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Journal of Nanomaterials
Volume 2012 (2012), Article ID 528256, 9 pages
Orientation of One-Dimensional Silicon Polymer Films Studied by X-Ray Absorption Spectroscopy
1Quantum Beam Science Directorate, Japan Atomic Energy Agency, Tokai-mura, Naka-gun, Ibaraki 319-1195, Japan
2Department of Chemistry and Applied Chemistry, Faculty of Science and Engineering, Saga University, Honjo-1, Saga 840-8502, Japan
Received 28 May 2012; Revised 7 August 2012; Accepted 20 August 2012
Academic Editor: Yanqiu Zhu
Copyright © 2012 Md. Abdul Mannan 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.
Molecular orientations for thin films of one-dimensional silicon polymers grown by vacuum evaporation have been assigned by near-edge X-ray absorption fine structure (NEXAFS) using linearly polarized synchrotron radiation. The polymer investigated was polydimethylsilane (PDMS) which is the simplest stable silicon polymer, and one of the candidate materials for one-dimensional molecular wire. For PDMS films deposited on highly oriented pyrolytic graphite (HOPG), four resonance peaks have been identified in the Si K-edge NEXAFS spectra. Among these peaks, the intensities of the two peaks lower-energy at 1842.0 eV and 1843.2 eV were found to be strongly polarization dependent. The peaks are assigned to the resonance excitations from the Si 1s to and px orbitals localized at the Si–C and Si–Si bonds, respectively. Quantitative evaluation of the polarization dependence of the NEXAFS spectra revealed that the molecules are self-assembled on HOPG surface, and the backbones of the PDMS are oriented nearly parallel to the surface. The observed orientation is opposite to the previously observed results for PDMS on the other surfaces such as oxide (indium tin oxide) and metal (polycrystalline copper). The flat-lying feature of PDMS observed only on HOPG surface is attributed to the interaction between CH bonds in PDMS and π orbitals in HOPG surface.
Polysilanes composed of silicon-silicon backbone have excellent properties in comparison with carbon-based polymers . Polysilanes are considered to be an ideal one-dimensional (1D) molecular wire with high electric conductivity since the σ electrons in polysilanes are delocalized comparable to those of π electrons in the conjugated carbon-based polymers. It has also been predicted that the polysilanes possess electronic structure similar to direct band-gap semiconductor .
Among polysilanes, polydimethylsilane (PDMS) is the most fundamental stable silane and considered to be one of the candidate materials in the future nanotechnology with high quality. One of the features of PDMS is the high electric conductivity along the 1D chain due to the smaller HOMO-LUMO band gaps . Thus PDMS and its derivatives are expected to be used as extremely thin wires in molecular electronics. Furthermore, thin films of PDMS possess outstanding physical properties such as photoconductivity and ultraviolet electroluminescence [4–6]. It should be noted that the electric and optical properties in thin films of 1D polymer depend on the configuration of the molecular skeleton. Especially for ultrathin films around monolayer or thinner than monolayer, electric conductivity would become anisotropic depending on the molecular orientation. So it is much important to precisely determine the molecular orientation of polymers on solid surfaces.
It has been found that thin films of silicon polymers synthesized by vacuum evaporation are sometimes self-ordered on solid surfaces. It has been reported that the direction of the backbone of silicon polymers on silicon becomes perpendicular to the surface at high substrate temperature and low evaporation rate [7, 8]. On the other hand, the direction becomes parallel to the surface at low substrate temperature with high evaporation rate [9–12]. In these works, X-ray diffraction was mainly used to determine the structures of the film, so the thickness of the layer is fairly thick in the order of μm. These works provide bulk crystal structures rather than molecular orientations in a thin film. Scanning tunnelling microscopy (STM) study confirmed the formation of self-assembled PDMS films of which the silicon backbone chain was perpendicular in respect to the basal plan of graphite substrate . However, STM images gave information about the image of the surface morphology, so the precise titled angle of the PDMS molecules with respect to the backbone configuration and substrate surface has not thoroughly been investigated yet.
In the previous paper, we have investigated the molecular orientation of PDMS films grown on indium tin oxide (ITO) surface which practically used transparent substrate with high electric conductivity. We found that the backbone of the Si–Si bond of PDMS molecules is perpendicularly oriented on the ITO surface, and the polymer has a helical conformation rather than zigzag structure with polar angle around 40° .
In this paper, we present the results for the orientation of PDMS films grown on highly oriented pyrolytic graphite (HOPG) substrate which is one of the ideal materials with completely flat and inert surface. The results are compared with the previously obtained ones on the different substrates, and the origin of the difference in the orientation is discussed.
2. Experimental Method
2.1. Experimental Setup
All the experiments were performed in situ at the end station of beam line 27A (BL-27A) of the Photon Factory, High Energy Accelerator Research Organization (KEK-PF). Details of the BL-27A were reported elsewhere . Briefly, double crystals of In Sb(111) were used as a monochromator. The total energy resolution of this monochromator was 0.90 eV at 1.84 keV (Si K-edge). The synchrotron radiation (SR) beam was generated from the bending magnet, and it was linearly polarized in the horizontal direction. The typical photon flux was ~1010 photons·cm−2·s−1.
The end station of the BL-27A has two ultrahigh vacuum chambers: (i) a main chamber for X-ray photoelectron spectroscopy (XPS) and NEXAFS measurements and (ii) a preparation chamber for vacuum evaporation. The base pressure of both the chambers was in the order of 1 × 10−8 Pa. The main chamber consisted of a five-axis manipulator, a hemispherical electron energy analyzer (VSW Co. Class-100) for XPS measurements. In the preparation chamber, a vacuum evaporator and a sample transfer systems were installed. For XPS measurements, the X-rays were irradiated at 55 degree from surface normal, and a take-off direction of photoelectrons was surface normal.
The vacuum evaporator consisted of a quartz crucible surrounded by spiral-type tungsten filament. The crucible was floated at +1.5 kV while the filament was grounded. Therefore, the crucible was heated by the electron bombardment. The distance between the crucible and the substrate was 15 cm. A shutter electrically isolated from the ground was equipped with it in order to control the evaporation rate of the source material. Since some of the evaporated molecules are ionized due to the surface ionization, a positive current was observed at the shutter. Thickness of the films was precisely determined by the product of the shutter current and the evaporation time which was calibrated by XPS measurements.
2.2. Film Synthesis
The source powder material purchased from GELEST Inc. was polydimethylsilane (PDMS) [Si(CH3)2]n. The average molecular weight of the PDMS is 2000 so the number of silicon atoms in a PDMS molecule was about 28. Fresh surface of the HOPG was obtained by cleaving in atmosphere, and it was attached on a sample holder by carbon tape and then immediately transferred into the preparation chamber.
The PDMS powder was put in the quartz crucible where the crucible was heated by the bombardment of 1.5 keV electrons from the backside. It was confirmed that the evaporation temperature of the crucible measured by a thermocouple was 250°C. The evaporation was performed for 5 min to 15 min at the working pressure of 2.2 × 10−5 Pa. The filament current was 4.1 A, whereas the shutter current was 500 pA. The substrate was kept at room temperature during deposition. We have measured the Si 1s and C 1s peaks in the XPS spectrum for the deposited samples, and then the thickness was calculated by the peak intensity ratio using photoionization cross-section  and inelastic mean free-paths (IMFP’s)  (see Section 3.1).
The electronic structure and molecular orientation were investigated by XPS and NEXAFS measurements. The NEXAFS spectra were taken with the total electron yield mode by recording the sample current. The total electron yields were normalized by the photon flux that was monitored by the current of aluminium foil located in front of the sample. The sample was horizontally located, and it was rotated around the vertical axis for the measurements of the polarization dependences.
Irradiation of intense X-rays on organic molecules would sometimes induce the decomposition. In order to check the radiation-induced decomposition, we have irradiated the PDMS films by SR X-rays for one day (total photon fluence was about 1015 photons·cm−2). However, neither XPS nor NEXAFS spectra changed probably because of the low photoabsorption cross-sections of silicon and carbon (in the order of 104 barn). So we can ignore the radiation-induced decomposition of molecules in the present experiments.
3. Results and Discussion
3.1. Electronic Structure and Film Thickness by XPS Analysis
Figure 1 shows XPS wide scan spectra for the PDMS films with two different deposition times. The XP spectrum for a clean HOPG surface before the deposition is also shown as a bottom spectrum. First, the thicknesses of the PDMS films is determined on the basis of the XPS peak intensities.
The intensities of Si 1s photoelectrons () and C 1s photoelectrons () were calculated by using the following two equations  supposing that the film is homogeneous: where is the constant depending on detection efficiency of the electron energy analyser, σ (barn) is photoionization cross-section, λ (nm) is IMFP of the photoelectrons of the respective elements, is the atomic concentration of the element in the material indicated as subscripts, and d (nm) is the thickness of the PDMS film. The values used for the calculation of σ for Si 1s and C 1s at 2.2 keV photons were 1.02 × 105 and 5.0 × 103 barns, respectively . The Figure 1(a) shows the relationship between the thickness d (nm) and the peak intensity ratio of Si 1s/C 1s. From the experimentally obtained Si 1s/C 1s values, the thicknesses of the PDMS films for two samples are determined to be 1.25 nm (middle spectrum) and 1.80 nm (upper spectrum).
Figure 2 shows the Si 1s XPS narrow scan for the samples with the different thickness. The sample surface was excited by the SR beam of 2.2 keV photons, and the spectra were taken at the step energy of 0.07 eV. Two sharp peaks at the binding energy of 1842.9 eV and 1840.7 eV are observed for the thin sample with the thickness of 1.25 nm. The intensity of the peak observed at 1842.9 eV becomes significantly low with the thickness (sample with the thickness of 1.80 nm). The energy of the main peak at 1840.7 eV is the same as the previously reported values for multilayered PDMS films . Also the binding energies of the C 1s peak for these two layers are located around 282.8 eV, which is similar to those for the SiC layer [19–21]. Thus the main peak observed at 1840.7 eV is surely attributed to the silicon atoms in PDMS molecules. One of the biggest questions is that why two peaks are found in the Si 1s spectra. We confirmed that the peak splitting is not due to the decomposition of PDMS by X-ray irradiation because the peak structures have never changed even after long-time irradiation. It was reported that the peaks for the low-dimensional Si always stay at the higher binding energy region than that for the bulk-Si [22, 23]. We consider that low-dimensional feature for thin film might be one of the reasons for the peak found at 1842.9 eV . So the possible explanations are that (i) the peak energy at 1842.9 eV is due to the formation of monolayer and (ii) the peak energy at 1840.7 eV is due to the formation of multilayer of the PDMS molecules.
Since XPS could not provide information regarding molecular orientation of chemical bonds, NEXAFS has been applied in order to elucidate molecular orientation and quantitative evaluation of polar angle with respect to the backbone configuration of PDMS in the subsequent section.
3.2. Quantitative Evaluation of Molecular Orientation by Si K-Edge NEXAFS Analyses
Figures 3(a) and 3(b) show Si K-edge NEXAFS spectra for the PDMS films with different thickness. The spectra were recorded at different incidence angles θ of the SR beam. In the spectra, polarization dependence of NEXAFS has been clearly observed for both samples. At the nearly normal incidence (θ = 80°) of the SR, four peaks marked by A, B, C, and D are observed. The photon energies of the four peaks are located at 1842.0, 1843.2, 1845.2, and 1848.6 eV, all of which are found to be the same as those observed for the samples deposited on ITO surface .
Among the four peaks, the peaks A and B are strongly polarization dependent. The intensity of the peak A is increased while the intensity of peak B is decreased at the small incidence angle of the SR beam (θ = 10°). For comparison, Si K-edge NEXAFS spectra for the PDMS films on ITO surface with different thickness are shown in Figure 4 . It has been observed that the intensity of peak A decreased and the intensity of peak B increased when the incident angle becomes low (θ = 10°). In the previous paper, we have concluded that the backbone of the PDMS, that is, the Si–Si bond is perpendicularly oriented on the ITO surface . The present result for the polarization dependence of PDMS on HOPG is really opposite to that of PDMS on ITO. The result suggests that the Si–Si bond is parallel to the HOPG surface.
Let us go back to Figure 3. As to the peaks in Si K-edge NEXAFS spectra for Si polymer, the origin of the resonance peaks for PDMS or similar compounds has been experimentally and theoretically assigned [3, 24]. According to McCrary et al., the low-energy resonance peak A at 1842.0 eV is due to the resonance excitation from the Si 1s to orbital localized at the Si–C bond, and the high-energy resonance peak B at 1843.2 eV is attributed to the resonance excitation from the Si 1s to orbital along the Si–Si bond . Since higher-energy peaks C and D are not apparently polarization dependent, we shall hereafter concentrate on the polarization dependences of the peaks A and B.
To our knowledge, there have been no experimental works for precise determination of the angle for silicon polymer films on solid surface. Concerning this fact, it is very important to elucidate the exact polar angle of the PDMS molecule. As seen, a remarkable feature observed in the peaks A and B is the clear polarization dependence of their intensity. The peak intensity for the NEXAFS spectra using SR beam of the electric field could be expressed by the following equation : where is the direction of the final state orbital, and δ is the angle between and . Therefore, considering the polarization dependences as found in the Figure 3, we can suppose that the final state orbitals represented by the peak A are perpendicular while those represented by the peak B are parallel to the basal plane of the HOPG. In this viewpoint, the σ* orbitals localized at the Si–C bond (hereafter we denote ) are almost perpendicular, and the σ* orbitals localized at the Si-Si bond (hereafter we denote ) are parallel to the HOPG substrate surface.
In order to get more quantitative clarification of the tilted angles, we estimate the angles of and with respect to the silicon backbone configuration and the substrate surface. In that case, the resonance intensity in the NEXAFS spectrum could be simplified by the following equation: where Ip and Iv are the transition intensities associated with the angle-dependent matrix elements parallel and vertical to the electric field vector, respectively, A is the normalization, and is the polarization factor . The polarization factor of the SR beam under the present experimental condition was estimated to be about 0.95. The PDMS molecule on the HOPG surface has symmetry higher than threefold, so the intensities can be simply expressed by the following four equations: in the case of vector type orbital, the equation becomes In the case of plane type orbital, the equation becomes where α is the polar angle, that is, the angle between the surface normal and the vector-type orbital (peak B). It should be noted that α is the same as the angle between surface and the Si–Si bond. γ is also the polar angle that is, the angle between the surface normal and the normal direction of the plane-type orbital (peak A). The value of γ is the same as the angle between surface and Si–C bond. The definition of the polar angles α and γ is shown in the Figure 5.
Figures 6(a) and 6(b) show the normalized peak intensity of the peaks A and B of the NEXAFS spectra as a function of the incident angle (θ) of the SR beam. The details of the normalization procedure have been described in the caption of Figure 6. The spectrum taken at the small incidence angle (θ = 10°) shows broad feature. It is seen that the intensity of the peak A decreased, while the intensity of the peak B increased when the spectra were taken at the incidence angle θ = 80° (See Figure 3). Therefore, the areas of the peaks A and B found strongly polarization dependent are calculated by peak deconvolution using Gaussian-curve fitting technique. The normalized intensities of the peaks A and B are plotted as filled circles with solid line which are shown in Figure 6.
It has been observed that the experimental data for both the samples almost follow the line with the polar angle ~65°. We already discussed the standing-up orientation in more detail on the basis of the zigzag and helical conformation of the PDMS films grown on ITO surface . We proposed that the multilayer film composed of helix structure was perpendicularly oriented on the ITO surface with the polar angle of around 40°. Present results confirmed that the experimental values of the polar angle for both the vector and plane type orbitals follow the theoretical line around 65° (See Figures 6(a) and 6(b)).
If the structure is flat-lying helical, α equals 48.5 degree, and γ equals 41.5 degree. These angles are just complementally angles of those of the standing-up helical configuration. On the other hand, for the flat-lying zigzag configuration, there are roughly two cases. One is that the Si–C plane is perpendicular to the surface. In this case, Si atoms locate close and far from the surface one by one. For this configuration, the α equals 54.5° and γ equals 0°. The second case is that the Si–Si bond is parallel to the surface. In this case, all of the Si atoms are close to the surface. For this configuration, α equals 90° and γ equals 0°.
The experimental data show that α equals 65°, and γ equals 65°. It is wonder that the values are not exactly the same as those of the flat-lying helical structure. But if the configuration is flat-lying zigzag, then at least γ value should be nearly 0 for both the cases. So we can suppose that the configuration is flat-lying helical structure with the polar angle of around 65°.
A question might be raised as why the orientations of the PDMS molecules are opposite between HOPG and ITO surfaces. At present, we cannot give a definite answer to this interesting phenomenon. One plausible speculation about standing-up configuration is as follows.
We have also investigated the orientation of PDMS on other substrates such as polycrystalline copper, and it was found that the backbones are perpendicular to the surface. As to the flatness of the surface, we observed that the ITO surface is vertically undulated in the order of 10 nm . The surface of copper seems to be also undulated in larger scale. Therefore, the first layer of PDMS on the ITO and Cu surfaces cannot lie down due to the stress in the molecular backbone. This is the reason why the PDMS molecules stand up on a rough surface. On the other hand, HOPG has perfectly flat surface without defects and steps, so the first layer of PDMS can lie flat along the surface. It is considered that the succeeding over layers follows the orientation of the first layer.
As to the question why PDMS molecules lie flat only on HOPG surface, one plausible explanation is the relatively strong interaction between CH bonds in PDMS and π orbitals (CH/π interaction) at the HOPG surface. The CH/π interaction is a kind of hydrogen bond operating between a soft acid CH and a soft base π-system like not only benzenes but graphites, fullerenes, and nanotubes. Nishio et al. have reported that the CH/π interaction exists as ubiquitous force and stressed the importance of the CH/π interaction in various fields of chemistry [27–29]. As to the solid surface, Linares et al. reported the configuration of a porphyrin derivatives on graphite by scanning tunneling microscopy and molecular simulation, and they have shown that methyl groups point toward the surface of graphite, suggesting the occurrence of CH/π hydrogen bonds . In the present case, a PDMS molecule has six CH bonds in each silicon atom, and one of the CH bonds would contribute to bind with HOPG surface through the CH/π interaction.
In summary, we have investigated the molecular configuration of PDMS films deposited on HOPG surface and demonstrated that the molecular skeleton of the polymer is just parallel to the basal plane of HOPG. More detailed analysis revealed that the PDMS molecules lie flat on the HOPG surface showing helical structure with the polar angle of around 65°. Since polysilanes composed of silicon-silicon backbone are one of the candidate materials as 1D molecular wire with high electric conductivity, the present results will shed light on the future applications of polysilanes to molecular electronic devices with high quality.
We have analysed the self-assembling, electronic structure, and molecular orientation of 1D PDMS films by XPS and NEXAFS spectroscopy using linearly polarized synchrotron radiation as an excitation source. XPS confirmed the formation of monolayer and multilayer films in the samples. In the Si K-edge NEXAFS, four resonance peaks are identified of which two peaks are found to be strongly polarization dependent. On the basis of the polarization dependence of NEXAFS, finally, we found that the backbones of the PDMS molecules are nearly parallel in respect to the HOPG surface. The results are just opposite to those for our previous study which described that the backbones of the PDMS are perpendicular in respect to the ITO surface. The flat-lying feature of PDMS observed only on HOPG surface is attributed to the interaction between CH bonds in PDMS and π orbitals in HOPG surface.
The authors like to express their gratitude to staff of the KEK-PF for their enough support throughout the experiments. The research has been done with the approval of the Photon Factory Program Advisory Committee (the proposal no. PF-PAC 2009G553).
- R. West, “The polysilane high polymers,” Journal of Organometallic Chemistry, vol. 300, no. 1-2, pp. 327–346, 1986.
- J. W. Mintmire, “Conformational effects in organopolysilanes: a first-principles approach,” Physical Review B, vol. 39, no. 18, pp. 13350–13357, 1989.
- K. Seki, H. Ishii, A. Yuyama et al., “Electronic structures of polysilanes and related compounds,” Journal of Electron Spectroscopy and Related Phenomena, vol. 78, pp. 403–406, 1996.
- J. F. Rabolt, D. Hofer, R. D. Miller, and G. N. Fickes, “Studies of chain conformational kinetics in poly(di-n-alkylsilanes) by spectroscopic methods. 1. Poly(di-n-hexylsilane), poly(di-n-heptylsilane), and poly(di-n-octylsilane),” Macromolecules, vol. 19, no. 3, pp. 611–616, 1986.
- V. M. Hallmark, R. Sooriyakumaran, R. D. Miller, and J. F. Rabolt, “Studies of chain conformational kinetics in poly(di-n-alkylsilanes) by spectroscopic methods. III. Fourier transform Raman studies of unsymmetric side chain substitution,” The Journal of Chemical Physics, vol. 90, no. 4, pp. 2486–2491, 1989.
- F. C. Schilling, A. J. Lovinger, J. M. Zeigler, D. D. Davis, and F. A. Bovey, “Solid-state structures and thermochromism of poly(di-n-butylsilylene) and poly(di-n-pentylsilylene),” Macromolecules, vol. 22, no. 7, pp. 3055–3063, 1989.
- S. Furukawa and K. I. Takeuchi, “Structure and orientation of polydimethylsilane films,” Solid State Communications, vol. 87, no. 10, pp. 931–934, 1993.
- S. Furukawa, K. Takeuchi, T. Nomura, T. Yasuda, and M. Tamura, “Estimation of the physical constants of a polydimethylsilane crystal and its evaporated film,” Journal of Physics, vol. 5, no. 27, pp. 4729–4736, 1993.
- S. Furukawa, M. Obana, T. Nakamine, Y. Shirakawa, A. Sorai, and M. Tamura, “Structure and optical properties of ternary Si:C:H films prepared by evaporation of organo-polysilane,” Journal of Physics, vol. 4, no. 22, pp. 5167–5172, 1992.
- K. I. Takeuchi, M. Mizoguchi, M. Kira, M. Shimana, S. Furukawa, and M. Tamura, “Orientation of films prepared by the evaporation of poly(dimethyl silane),” Journal of Physics, vol. 6, no. 49, pp. 10705–10712, 1994.
- S. Furukawa, “Structure and orientation control of organopolysilanes and their application to electronic devices,” Thin Solid Films, vol. 331, no. 1-2, pp. 222–228, 1998.
- S. Furukawa and H. Ohta, “Structure and orientation of vacuum-evaporated poly(di-methyl silane) film,” Thin Solid Films, vol. 438-439, pp. 48–55, 2003.
- M. Gröppel, W. Roth, N. Elbel, and H. von Seggern, “Self-assembly of organopolysilanes on graphite: a scanning tunneling microscopy study,” Surface Science, vol. 323, no. 3, pp. 304–310, 1995.
- M. A. Mannan, Y. Baba, T. Sekiguchi et al., “Self-ordering of silicon polymer thin film grown on indium tin oxide surface investigated by X-ray absorption spectroscopy,” Journal of Electron Spectroscopy and Related Phenomena, vol. 181, no. 2-3, pp. 242–248, 2010.
- H. Konishi, A. Yokoya, H. Shiwaku et al., “Synchrotron radiation beamline to study radioactive materials at the Photon Factory,” Nuclear Instruments and Methods in Physics Research A, vol. 372, no. 1-2, pp. 322–332, 1996.
- J. H. Scofield, “Theoretical photoionization cross section from 1 to 1500 keV,” Livermore UCRL 51326, Lawrence Livermore Laboratory, Livermore, Calif, USA, 1973.
- M. P. Seah and W. A. Dench, “Quantitative electron spectroscopy of surfaces: a standard data base for electron inelastic mean free paths in solids,” Surface and Interface Analysis, vol. 1, no. 1, pp. 2–11, 1979.
- Y. Baba, T. Sekiguchi, I. Shimoyama, and K. G. Nath, “Structures of sub-monolayered silicon carbide films,” Applied Surface Science, vol. 237, no. 1–4, pp. 176–180, 2004.
- K. Sakamoto, D. Kondo, Y. Ushimi et al., “Temperature dependence of the electronic structure of films adsorbed on Si(001)-(2x1) and Si(111)-(7x7) surfaces,” Physical Review B, vol. 60, no. 4, pp. 2579–2591, 1999.
- T. M. Parrill and Y. W. Chung, “Surface analysis of cubic silicon carbide (001),” Surface Science, vol. 243, no. 1–3, pp. 96–112, 1991.
- G. Dufour, F. Rochet, F. C. Stedile et al., “SiC formation by reaction of Si(001) with acetylene: electronic structure and growth mode,” Physical Review B, vol. 56, no. 7, pp. 4266–4282, 1997.
- K. G. Nath, I. Shimoyama, T. Sekiguchi, and Y. Baba, “Chemical-state analysis for low-dimensional Si and Ge films on graphite,” Journal of Applied Physics, vol. 94, no. 7, pp. 4583–4588, 2003.
- K. G. Nath, I. Shimoyama, T. Sekiguchi, and Y. Baba, “Synchrotron radiation photoabsorption and photoemission spectroscopy for thermal-induced reoriented Si polymer,” Journal of Electron Spectroscopy and Related Phenomena, vol. 144-147, pp. 323–326, 2005.
- V. R. McCrary, F. Sette, C. T. Chen et al., “Polarization effects in the valence and inner-shell spectra of poly(di-n-hexylsilane),” The Journal of Chemical Physics, vol. 88, no. 9, pp. 5925–5933, 1988.
- J. Stöhr, NEXAFS Spectroscopy, vol. 25 of Springer Series in Surface Sciences, Springer, Berlin, Germany, 1996.
- J. Deng, Y. Baba, T. Sekiguchi, N. Hirao, and M. Honda, “Effect of substrates on the molecular orientation of silicon phthalocyanine dichloride thin films,” Journal of Physics Condensed Matter, vol. 19, no. 19, Article ID 196205, 2007.
- M. Nishio, “CH/π hydrogen bonds in crystals,” CrystEngComm, vol. 6, pp. 130–158, 2004.
- M. Nishio, Y. Umezawa, K. Honda, S. Tsuboyama, and H. Suezawa, “CH/π hydrogen bonds in organic and organometallic chemistry,” CrystEngComm, vol. 11, no. 9, pp. 1757–1788, 2009.
- M. Nishio, “The CH/π hydrogen bond in chemistry. Conformation, supramolecules, optical resolution and interactions involving carbohydrates,” Physical Chemistry Chemical Physics, vol. 13, no. 31, pp. 13873–13900, 2011.
- M. Linares, P. Iavicoli, K. Psychogyiopoulou et al., “Chiral expression at the Solid-Liquid interface: a joint experimental and theoretical study of the self-assembly of chiral porphyrins on graphite,” Langmuir, vol. 24, no. 17, pp. 9566–9574, 2008.