structural, electrical and optical properties of gd doped and undoped zno:al (zao) thin films...
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Applied Surface Science 253 (2007) 5179–5183
Structural, electrical and optical properties of Gd doped and undoped
ZnO:Al (ZAO) thin films prepared by RF magnetron sputtering
Wei Lin, Ruixin Ma *, Wei Shao, Bin Liu
Department of Non-Ferrous Metallurgy, University of Science and
Technology Beijing, Beijing 100083, People’s Republic of China
Received 14 June 2006; received in revised form 11 October 2006; accepted 21 November 2006
Available online 12 December 2006
Abstract
The influence of the gadolinium doping on the structural features and opto-electrical properties of ZnO:Al (ZAO) films deposited by radio
frequency (RF) magnetron sputtering method onto glass substrates was investigated. X-ray analysis showed that the films were polycrystalline
fitting well with a hexagonal wurtzite structure and have preferred orientation in [0 0 2] direction. The Gd doped ZAO film with a thickness of
140 nm showed a high visible region transmittance of 90%. The optical band gap was found to be 3.38 eV for pure ZnO film and 3.58 eV for ZAO
films while a drop in optical band gap of ZAO film was observed by Gd doping. The lowest resistivities of 8.4 � 10�3 and 10.6 � 10�3 V cm were
observed for Gd doped and undoped ZAO films, respectively, which were deposited at room temperature and annealed at 150 8C.
# 2006 Elsevier B.V. All rights reserved.
PACS : 81.05.�t; 81.05.Je; 81.15.Cd
Keywords: Zinc oxide; RF magnetron sputtering; Transparent conductive thin film; Optical and electronic properties
1. Introduction
Zinc oxide (ZnO) has a wide direct band gap of 3.37 eV and
a relatively large exciton binding energy of 60 meV that makes
it attractive for a variety of electronic and electro-optical
applications [1]. For the band gap of ZnO is well above the
visible range, prepared films are electrically conductive, which
is leading to applications for transparent conducting oxides
(TCO) thin films such as transparent electrodes for liquid
crystal displays, solar cell, photo-thermal conversion system
and so on [2–4]. The high quality of ITO films deposited by
sputtering of oxide targets has already been successfully
achieved on a commercialized production scale. However, both
ITO target and its film contain a very high concentration of
indium (90% In2O3 + 10% SnO2 in weight) that is a very
expensive material. ZnO is considered as one of the most
* Corresponding author at: Mailbox HaiPu, University of Science and Tech-
nology Beijing, Xueyuan Road, Haidian District, Beijing, People’s Republic of
China. Tel.: +86 10 8238 4751; fax: +86 10 8238 4751.
E-mail address: [email protected] (R. Ma).
0169-4332/$ – see front matter # 2006 Elsevier B.V. All rights reserved.
doi:10.1016/j.apsusc.2006.11.032
promising materials by taking the advantages of abundance in
nature, non-toxicity and good stability in hydrogen plasma
process. Moreover, though some dopant is very expensive, only
a small amount of dopant can make ZnO film’s electrical and
optical properties comparable to ITO film. This means that the
cost price of doped ZnO film is still lower than that of ITO film.
Based on the viewpoint that ZnO films are more potential than
ITO films, we believe that it’s valuable for our further
investigation about ZnO films [5,6]. The electrical conductivity
and optical transmittance of ZnO are related to the free carrier
density generated by dopant atom substitution of Zn atom
(giving out one extra electron), and oxygen vacancies (acting as
two electron donors).
A lot of studies have focused on changing various technics
parameters and the dopant concentration to improve the
performance of ZnO:Al (ZAO). Chung et al. [7] have
researched working pressure effect on the physical properties
of ZAO films. However, only a few studies on the effects of
doping on the electrical properties and their dependence with
the film structure have been reported. It is generally
considered that the ion radii of dopants for transparent and
conductive ZnO films should be small and close to that of
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W. Lin et al. / Applied Surface Science 253 (2007) 5179–51835180
Zn2+. But the co-doping effect of a big ion radius rare earth
impurity and Al3+ has not been reported before. Gd2O3 has
certain and useful physical property in optical applications,
which was selected as dopant and expected to improve the
transmittance for ZAO film. The aim of this work is to
comparatively establish structural, optical and electrical
property comparative relations between the undoped and
Gd doped ZAO films.
2. Experimental
2.1. Ceramic targets preparation
The ceramic sputtering targets, of which raw materials were
mechanical mixed powders, were fabricated by sintering in the
air after die pressing and cold isostatic pressing. The following
compositions were chosen: 97% ZnO + 3% Al2O3 and 97%
ZnO + 2% Al2O3 + 1% Gd2O3 (in weight). Raw materials were
commercially available ZnO, Al2O3 and Gd2O3 (99.99% in
purity) powders. The linear shrinkage ratios of sintered targets
reached to about 20%, as well as the relative density was over
90% (highest is 97.63%). The sintered circular ceramic targets
with a diameter of 65 mm were used in thin films’ preparation.
2.2. Thin films preparation
Gd doped and undoped ZnO thin films on Corning eagle
2000 glass substrates were deposited at room temperature by
ratio frequency (RF) magnetron sputtering. Glass substrates
were thoroughly cleaned using acetone, ethanol absolute and
water as solvents and ultrasonic technology, and then dried
before loading it in the deposition chamber. The base pressure
in sputtering chamber was about 2 � 10�4 Pa. A sputter-etch of
20 min was used to remove the target surface contamination. At
last, argon was introduced, and the gas pressure was adjusted.
The deposition conditions are shown in Table 1.
The thin film’s thickness was measured by elliptical
polarization Instrument (Jobin-Yvon). Electrical properties of
the films were measured by a dc four-point probe technique.
The optical transmittances of the studied films were determined
at room temperature for photon wavelengths ranging from 320
to 800 nm, using a UV-250 spectrophotometer. Crystallo-
graphic and phase structures were determined by an X-ray
diffractometer (Rigaku) with Cu Ka radiation. The surface
morphologies and thickness of the deposited films were
investigated by a Cambridge S-360 scanning electron micro-
scope (SEM).
Table 1
Deposition conditions of Gd doped and undoped ZAO films
Parameters Value
Power mode RF
Substrate temperature Room temperature
Deposition time (min) 17
Partial pressure of O2 (Pa) 0.45
Target–substrate distance (mm) 119
Pressure (Pa) 10�4
3. Results and discussions
3.1. Structural characterization
Fig. 1 shows the X-ray diffraction patterns for the Gd doped
and undoped ZAO thin films deposited at room temperature.
The (0 0 2), (1 0 2), (1 0 3) peaks are observed. The results of
the films were in good agreement with those reported in the
PDF for ZnO (PDF75-576, a = 3.24270 A, b = c = 5.19480 A),
and the peaks correspond to a hexagonal wurtzite structure
with no additional peaks of gadolinium and aluminum phases
[8]. The (0 0 2) reflex for both films is dominating in the XRD
spectra. For both films, the crystalline granule grew along its
c-axis and perpendicular to the surface of the substrate. There
was no any peak shift of Gd doped film as compared with ZAO
film, which indicates that gadolinium atoms doping did not
distort the original crystalline structure [9,10]. It was same
with the report by Lin et al. [11] who studied heavily Al doped
ZnO films by simultaneous rf and dc magnetron sputtering
methods. The crystal size g can be estimated using Scherrer
formula:
g ¼ 0:94l
Dð2uÞ cos u; (1)
where l is the X-ray wavelength, u the Bragg diffraction angle
in degrees and D(2u) is the FWHM in radian [12–14]. The
crystallite size is in the 28–42 nm range.
Fig. 2 illustrates the surface morphology of Gd doped and
undoped ZAO thin films deposited at room temperature. The
films show different morphology of surface grains, which are
dependent on the deposition temperature and addition of
dopants [15]. For the obtained ZAO thin films, uniform and
dense surface with small grain size is observed. For gadolinium
oxide doping, the surface morphology shows a noticeable
variation of the film surface with appearing of some big grains.
It indicates that, during deposition of Gd doped ZAO film by
sputtering onto substrates the growth has taken place by
Fig. 1. The XRD patterns of Gd doped and undoped ZAO thin films deposited
at room temperature.
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Fig. 2. SEM micrographs of undoped (a) and doped (b) ZAO thin films deposited on glass substrates annealed at 150 8C.
W. Lin et al. / Applied Surface Science 253 (2007) 5179–5183 5181
nucleation and coalescence process. Randomly distributed
(0 0 2) oriented nuclei may have first formed and these nuclei
then have grown to form observable islands. As islands increase
their size by further deposition and come closer to each other,
the larger ones appeared to grow by coalescence of smaller one.
Flattening of islands to give increased surface coverage of the
clusters follows this step [8,16].
3.2. Optical and electrical properties
The transmittance of the Gd doped and undoped ZAO films
of thickness 170 nm is depicted in Fig. 3. The transmittance of
all deposited films at l = 550 nm is better than 87.0%. In the
visible region, the undoped ZAO film shows the transmittance
of the order of 87% while that of Gd doped ZAO film was of the
order of 92%. Al doping affects the transmittance of ZnO films
Fig. 3. Variation of absorption (at) and transmittance (%T) with wavelength (l)
of Gd doped and undoped ZAO thin films.
a little. It’s noticed that the additional Gd doping improves the
optical properties. This attributed to decrease in free carrier
absorption due to the elevated carrier mobility of the film [17].
The absorbance has slightly increased after Gd doping, which is
related to the introduction of the Gd defect states within the
forbidden band leading to absorption of incident photons. In the
ultraviolet region, the optical transmittance of the film falls
sharply due to the onset of the fundamental absorption in this
region. The absorption edge of the Gd doped ZAO film
appeared to shift towards the longer wavelength side. The
optical absorption coefficient provides information on the band
structure. a is given by the formula [18]:
T
1� R¼ expð�atÞ; (2)
where T is the optical transmittance, R the optical reflectance, a
the absorption coefficient and t is the film thickness. The optical
band gap, Eg, can be determined from the experimental spectra
of the absorption coefficient, a, as a function of the photon
energy, hn, using the following equation [19,20]:
ahn ¼ Cðhn� EgÞ1=2; (3)
where C is a constant dependent on the electron–hole mobility.
Plot of ðahnÞ2 as a function of photon energy against hn of
undoped and Gd doped ZAO films is shown in Fig. 4. The
values of the optical energy gap determined by extrapolating
the linear portion of the curves to a = 0 are in agreement with
those reported in the literature [21–23]. The optical band gap
was found to be 3.37 eV for pure ZnO film and it increases to
3.58 eV for ZnO:Al films. The widening of optical band gap
may be attributed to Moss–Burstein shift effect [24]. This effect
is due to that the conduction band filling in highly degenerate
semiconductor makes the Fermi level exceed the conduction
band minimum. The band gap was found to be decreased to
3.45 eV for Gd doped ZAO film (1 wt.% Gd doping concen-
tration), which is similar to the report of Kim and Park [25] who
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Fig. 4. Plot of ðahnÞ2 as a function of photon energy against, hn, for pure ZnO,
undoped and Gd doped ZAO films deposited at room temperature.
W. Lin et al. / Applied Surface Science 253 (2007) 5179–51835182
observed the band gap shift from 3.25 to 3.13 eV for Co doped
ZnO film (8% doping concentration).
Resistivity of doped and Gd doped ZAO films deposited at
room temperature and annealed at different temperature is
illustrated in Fig. 5. The lowest resistivities of 8.4 � 10�3 and
10.6 � 10�3 V cm are observed for Gd doped and undoped
ZAO films, respectively, deposited at room temperature and
Fig. 5. Resistivity of Gd doped and undoped ZAO films annealed at 20, 100,
150, 200, 250 and 300 8C.
annealed at 150 8C. Gd doped ZAO films exhibit a sensitivity to
the different annealing temperatures from 20 to 300 8C. For Gd
doped and undoped ZAO films, the electrical resistivities are
decreasing with increasing of the annealing temperature from
20 to 300 8C and exhibit a minimum of resistivity value at
approximately 150 8C. Raising the annealing temperature, the
atoms receive energy and migrate to relative equilibrium
positions. This induces a series of effects, for example, reducing
the lattice strain and the oxygen defect levels, appearing a more
perfect crystallite, pilling up of donor, weakening the grain
boundary scattering and increasing the number of current
carrier [26,27]. However, excessive annealing temperature
causes coarsening of grain, deteriorating of crystal orientation
and bringing overmuch defects at grain boundary, which are
closely related to the increase in resistivity. After doped Gd,
ZAO thin film has an obvious increase in resistivity under the
same deposition condition. This is similar to the results of
Shinde et al. [8] and Han et al. [28].
4. Conclusions
Gd doped and undoped ZAO films on glass substrates grown
by RF magnetron sputtering method at room temperature
annealing at different temperature from 20 to 300 8C. A small
amount of Al and Gd impurities in the films did not alter the
wurtzite structure of ZnO. All of the deposited films
demonstrated a c-axis preferred orientation with grain size
ranging from 28 to 42 nm. Among all the studied films, ZAO
films (3 wt.%) deposited at room temperature annealing at
150 8C have the most interesting and useful properties, which
are equal to the application in solar cell. They have a
transmittance to visible light above 87% and an electrical
resistivity of the order of 8.4 � 10�3 V cm. Moreover, the
electrical properties of Gd doped ZAO films (2 wt.% Al and
1 wt.% Gd) films deposited at room temperature are very
sensitive to the annealing temperature. This feature is not
obviously exhibited by ZAO and pure ZnO films. The optical
band gap of pure ZnO film is 3.37 eVand it increases to 3.58 eV
for ZnO:Al films, which is generally attributed to Burstein–
Moss effect. The optical band gap was found to be decreased
from 3.58 to 3.45 eV by Gd doping for ZAO films. The
electrical conductivity of the studied Gd doped ZAO films has
been correlated to the existence of Gd and Al atoms in the ZnO
matrix and the role of Gd doping effect in the grain growth
process by crystallite aggregation. The grain size coarsening for
the Gd doped ZAO films deposited at room temperature leads to
considerable grain boundary effects, which distributes their
electrical properties.
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