Journal of Atomic, Molecular, and Optical Physics
Volume 2011 (2011), Article ID 270540, 7 pages
Bandgap Engineering in ZnO By Doping with 3d Transition Metal Ions
1Materials Science Centre, Department of Nuclear Physics, University of Madras, Guindy Campus, Chennai 600025, India
2Center for Condensed Matter Sciences, National Taiwan University, Taipei 10617, Taiwan
Received 6 November 2010; Accepted 21 February 2011
Academic Editor: Robert Moshammer
Copyright © 2011 D. Paul Joseph and C. Venkateswaran. 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.
Bulk Zn0.95TM0.05O (, Mn, Fe, Co, and Ni) were synthesized by the standard ceramic method and explored for variation in their band gap energies using Diffuse Reflectance Spectroscopy in the ultraviolet-visible region. Phase quantification and compositional studies were performed using Rietveld analysis of the X-Ray Diffraction patterns, Scanning Electron microscopy, and Energy Dispersive X-Ray Analysis. Due to 3d transition ion doping, the samples have brilliant colors, and the absorption edge of Zn0.95TM0.05O was found to shift towards the visible and ultraviolet-visible region. The blue and red shifts in band gaps observed for various transition metal ion-doped ZnO are discussed.
Zinc Oxide (ZnO), a direct wideband gap semiconductor, has been of great interest for application in optical devices such as blue-violet and UV-light emitting diodes and laser diodes [1, 2]. Recently, ZnO is alloyed with various “3d” transition metal (TM) ion for exploring its applicability in the field of SPINTRONICS (Spin Transport Electronics) [3–7]. Theoretical simulation of electronic structures of 3d transition metal ion- doped ZnO has been reported by Toyoda et al. . The ferromagnetic behavior and high transition temperature of the wide band gap semiconductors have wide controversy. Theory of spinodal decomposition for the observed magnetic behavior in wide band gap semiconductors has been framed recently by abinitio electronic structure calculations [9–11]. Owing to the transparency of ZnO, “transparent magnets”  exhibiting a number of unique magnetic, magneto-optical, and magnetotransport properties are also expected. Oxide-based Diluted Magnetic Semiconductors (DMSs) are superior to their III–V counterparts, and a number of review articles were published on them [12–15]. To exploit materials for optoelectronic applications, it is essential to tune the optical band gap which can be done by way of doping with various “3d” transition metal ions apart from introducing spin degree of freedom into the ZnO matrix. Band gap tailoring at the ultraviolet end and visible region of the solar spectrum is of considerable interest for large area optical coatings. As most of the optical studies on ZnO DMS were on thin films only, the present study is aimed at measuring directly the band gap energies of bulk Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) using Diffuse Reflectance Spectrocopy (DRS) which is particularly suitable for the determination of absorption edges of powdered materials. Bulk Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co & Ni) prepared by ceramic method were explored for their structural, compositional, and optical properties.
2. Sample Preparation
We adopted the standard ceramic method for the preparation of bulk samples of Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) from high pure starting materials. The stoichiometric mixture for the composition Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) was separately weighed and mixed manually (for 10 h) in the presence of volatile acetone/isopropyl alcohol medium in an agate pestle and mortar to achieve homogenized mixture of the solid state reactants.
The surface area of reacting solids has a great influence on reaction rates; hence the area of contact between the reactants was increased by pressing the reacting powder into pellets. The green pellets were then placed over fresh alumina tray and sintered separately at various temperatures in air for various durations to attain single phase, with intermediate grindings. Zn0.95Cr0.05O samples were sintered using a gold foil placed over an alumina tray since Cr2O3 readily reacts with Al2O3 at high temperatures. The details of preparation of bulk Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) samples are given in Table 1.
3. Results and Discussion
The X-Ray Diffraction (XRD) patterns of Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) are shown in Figure 1. Though the dopants and the host cation elements belong to the same 3d series, only Mn and Co have the highest solubility in ZnO and form single phase. The other three dopants, Cr, Fe, and Ni, do not form single phase with ZnO even after repeated trials by optimizing the processing temperatures and duration. Their solubility in ZnO is less, and the traces of formed secondary phases are listed in Table 1. Presence of ZnCr2O4 (Zincochromite), Zn0.98Fe2.02O4 (Franklinite) and NiO has been confirmed in the bulk Cr, Fe, and Ni doped ZnO, respectively. Phase quantification was done using the program MAUD , which combines the Rietveld method and Fourier transform analysis. The estimated percentage of secondary phases for Cr, Fe, and Ni doped ZnO and the refined lattice parameters for Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) samples are shown in Table 1 .
The Energy Dispersive X-Ray Analysis (EDAX) results shown in Figure 2 indicate that all the samples have a nominal variation in composition, which is attributed to the random substitution of the magnetic dopants at the cationic site. The Scanning Electron Microscope (SEM) images show aggregates of micron-sized particles (Figure 3). Since the ceramic method involves sintering of the stoichiometric mixtures at high temperatures, the crystallites are in the order of micrometer with relatively smooth surface. The aggregate of crystallites of various sizes indicating a size distribution is also clearly evident in the micrographs. The variation in size of the particles among the different Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) samples is due to the difference in processing temperatures. Interested readers may refer to detailed structural and magnetic aspects of some of these samples in previously published papers [18–20].
The DRS measurements on bulk Zn 0.95TM0.05O were performed in the ultraviolet-visible region (UV-Vis region) from 350 nm to 800 nm as it is the more appropriate method for the determination of absorption edges of powdered (colored and opaque) materials [21, 22]. Slightly thick samples were used to avoid accidental loss by partial transmission during the measurement of percent reflectance. The Zn 0.95TM0.05O samples prepared by processing at high temperatures have bulk crystallites with size falling in the range of microns resulting in a considerably sharp fall in percent reflectance. Figures 4(a) to 4(f) show the Diffuse Reflectance Spectra (DRS) of Zn0.95TM0.05O compounds. The DRS of bulk ZnO shows sharp fall in reflectance corresponding to the absorption edge with maximum transparency in the visible region. All the Zn0.95TM0.05O compounds show a decrease in percent reflectance than pure bulk ZnO indicating dominant band gap excitations in the visible region. The reflectance edge of some of the Zn0.95TM0.05O samples shift towards the visible region indicating the band gap excitations by visible light (Figure 4(a)).
The increase in the diffuse reflectivity has a definite linear region of the greatest slope. This is attributed to an exponential drop in the absorption coefficient . The onset of this exponential drop had been suggested as a more universal method of determining absorption edges from which the band gap can be deduced. A linear fit was given to the linear part of the increase in reflectivity for deducing the absorption edge. In case of two linear parts in the onset of increase in reflectance, the edge was determined from the intersection of the linear fit of the two linear portions . The brilliant color of Zn0.95TM0.05O is the main feature. “Cr” doping in ZnO induced grayish brown color, red color for “Mn” doping, saffron for “Fe”, bluish green for “Co,” and green for “Ni” doping. The striking colors are attributed to interatomic transitions between the “3d” TM ions that are substituted at the cationic site of ZnO.
The estimated band gap value of bulk ZnO is 3.37 eV. The spectrum of Zn0.95Cr0.05O has two linear parts, and the band gap value 2.96 eV is deduced from the intersection of the two linear regions (Figure 4(b)). Red shift is observed on substitution with “Cr.” Three absorption bands are observed between 475 and 750 nm. These bands are due to electronic transitions in Cr3+. The transitions and the reflectance maxima correspond to the following transitions: 4A2 to 4T2 around 720 nm, 4A2 to around 625 nm, and 4A2 to around 525 nm .
The band gap of Zn0.95Mn0.05O shows blue shift (Figure 4(c)) with a value of 3.42 eV, which is greater than pure ZnO. This behavior agrees with the literature [24–26] values. The Zn0.95Mn0.05O sample is red in color, which is due to interatomic transitions between the divalent Mn2+ metal ions. The red color deepens with increasing sintering temperatures due to the increase in electron concentration by increase in O2- vacancies. This feature is observed for all Zn0.95TM0.05O compounds. Mn2+ does not produce any reflectance maxima as it does not show crystal field splitting. The reflectance spectrum of Zn0.95Fe0.05O in Figure 4(d) shows a shift towards lower energies, with a band gap value of 2.09 eV. This red shift is interpreted in terms of the sp-d exchange interaction between the band electrons and the localized “d” electrons of the transition metal ion at the cationic site . Similar to Mn2+, Fe3+ also does not produce any reflectance maxima due to absence of crystal field splitting.
The reflectance spectrum of Zn0.95Co0.05O shows blue shift with a band gap value of 3.52 eV. The spectrum (Figure 4(e)) also shows Co2+ characteristic transitions in the visible region [28, 29] that imparts deep green color to the sample . The series of reflectance maxima without much resolution are assigned to transition  from ground state of Co3+. The reflectance spectrum of “Ni” doped ZnO shows red shift with a band gap value of 2.98 eV (Figure 4(f)). Ni2+ in ZnO shows three reflectance maxima corresponding to the following transitions: to (585 nm), to (545 nm), and to (515 nm) . Thus bulk ZnO is found to present a different trend in variation of band-gap and brilliant colors on doping with “3d” TM ions. The representation of the variation of band gap of bulk Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) samples with respect to the band gap of pure ZnO is shown in Figure 5. The samples which are single phase show blue shift, whereas the samples with secondary phases lie below the dotted line (Figure 5) indicating red shift. The offset towards red shift is higher compared to the offset towards blue region of the band gap with respect to pure ZnO. This might be due to the coexistence of the secondary phases (Table 1) within the sample. Sernelius et al.  have discussed the theory of band gap widening and narrowing in Al-doped ZnO. The observation of red and blue shift in band gap of Zn0.95TM0.05O (TM = Cr, Mn, Fe, Co, & Ni) can be plausibly explained in analogy with Al-doped ZnO . The widening of band gap in case of heavily doped semiconductors is due to the blocking of the low-energy transitions by the donor electrons occupying the states at the bottom of the conduction band which is known as the Burstein-Moss effect.
ZnO being a “polar” semiconductor, there is a displacement of charge from one of the atomic species to the other, and hence the host atoms are charged. These moving charged particles cause a displacement polarization, wherein an electron in the conduction band forms a cloud of positive charge and the hole in valence band forms a cloud of negative charge around it. This particle and its charge cloud constitute a polaron which modifies the self-energy and cause a downward shift due to many-body interactions . In a “nonpolar” semiconductor, due to the electrons of equal spin avoiding each other due to statistical reasons and coulomb repulsion and by the doped impurities, the electrons are surrounded by excess of holes thereby lowering its energy leading to downward shift of the conduction band along with a distortion in band structure and band tailing. Also, the holes in the valence band are repelled by the positively charged donor ions and have a tendency to avoid them thereby causing a shift in their energy . All these effects shift the valence band towards the conduction band and the conduction band edge towards the valence band ultimately leading to the narrowing of the band gap. Thus the red and blue shift of band gap of “3d” transition metal ion-doped ZnO into the visible and UV region extends the possibility of ZnO to be tailor-made for applications in the UV-Vis region.
Blue and red shifts in the band gap of TM ion-doped ZnO prepared by ceramic method were observed from the onset of the linear increase of the diffuse reflectivity spectrum. The estimated values of band gap need to be correlated with extended systematic experimental results so as to precisely tune the band gap of ZnO for a specific application by varying the composition of each of the substitutionally doped 3d transition metal ions at the cationic site. The observed variation in band gap is pertained to the experimental conditions and samples described here. A systematic study on the composition (from lower to higher value) of each of the dopant would yield a trend for the entire range of composition using in which the TM-doped ZnO compounds could be exploited for magneto-optical device applications.
The authors thank Professor Dr. M. Palanichamy, Department of Chemistry, Anna University for fruitful discussions. The author D. P. Joseph thanks the CSIR, Government of India for the support of this work by the award of Senior Research Fellowship, 2007.
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