PMCCPMCCPMCC

Search tips
Search criteria 

Advanced

 
Logo of scirepAboutEditorial BoardFor AuthorsScientific Reports
 
Sci Rep. 2017; 7: 44196.
Published online 2017 March 8. doi:  10.1038/srep44196
PMCID: PMC5341155

Critical increase in Na-doping facilitates acceptor band movements that yields ~180 meV shallow hole conduction in ZnO bulk crystals

Abstract

Stable p-type conduction in ZnO has been a long time obstacle in utilizing its full potential such as in opto-electronic devices. We designed a unique experimental set-up in the laboratory for high Na-doping by thermal diffusion in the bulk ZnO single crystals. SIMS measurement shows that Na concentration increases by 3 orders of magnitude, to ~3 × 1020 cm−3 as doping temperature increases to 1200 °C. Electronic infrared absorption was measured for Na-acceptors. Absorption bands were observed near (0.20–0.24) eV. Absorption bands blue shifted by 0.04 eV when doped at 1200 °C giving rise to shallow acceptor level. NaZn band movements as a function of doping temperature are also seen in Photoluminescence emission (PL), Photoluminescence excitation (PLE) and UV-Vis transmission measurements. Variable temperature Hall measurements show stable p-type conduction with hole binding energy ~0.18 eV in ZnO samples that were Na-doped at 1200 °C.

Invention of GaN based blue light-emitting diode (LED)1 has benefitted the mankind as it has been used for making short-wavelength LEDs and lasers diodes (LDs). GaN success has fueled the search for the other cheap and environment friendly potential materials as the demands of illumination, and digital information storage is rapidly increasing. ZnO, with a direct band gap of 3.37 eV at room temperature (RT), attracts considerable attention because of its promising applications for blue-UV LED, diode lasers and spintronics2,3,4,5,6,7. In ZnO the free exciton binding energy is 0.060 eV, which makes the excitons stable at RT8. ZnO bandgap can also be tuned from 3 eV to 4.5 eV by Cd and Mg alloying, respectively9. ZnO turns red by annealing in Zn or Ti environment and the reason has been attributed to oxygen vacancies and hydrogen complexes10,11,12. ZnO has a broad green luminescence band and scientists have no consensus on its origin13,14. N-type conductivity in ZnO has been due to the impurities, point defects and hydrogen as unintentional donor15,16. N-type ZnO doping can be done easily but stable and reliable p-type doping has been a challenge17,18. Look et al.19, and Tsukazaki et al.20, reported shallow p-type conduction and p-n junction devices in nitrogen doped ZnO thin films but the realization of ZnO based p-n devices could not be achieved in last 10–15 years. This cast doubt over the stability and the reproducibility of the most promised nitrogen as a shallow acceptor in ZnO. Recently Lyons et al.21, showed by the first-principles calculations that nitrogen is a deep acceptor, with an high ionization energy of 1.3 eV and can’t lead to p-type conduction in ZnO. Tarun et al.22, experimentally showed similar results in number of bulk ZnO crystals and found that nitrogen is too deep acceptor. There are a number of other reports on p-type ZnO and p-n devices23,24,25 however, reliability of p-type ZnO remains controversial26,27. It seems, somehow acceptor doping in ZnO thin films could not produce a stable, shallow and reproducible p-type conduction and now p-type doping in bulk ZnO has to be explored aggressively. P-type doping in bulk ZnO can be realized during the growth or by post processing. Some other interesting p-type oxide semiconductors have been reported28,29,30 recently with a possibility of wide range of applications. However, they can’t be useful for UV/blue light related emission due to the unsuitability of the band gap. Recent, developments on nano scale ZnO also seem very promising and can potentially impact opto-electronic industry31,32,33,34,35,36,37,38.

Meyer et al.39 showed that Na, incorporated by thermal diffusion can also result in relatively shallow acceptors. They carried Na-diffusion by using salts (Na2CO3, NaOH and Li3N) at <900 °C in the bulk ZnO crystals and Na-solubility was ~1017 cm−3. Recently Parmar et al.40 showed the substitutional Na doping in the bulk ZnO crystals using positron annihilation spectroscopy that gave NaZn broad level PL emission peak at ~0.27 eV. Na-doping was done at 900 °C in air using Na2CO3 salt. Na concentration and RT resistivity was ~(1–3.5) × 1017 cm−3 and (104–105) ohm-cm, respectively in these Na-doped ZnO crystals. Hall measurement was not possible due to the high resistivity and low Hall voltage on these ZnO crystals. Few other groups have reported their experimental work and first-principles calculations for alkali metals doping (Li, Na, and K) in ZnO41,42,43,44. Park et al.45 calculation found substitutional Na in ZnO has ~0.17 eV ionization energy. Du and Zhang46, using hybrid density-functional calculations, found Na-acceptor levels ~0.30 eV. But no studies have been reported on increasing Na-acceptor concentration and their correlation to Na-acceptor level in ZnO crystals. The increase in Na-acceptor concentration was required to realize p-type bulk ZnO crystals. Here we report Na-doping at high temperature (1000 °C −1200 °C) under vacuum environment using Na-metal source. This doping method leads to the increase up to ~3 orders of magnitude (~3 × 1020 cm−3) in Na-acceptor concentration. Such a high doping concentration lowers the hole activation energy by moving Na-acceptor level close to the valence band and thus achieving shallow p-type Hall conduction in ZnO crystals.

Experimental Methods and Results

Na-doping

Melt grown ZnO bulk single crystals (10 mm × 10 mm × 0.5 mm) were used for Na-doping and Na-metal (Alfa Aeser, 99.95%) was used as a doping source. Na-doping was carried in a laboratory built HV chamber for doping purposes, with in housed HV button heater along with two K-type thermocouples. One thermocouple was near the Na-source while the other one was on the heater. Na-metal was placed in an Alumina boat and ZnO crystal was mounted on the heater (Supplementary Figure S1). The position of the heater and Na-metal was aligned vertically. The distance between the heater and the Na-source was optimized to achieve the average temperature of ~(70–90)°C near Na-source, while the heater was at 1000 °C–1200 °C. The heater was mounted on a manipulator to have the freedom to move it vertically and horizontally to the desired distance from Na-source. The measured optimized distance was 4”– 6” for Na-doping temperatures ranges. This unique experimental set up with the single heater was designed to evaporate Na and dope ZnO, simultaneously. The doping chamber was evacuated to ~(10−4–10−5) torr and the vacuum valve of the chamber was closed prior to the start of Na-doping. Na-doping was done at 1000 °C, 1100 °C, and 1200 °C on ZnO crystals for ~24 hours each.

Secondary-ion mass spectrometry

Secondary-ion mass spectrometry (SIMS) was performed to examine the incorporation and concentration of Na-dopants. SIMS depth profile measurements of Na-doped ZnO crystals are shown in Fig. 1. These SIMS measurements show the depth profile of Na in excess of 8 microns and with Na concentration ~1 × 1020 cm−3 when doping was done at 1200 °C. SIMS Na-detection limit was >5 × 1015 atoms cm−3 and Na was below the detection limit in the control ZnO crystal (annealed at 1200 °C in vacuum).

Figure 1
Secondary ion mass spectroscopy (SIMS) of Na-doped ZnO crystals.

Photoluminescence Measurements

Photoluminescence emission (PL) spectra were collected at RT using excitation wavelength of 325 nm. Broad PL emission was collected in Na-doped samples with the peak intensity at 400–406 nm region. High Na-doping leads to the blue shift of Na-bands by ~0.05 eV. These PL emission peaks were not observed in the control or Na-doped at 900 °C samples25. To further investigate the electronic state of the NaZn defects, the PL excitation (PLE) technique for 525 nm emission was employed (Fig. 2a). For ZnO crystal that was Na-doped at 1000 °C, the PLE spectrum with a peak at 3.12 eV (397 nm) was observed, (Fig. 2b), confirming a new defect band that acts as a source for 525 nm emission. The control sample does not have this PLE emission while, Na-doped at 900 °C has it at ~3.10 eV. For Na-doped ZnO crystals at 1100 °C and 1200 °C, the PLE peaks were observed at 3.14 eV and 3.17 eV, respectively. This shows that after Na-doping at 1200 °C the NaZn absorption band was blue shifted by ~0.07 eV giving rise to shallow ~(0.17–0.20) eV Na-acceptor level.

Figure 2
Room temperature (RT) Photoluminescence emission (PL) and excitation (PLE) measurements (a) PL emission, showing emergence of donor acceptor pair (DAP) emission after Na-doping (b) PLE spectra for 525 nm emission for control and Na-doped ZnO crystals ...

UV-Vis Transmission Measurements

UV-Vis transmission data at RT were collected in Na-doped ZnO crystals (Supplementary Figure S2). No NaZn band absorption was seen when ZnO crystal was doped at 900 °C, this could be due to low Na-acceptor concentration. NaZn absorption bands were observed when Na-doping was done at 1000 °C, 1100 °C and 1200 °C. This could be due to the critical increase in Na-acceptor concentration leading to acceptor band formation. UV-Vis transmission data shows NaZn absorption bands blue shift by ~0.07 eV after doping at 1200 °C.

For a comparison, as-received ZnO sample was annealed at 1200 °C for 24 hours, with the same experimental conditions, without Na-source. NaZn related absorption bands were not seen in PL, PLE and UV-Vis measurements. This confirms that observed bands are not the annealing effect but are the consequence of Na-doping.

Infrared Spectroscopy

Low temperature (10 K) Infrared transmission measurements were done to acceptors related transitions. Series of IR absorption peaks were seen in Na-doped samples in ~(0.20–0.26) eV range (Fig. 3a). IR absorption bands show shift towards the lower energy as Na-doping concentration increases.

Figure 3
Fourier transform Infrared spectroscopy (FTIR) measurements (a) IR absorption bands are shown after Na-doping in ZnO crystals. Absorption band movements are seen towards the low energy (valence band) as Na-doping concentration increases, data are moved ...

To confirm, these IR absorption are not hydrogen related, a Na-doped (at 1200 °C) sample was annealed at 500 °C in a sealed silica ampoule that was filled with 500 torr H2 gas prior to sealing. The annealing was performed in a horizontal tube furnace for 60 hours. In the hydrogenated sample, an O–H local vibrational mode (LVM) was observed at 3304 cm−1 at a temperature of 9 K (Fig. 3b) as previously reported by Parmar et al.14, while no absorption peaks were seen in (0.20–0.26) eV range. The hydrogenated sample turned semi-insulating and Hall measurement could not be done. This hydrogenated sample was oxygen annealed at 900 °C for 45 min. After oxygen annealing, IR absorption bands (0.20–0.26) eV appeared, while the LVM at 3304 cm−1 disappeared and Hall measurements achieved p-type conduction. This confirms Na-acceptors were compensated by hydrogen annealing giving rise to 3304 cm−1 LVM peak. After oxygen annealing, hydrogen was diffused out that activated Na-acceptors14 and IR absorption bands (0.20–0.26) eV emerged. Acceptor activation is also required in Mg-doped GaN thin films as Mg-acceptors are compensated by hydrogen during growth47.

Hall Measurements

Variable temperature Hall effect measurements were done using Van der Pauw method. For electrical measurements, Ohmic contacts were made on Na-doped samples using MoO225. At RT the control ZnO crystal has <1 ohm-cm resistivity, electron density ~(5–6) × 1016 cm−3 and mobility ~190 cm2/V-s, after Na-doping at 1000 °C the resistivity increased to 8000 ohm-cm. The RT resistivity decreased to ~2100 ohm-cm and ~(60–70) ohm-cm after Na-doping at 1100 °C and 1200 °C, respectively. The decrease in RT resistivity is consistent with the increase in Na-acceptor concentration as the doping temperature increases. The majority charge carrier concentration on Na-doped samples at 1000 °C and 1100 °C could not be determined as Hall measurements were not conclusive. However, Na-doped at 1200 °C samples show stable p-type conduction and variable temperature Arrhenius fit gives hole activation energy ~0.184 eV. Na-doped (1200 °C) sample that was hydrogenated and subsequently oxygen annealed at 900 °C also achieves p-type conduction with ~0.182 eV hole binding energy. The observed hole mobility in these Na-doped ZnO crystals was ~2 cm2/V-s at RT (Fig. 4).

Figure 4
Variable temperature Hall measurements data for Na-doped at 1200 °C and Na-doped at 1200 °C followed by H2 and subsequently O2 annealed samples (a) resistivity (log ρ) vs 1/kBT (b) hole density (log p) vs 1/kBT ...

Discussion

Heavy doping modifies the electronic properties of a semiconductor are commonly understood in terms of band tailing and of a reduction of the fundamental energy gap. Band tailing is a result of the random nature of the impurity distribution and the band gap shrinkage represents the self-energy of the various interactions of the charge carriers. In Na-doped samples no band tailing or shrinkage effect was seen as band edge and bandgap remains intact as seen in optical transmission measurements.

The ionization energy of an acceptor atom may be estimated by assuming hydrogenic model of the acceptor,

An external file that holds a picture, illustration, etc.
Object name is srep44196-m1.jpg

where, An external file that holds a picture, illustration, etc.
Object name is srep44196-m2.jpg is the hole effective mass, εr is the relative permittivity of ZnO, h is Planck’s constant and q is the electronic charge. Optical measurements shows large (0.04–0.07) eV blue shifts in Na-acceptor level. The favorable change in An external file that holds a picture, illustration, etc.
Object name is srep44196-m3.jpg will decrease the hole binding energy. Very high Na-doping can also broaden the acceptor level to form an impurity band due to the wave functions overlap. Broadening of Na-acceptor level is seen in all optical measurements (Supplementary Table S1), Na-acceptor band can be formed at such a high doping concentration which can result in the decrease in Na-acceptor hole binding energy as observed in optical and electrical measurements in number of samples. However, the increase in the relative permittivity (εr) of ZnO crystals after heavy Na-doping can’t be ruled out completely, which can also contribute in the decrease of Na-acceptor energy level.

Na-doped at 1200 °C sample showed two major IR absorption peaks at 0.203 eV and 0.210 eV followed by continuum absorption. These peaks were not present in the control sample. We attribute the peaks to electronic transitions of neutral Na-acceptors. Such transitions can be modeled by a single-hole hydrogenic model. The dip at 0.208 eV and 0.218 eV is due to multiphonon absorption (LO + nTA). Na-doped at 1000 °C and 1100 °C samples also show two major IR absorption peaks at (0.233, 0.231) eV and (0.239, 0.247)eV, respectively and multiphonon absorption dips followed by continuum absorption. The major IR absorption peaks at (0.239 eV) is blue shifted by 0.037 eV, when doped at 1200 °C (Fig. 3). The intensity of IR absorption peaks increases with Na-doping which is expected due to the increase in Na-acceptor concentration rendering more hole in the valence band. Assuming Na-doping concentration ~1 × 1020 cm−3 as measured by SIMS, with ~(0.18–0.19) hole energy, ionization of ~(7.4–5) × 10−2 % of Na-acceptors will occur, which is equivalent to ~(7.4–5) × 1016 holes.cm−3 at RT. Hall measurement shows (4.5–5.5) × 1016 holes.cm−3 at RT. The observed hole concentration is close to the theoretical prediction of ionized population by Fermi-Dirac statistics. Prior to Na-doping, samples were n-type having electron concentration ~(5–6) × 1016 cm−3 at RT with the activation energy ~0.065 eV (Supplementary Figure S3), which leads to ~1018 cm−3 donor impurity presence. This indicates ~1% of Na-dopants were lost to overcome the n-type conduction and to move the Fermi level towards the valence band.

The carrier density was calculated from the Hall coefficient assuming single band conduction, i.e., p = 1/qRH. The carrier density increased by a factor of 3.5 from ~5 × 1016 holes.cm−3 at 290 K to ~1.8 × 1017 holes.cm−3 at 340 K. Assuming the model of thermal activation of carriers from defect to band states is valid, then the hole carrier density is given by:

An external file that holds a picture, illustration, etc.
Object name is srep44196-m4.jpg

where, p0 is temperature dependent prefactor, EA is the acceptor activation energy relative to the valence band edge and kB is Boltzmann’s constant. Data appear linear on a log p vs 1/kBT plot and ignoring the prefactor temperature dependency, we obtain the slope of the line EA = (0.185–0.190) eV (Fig. 4b). This suggests thermal activation of the holes from defect (NaZn) to valence band states, and subsequent hole conduction in valence band.

The resistivity data also appear linear on a log ρ vs 1/T plot (Fig. 4a). In a band-conduction model, the resistivity is given by Arrhenius-type behavior:

An external file that holds a picture, illustration, etc.
Object name is srep44196-m5.jpg

but the prefactor temperature dependency may be significant. Nevertheless, if we ignore the prefactor temperature dependency, we obtain EA = (0.176–0.178) eV. These values are close to the values EA = (0.185–0.190) eV, extracted from the carrier-density data, which indicates that temperature dependency of the prefactor in Eq. (2 &3) is sufficiently weak to ignore. Observed hole mobility varied ~(10–1 cm2/V-s) in 220 < T < 340 K temperature range (Fig. 4c). Reliable and reproducible results with low contact resistance were limited to in the temperature range (220 < T < 340 K). The Hall coefficient (RH) was positive at all temperatures (Fig. 4d), varying (900 > RH > 35 cm3 C−1) confirming p -type conduction. Na-doped at 1000 °C and 1100 °C samples have much higher resistance which resulted in very low Hall voltage VH and it was below the detection limit of the hall apparatus and thus definite majority charge carrier could not be determined. Also, if mobility is very low it’s hard to get conclusive Hall measurements48. Further, a ZnO crystal was Na-doped at 1200 °C and was subsequently polished for ~20 min to remove any surface effects in IR and electrical measurements. In this polished sample Na-acceptor IR bands (Supplementary Figure S4), and p-type Hall conduction (Supplementary Figure S5) were observed, confirming p-type behavior is not the surface but the bulk effect.

In conclusion, novel designed setup led the significant increase ~1020 cm−3 in Na-acceptor concentration when doped at 1200 °C. This resulted in the decrease of Na-acceptor energy to ~(0.18–0.19) eV. Shallow p-type Hall conduction was achieved due to the blue shift of Na-acceptor level/band (Supplementary Figure S6) caused by heavy Na-doping. These results can potentially pave a way to get ZnO based optoelectronic devices. Future work includes to further increase the doping temperature and investigate NaZn acceptor energy band response and Hall conduction.

Additional Information

How to cite this article: Parmar, N. S. et al. Critical increase in Na-doping facilitates acceptor band movements that yields ~180meV shallow hole conduction in ZnO bulk crystals. Sci. Rep. 7, 44196; doi: 10.1038/srep44196 (2017).

Publisher's note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Supplementary Material

Supplementary Information:

Acknowledgments

This research was supported by the Korea Research Fellowship Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Science, ICT and Future Planning (2016H1D3A1909335). This research was also supported by the ATC program (No. 10048059) funded by the Ministry of Trade, Industry & Energy, and the KIST Future Research Program (2E27120).

Footnotes

The authors declare no competing financial interests.

Author Contributions The manuscript was written through contributions of all authors. All authors have given approval to the final version of the manuscript. J.-W. Choi and N.S. Parmar conceived the idea. N.S. Parmar and H.Yim, did experiments and analysis. All authors discussed the results and contributed in the manuscript.

References

  • Nakamura S. The roles of structural imperfections in InGaN-Based blue light-emitting diodes and laser diodes. Science 281, 956–961, doi: (1998).10.1126/science.281.5379.956 [PubMed] [Cross Ref]
  • Ozgur U. et al. . A comprehensive review of ZnO materials and devices. Journal of Applied Physics 98, doi: (2005).10.1063/1.1992666 [Cross Ref]
  • Sharma P. et al. . Ferromagnetism above room temperature in bulk and transparent thin films of Mn-doped ZnO. Nature Materials 2, 673–677, doi: (2003).10.1038/nmat984 [PubMed] [Cross Ref]
  • Kittilstved K. R., Liu W. K. & Gamelin D. R. Electronic structure origins of polarity-dependent high-T-C ferromagnetismin oxide-diluted magnetic semiconductors. Nature Materials 5, 291–297, doi: (2006).10.1038/nmat1616 [PubMed] [Cross Ref]
  • Kundaliya D. C. et al. . On the origin of high-temperature ferromagnetism in the low-temperature-processed Mn-Zn-O system. Nature Materials 3, 709–714, doi: (2004).10.1038/nmat1221 [PubMed] [Cross Ref]
  • Lee J. et al. . Towards a new class of heavy ion doped magnetic semiconductors for room temperature applications. Scientific Reports 5, doi: (2015).10.1038/srep17053 [PMC free article] [PubMed] [Cross Ref]
  • Zhu D. P. et al. . Oxygen vacancies controlled multiple magnetic phases in epitaxial single crystal Co-0.5(Mg0.55Zn0.45)(0.5)O1-v thin films. Scientific Reports 6, doi: (2016).10.1038/srep24188 [PMC free article] [PubMed] [Cross Ref]
  • Thomas D. G. The exciton spectrum of zinc oxide. Journal of Physics and Chemistry of Solids 15, 86–96, doi: (1960).10.1016/0022-3697(60)90104-9 [Cross Ref]
  • Makino T. et al. . Band gap engineering based on MgxZn1-xO and CdyZn1-yO ternary alloy films. Applied Physics Letters 78, 1237–1239, doi: (2001).10.1063/1.1350632 [Cross Ref]
  • Halliburton L. E. et al. . Production of native donors in ZnO by annealing at high temperature in Zn vapor. Applied Physics Letters 87, doi: (2005).10.1063/1.2117630 [Cross Ref]
  • Selim F. A., Weber M. H., Solodovnikov D. & Lynn K. G. Nature of native defects in ZnO. Physical Review Letters 99, doi: (2007).10.1103/PhysRevLett.99.085502 [PubMed] [Cross Ref]
  • Weber M. H., Parmar N. S., Jones K. A. & Lynn K. G. Oxygen Deficiency and Hydrogen Turn ZnO Red. Journal of Electronic Materials 39, 573–576, doi: (2010).10.1007/s11664-010-1115-6 [Cross Ref]
  • Kohan A. F., Ceder G., Morgan D. & Van de Walle C. G. First-principles study of native point defects in ZnO. Phys. Rev. B 61, 15019–15027 (2000).
  • Parmar N. S., Swain S. K. & Lynn K. G. Green photoluminescence in ZnO crystals: a combined study using positron annihilation, photoluminescence, and hall measurements. Journal of Materials Science-Materials in Electronics 26, 10138–10140, doi: (2015).10.1007/s10854-015-3699-3 [Cross Ref]
  • Janotti A. & Van de Walle C. G. Hydrogen multicentre bonds. Nature Materials 6, 44–47, doi: (2007).10.1038/nmat1795 [PubMed] [Cross Ref]
  • Van de Walle C. G. Hydrogen as a cause of doping in zinc oxide. Physical Review Letters 85, 1012–1015, doi: (2000).10.1103/PhysRevLett.85.1012 [PubMed] [Cross Ref]
  • Wardle M. G., Goss J. P. & Briddon P. R. Theory of Li in ZnO: A limitation for Li-based p-type doping. Physical Review B 71, doi: (2005).10.1103/PhysRevB.71.155205 [Cross Ref]
  • Parmar N. S., McCluskey M. D. & Lynn K. G. Vibrational Spectroscopy of Na-H Complexes in ZnO. Journal of Electronic Materials 42, 3426–3428, doi: (2013).10.1007/s11664-013-2723-8 [Cross Ref]
  • Look D. C. et al. . Characterization of homoepitaxial p-type ZnO grown by molecular beam epitaxy. Applied Physics Letters 81, 1830–1832, doi: (2002).10.1063/1.1504875 [Cross Ref]
  • Tsukazaki A. et al. . Repeated temperature modulation epitaxy for p-type doping and light-emitting diode based on ZnO. Nature Materials 4, 42–46, doi: (2005).10.1038/nmat1284 [Cross Ref]
  • Lyons J. L., Janotti A. & Van de Walle C. G. Why nitrogen cannot lead to p-type conductivity in ZnO. Applied Physics Letters 95, doi: (2009).10.1063/1.3274043 [Cross Ref]
  • Tarun M. C., Iqbal M. Z. & McCluskey M. D. Nitrogen is a deep acceptor in ZnO. Aip Advances 1, 7, doi: (2011).10.1063/1.3582819 [Cross Ref]
  • Lim J.-H. et al. . UV electroluminescence emission from ZnO light-emitting diodes grown by high-temperature radiofrequency sputtering. Advanced Materials 18, 2720-+, doi: (2006).10.1002/adma.200502633 [Cross Ref]
  • Minegishi K. et al. . Growth of p-type zinc oxide films by chemical vapor deposition. Japanese Journal of Applied Physics Part 2-Letters 36, L1453–L1455 (1997).
  • Ryu Y. R. et al. . Synthesis of p-type ZnO films. Journal of Crystal Growth 216, 330–334, doi: (2000).10.1016/s0022-0248(00)00437-1 [Cross Ref]
  • Look D. C. & Claftin B. P-type doping and devices based on ZnO. Physica Status Solidi B-Basic Solid State Physics 241, 624–630, doi: (2004).10.1002/pssb.200304271 [Cross Ref]
  • McCluskey M. D. & Jokela S. J. Defects in ZnO. Journal of Applied Physics 106, 13, doi: (2009).10.1063/1.3216464 [Cross Ref]
  • Saji K. J., Subbaiah Y. P. V., Tian K. & Tiwari A. P-type SnO thin films and SnO/ZnO heterostructures for all-oxide electronic and optoelectronic device applications. Thin Solid Films 605, 193–201, doi: (2016).10.1016/j.tsf.2015.09.026 [Cross Ref]
  • Narushima S. et al. . A p-type amorphous oxide semiconductor and room temperature fabrication of amorphous oxide p-n heterojunction diodes. Advanced Materials 15, 1409–1413, doi: (2003).10.1002/adma.200304947 [Cross Ref]
  • Snure M. & Tiwari A. CuBO2: A p-type transparent oxide. Applied Physics Letters 91, doi: (2007).10.1063/1.2778755 [Cross Ref]
  • Song J. Z. et al. . Epitaxial ZnO Nanowire-on-Nanoplate Structures as Efficient and Transferable Field Emitters. Advanced Materials 25, 5750-+, doi: (2013).10.1002/adma.201302293 [PubMed] [Cross Ref]
  • Zeng H. B. et al. . ZnO-based hollow nanoparticles by selective etching: Elimination and reconstruction of metal-semiconductor interface, improvement of blue emission and photocatalysis. Acs Nano 2, 1661–1670, doi: (2008).10.1021/nn800353q [PubMed] [Cross Ref]
  • Zeng H. B. et al. . Template Deformation-Tailored ZnO Nanorod/Nanowire Arrays: Full Growth Control and Optimization of Field-Emission. Advanced Functional Materials 19, 3165–3172, doi: (2009).10.1002/adfm.200900714 [Cross Ref]
  • Zeng H. B. et al. . Blue Luminescence of ZnO Nanoparticles Based on Non-Equilibrium Processes: Defect Origins and Emission Controls. Advanced Functional Materials 20, 561–572, doi: (2010).10.1002/adfm.200901884 [Cross Ref]
  • Faraji N. et al. . Visible-Light Driven Nanoscale Photoconductivity of Grain Boundaries in Self-Supported ZnO Nano- and Microstructured Platelets. Advanced Electronic Materials 2, doi: (2016).10.1002/aelm.201600138 [Cross Ref]
  • Grottrup J. et al. . Three-dimensional flexible ceramics based on interconnected network of highly porous pure and metal alloyed ZnO tetrapods. Ceramics International 42, 8664–8676, doi: (2016).10.1016/j.ceramint.2016.02.099 [Cross Ref]
  • Mishra Y. K. et al. . Crystal growth behaviour in Au-ZnO nanocomposite under different annealing environments and photoswitchability. Journal of Applied Physics 112, doi: (2012).10.1063/1.4752469 [Cross Ref]
  • Mishra Y. K. et al. . Fabrication of Macroscopically Flexible and Highly Porous 3D Semiconductor Networks from Interpenetrating Nanostructures by a Simple Flame Transport Approach. Particle & Particle Systems Characterization 30, 775–783, doi: (2013).10.1002/ppsc.201300197 [Cross Ref]
  • Meyer B. K. et al. . On the role of group I elements in ZnO. Applied Physics a-Materials Science & Processing 88, 119–123, doi: (2007).10.1007/s00339-007-3962-4 [Cross Ref]
  • Parmar N. S. & Lynn K. G. Sodium doping in ZnO crystals. Applied Physics Letters 106, doi: (2015).10.1063/1.4905594 [Cross Ref]
  • Lee E. C. & Chang K. J. P-type doping with group-I elements and hydrogenation effect in ZnO. Physica B-Condensed Matter 376, 707–710, doi: (2006).10.1016/j.physb.2005.12.177 [Cross Ref]
  • Zeng Y. J. et al. . Identification of acceptor states in Li-doped p-type ZnO thin films. Applied Physics Letters 89, doi: (2006).10.1063/1.2236225 [Cross Ref]
  • Corolewski C. D., Parmar N. S., Lynn K. G. & McCluskey M. D. Hydrogen-related complexes in Li-diffused ZnO single crystals. Journal of Applied Physics 120, doi: (2016).10.1063/1.4959106 [Cross Ref]
  • Parmar N. S., Corolewski C. D., McCluskey M. D. & Lynn K. G. Potassium acceptor doping of ZnO crystals. Aip Advances 5, doi: (2015).10.1063/1.4919932 [Cross Ref]
  • Park C. H., Zhang S. B. & Wei S. H. Origin of p-type doping difficulty in ZnO: The impurity perspective. Physical Review B 66, doi: (2002).10.1103/PhysRevB.66.073202 [Cross Ref]
  • Du M. H. & Zhang S. B. Impurity-bound small polarons in ZnO: Hybrid density functional calculations. Physical Review B 80, doi: (2009).10.1103/PhysRevB.80.115217 [Cross Ref]
  • Nakamura S., Mukai T. & Senoh M. Candela-Class High-Brightness Ingan/Algan Double-Heterostructure Blue-Light-Emitting Diodes. Applied Physics Letters 64, 1687–1689, doi: (1994).10.1063/1.111832 [Cross Ref]
  • Zhang K. H. L. et al. . Perovskite Sr-Doped LaCrO3 as a New p-Type Transparent Conducting Oxide. Advanced Materials 27, 5191–5195, doi: (2015).10.1002/adma.201501959 [PubMed] [Cross Ref]

Articles from Scientific Reports are provided here courtesy of Nature Publishing Group