Print version ISSN 0038-2353
S. Afr. j. sci. vol.105 no.1-2 Pretoria Jan./Feb. 2009
The structural characterisation of HWCVD-deposited nanocrystalline silicon films
Bibhu P. SwainI, II
IDepartment of Physics, University of Cape Town, Private Bag, Rondebosch 7701, South Africa
IIDepartment of Metallurgical Engineering and Materials Science, Indian Institute of Technology, Mumbai, India. E-mail: firstname.lastname@example.org
Nanocrystalline silicon (nc-Si) films were deposited by hot-wire chemical vapour deposition (HWCVD) in the presence of varying H2 concentrations and their structural and interfacial character investigated by X-ray diffraction, small-angle X-ray scattering (SAXS) and Raman spectroscopy. The crystalline fraction was around 3050% and the nc-Si crystallite size was in the range 2035 nm. The SAXS results were analysed by Guinier plot, scaling factor, and correlation distance. The nc-Si grains displayed a mass fractal appearance, and the interfacial inhomogeneity distance was ~2 nm.
Key words: HWCVD, SAXS, Raman, XRD
Nanocrystalline silicon (nc-Si:H) prepared as thin films by hot-wire chemical vapour deposition (HWCVD) at low substrate temperature has attracted much attention because of its potential application in low-cost, large-area electronic devices, such as flat panel displays and solar cells.1 Hydrogen dilution of silane strongly affects the microstructure of silicon films so deposited.2,3 Hydrogen-diluted nc-Si reportedly exhibits high stability against light soaking,4,5 increases crystallite size and enhances mobility compared with amorphous silicon. Silane dilution can lead to a phase transition of silicon from an amorphous to a nanocrystalline and polycrystalline state.4,5 However, macroscopic inhomogeneity in the growth direction, as well as in the growth plane of nc-Si, has been observed in HWCVD films.6,7 Another aspect of nc-Si or poly-Si growth on glass and a-Si:H on graphite substrates in HWCVD processes is that nucleation of nanocrystalline material does not occur before the film thickness reaches 5 nm.8 This means that the initial growth of the films, during the deposition of the first few nanometres, is structurally amorphous. Methods based on scattering phenomena are useful for studying material which is heterogeneous at a nanoscale,9,10 especially those exhibiting nanocrystalline features. To calculate grain size and other characteristics of the crystallite interface, the following assumptions were made: (a) the scattering particles and their surrounding medium have uniform but different electron densities, (b) the volume fraction of the particles is low, and (c) the scattering particles are of an approximately known shape. Bingqing et al. analysed the influence of structural diversity and the size of spherical particles on the calculated size of distributions.11
The interpretation of the scattering effect from complex, disordered materials is notably simplified when fractal geometry is invoked to describe their structure. Much attention has been paid to the structural properties of nc-Si of HWCVD-deposited films derived from small-angle X-ray (SAXS) measurements,8,12 but few papers describe the structural and interfacial nature of nanocrystalline silicon. This article reports on structural and interfacial studies of nanocrystalline silicon using both SAXS as well as X-ray diffraction (XRD) and Raman spectroscopy.
Nc-Si:H films were formed on glass and crystalline Si substrates by hot-wire chemical vapour deposition under various H2 dilution conditions in silane. Deposition parameters are shown in Table 1. XRD samples were studied with a vertical Philips X-pert (PANalytical) Model 3040/60 X-ray diffractometer. Raman spectra were recorded using a Labram-1 (Dilor-Jobin Yvon-Spex) spectrometer in backscattering mode with a spectral resolution of 2 cm1. The 488.0 nm (approximately 2.54 eV) line of an argon laser was used for excitation and the Raman scattered light was analysed using a charge-coupled device (CCD) camera for multi-channel detection. SAXS data were collected from a SAXSess Anton Parr, Model 3040/60 X-ray generator: PW 3830 PANalytical in-line collimating geometry using the transmission method at a wavelength of 0.154 nm. The experimental samples were deposited on Si(100) wafers, which were folded into two layers for signal enhancement. The X-ray intensity scattered at an angle of 2θ relative to the incident beam passing through the sample was obtained with a highly collimated beam. (The angle 2θ is usually converted into a scattering vector in terms of h = 4π(sin θ)/λ.) The X-ray intensity measured as a function of the scattering angle 2θ was corrected for absorption and scattering from the substrate. It was normalised by incident beam intensity Io and film thickness to yield the normalised SAXS intensity, I(h). After correction for background, data were analysed by Guinier plot, Porod plot, scaling behaviour and correlation distance.
Interpretation of SAXS results
Figure 1 shows SAXS intensities I(q) obtained from nc-Si nanocrystals as a function of wavenumber (q = (4π/λ)sinθ). The scattering profiles have quantitatively similar features and can be divided into three regions on the q-axis by shape profile. The low q region (Region I; q > 0.001) gives an idea of grain size and shape of the nanocrystalline material. The sufficient condition for measuring radius of gyration is qmaxRg < 1. The Guinier approximation to determine radius of gyration is I(q) = Io exp (q2Rg2/3). In the interface, the electron inhomogeneities are different from those in a crystalline or purely amorphous network. The scattering vector corresponding to Region II (0.05 < q < 0.15) provides information about the interface and interfacial inhomogeneities of crystalline materials. Scaling behaviour and the Debye law are applicable to this region, where scattering exhibits self-similarity, based on fractals. Scaling law, the Power law or the presence of fractals gives a further idea of the distribution of nanocrystalline materials in a deposit, depending largely on cluster mobility. A Power plot is defined by the equation I(q) = Aqα, where A is a constant related to the structural configuration of the nc-Si. α represents the fractal dimension and is equal to three for perfectly ordered materials. The material is considered to be mass fractal if 3 < α < 0 and surface fractal if 4 > α > 3. Debye theory provides a general description of an inhomogeneous system, from which scattering measurements can be used to indicate average electron density and the degree of correlation between two fluctuations as a function of their distance of separation. In Region III, correlation length is evaluated using the equation I(q)2/3 = Bq2 + C, such that the electron inhomogeneity distance is λ = (B/C)1/2.(refs 13,14).
Results and discussion
The XRD spectra of silicon films prepared under different H2 dilution conditions are shown in Figure 2. With increasing H2 dilution, the appearance of three prominent peaks at about 28.4°, 47.28° and 56.8° indicates progressive crystallisation in the <111>, <220> and <311> directions, respectively. Figure 2 also shows that the full width at half maximum (FWHM) height of the XRD peak pattern decreased as the hydrogen dilution ratio increased. This indicated that the intermediate range order improves with H2 flow rate. The average grain size of the experimental films is therefore estimated by the Debye-Scherrer formula to be 2035 nm. The intensities, the positions and the FWHM of different XRD peaks of the experimental films are listed in Table 2. For clarity, the intensities were normalised to the (220) peak intensity. In the XRD data, the peak intensities, I(hkl), of nc-Si:H films listed in Table 2 show that the I(111)/I(220) ratio was in the range 0.682.11, whereas the I(111)/I(311) ratio was in the range 45.9.
Figure 3(a) shows a typical Raman spectrum from a nc-Si:H film, which can be identified as four regions corresponding to two kinds of phonon modesa longitudinal optical (LO) branch with a peak at ~400 cm1 and a transverse optical (TO) mode. Further, the TO band can be further divided into three parts: a transverse optical branch (TO1) with a peak at 480 cm1 from the amorphous Si contribution, a transverse optical mode (TO1) at about 510 cm1 from the contribution of Si interfacial nanocrystals, and another transverse optical mode (TO2) at 520 cm1 from the contribution of Si core nanocrystal. These modes are depicted in Figure 3(a), from which the LO and a-TO, TO1 and TO2 branches can be seen to fit well to a Gaussian distribution. This implies that every fitted line can be approximately represented by every mode deconvoluted from an experimental Raman spectrum.15
The crystalline fraction (X%) is estimated from the formula δIc/(Ia + Ic) = (I510 + I 520)/(I475 + I510 + I520), where I480 is the amorphous silicon peak intensity and I520 is the Raman scattering for crystalline silicon. Figure 3(b) shows micro-Raman spectra of nc-Si:H as a function of H2 flow rate. An obvious effect of increasing the H2 concentration is the shift of the Si TO band towards higher frequency as depicted by the dashed line. The peak intensity observed at 517 cm1 corresponded to a 15 sccm H2 flow rate, whereas it shifted to 519 cm1 for a flow rate of 35 sccm; the corresponding crystalline fractions were 37% and 49%. Also clearly indicated is that H2 dilution suppresses the amorphous fraction in the nc-Si network and increases the crystalline fraction. It is the growth and the shift of the second TO band relative to the 475 cm1 band that causes the peak of the overall TO band to shift to higher frequencies. This shift indicates increasingly ordered structure as found in H2-diluted films16 and is consistent with recent calculations which have depicted an increase of the TO peak frequency with a decrease of the mean bond-angle deviation.20 Figure 3(c) shows the I510/I520 and (I510+ I520)/(I480 + I510 + I520) ratios as a function of H2 flow rate. It indicates that the grain boundary contribution was reduced with increase in H2 dilution in the nc-Si network. This indicated that the thickness of the inhomogeneous layer was almost constant in the nc-Si:H films. The I510/I520 ratio indicates surface scattering in relation to scattering by the crystalline core in the experimental films. This ratio decreased from 2.2 to 1.1, reflecting a reduction in interfacial inhomogeneity with hydrogen dilution.
Figure 4 illustrates ln(I) in relation to normalised SAXS intensity as a function of H2 flow rate. The slope of the SAXS intensity decreased progressively with increase in flow rate.
The splitting SAXS scattering at higher q values was more prominent and this was due to scattering from a nanocrystalline silicon surface. Figure 5(a) shows that ln(I) versus ln(q) exhibits power law behaviour for a hydrogen flow rate of 15 sccm, as in a two-phase system where nanocrystalline silicon is surrounded by an amorphous a-Si:H network. At q >0.03 Å, the nanocrystalline silicon indicates enhanced order; a slope of more than three indicates surface fractal characteristics. Table 3 shows the scaling factor for films deposited at different H2 flow rates. This result suggests that this particular crystallite network consists of fractal clusters (Dm = 2.95 ± 0.02) of particles with smooth surfaces. Figure 5(b) is a Guinier plot, in which the slope is taken over the range where Rgq < 1. Rg, the radius of gyration of the clusters, varies from 9.8 nm to 12.9 nm as H2 dilution increases from 15 to 35 sccm. Assuming the presence of uniform spheres, the corresponding cluster diameter is equal to 2Rg(5/3).0.5 Grain size increases from 25 to 33 nm and corresponds with crystallite size determined by XRD. Figure 5(c) shows a Debye plot as a measure of the mean inhomogeneity in the experimental materials. The inhomogeneity distance is approximately 2 nm for a H2 flow rate in the range 1535 sccm.
These various studies based on SAXS, XRD and Raman spectra of nc-Si:H films deposited by HWCVD techniques under varying hydrogen dilution conditions, indicate that crystallite size and crystalline fraction increased from 20 nm to 35 nm and from 40% to 49%, respectively. Crystallites of nanocrystalline silicon displayed a mass fractal nature and interfacial inhomogeneities were of the order of 2 nm in size. The relative effect of grain boundaries in relation to grain size declined in films deposited with reduced H2 flow rate.
This paper has been presented at Nanoafrica 2006, University of Cape Town. The author gratefully acknowledges D.T. Britton and M. Harting, Department of Physics, University of Cape Town, for financial support and helpful discussions.
1. Brühne K., Schubert M.B., Köhler C. and Werner J.H. (2001). Nanocrystalline silicon from hot-wire depositiona photovoltaic material? J. Non-Cryst. Solids 395, 163168. [ Links ]
2. Pan B.C. and Biswas R. (2004). Simulation of hydrogen evolution from nano-crystalline silicon. J. Non-Cryst. Solids 333, 4447. [ Links ]
3. Tamir S. and Berger S. (2000). Electroluminescence and electrical properties of nano-crystalline silicon. Mater. Sci. Engng. B. 6970, 479483. [ Links ]
4. Ziegler Y., Daudrix V., Droz C., Platz R., Wyrsch N. and Shah A. (2001). More stable low gap a-Si:H layers deposited by PE-CVD at moderately high temperature with hydrogen dilution. Solar Ener. Mater. Solar Cell. 66, 413419. [ Links ]
5. Bauer S., Schröder B. and Oechsner H. (1998). The effect of hydrogen dilution on the microstructure and stability of a-Si:H films prepared by different techniques. J. Non-Cryst. Solids 227230, 3438. [ Links ]
6. Koh J., Fujiwara H., Collins R.W., Lee Y. and Wronski C.R. (1998). Microstructural evolution of a-Si:H prepared using hydrogen dilution of silane studied by real time spectroellipsometry. J. Non-Cryst. Solids 227230, 7377. [ Links ]
7. Cabarrocas R.I, Layadi N., Drevillon B. and Solomon I. (1996). Microcrystalline silicon growth by the layer-by-layer technique: long term evolution and nucleation mechanisms. J. Non-Cryst. Solids 198200, 871874. [ Links ]
8. Zhu M., Guo X., Chen G., Han H., He M. and Sun K. (2000). Microstructures of microcrystalline silicon thin films prepared by hot wire chemical vapor deposition. Thin Solid Films 360, 205212. [ Links ]
9. Gracin D., Juraic K., Dubcek P., Gajovic A. and Bernstorff S. (2006). The nano-structural properties of hydrogenated a-Si and SiC thin films alloys by GISAXS and vibrational spectroscopy. Appl. Surf. Sci. 252, 55985601. [ Links ]
10. Gracin D., Juraic K., Dubcek P., Gajovic A. and Bernstorff S. (2005) Analysis of the nano-structural properties of thin film siliconcarbon alloys. Vacuum 80, 98101. [ Links ]
11. Zhou B., Liu F., Gu J., Zhang Q., Zhou Y. and Zhu M. (2006). Nano-structure in micro-crystalline silicon thin films studied by small-angle X-ray scattering. Thin Solid Films 501, 113116. [ Links ]
12. Ray P.P., Gupta N.D., Chaudhuri P., Williamson D.L., Vignoli S. and Longeaud C. (2002). Properties of Si:H thin films deposited by rf-PECVD of silaneargon mixtures with variation of the plasma condition. J. Non-Cryst. Solids 299302, 123127. [ Links ]
13. Martin J.E. and Hurd A.J. (1987). Scattering from fractals. J. Appl. Cryst. 20, 6178. [ Links ]
14. Teixeira J. (1988). Small-angle scattering by fractal systems. J. Appl. Cryst. 21, 781785. [ Links ]
15. Tsu D.V., Chao B.S., and Ovshinsky S.R., Guha S. and Yang J. (1997). Effect of hydrogen dilution on the structure of amorphous silicon alloys. Appl. Phys. Lett. 71, 13171319. [ Links ]
16. Koh J., Ferlauto A.S., Rovira P.I., Wronski C.R. and Collins R.W. (1999). Evolutionary phase diagrams for plasma-enhanced chemical vapor deposition of silicon thin films from hydrogen-diluted silane. Appl. Phys. Lett. 75, 22862288. [ Links ]
Received 30 January 2007. Accepted 2 March 2009.