Research Article | Open Access
Paweł Borowicz, Adrian Kuchuk, Zbigniew Adamus, Michał Borysiewicz, Marek Ekielski, Eliana Kamińska, Anna Piotrowska, Mariusz Latek, "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", International Scholarly Research Notices, vol. 2012, Article ID 852405, 11 pages, 2012. https://doi.org/10.5402/2012/852405
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
Three samples of 4H polytype of silicon carbide (4H-SiC) covered with the following sequence of layers: carbon/nickel/silicon/nickel/silicon were investigated with micro-Raman spectroscopy. Different thermal treatments of each sample result in differences of carbon layer structure and migration of carbon atoms thorough silicide layer. Two ranges of Raman shift were investigated. The first one is placed between 1000 and 2000 . The main carbon bands D and G are observed in this range. Analysis of the positions of these bands and their intensity ratio enables one to determine the graphitization degree of carbon layer. Additional information about the changes of the carbon layer structure was derived from analysis of 2D band placed around 2700 . Application of deep ultraviolet excitation delivered information about the structure of carbon layer formed on the free surface of silicides and the distribution of the carbon inside the silicide layer.
The following combination of silicon carbide (SiC) physical properties: wide band gap, high critical electric field, simple method of dielectric layer fabrication (surface oxidation), and large thermal conductivity makes from SiC very promising material for fabrication high power, high-temperature, and high-frequency electronic devices . The crucial issue in technology of manufacturing SiC-based devices is the capability to form reproducible and reliable ohmic contacts with a low specific contact resistance [2–4].
Formation of ohmic contacts to SiC is typically manufactured by the deposition of metals followed by high-temperature annealing (HTA: ~1000°C) [3–5]. As was shown previously [4–11] metal/SiC structures are not thermally stable. The following reactions of metals with SiC are possible:(i)SiC + refractory metals (Ti, Ta, W, etc.)→HTA→carbides (TiC, TaC, WC, etc.) + silicides (TiSix, , , etc.) + ternary phases (, , , etc.);(ii)SiC + other metals (Ni, Pd, Pt, etc.)→HTA→silicides (, , ) + C.
Nickel is the most widely used metal for fabrication of ohmic contacts to n-type SiC due to the formation of contacts with very low specific contact resistance (~10−6 Ω cm2) [2, 3]. In spite of numerous publications and progress in study of interaction between Ni and SiC, there are still many open questions concerning mechanism of contact formation and its reliability. There are different versions of the ohmic contact formation mechanism:(i)inhomogeneity of metal-SiC Schottky barrier ;(ii)creation of carbon vacancies [1, 13] or defect states  near the interface region;(iii)“snowplow effect” of dopants in the SiC substrate .
The noncontrolled high temperature reaction between Ni and SiC, followed by creation of silicides and free carbon atoms, limits the reliability of the Ni-based ohmic contacts. In previous works it was shown  that the creation of silicides at metal/SiC interface is not sufficient for ohmic contact formation. The role of carbon species at SiC/silicide is not fully understood yet. The results obtained by Lu et al. [5, 14] point to crucial role of graphitic structures in the formation of ohmic contacts on SiC substrate. The type of the starting carbon materials: C atoms or C60 molecules, has no significant impact on the process.
In our earlier works [15, 16] we have investigated various Ni- and Ni/Si-based contacts to SiC and reported on their electrical and structural properties. The characterization was performed by X-ray diffraction (XRD), Rutherford Backscattering Spectrometry (RBS) and Secondary Ion Mass Spectrometry (SIMS). These results have shown that the best ohmic contacts are obtained by using Si/Ni/Si/Ni metallization scheme with thickness of Si and Ni layers optimal for building Ni2Si silicide. In this work we focus our attention on the role of carbon phase in the reaction of ohmic contact formation. We have modified our metallization scheme by inserting an additional carbon layer on SiC surface prior to metallization procedure. To investigate the changes of carbon layer structure under thermal treatment we have chosen Raman spectroscopy, because this technique demonstrated its utility in structural study.
The nitrogen-doped n-type (~1 × 1019 cm−3) 4H-SiC 2.97 μm thick layers which were grown on 4H-SiC wafer by chemical vapor deposition (Cree Research Inc.) were used as substrates. The 4H-SiC substrates were 8°-off axis, Si-terminated (0001) surfaces. Before deposition of contacts the wafers surface was cleaned according to the procedure described in . Ni, Si, and C layers were deposited from high purity elemental targets in Ar plasma discharge at the room temperature. Three samples with following sequence of layers Si(33 nm)/Ni(30 nm)/Si(33 nm)/Ni(30 nm)/C(3 nm)/SiC(substrate) were prepared. The structures were annealed at 600°C (N2, 15 min.) to form silicides. Annealing was followed by thermal treatment at different temperatures: 800°C, 950°C, and 1000°C (N2, 3 min.) to obtain ohmic contact [15, 16]. Specific contact resistance and temperature used in second step of annealing are presented in Table 1 for samples investigated with Raman spectroscopy hereafter signed by: nsc1_1, nsc1_2, and nsc1_3.
The example of microscopic image and scheme of the sample as an inset is shown in Figure 1. The glossy area corresponds to image of 4H-SiC substrate, the rough one—to the area covered with sequence of described above Ni/Si layers. Hereafter this area will be called structure. Small bright spot in the center shows focused laser light.
The samples were characterized by means of transmission electron microscopy (TEM) and secondary ion mass spectrometry (SIMS). Both methods showed changes in the structure of Ni/Si/Ni/Si layer sequence upon thermal treatment and presence of carbon layer between silicon-carbide substrate and silicide layer .
The Raman scattering was measured with MonoVista Raman microspectrometer (Spectroscopy and Imaging GmbH, Germany). The micro-Raman spectrometer was based on Olympus BX51 microscope equipped with the following types of objectives:(i)magnification: 20x, 50x and 100x, for visible light (VIS);(ii)magnification 40x, designed for ultraviolet (UVB).
Images from microscope were recorded with imaging camera TM2040GE (JAI, Japan) with 16 bit AD image conversion. The spectral part of the micro-Raman spectrometer was based on SpectraPro 2750i spectrograph (Princeton Instruments, USA) with triple grating turret. The turret is equipped with three gratings:(i)1800 lines/mm and 2400 lines/mm blazed for visible spectral range;(ii)3600 lines/mm blazed for ultraviolet (250 nm).
The spectral detection was done with CCD camera Spec-10 System (Princeton Instruments). Maximum efficiency of the camera was at 250 nm. The , , motor driven (Ludl Electronics, USA) stage allowed positioning with 20 nm step in or direction and 50 nm in direction.
2.3. Experimental Conditions
As a fundamental wavelengths (excitation) the visible line of Ar+ laser (INNOVA 90C FRED, Coherent Inc., USA) and its second harmonic were used. The power of the laser beam on the sample was below 1 mW for each fundamental wavelength. Visible Raman spectra were recorded with the grating with 1800 lines/mm and the objective lens of magnification equal to 100x designed for visible spectral range. In the case of ultraviolet excitation the UV objective lens (magnification 40x) and blazed for 250 nm grating with 3600 lines/mm were used. The exposition time used for measurement of single spectrum was equal to 1 hour. In the case of linear scan the exposition time for one spectrum was reduced to 15 minutes.
2.4. Spectra Analysis
Measured spectra were mathematically corrected prior to analysis. This mathematical treatment included offset removing, baseline correction, and normalization of intensities to value equal to 1. The mathematical processing made possible the comparison of following features: the shapes of measured spectra and D-to-G intensity ratio. Mathematical treatment of measured Raman spectra was done with GramsSuitev. 8 program (Thermo Scientific, USA). The analysis of normalized spectra was performed by fitting Lorentzian function with open source program Fityk0.8.6 (Levenberg-Marquardt algorithm).
In Figure 2 an example of scan performed in plane of SiC/C interface is presented. The direction of the scan was perpendicular to the edge of the structure. The measurement was done for nsc1_1 along coordinate in this particular case. Position corresponds to the edge of the structure, , to laser beam focused on the area covered with sequence of layers, , to laser beam focused on SiC substrate outside of the covered area. Panel (a) presents measured spectra as 3D surface, panel (b) is corresponding map. Panel (c) presents an example of measured spectrum with color scale used in panels (a) and (b). It is clearly visible that spectra change in the vicinity of . Vicinity means here about ±1 μm. Starting from negative values of -coordinate: main Raman bands observed for carbon structures, D and G, are changing to standard two-phonon Raman scattering of 4H-SiC  for positive values of . The data obtained from spatial scans performed for other samples, nsc1_2 and nsc1_3, are very similar.
Normalized Raman spectra of carbon structures measured for different samples are presented in Figure 3. D band has the maximum placed at about 1350 cm−1 in the case of each sample. The shape of this band is symmetrical. D bands recorded for different samples have different values of FWHM. Differences between band recorded for different samples concern the position of the maximum of the band and its halfwidth. Samples nsc1_1 and nsc1_3 have asymmetric band with maximum placed at about 1580 cm−1. G band observed for nsc1_2 has symmetric shape but its maximum is shifted to about 1600 cm−1. The signal-to-noise ratio in the case of nsc1_2 is unfavorable. Such effect in the case of nanocrystalline graphite in ohmic contacts was already reported . Based on mathematical treatment detailed analysis of the spectra is presented in part Section 4.
Additional information about carbon structure can be derived from 2D band placed around 2700 cm−1 . This band was observed for nsc1_1 and nsc1_3, whereas for nsc1_2 weak increase of the background was detected in the corresponding range of Raman shift. In Figure 4 are presented normalized Raman spectra recorded for all samples. Due to low intensity of the band around Raman shift 2700 cm−1 and unfavorable signal-to-noise ratio 2D band in the case of nsc1_2 must be treated as negligible. The maxima of 2D band observed for nsc1_1 and nsc1_3 had the maxima almost at the same value of Raman shift (see Figure 4). Spectra show small difference in FWHM, namely the band observed for nsc1_3 is broader in comparison with the band recorded for nsc1_1. The difference between spectra was observed on the left slope of 2D band. The “hole” observed for all samples had the maximum at the same value of Raman shift (about 2715 cm−1). This kind of hole was not observed in spectra measured from these parts of the sample that were not covered with carbon and silicide layers. Because of this the origin of the hole should be treated as real and related to the presence carbon or/and silicide layers. The detailed origin of the effect is for authors not unequivocal and it will be discussed in subsequent paper.
In Figure 5 are presented normalized Raman spectra measured with application of UV excitation (). In panel (a) are presented spectra measured for nsc1_1, in panel (b) for nsc1_3 and in panel (c) for nsc1_2. The arrows in panels (a) and (b) are placed in the position corresponding to maxima of carbon bands. The arrow in panel (c) is placed at about 1605 cm−1. For this value of Raman shift the maximum of G band is expected for nanocrystalline graphite. In the case of each sample spectra were measured at different position with respect to the edge of the structure: outside of the structure (blue line), on the edge (green line), on the structure near the edge (red line) and on the structure far from the edge (black line). In the cases of nsc1_1 and nsc1_3 samples the carbon band appears around 1590 cm−1. The intensity of the band increases with the increase of the distance from the edge of the structure. In the case of nsc1_2 very weak signal with maximum slightly above 1600 cm−1 appears for the measurement “on the structure far from the edge.” Spectra registered in the vicinity of the edge are mainly composed of two-phonon scattering generated by 4H-SiC. Numerous narrow lines in UV Raman spectra were already observed by investigation of carbon inclusions in SiC/SiO2 interface . Since the origin of these lines is not related to the carbon layer, the discussion concerning these lines is omitted. Also the signal from interface is taken into account. Raman signal from thin interface layer is usually very weak. Since the investigation of the interface structure do not belong to the main aim of this work it will be not discussed here.
Figure 6 presents results of analysis of Raman spectra measured for all samples with visible excitation. Panel (a) shows results obtained for nsc1_1, panel (b) for nsc1 3, and panel (c) for nsc1_2. The main plot in each panel presents experimental points (red) and fitted profiles (black line). The positions of profiles maxima are given in the panels. The upper inset compares experimental data with whole fitted function. Lower inset presents autocorrelation function. The number of Lorentzian fitting components necessary for proper spectra reproduction varies. In the case of nsc1_1 three profiles are necessary, for nsc1_3—four, and for nsc1_2—two. Generally, the shapes of fitted functions follow the experimental data. Small differences between the experimental data and the fitted functions are visible in autocorrelation functions. The values presented in these insets were calculated by subtracting the fitted function from experimental data. Increase of the number of Lorentzian fitting components does not improve the quality of the fit in the case of any sample. The profile reproducing the “hole” in band of nsc1_3 is shifted in the top of panel (b).
Generally, recorded for nsc1_1 Raman spectra are very similar to the spectra found in literature and observed for samples after similar temperature treatment . Position of band observed for nsc1_2 is shifted towards larger values of Raman shift and equals to about 1603 cm−1. This value corresponds to the maximum observed for nanocrystalline graphite [21, 22]. Shift of the maximum position of observed for nanocrystalline graphite results from convolution of and bands so it is impossible to split observed band into unequivocal components . In the case of nsc1_2 it is possible that observed band consists of even three components: “pure G,” and probably small addition of Ni-GIC.
In Table 3 there is presented intensity ratio of bands and G (I()/I()) and to G (I()/I()). Since FWHM of carbon bands contains the information about different structures (like 5-member rings) and the height of the band contains the information about the concentration of the main structure  it is more reliable to compare heights of fitted profiles instead of profiles area. The values presented in Table 3 refer to the ratio of fitted Lorentzian heights. The ratio I()/I() is smaller for nsc1_1 than for nsc1_3. This difference shows larger graphitization degree in the case of nsc1_1. In the case of nsc1_2 the value given in Table 2 can be affected by impossibility of splitting observed “G” band into components. However, presented in Table 2 descending FWHM’s values (nsc1_2→nsc1_3→nsc1_1) of band suggest increase of the graphitization degree in the row: nsc1_2 → nsc1_3 → nsc1_1. The difference in maximum intensity ratio of I()/I() obtained for nsc1_1 and nsc1_3 reflects smaller concentration of carbon structures responsible for band in nsc1_1. This decrease of concentration of carbon structures responsible for band is not fully compensated by increase of concentration of Ni-GIC species.
In Figure 7 there are presented results of the analysis of 2D band measured for nsc1_1 and nsc1_3. Panel (a) presents the data obtained for nsc1_1, (b)—nsc1_3. Due to negligible intensity of UV Raman spectra obtained for sample nsc1_2 (see Figure 5(c)) the spectra measured for this sample were not analyzed. The convention used in Figure 7 is the same as in Figure 6. Main plots show experimental points and fitted Lorentzian components with given maxima positions. Upper insets compare the experimental data with whole fitted function. Lower insets show the autocorrelation functions. Three Lorentzian fitting components are necessary for reasonable reproduction of 2D band in the case of each sample. One of these profiles is used to model the “hole” placed near maximum of the band. The profiles reproducing the “hole” are shifted up to the normalization limit. The shape of the fitted function corresponds to distribution of experimental points. Small differences between fitted function and experimental data are visible in autocorrelation functions. The increase of the number of Lorentzian components does not reduce small discrepancies between fitted function and experimental data.
In Table 4 results of analysis of 2D band are presented. The function used to reproduce the hole is omitted because the origin of the hole is not discussed. Position of the maximum of Lorentzian component is similar for both samples: the difference between maxima position is equal to 0.7 cm−1. In the case of maximum position obtained for nsc1_1 is shifted towards smaller values in comparison with nsc1_3. The difference between maxima positions of component is equal to 1.1 cm−1. Intensity ratio I()/I() was calculated as the ratio of the heights of Lorentzian fitting components. The contribution of component in the case of nsc1_3 is significantly larger in comparison with nsc1_1. Generally the reproduction of 2D band generated by graphitic structures requires four Lorentzian components [19, 23]. This rule can be modified by interaction with substrate or structure . For example: 2D band of “few layers graphene” looks very similar to 2D bands observed for nsc1_1 and nsc1_3 . Small differences between maxima positions reported in literature and observed here may result from dispersive behavior of and, of course, 2D bands. The typical wavelength of fundamental line reported in literature equals 514.5 nm whereas here authors used 488 nm. The components of band: and are related to mutual orientation of A and B layers . The profiles fitted to 2D band correspond to and overtones. The shape of 2D band depends on excitation wavelength and number of “graphene layers” in the sample [19, 26]. 2D band generated by “single graphene layer” fits single Lorentzian function [19, 25, 27]. However, it was recently shown that even “graphene flakes” can generate 2D bands composed of more than one Lorentzian fitting component . The interlayer distance in graphite equals to about 0.335 nm  and slightly varies with stacking order . Since the processes of migration of carbon atoms from SiC interface and decomposition of silicon-carbide substrate are going simultaneously one should not expect drastic change of the thickness of deposited carbon layer. Also the rate of these processes is so small that cannot significantly affect the thickness of carbon layer. For example formation of “graphene layer” at 1450°C requires 1 hour . This is in agreement with data obtained TEM that showed the carbon layer between 4H-SiC substrate and silicide layer . Taking into account thickness of deposited C-layer equal to about 3 nm one can expect carbon film placed on SiC substrate has thickness corresponding to 8–10 carbon layers. The shape of 2D band is also a function of staking order . Although the shape of 2D band depends on excitation wavelengths there is one common feature observed for the band in the cases of all reported excitations . The maximum of 2D band is shifted towards smaller values of Raman shift in the case of ABC stacking order whereas the maximum of 2D band observed for ABA stacking order is placed at larger values of Raman shift . This difference increases with excitation energy . Natural graphite is a mixture of different species. The most important are hexagonal (α or Bernal) structure and rhombohedral (β) structure. The content of β-form varies typically from 5 to 15% [33, 34]. The domains having ABC stacking order are stable up to temperatures above 800°C . The conversion of rhombohedral graphite to the hexagonal form occurs effectively at temperature higher than 1025°C . The rhombohedral phase may be completely converted to the hexagonal one in the case of heating above 3000°C . The preferential formation of rhombohedral graphite on SiC interface was observed during the process of thermal decomposition of silicon-carbide substrate . The most probable explanation of spectral differences between the samples nsc1_1 and nsc1_3 in the range corresponding to 2D band is following: the different content of rhombohedral and hexagonal phases in nsc1_1 and nsc1_3 should be the reason of the differences observed for 2D band.
The last problem to be discussed for measurements carried out for visible fundamental wavelength is the negligible intensity of 2D band in the case of nsc1_2. In following cases 2D band is not observed:(i)for amorphous carbon (a-C);(ii)for tetrahedral amorphous carbon (ta-C) .
However, for a-C and ta-C the intensity of D band should be negligible or at least much smaller than the intensity of band  which is not valid for nsc1_2. The other possible explanation of negligible intensity observed for 2D band in the spectrum of nsc1_2 is the dependence between intensity of 2D band and the type of metallic layer placed on carbon structure . Such metallic layer may reduce the intensity of 2D band . The intensity of 2D band in some cases is much smaller than the intensity of band [14, 38], or even has the tendency to disappear like for nanocrystalline graphite . Since the intensities of main carbon bands (D and G) were small in the case of nsc1_2 the intensity of 2D band was too weak to obtain good signal-to-noise ratio, although the band seems to be present. The annealing temperature used in the second step of nsc1_2 thermal treatment (800°C) is the lower limit when 2D band can appear in ohmic contacts [14, 38]. One more factor which can influence the intensity of observed Raman spectra is heating time used in ohmic contact formation. According to literature concerning Raman study it usually takes 2 hours [14, 38], whereas in the case of nsc1 series of samples it was 15 minutes at 600°C and additional 3 minutes for the second step (800°C and above). The first step of thermal treatment is below the reported temperature limit necessary for 2D band appearance.
In Figure 8, the results of analysis of Raman spectra measured with UV irradiation are presented. Panel (a) shows the data obtained for nsc1_1, (b)—nsc1_3. The main plot in each panel shows experimental data (red points) together with fitted profiles (black line). The maxima positions are listened in the plot. The upper inset in each panel compares the experimental points with fitted function. The lower inset presents the autocorrelation function. In the case of each sample fitted function reproduces quite well the shape of measured spectrum. Small differences between experimental data and fitted function are visible in autocorrelation function.
In Table 5 results of analysis of Raman bands observed with irradiation by UV laser light “on the structures far from the edge” are presented. The main band observed for irradiation “on the structure far from the edge” is well reconstructed by two Lorentzian fitting components in the case of nsc1_1 and one Lorentzian fitting component in the case of nsc1_3. profile has the maximum at Raman shift equal to ~1589 cm−1 in the case of nsc1_1 and ~1591 cm−1 in the case of nsc1_3. The maximum position of the band corresponds to the maxima observed for G band of graphite layers [19, 23]. The difference in the position of maximum of the band reflects small structural changes between the layers appearing on the surface of nsc1_1 and nsc1_3 samples. This kind of dependence was already observed . The decrease of FWHM from 35 cm−1 for nsc1_3 to 30 cm−1 for nsc1_1 suggests larger homogeneity for nsc1_1. The second Lorentzian fitting component () used in reproduction of spectrum measured for nsc1_1 has the maximum at 1605 cm−1 and corresponds to the band reported for nanocrystalline graphite . The FWHM obtained (21 cm−1) for component is similar to the values obtained for profile from Table 2 and about three times smaller than FWHM obtained for nsc1_2 from VIS irradiation.
The main problem to be discussed is the type of structure which generates Raman scattering observed in the case of irradiation with ultraviolet laser line. Annealing at temperature higher than 600°C leads not only to the formation of silicides but also to redistribution of carbon atoms [6, 11, 13]. The layer of nickel-silicides is the mixture of silicides and carbon structures. The other important feature is graphite thin layer placed on the free surface of silicide layer. Annealing at the temperature higher than 950°C leads to changes in the structure of graphite species placed in Ni-silicide layer . The dimensions of clusters are larger. Large clusters are concentrated inside the silicide layer near SiC/Ni-silicide interface. Optical properties of both Ni-silicide layer mixed with carbon and graphite thin layer placed on free surface of Ni-silicide film are important in the interpretation of ultraviolet Raman spectra.
Thin graphite film does not decrease significantly the intensity of the light in ultraviolet and visible spectral range [39–41]. The silicide film with thickness of about 100 nm is transparent in the visible and ultraviolet spectral ranges [8, 42–44]. Silicides mixed with carbon species show absorption which increases significantly if spectral range is changed from visible to ultraviolet . Also the mixture of nanocrystalline graphite and diamond-like structures has significantly larger absorption in UV than in visible spectral range . Coming back to Raman spectra: the main Lorentzian fitting component () reproduces the spectra of nsc1_1 and nsc1_3 coming from thin graphite layer placed on the free surface of silicide because Ni-silicide film mixed with carbon strongly absorbs UV light hindering effective scattering from the carbon layer placed at the 4H-SiC/Ni-silicide interface. The other Lorentzian fitting component () observed for nsc1_1 corresponds to band coming from nanocrystalline graphite located inside the Ni-silicide film. The absence of or band in measured UV Raman spectra can be explained by the quality of graphite layer, which means by negligible concentration of defects. In the case of nanocrystalline species placed inside the silicide layer the vibrations of carbon atoms placed at the border of nanocrystals can be modified by interaction with silicides. This kind of modification results in change of Raman spectrum.
Profiles and describe narrow lines with maxima at about 1538 cm−1 and 1560 cm−1, respectively. The halfwidth of these profiles, 3 cm−1 and 4 cm−1, can be treated as equal within accuracy of measurements with UV excitation. The line with maximum at about 1530 cm−1 was reported for nanographite species [47, 48]. The broad band from  can be associated with amorphous carbon . The narrow line reported in  was assigned to armchair-shaped edge of graphite nanoribbon. Generally the lines with FWHM equal to a few cm−1 are typical traces of localized vibrational modes (LVM’s) associated with defects of crystal structure . Typical edges of graphite nanoparticles or nanoribbons are classified as arm-chair-shaped (A-shaped), zigzag-shaped (Z-shaped), or mixed-shaped (M-shaped): a combination of A- and Z-shaped . The line associated with Z-shaped edge expected at about 1450 cm−1  was not observed here. Lines having maxima at 1530 cm−1, 1531 cm−1 as well as around 1560 cm−1 (1556 cm−1, 1558 cm−1, and 1567 cm−1) were observed for polyenic backbone molecules . The vibration around 1560 cm−1 was reported in UV-Raman spectra of polycyclic aromatic hydrocarbons (PAHs) are anthracene (1567 cm−1, 1562 cm−1) [51, 52], phenanthrene (1563 cm−1) , and pyrene (1560 cm−1, 1563 cm−1) [51, 52]. Vibrations 1533 cm−1 in pentacene and 1570 cm−1 in perylene were classified as “aromatic C-C stretching” . Taking into account summed-up above information we divide the carbon structures associated with lines: 1538 cm−1 and 1560 cm−1 into two types: (i)ribbon- or chain-like;(ii)PAH-like.
The first type is showed in Raman UV-spectra two lines 1538 cm−1 and 1560 cm−1, whereas the second type contributes to the line with maximum at 1560 cm−1. Thermal treatment at 950°C results in formation of ribbon-like (chain-like) and PAH-like structures. Increase the temperature up to 1000°C limits the type of carbon structure to PAH-like. This is confirmed by disappearing of the line 1538 cm−1. Since the carbon layer placed on free silicide surface seems to be homogeneous ribbon-like and PAH-like structures should be placed rather inside silicide layer than on its surface.
The application of different excitation wavelengths makes possible to investigate the structural changes of carbon species placed at different locations of SiC-based ohmic contacts.
Increase of I(D)/I(G) ratio in pair nsc1_3, nsc1_1 suggests increase of graphitization of the carbon layer with the increase of the temperature used in thermal treatment. Changes of structure of carbon layer are caused not only by the temperature but also by interaction with metallic layer used in the process of ohmic contact formation. The following changes of carbon structures upon thermal treatment are proposed:(i)nsc1_2—nanographitic structure where band is probably the combination of “pure G” and coming from carbon structures with C=C bonds; the contribution of the band generated by Ni-GIC structures should be very low or even negligible;(ii)nsc1_3—graphitic structure with band consisting of “pure G” with small contribution of band originated from carbon structures having C=C bonds ; probably there is also small contribution generated by Ni-GIC species;(iii)nsc1_1—graphitic structure with band consisting of “pure G” and band generated by Ni-GIC; optionally small addition of (C=C bonds) is also possible;(iv)the increase of graphitization between nsc1_3 and nsc1_1 is accompanied by increase of content of ABA stacking in the mixture of ABC and ABA stacking orders.
Large contribution of “Ni-GIC” band in the case of nsc1_1 results from high temperature of thermal treatment (1000°C) in which the structures Ni-GIC are generated effectively . Negligible intensity of 2D band in the spectrum observed for nsc1_2 results probably from the combination of lower limit of the temperature what makes possible observation of 2D band (800°C) and short time of application of the temperature .
Application of ultraviolet laser line makes possible to observe the signals from thin carbon layer built on the free surface of nickel-silicide film during the process of annealing and the from nanocrystalline species placed in the silicide film. The analysis of the UV-Raman spectra makes possible to derive information about details of the structure of carbon layer placed on the free surface of nickel silicide. The UV-Raman spectrum consist of the band and narrow lines assigned to ribbon- (chain-) like and PAH-like carbon structures. These structures are placed inside silicide layer than on its free surface. Increase of the temperature up to 1000°C removes the trace of chain-like structures from the spectrum.
Small changes between experimental data and the sum of fitted profiles appear in autocorrelation function. These discrepancies suggest that the model used in this paper cannot described all features of carbon structures in ohmic contacts. Discussion of the details not included in the presented model will be the subject of subsequent paper.
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”).
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