- Nano Express
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Determination of InN/Diamond Heterojunction Band Offset by X-ray Photoelectron Spectroscopy
© Shi et al. 2010
Received: 26 July 2010
Accepted: 10 September 2010
Published: 30 September 2010
Diamond is not only a free standing highly transparent window but also a promising carrier confinement layer for InN based devices, yet little is known of the band offsets in InN/diamond system. X-ray photoelectron spectroscopy was used to measure the energy discontinuity in the valence band offset (VBO) of InN/diamond heterostructure. The value of VBO was determined to be 0.39 ± 0.08 eV and a type-I heterojunction with a conduction band offset (CBO) of 4.42 ± 0.08 eV was obtained. The accurate determination of VBO and CBO is important for the application of III-N alloys based electronic devices.
Among the group III nitrides, InN is of great interest because of its extremely high predicted electron mobility , small effective mass [2, 3], and large electron saturation drift velocity . With the latest progress in improving the film quality these years, InN film has been considered to be able to meet the requirements for application to practical devices [5, 6]. It is expected to be a highly promising material for the fabrication of high performance,high electron mobility transistor (HEMT) due to its electronic properties. Moreover, the re-evaluation of the InN bandgap and subsequent findings [7, 8] have opened up interesting opportunities for using InN in new applications, such as high-efficiency solar cells , solid state lighting [10–12], and 1.55 μm emission for fiber optics [13, 14]. As the hardest material with high optical transparency from ultraviolet to infrared range, diamond is an excellent transparent window for InN based photoelectric devices mentioned above. It can also be used as lens coatings for infrared transmissions. The bandgap of diamond at room temperature is ~5.45 eV, so it is a promising carrier confinement layer for InN based HEMT, which requires a larger bandgap barrier to confine electrons. Furthermore, because of the combination of its unique electronic and thermal properties, diamond plays a vital or somewhat irreplaceable role in some special applications, such as in abominable environments and military fields. Up to now, the GaN/diamond system has already been studied by a lot of groups [15, 16]. However, there is lack of experimental data available on the interface band alignment parameters for InN/diamond system. X-ray photoelectron spectroscopy (XPS) has been demonstrated to be a direct and powerful tool for measuring the valence band offsets (VBOs) of heterojunctions [6, 17–19]. In this letter, we report an experimental measurement of the VBO in InN/diamond heterojunction by XPS.
Three samples were used in our XPS experiments, namely, a 350-nm-thick InN layer grown on c-plane sapphire, a 2-mm-thick single-crystal diamond synthesized at high temperature and high pressure(HTHP), and a ~5-nm-thick InN grown on diamond. InN films in this study were grown by horizontal low-pressure metal-organic chemical vapor deposition, as reported elsewhere .The crystal structures were characterized using the high-resolution X-ray diffraction (HRXRD) apparatus at Beijing Synchrotron Radiation Facility (BSRF). The incident X-ray beam is monochromized to 0.154791 nm by a Si (111) monocrystal. According to the XRD results, single-crystal diamond (400) and wurtzite InN (002) were obtained. Both diamond and InN in our experiment are undoped, while the InN films are unintentionally n-type doped, with carrier concentration and Hall mobility being 6.2 × 1019 cm-3 and 370 cm2/Vs respectively, as determined by Hall effect measurement in the InN/sapphire film.
The XPS measurements were performed on a PHI Quantera SXM instrument with Al Kα (energy 1486.6 eV) as the X-ray radiation source, which had been carefully calibrated utilizing work function and Fermi energy level (EF). A large number of electrons are excited and emitted from the sample during the test, so the sample is always positively charged and the consequent electric field can affect the measured kinetic energy of photoelectron. A low-energy electron flood gun was utilized to achieve charge compensation. The total energy resolution of this XPS system is about 0.5 eV, and the accuracy of the observed binding energy is within 0.03 eV after careful calibration. The measurements were as follows: first, low-resolution survey scan mode was used to determine which elements were present on the sample surfaces. Then, very-high-resolution spectra were acquired to determine the binding energy (i.e., chemical state) in the survey spectra. Since only the relative energy position in each sample is needed to determine the VBO, the absolute energy calibration for a sample has no effect on the universal energy reference.
Results and Discussion
XPS CL spectra fitting results and VBM positions obtained by linear extrapolation of the leading edge to the extended base line of the VB spectra
Binding energy (eV)
Here n is the carrier concentration, ε(∞) is the high frequency dielectric constant, and m* is the effective mass of the conduction electrons. Compared with the metals in his model, the carrier concentration in our sample surface is much lower, which means that only small energy separations exist between the screened and unscreened core-level components. This results in an asymmetric core-level XPS lineshape with just a weak high binding energy tail due to plasmon losses, which is consistent with our experimental results.
Based on all the arguments made above, we attribute the lower-binding energy component (443.42 eV) in Figure 1a to the "screened" final-state peak in In3d5/2 photoemission, the higher-binding energy component (445.27 eV) to the "unscreened" final-state peak, and the mid-binding energy component (444.21) to the In–O bonding. In Figure 1c, the lower-binding energy component (284.9 eV) and the higher-binding energy component (286.00 eV) are considered to be C–C bonding and C–O bonding respectively [28, 29].
In order to avoid the surface oxidation and reduce the contamination effect, the InN/diamond sample was subjected to a surface clean procedure by Ar+ bombardment with a voltage of 1 kV at a low sputtering rate of 0.5 nm/min, which alleviates damages to the sample. The reduced thickness (less than 1 nm) is calculated by the sputtering rate, and the O-related bondings were absent in cleaned InN/diamond heterojunction because of the sputtering process. In Figure 1e, the lower-binding energy component (442.59 eV) and the higher-binding energy component (443.50 eV) are attributed to be screened In–N bonding and unscreened In-N bonding respectively. Finally, in Figure 1f, we suggest assignments of screened C–C bonding and unscreened C–C bonding for the lower- (283.80 eV) and higher-binding (284.50 eV) energy components, respectively. The VBM of the two thick samples are determined to be 0.66 and 1.32 eV, respectively. All of them are summarized in Table 1.
As XPS measurements are spatially averaged due to the finite mean free path of elastic electrons (1.5–2 nm), band bending could induce a systematic error in our measurements. Due to the lattice mismatch between InN and diamond, especially the small linear pressure coefficient of InN (~0.06 meV/GPa) , the band gap change induced by the interface strain could be neglected. So the systematic error related to band bending is expected to be much smaller than the average standard deviation of 0.08 eV given above. Another factor that may affect the precision of the VBO value is the strain-induced piezoelectric field in the overlayer of the heterojunction, as described in the III-nitrides system . By using the constants and equation in Martin's work , the field magnitude is estimated to be in the order of 107 V/m. Assuming the heterojunction InN overlayer thickness of ~4 nm after Ar+ bombardment, the error of VBO induced by lattice mismatch is less than 60 meV. Besides, practically all nitride epitaxial layers are characterized by dense networks of threading defects extending from the substrates to the surfaces , the strains in pseudomorphic epi-films relieve mostly, which means the "residual" effect of piezoelectric field is greatly reduced. As a result, the strain-induced piezoelectric effect can be neglected here.
In summary, the valence band offset of the InN/diamond heterojunction has been measured by XPS. A type-I band alignment with a valence band offset of ΔE v ~ 0.39 ± 0.08 eV and conduction band offset of ΔE c ~ 4.42 eV was obtained. The accurate determination of the band alignment of InN/diamond indicates that the diamond can provide an effective carrier confinement in InN/diamond based electronic devices.
The authors are grateful to Professor Huanhua Wang and Dr. Tieying Yang in the Institute of High Energy Physics, Chinese Academy of Sciences. This work was supported by the 863 High Technology R&D Program of China (Grant Nos. 2007AA03Z402 and 2007AA03Z451), the Special Funds for Major State Basic Research Project (973 program) of China (Grant No. 2006CB604907), and the National Science Foundation of China(Grant Nos. 60506002 and 60776015).
- Polyakov VM, Schwierz F: Appl Phys Lett. 2006, 88: 032101. 10.1063/1.2166195View ArticleGoogle Scholar
- Fu SP, Chen YF: Appl Phys Lett. 2004, 85: 1523. 10.1063/1.1787615View ArticleGoogle Scholar
- Chang Y-M, Chu HW, Shen CH, Chen HY, Gwo S: Appl Phys Lett. 2007, 90: 072111. 10.1063/1.2679926View ArticleGoogle Scholar
- Bhuiyan AG, Hashimoto A, Yamamoto A: J Appl Phys. 2003, 94: 2779. 10.1063/1.1595135View ArticleGoogle Scholar
- Mahmood ZH, Shah AP, Kadir A, Gokhale MR, Ghosh S, Bhattacharya A, Arora BM: Appl Phys Lett. 2007, 91: 152108. 10.1063/1.2794788View ArticleGoogle Scholar
- Wu C-L, Shen C-H, Gwo S: Appl Phys Lett. 2006, 88: 032105. 10.1063/1.2165195View ArticleGoogle Scholar
- Davydov VY, et al.: Phys Stat Sol B. 2002, 234: 787. 10.1002/1521-3951(200212)234:3<787::AID-PSSB787>3.0.CO;2-HView ArticleGoogle Scholar
- Haller EE, Lu H, Schaff WJ: Phys Rev B. 2002, 66: 201403. 10.1103/PhysRevB.66.201403View ArticleGoogle Scholar
- Wu J, Walukiewicz W, Yu KM, Shan W, Ager JW, Haller EE, Lu H, Schaff WJ, Metzger WK, Kurtz S: J Appl Phys. 2003, 94: 6477. 10.1063/1.1618353View ArticleGoogle Scholar
- Shih CF, Chen NC, Chang CA, Liu KS: Jpn J Appl Phys. 2005, 44: L140. 10.1143/JJAP.44.L140View ArticleGoogle Scholar
- Zheng XH, Chen H, Yan ZB, Li DS, Yu HB, Huang Q, Zhou JM: J Appl Phys. 2004, 96: 1899. 10.1063/1.1769099View ArticleGoogle Scholar
- Enya Y, Yoshizumi Y, Kyono T, Akita K, Ueno M, Adachi M, Sumitomo T, Tokuyama S, Ikegami T, Katayama K, Nakamura T: Appl Phys Express. 2009, 2: 082101. 10.1143/APEX.2.082101View ArticleGoogle Scholar
- Che SB, Mizuno T, Wang X, Ishitani Y, Yoshikawa A: J Appl Phys. 2007, 102: 083539. 10.1063/1.2800843View ArticleGoogle Scholar
- Yoshikawa A, Che SB, Yamaguchi W, Saito H, Wang XQ, Ishitani Y, Hwang ES: Appl Phys Lett. 2007, 90: 073101. 10.1063/1.2456132View ArticleGoogle Scholar
- Hageman PR, Schermer JJ, Larsen PK: Thin Solid Films. 2003, 443: 9. 10.1016/S0040-6090(03)00906-4View ArticleGoogle Scholar
- Oba M, Sugino T: Jpn J Appl Phys. 2000, 39: L1213. 10.1143/JJAP.39.L1213View ArticleGoogle Scholar
- Chen J-J, Gila BP, Hlad M, Gerger A, Ren F, Abernathy CR, Pearton SJ: Appl Phys Lett. 2006, 88: 042113. 10.1063/1.2170140View ArticleGoogle Scholar
- King PDC, Veal TD, Jefferson PH, McConville CF, Wang T, Parbrook PJ, Lu H, Schaff WJ: Appl Phys Lett. 2007, 90: 132105. 10.1063/1.2716994View ArticleGoogle Scholar
- Zhang PF, Liu XL, Zhang RQ, Fan HB, Song HP, Wei HY, Jiao CM, Yang SY, Zhu QS, Wang ZG: Appl Phys Lett. 2008, 92: 042906. 10.1063/1.2839611View ArticleGoogle Scholar
- King PDC, Veal TD, Payne DJ, Bourlange A, Egdell RG, McConville CF: Phys Rev Lett. 2008, 101: 116808. 10.1103/PhysRevLett.101.116808View ArticleGoogle Scholar
- Christou V, Etchells M, Renault O, Dobson PJ, Salata OV, Beamson G, Egdell RG: J Appl Phys. 2000, 88: 5180. 10.1063/1.1312847View ArticleGoogle Scholar
- King PDC, Veal TD, Lu H, Hatfield SA, Schaff WJ, McConville CF: Surf Sci. 2008, 602: 871. 10.1016/j.susc.2007.12.026View ArticleGoogle Scholar
- Egdell RG, Walker TJ, Beamson G: J Electron Spectrosc Relat Phenom. 2003, 128: 59. 10.1016/S0368-2048(02)00207-4View ArticleGoogle Scholar
- Egdell RG, Rebane J, Walker TJ, Law DSL: Phys Rev B. 1999, 59: 1792. 10.1103/PhysRevB.59.1792View ArticleGoogle Scholar
- Payne D, Egdell R, Hao W, Foord J, Walsh A, Watson G: Chem Phys Lett. 2005, 411: 181. 10.1016/j.cplett.2005.06.023View ArticleGoogle Scholar
- Wertheim GK: Chem Phys Lett. 1979, 65: 377. 10.1016/0009-2614(79)87085-2View ArticleGoogle Scholar
- Campagna M, Wertheim GK, Shanks HR, Zumsteg F, Bank E: Phys Rev Lett. 1975, 34: 738. 10.1103/PhysRevLett.34.738View ArticleGoogle Scholar
- Ballutaud D, Simon N, Girard H, Rzepka E, Bouchet-Fabre B: Diam Relat Mater. 2006, 15: 716. 10.1016/j.diamond.2006.01.004View ArticleGoogle Scholar
- Humbert B, Hellala N, Ehrhardt JJ, Barrat S, Bauer-grosse E: Appl Surf Sci. 2008, 254: 6400. 10.1016/j.apsusc.2008.04.067View ArticleGoogle Scholar
- Wu J, Walukiewicz W, Yu KM, Ager JW III, Haller EE, Lu H, Schaff WJ, Saito Y, Nanishi Y: Appl Phys Lett. 2002, 80: 3967. 10.1063/1.1482786View ArticleGoogle Scholar
- Martin G, Botchkarev A, Rockett A, Morkoc H: Appl Phys Lett. 1996, 68: 2541. 10.1063/1.116177View ArticleGoogle Scholar
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