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Journal of Nanomaterials
Volume 2011 (2011), Article ID 579427, 7 pages
http://dx.doi.org/10.1155/2011/579427
Research Article

Characterizations of InN Thin Films Grown on Si (110) Substrate by Reactive Sputtering

Nano-Optoelectronics Research and Technology Laboratory, School of Physics, Universiti Sains Malaysia, 11800 Penang, Malaysia

Received 19 February 2011; Revised 18 April 2011; Accepted 21 May 2011

Academic Editor: Gong Ru Lin

Copyright © 2011 M. Amirhoseiny 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

Indium nitride (InN) thin films were deposited onto Si (110) by reactive sputtering and pure In target at ambient temperature. The effects of the Ar–N2 sputtering gas mixture on the structural properties of the films were investigated by using scanning electron microscope, energy-dispersive X-ray spectroscopy, atomic force microscopy, and X-ray diffraction techniques. The optical properties of InN layers were examined by micro-Raman and Fourier transform infrared (FTIR) reflectance spectroscopy at room temperature. Structural analysis specified nanocrystalline structure with crystal size of 15.87 nm, 16.65 nm, and 41.64 nm for InN films grown at N2 : Ar ratio of 100 : 0, 75 : 25, and 50 : 50, respectively. The Raman spectra indicates well defined peaks at 578, 583, and 583 cm−1, which correspond to the A1(LO) phonon of the hexagonal InN films grown at gas ratios of 100 : 0, 75 : 25 and 50 : 50 N2 : Ar, respectively. Results of FTIR spectroscopy show the clearly visible TO [E1(TO)] phonon mode of the InN at 479 cm−1 just for film that were deposited at 50 : 50 N2 : Ar. The X-ray diffraction results indicate that the layers consist of InN nanocrystals. The highest intensity of InN (101) peak and the best nanocrystalline InN films can be seen under the deposition condition with N2 : Ar gas mixture of 50 : 50.

1. Introduction

Recent research popularity indicates that InN has a large potential for photonic and high-speed electronic applications. This includes fundamental properties such as the band gap, which is important to assess the suitability of InN for multifarious device applications. The energy of the band gap can be varied by mixing the nitrides to their ternary combinations. The InN band gap had originally been specified to be around 2 eV [1], with some recent measurements suggesting alternatively a band gap of 0.7 eV [2] and 1.4-1.5 eV [3] based on photoluminescence and absorption experiments. If the band gap of InN is almost 0.7 ev, a new inoffensive high-efficiency solar cell including most of solar spectrum can be produced using only InN and its alloys. However, InN has received little attention, because high-grade single crystal InN is difficult to grow due to its low dissociation temperature [4] and less suitable substrates [5].

Silicon (Si) is a very interesting substrate material for the fabrication of InN-based devices because of the advantages in thermal and electrical conductivity as well as cost-efficient substrates and accessibility in large diameters. Recently, the growth of GaN on Si (110) substrates has been studied [6]. However, to the best of our knowledge, the growth of InN on Si (110) has not been explored. Si (110) is a surface orientation generally used in silicon technology, and the growth of InN on such substrates should be suitable for future III-N device integration.

InN films have been prepared by multiple methods such as metal organic chemical vapor deposition (MOCVD), molecular beam epitaxy (MBE), atomic layer epitaxy, radio-frequency (RF) sputtering, and direct current sputtering. MOCVD and MBE can be used to grow single crystalline InN, but they are so costly and the size of the grown epi-layer is limited. Generally, RF sputtering can be used for fabricating noncrystalline or polycrystalline InN.

Up to now, there are few works devoted to studies of the InN thin films deposition by reactive sputtering. For example, Sullivan et al. investigated the optical properties and microstructure of reactive sputtered InN thin films with spectroscopic ellipsometry [7]. Guo et al. studied the effects of substrate temperature and also nitrogen : argon (N2 : Ar) ratio on the composition and the structure of InN [8, 9]. Inoue et al. fabricated the InN thin films in pure nitrogen (N2) gas [10]. Despite these studies, the knowledge on the effects of deposition conditions on the InN films sputtered by pure N2 gas is still remain unclear. Nanocrystal solar cells are as cheap and easy to make as solar cells made from organic polymers and offer the added advantage of being stable in air, because they contain no organic materials.

In order to verify the characteristics listed above, a series of InN samples on Si (110), obtained with different N2 : Ar ratio, were fabricated and characterized in order to correlate the films properties with the N2 : Ar ratio.

2. Experimental Details

InN films were obtained at ambient temperature by reactive RF sputtering with a 13.56 MHz RF power supply and a pure 3 inch diameter Indium target with purity of 99.999% in Ar and N2 atmosphere. The mixture of gaseous compositions was varied from high N2 to 50% N2 and Ar concentrations. The deposition pressure and the RF power was maintained constant at approximately  Torr and 65 W, respectively. The base vacuum pressure was around  Torr and the target was cleaned with a 5 min presputter by Ar plasma.

The films were deposited onto -type (110) single crystalline silicon substrates. To remove the surface contamination, the Si wafers were previously cleaned by the standard RCA method [11]. Sputtering gases (Ar and N2: 99.999%) were introduced into the chamber for three different types of gas ratio (N2 : Ar = 100 : 0, 75 : 25, and 50 : 50). The growth conditions are summarized in Table 1.

tab1
Table 1: Sputtering condition for InN deposition.

The obtained films were characterized with X-ray diffraction (XRD, PAN alytical X’pert PRO MRD PW3040), atomic force microscopy (AFM, ULTR Objective), scanning electron microscopy (SEM, FESEM LEO Supra 50VP) and energy dispersive X-ray spectroscopy (EDX) attached to SEM. The optical properties of InN layers were examined by Fourier transform infrared (FTIR, Perkin Elmer Spectrum GX) and micro-Raman spectroscopy (Jobin Yvon HR 800 UV) at room temperature.

3. Results and Discussion

The morphology and nanocrystalline structure of the InN thin films deposited on Si (110) were examined by using SEM. The results are shown in Figure 1. It can be seen that the films consists of agglomerated nanocrystals. The thickness of the InN films as obtained from the SEM image cross section are approximately 0.38, 0.45, and 0.70 μm for the gas ratio of 100% N2, 75% N2, and 50% N2, respectively, as shown in Figure 2. These results clearly indicate that by adding the Ar gas during the deposition, the thickness of InN increase considerably. This fact may be determined from the fact that nitrogen has a higher electron capture ability and a lower sputtering yield than Argon, which decreases the density of plasmas. The higher density of plasma will bomb down more In particles from the target, which react with nitrogen to form more InN particles on the substrates and consequently increase the thickness of the layer [12]. Figure 3 shows the EDX spectra for the InN thin films grown on Si (110) substrates with different ratio of N2/Ar. It can be seen that the films consist of In, large amount of N, and very little O. This result suggests that the film might possibly contain some InN, In2O3 or, even InNxOy. However, the growth of In2O3 needs rigorous conditions such as high temperature and high pressure [13]. Therefore, it is difficult to obtain In2O3 by RF sputtering. The element of oxygen in all the films most probably arises from the SiO2. The Si surface is prevalently oxidized by dissolved oxygen during cleaning the substrates by RCA method. Note that the potassium element is most probably arisen from the contamination from the previous measurements.

fig1
Figure 1: SEM images of InN grown on Si (110) while the deposition gas is (a) 100% N2, (b) 75% N2-25% Ar, and (c) 50% N2-50% Ar.
fig2
Figure 2: SEM cross-section view of InN grown on Si (110) while the deposition gas is (a) 100% N2, (b) 75% N2-25% Ar, and (c) 50% N2-50% Ar.
fig3
Figure 3: EDX of InN grown on Si (110) while the deposition gas is (a) 100% N2, (b) 75% N2-25% Ar, and (c) 50% N2-50% Ar.

The 2θ/ω X-ray diffraction patterns of the InN thin films grown on Si (110) substrates at room temperature in the three types of sputtering gases are given in Figure 4. The results reveal that the three InN films grown in different gases ratio have a qualitatively similar crystalline structure. The same InN (101) and InN (100) peaks was observed in XRD 2θ spectra for the three samples, while slightly higher peak intensity was observed when the sample was deposited with N2 : Ar, 50 : 50. This means that the gas ratio directly affects the crystalline quality of InN nanostructure and with increase of the Ar gas, the intensities of the InN (101) and InN (100) diffraction peaks increased. The activation energy on the substrate surface may be declined with increasing N2 concentration, because various high-energy metal particles reach the substrate surface [9]. As a result, the crystallinity of the film degraded. A similar trend is also observed in the cases of AlN [14, 15] and GaN [16], where the crystallity degraded when the N2 content in the sputtering gas exceeds the critical values.

fig4
Figure 4: XRD spectrum of InN thin film on Si (110) substrates.

In order to obtain the detailed structure information, we calculated the crystal size of InN nanocrystals based on the XRD results, that is, by using the Scherrer formula [17] where is wavelength (in Angstrom), is the (full-width at half maximum (FWHM)) ×  , is diffraction peak angle.

Table 2 shows the dependence of FWHM of InN (101) diffraction peak and the crystal size of InN on the N2/Ar concentrations during deposition. Again, it is perceived that the higher Ar flow leads to enhanced structural order for Si (110) substrates, as displayed by the smaller FWHM attained for this case. It is well known that FWHM of the peak of XRD in 2θ-mode is affected by the grain size and the distribution of lattice constant due to the lattice distortion [8]. The FWHM of InN (101) peak decreases with the increasing of Ar gas, while the crystal size of InN nanocrystals increased.

tab2
Table 2: Full-width at half maximum (FWHM) of InN (101) diffraction peak and Crystal size of InN with different percentage of Ar gas ratio during deposition.

From Table 2, it is also can be seen that the crystal sizes of the InN films are less than 50 nm. At N2 : Ar ratio of 50 : 50 where the strongest reflection from -plane is observed, the crystal size reaches its maximum due to its smallest FWHM, and it is indicated that InN films which grew at N2: Ar ratio of 50 : 50 has the best nanocrystallite. The reason is mainly due to the higher ratio of N2: Ar will tend to create higher plasma density. Consequently, more In particles can react with N2.

To obtain further information about structure and bond formation, FTIR measurements were performed for the same InN films previously analyzed by XRD. The FTIR spectra of InN thin films grown on the Si (110) substrates are shown in Figure 5. For InN films, the feature corresponding to the E1(TO) phonon modes of the InN are clearly observed at 479 cm−1 for the deposition condition of N2/Ar gas mixture of 50 : 50, which is comparable to the reported values for wurtzite InN [18]. However, we did not observe similar peak in other gas ratio compositions. This is mainly due to the weak crystalline structure. These results are consistent with the XRD results as discussed previously.

579427.fig.005
Figure 5: InN FTIR spectra on Si (110).

Micro-Raman measurements were carried out at room temperature in backscattering geometry using an Ar-ion laser. Figure 6 illustrates Raman spectra for the grown InN film in the spectral range from 100 to 800 cm−1. The Si substrate peak is visible at 520 cm−1. For InN thin films, only the allowed phonon mode of A1(LO) is visible at 578 cm−1, 583.4 cm−1, and 583.36 cm−1, for films grown at three different types of N2 : Ar gas ratio: 100 : 0, 75 : 25, and 50 : 50, respectively. It is clear that the strongest A1(LO) is for InN which is grown in a 50 : 50, N2 : Ar gas ratio.

fig6
Figure 6: (a, b, and c) Room temperature micro-Raman spectrum of InN/Si (110) substrates in different gas ratios.

The zincblende structure (spatial group -F43 m) has only two Raman-active phonons F2(TO) and F2(LO). The wurtzite structure (spatial group -P63mc), which is the most stable, has six Raman-active phonons, A1(TO), A1(LO), E1(TO), E1(LO), and 2E2 [19]. Therefore, the A1(LO) peak which observed in the spectra indicates that the wurtzite phase must be present. Scattering intensities and phonon frequencies, determined by means of Raman spectroscopy, are sensitive to composition, presence of disorder, impurities, and the crystal quality of the structure under investigation [20]. The structural analyses of Raman spectra and comparison with the results obtained from XRD measurements allow us to conclude that InN films which grew at N2: Ar ratio of 50 : 50 has the best crystalline quality.

To characterize the surface morphology of InN films grown on Si substrate, we measured the surface roughness using AFM. Figure 7 shows the AFM images of the InN films. The films contain small grains. The surface is flat in nano scale and the root mean square (RMS) surface roughness measured by AFM are about 2.78, 2.97, and 3.32 nm over a 4000×4000 nm2 scan area, respectively, for 100%, 75%, and 50% of N2 gases. The AFM measurements agreed with SEM images, because small grain size induces a smooth surface [21].

fig7
Figure 7: AFM images of the InN film deposited on Si (110) while the deposition gas is (a) 100% N2, (b) 75% N2-25% Ar, and (c) 50% N2-50% Ar.

4. Conclusion

Nanocrystalline InN films on Si (110) have been successfully grown by RF reactive magnetron sputtering in different N2 : Ar gas ratio in ambient temperature. The structure of films was characterized by XRD, SEM, EDX, AFM, FTIR, and Raman spectroscopy. Both XRD and Raman scattering revealed that the film contains hexagonal InN. The crystalline size of the InN films calculated by the Scherrer equation are about 15.87 nm, 16.65 nm, and 41.63 nm for 100 : 0, 75 : 25, and 50 : 50 N2 : Ar proportion, respectively. The best nanocrystalline InN films with highly -axis preferred orientation were attained when the deposition gas ratio of N2: Ar was 50 : 50.

Acknowledgments

Financial support from RU Grant (no. 1001/PFIZIK/814090) and University Sains Malaysia are gratefully acknowledged. The authors thank Mr. Ooi Poh Kok for FTIR measurements.

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