Biological Chemistry*, vol. 285, no. 42, pp. 32458–32466, 2010. View at Publisher · View at Google Scholar · View at Scopus - P. H. Tan, C. Y. Hu, J. Dong, and W. C. Shen, “Double resonance Raman scattering of second-order Raman modes from an individual graphite whisker,”
*Physica E*, vol. 37, no. 1-2, pp. 93–96, 2007. View at Publisher · View at Google Scholar · View at Scopus - M. A. Pimenta, G. Dresselhaus, M. S. Dresselhaus, L. G. Cançado, A. Jorio, and R. Saito, “Studying disorder in graphite-based systems by Raman spectroscopy,”
*Physical Chemistry Chemical Physics*, vol. 9, no. 11, pp. 1276–1291, 2007. View at Publisher · View at Google Scholar · View at Scopus - R. Narula and S. Reich, “Double resonant Raman spectra in graphene and graphite: a two-dimensional explanation of the Raman amplitude,”
*Physical Review B*, vol. 78, no. 16, Article ID 165422, 2008. View at Publisher · View at Google Scholar · View at Scopus - D. Yoon, H. Moon, H. Cheong, J. S. Choi, J. A. Choi, and B. H. Park, “Variations in the Raman spectrum as a function of the number of graphene layers,”
*Journal of the Korean Physical Society*, vol. 55, no. 3, pp. 1299–1303, 2009. View at Google Scholar · View at Scopus - A. C. Ferrari, J. C. Meyer, V. Scardaci et al., “Raman spectrum of graphene and graphene layers,”
*Physical Review Letters*, vol. 97, no. 18, Article ID 187401, 2006. View at Publisher · View at Google Scholar · View at Scopus - P. Xu, Y. Yang, I. D. Qi et al., “A pathway between Bernal and rhombohedral stacked graphene layers with scanning tunnelling microscopy,”
*Applied Physics Letters*, vol. 100, Article ID 201601, 2012. View at Publisher · View at Google Scholar - S. Latil and L. Henrard, “Charge carriers in few-layer graphene films,”
*Physical Review Letters*, vol. 97, no. 3, Article ID 036803, 2006. View at Publisher · View at Google Scholar · View at Scopus - Y. Wang, D. C. Alsmeyer, and R. L. McCreery, “Raman spectroscopy of carbon materials: structural basis of observed spectra,”
*Chemistry of Materials*, vol. 2, no. 5, pp. 557–563, 1990. View at Google Scholar · View at Scopus - P. C. Eklund, J. M. Holden, and R. A. Jishi, “Vibrational modes of carbon nanotubes; Spectroscopy and theory,”
*Carbon*, vol. 33, no. 7, pp. 959–972, 1995. View at Google Scholar · View at Scopus - R. Kostić, M. Mirić, T. Radić, M. Radović, R. Gajić, and Z. V. Popović, “Optical characterization of graphene and highly oriented pyrolytic graphite,”
*Acta Physica Polonica A*, vol. 116, no. 4, pp. 718–721, 2009. View at Google Scholar - K. Stock, C. Schriever, S. Lochbrunner, and E. Riedle, “Reaction path dependent coherent wavepacket dynamics in excited state intramolecular double proton transfer,”
*Chemical Physics*, vol. 349, no. 1–3, pp. 197–203, 2008. View at Publisher · View at Google Scholar · View at Scopus - L. B. Biedermann, M. L. Bolen, M. A. Capano, D. Zemlyanov, and R. G. Reifenberger, “Insights into few-layer epitaxial graphene growth on 4H-SiC (000 1
*̄*) substrates from STM studies,”*Physical Review B*, vol. 79, no. 12, Article ID 125411, 2009. View at Publisher · View at Google Scholar · View at Scopus - P. R. Bandaru, “Electrical properties and applications of carbon nanotube structures,”
*Journal of Nanoscience and Nanotechnology*, vol. 7, no. 4-5, pp. 1239–1267, 2007. View at Publisher · View at Google Scholar · View at Scopus - L. Kumari and S. V. Subramanyam, “Structural and electrical properties of amorphous carbon-sulfur composite films,”
*Bulletin of Materials Science*, vol. 27, no. 3, pp. 289–294, 2004. View at Google Scholar · View at Scopus