Greatly reduced leakage current and defect mechanism in atmosphere sintered BiFeO3–BaTiO3 high...
Transcript of Greatly reduced leakage current and defect mechanism in atmosphere sintered BiFeO3–BaTiO3 high...
Greatly reduced leakage current and defect mechanismin atmosphere sintered BiFeO3–BaTiO3 high temperaturepiezoceramics
Zhonghua Yao • Chaobing Xu • Hanxing Liu •
Hua Hao • Minghe Cao • Zhijian Wang •
Zhe Song • Wei Hu • Atta Ullah
Received: 10 June 2014 / Accepted: 16 August 2014 / Published online: 29 August 2014
� Springer Science+Business Media New York 2014
Abstract In current work, the effect of sintering atmo-
spheres (N2, air and O2) on the structure, electrical prop-
erties, and defect mechanism of 0.8BiFeO3–0.2BaTiO3
lead-free piezoelectric ceramics has been investigated.
X-ray diffractometer results indicated all the samples
crystallized into the rhombohedrally distorted perovskite
structure which was independent on the sintering atmo-
spheres. Bi-containing impurity phases were observed in
N2 sintered samples while not appearing in other atmo-
spheres. X-ray photoelectron spectrum analysis indicated
more Fe2? ions, which can result in high leakage current,
were involved in N2 sintered ceramics than that in O2- and
air sintered compositions. However, greatly reduced leak-
age currents were obtained in N2 sintered ceramics which
should be ascribed to the formation of secondary phases.
The largest polarization and lowest leakage current were
obtained in the sample sintered in N2 (2 h), which
owned the optimal ferroelectric, piezoelectric, and elec-
tromechanical properties with piezoelectric constant
d33 = 98 pC/N, planar electromechanical coupling factors
kp = 26.1 %, remnant polarization Pr = 25.7 lC/cm2,
coercive field Ec = 74.6 kV/cm, and a high Curie tem-
perature Tc = 632 �C, respectively.
1 Introduction
Ferroelectric materials are widely used as dielectric mate-
rials in contemporary electronics, serving functions such as
bypassing, coupling, filtering, smoothing, and power con-
ditioning [1–3]. One of the challenges currently faced by
industry is that most dielectric materials are not able to
work properly at temperatures higher than 150 �C, whereas
the advance of technology demands electronic devices that
can be used under harsh environments ([200 �C) such as
dynamic fuel injection nozzle in car engines (*300 �C)
and acoustic transducer in oil well (200–300 �C) [4].
Recently, BiFeO3 material exhibiting coupling between
different degrees of freedom, such as strain, polarization
and magnetization, has received great scientific and tech-
nological interest as piezoelectric material due to its high
transition temperatures and large polarization character-
ization. Here, it is the Bi ion with two electrons on the 6 s
orbital (lone pair) that moves away from the centrosym-
metric position in its oxygen surrounding and gives rise to
ferroelectricity. However, so far it has not been possible to
exploit the compositions for commercial applications in the
bulk state due to large leakage current and extremely large
coercive field, as a result of which the bulk ceramic cannot
be electrically poled efficiently. Moreover, it is difficult to
fabricate pure BiFeO3 material in bulk state due to the
formation of secondary phases such as Bi2O3, Bi2Fe4O9,
Bi25FeO39, Bi25FeO40, or Bi46Fe2O72 [5–7]. Many attempts
have been made to overcome these problems by rapid
liquid-phase sintering [8–10], doping with Mn, Nb, La, Ti,
and Mo ions [11–16], forming solid solutions with other
perovskites [17, 18], and even annealing under different
extreme conditions, such as magnetic field [19]. Among the
various modifications reported in the literature, modifica-
tion by BaTiO3 i.e. (1-x)BiFeO3–xBaTiO3 (BF–BT) has
Z. Yao (&) � C. Xu � H. Liu � H. Hao � M. Cao � Z. Wang �Z. Song � W. Hu � A. Ullah
State Key Laboratory of Advanced Technology for Materials
Synthesis and Processing, Wuhan University of Technology,
Wuhan 430070, People’s Republic of China
e-mail: [email protected]
H. Liu
e-mail: [email protected]
123
J Mater Sci: Mater Electron (2014) 25:4975–4982
DOI 10.1007/s10854-014-2260-0
shown some very interesting features such as high Curie
point ([450 �C) and large polarization characterization.
For example, Eitel et al. [11] found small amount of Mn
modified BF-BT ceramics with BT content of 0.25 sintered
under oxygen atmosphere showed enhanced DC resistivity
of 7.6 9 1012 X m, and its piezoelectric constant d33 and
Curie temperature Tc were 116 pC/N (low field) and
580–619 �C, respectively. Chen et al. [20] reported that the
introduction of excess Bi content (*1 %) in 0.75BF–
0.25BT ceramics could sharply improve the temperature
stability of dielectric and piezoelectric properties which
exhibited a Curie temperature Tc of 508 �C, dielectric
constant of 440, tan d (1 kHz) of 4.6 %, remnant polari-
zation of 34.4 lC/cm2, piezoelectric constant d33 of 114
pC/N, and planar electromechanical coupling factor kp of
0.31, respectively.
As in very pure BiFeO3, due to the spontaneous change
of the oxidation state of Fe (3 ?/2 ?), oxygen vacancies
are formed as a result of the electrical neutrality require-
ment, giving rise to thermal activated hoping conductivity.
Recently, it has been reported that the sintering atmosphere
plays an important role in the structure and properties of
BiFeO3 system [21–27]. Most studies reported in BiFeO3
system were to reduce the concentration of oxygen
vacancies and to hinder the changes of Fe3? valence states
[9]. It is possible that reducing the concentration of oxygen
vacancies and stabilizing Fe3? valence states can be arti-
ficially achieved by the improvement of sintering technique
under different atmospheres. Some researchers [21–24]
reported in BiFeO3 materials that oxygen treatment could
result in improved leakage current while others [25–27]
draw the opposite conclusion and obtained superior prop-
erties by nitrogen treatment. Up to now, the exact mecha-
nism of the improvement of leakage current in BiFeO3-
based materials processed in various atmospheres is still
under debate and research in BF–BT systems by atmo-
sphere sintering is currently reporting new data. In this
work, 0.8BiFeO3–0.2BaTiO3 (8BF–BT) ceramics were
sintered in N2, air, and O2, respectively. The influences of
atmosphere sintering on structure, electrical properties, and
the possible defect mechanism were intensively discussed.
2 Experimental procedure
Specimens with the compositions of 0.8BiFeO3–0.2BaTiO3
(8BF–BT) were prepared by conventional solid-state
method. The reagent-grade materials of Bi2O3, Fe2O3,
BaCO3, and TiO2 powders were weighed as starting pow-
ders according to the nominal stoichiometric ratio. The
powders were mixed, calcined (730 �C, 2 h), ground, dried
and then re-mixed with 1.5 wt% polyvinyl alcohols (PVA)
binder. The powders were pressed into pellets with 12 mm
in diameter and *1.0 mm in thickness at 200 MPa. These
green pellets were burnt out at 650 �C and then sintered at
980 �C for 2–4 h using a quartz tube furnace under various
atmospheres.
Densities of the pellets were measured by Archimedes
method and the relative density was measured to lie in the
range of 95.1–96.5 %. Phase structures were detected by a
Philips vertical X-ray diffractometer (XRD, PW3050/60,
high resolution X’Celerator detector, MPSS) using Cu Ka1
radiation confirmed the formation of perovskite-type pha-
ses with 2h in the range of 10�–80�. The microstructure
observations of the fresh fractured surfaces of sintered
specimens were examined using a scanning electron
microscopy (SEM, Akashi Seisakusho JSM-5610LV).
Changes in chemical valence were detected by X-ray
photoelectron spectroscopy (XPS, XSAM-800). For elec-
trical characterizations, the samples were polished down to
0.6–0.7 mm in thickness. The pellets were printed on both
sides by high-temperature silver electrodes, burnt out the
binder in silver paste at 450 �C for 30 min in air, and then
fired at 800 �C for 20 min under the same atmosphere as
the samples sintered to eliminate the effects of firing
atmospheres on the valence states of the compositional
elements. The sintered ceramics were poled in an oil bath
under an electric field of 6–10 kV/mm at 120 �C for
15 min. Temperature dependence of dielectric properties of
the ceramic samples was measured using an LCR meter
(Agilent E4980A) at different temperatures. The piezo-
electric constant d33 and the electromechanical coupling
factor kp of the specimens were measured 1 day after
poling using a quasi-static piezoelectric d33 meter (Model
ZJ-3D, Institute of Acoustics Academic, China) and an
impedance analyzer (HP4294A) by the resonance and anti-
resonance technique on the basis of IEEE standards,
Fig. 1 Room-temperature XRD patterns of 8BF–BT samples sintered
in different atmospheres
4976 J Mater Sci: Mater Electron (2014) 25:4975–4982
123
respectively [28]. Both the room-temperature hysteresis
loops of polarization and leakage current density were
performed using RT66A ferroelectric testing system
(Radiant Technologies) in silicon oil under different elec-
tric field. For each electrical measurement, at least three
samples were measured to obtain the average electrical
properties.
3 Results and discussion
3.1 Phase structure and microstructures
Figure 1 shows the XRD patterns of 8BF–BT samples
sintered for 2–4 h in different atmospheres. It is evident
from this figure that, for all sintered samples, the peak at
2h–45� is a singlet, while at 2h–39� is doublet, as expected
for the rhombohedral structure of BiFeO3. Hence, all the
samples crystallize into the rhombohedrally distorted
perovskite structure with R3c space group reported
everywhere [29, 30], which is independent on the sintering
atmospheres. However, a weak diffraction peak can be
observed at 2h–27.4� only in the samples sintered in N2
which belong to Bi-containing impurity phases [5–7].
Figure 2 shows typical SEM pictures of the fresh frac-
tured surfaces of 8BF–BT ceramics sintered for 2–4 h in
different atmospheres. All samples give rise to non-uni-
form grains about 3–5 lm except for the samples sintered
for 2 h in O2 (*1 lm), but clear grain boundary can be
observed. The longer sintering time in O2 at the same
temperature the bigger grain size can be obtained. When
sintered at high temperatures, the evaporation of Bi will
Fig. 2 Typical SEM pictures of the fresh fractured surfaces of 8BF–BT ceramics sintered at 980 �C in different atmospheres. Where, a O2 for
4 h; b O2 for 2 h; c Air for 2 h; d N2 for 2 h; e N2 for 4 h
J Mater Sci: Mater Electron (2014) 25:4975–4982 4977
123
seriously influence the microstructure and electrical char-
acterization. So, the only factor leading to abnormal grain
sizes can be ascribed to the evaporation of Bi as sintering
aid (low melting point) which can be beneficial for grain
growth. This also indicates the less volatility of Bi in the
ceramics sintered in O2 for 2 h than that in other
conditions.
3.2 Dielectric properties and leakage current
characterization
Clear dielectric anomalies of unmodified 8BF–BT ceram-
ics were seldomly reported, which may be due to the
significantly increased DC conductivity at elevated tem-
peratures. Figure 3 shows the dielectric temperature spec-
tra (1 kHz) of N2 sintered 8BF–BT ceramics. As for air-
and O2 sintered ceramics, the datum of dielectric properties
could not be obtained entirely at elevated temperatures due
to DC conductivity beyond measurement limitation. It is
found that obvious dielectric peaks are observed for N2
sintered ceramics, reflecting that the high temperature DC
resistivity is improved. Additional data for comparison
with sintered BF–BT ceramics are presented in Table 1. It
can be observed that the ceramics sintered in O2 and air
exhibit high dielectric constant at room temperature as well
as dielectric loss. In the case of N2 sintered compositions,
significantly lower dielectric loss values were achieved
compared with that sintered in other atmospheres.
The leakage current is one of the most vital characteris-
tics for any ferroelectric material to be used in devices.
Figure 4 shows the leakage current density and resistivity
versus electric field curves of 8BF–BT ceramics sintered in
for 2–4 h various atmospheres. As the field increases, a
sharp increase in the current density of sintered ceramics is
observed. The great difference of current density can be
observed for the ceramics under different sintering atmo-
spheres. It can be seen that, under the same electric field, N2
sintered samples exhibit the lowest current densities while
the O2 sintered ceramics are leakier than those sintered in
air. For example, at 1.0 kV/cm, the leakage current density
and resistivity are 2.22 9 10-4 A/cm2 and 4.43 9 107
Ohms cm in O2 (4 h), 1.77 9 10-4 A/cm2 and 5.56 9 107
Ohms cm in O2 (2 h), 7.66 9 10-7 A/cm2 and 1.28 9 1010
Ohms cm in air (2 h), 1.69 9 10-9 A/cm2 and 5.81 9 1012
Ohms cm in N2 (2 h), 2.72 9 10-9 A/cm2 and 3.61 9 1012
Ohms cm in N2 (4 h), respectively.
3.3 Ferroelectric properties
The hysteresis loop is one of the most important charac-
teristics of a ferroelectric material and gives information on
its dynamic polarizability. It has been known that the
coercive field of BF-rich ferroelectric ceramic is very high
[36]. Figure 5 shows the room temperature P-E loop
behavior for 8BF–BT ceramics sintered in various atmo-
spheres till to breakdown. The P-E loops of the O2 sintered
samples appeared round and leaky under a low field, which
failed to get saturated due to the large leakage current,
shown as in Fig. 5a. When the ceramics were sintered in
N2 and air, the lossy response was suppressed and
decreased. Compared with N2 sintered samples, the loops
of air sintered samples seem to be of unsaturated behavior
because of a higher leakage current and partial reversal of
polarization. As shown in Fig. 5, the optimal values of
remnant polarization Pr and coercive field Ec are about
12.6 lC/cm2 (54.4 kV/cm), 25.7 lC/cm2 (74.6 kV/cm)
Fig. 3 Dielectric temperature spectra (1 kHz) of N2 sintered 8BF–BT
ceramics
Table 1 Ferro- and piezoelectric properties of present 8BF–BT
system at room temperature, compared to the other Bi-based systems
Material Tc
(�C)
er tan d d33
(pC/N)
kp (%) Ref.
0.85BF–0.15BT 700 242 0.022 - - [11]
0.8BF–0.2BT 570 412 0.058 - - [31]
0.8BF–0.2BT [600 300 *63 *14.0 [32]
0.75BF–0.25BT 508 440 0.046 114 31.0 [20]
BSPT57 crystal 402 3,000 0.040 1,150 [33]
0.36BS–0.64PT 450 2,010 0.027 460 56.0 [34]
0.47BSF–0.53PT 428 830 0.040 290 50.0 [35]
0.8BF–0.2BT
O2, 4 h - 589 0.942 - -
O2, 2 h - 417 0.364 - -
Air, 2 h - 284 0.142 38 13.5
N2, 2 h 632 333 0.065 98 26.1
N2, 4 h 631 232 0.061 56 16.3
4978 J Mater Sci: Mater Electron (2014) 25:4975–4982
123
and 16.2 lC/cm2 (59.6 kV/cm) for air, N2 (2 h), and N2
(4 h) sintered samples, respectively. It can be noticed that
the remnant polarization is enhanced apparently in the N2
sintered samples compared with that of air sintered
samples.
3.4 XPS analysis
As mentioned above, the ceramics sintered in N2 can be
poled completely and exhibit large ferro- and piezoelectric
characterization due to low leakage current. It has been
well proved that the larger leakage currents in magneto-
electrics often result from mixed valence for the magnetic
ions (e.g., Fe2? and Fe3?), from oxygen vacancies, or from
both.
As in easily volatile elements such as bismuth exist in
8BF–BT ceramics, defects are easily produced during
sintering. According to the study of Bi4Ti3O12 by Hiruma
et al. bismuth vacancy is easily generated at high temper-
atures accompanied with the nearest-neighbor oxygen
vacancies to maintain charge balance during defect for-
mation, while bismuth escapes from the lattice position and
evaporates as Bi2O3. The formation of oxygen vacancies
arises from the evaporation of Bi and lower oxygen
atmosphere, which is accompanied with the Ti valence
transition to maintain charge balance during defect for-
mation [37]. Similarly, the sintering atmosphere can also
induce oxygen vacancies and Fe valence transition in 8BF–
BT ceramics when sintering. The reaction can be described
as follows:
Fig. 4 The leakage current
density and resistivity versus
electric field curves of 8BF–BT
ceramics sintered for 2–4 h in
various atmospheres
J Mater Sci: Mater Electron (2014) 25:4975–4982 4979
123
2Fe3þ þ O2� ) 2Fe2þ þ 0:5O2½volatilization� þ V2þO
ð1Þ
2Bi3þ þ 3O2� ) Bi2O3½volatilization� þ 2V3�Bi þ 3V2þ
O
ð2Þ
Many attempts have been made to see whether both
Fe3? and Fe2? are present in BiFeO3, based on the shape of
the Fe 2p X-ray photoelectron spectrum (XPS) [38–41].
The approach applied suggested a priori that the Fe 2p XPS
of BiFeO3-based samples can be treated in the usual way,
when the peak maximum of the Fe 2p3/2 X-ray spectra is
decomposed into a superposition of symmetric compo-
nents. The Fe 2p3/2 component with the binding energy of
*710.8 eV was assigned to the Fe3? state while that with
*709.4 eV to the Fe2? state [42, 43]. Figure 6 shows the
deconvolution of XPS Fe 2p3/2 spectra of 8BF–BT
ceramics sintered for 2–4 h in different atmospheres with
the peaks corresponding to Fe element after Shirley-type
background. The broad asymmetric Fe 2p3/2 peaks suggest
the coexistence of Fe2? and Fe3? in these ceramics. The Fe
2p3/2 spectra can be divided into two subbands centered at
*709.4 and *710.8 eV by XPSPEAK 4.1 software,
respectively. The percentage of Fe2? to the total ions
(Fe3? ? Fe2?) is determined by the relative area of Fe2?
peak to the whole peak, which is 18.9 % in O2 (4 h), 9.4 %
in O2 (2 h), 27.2 % in air, 36.2 % in N2 (2 h), while
43.8 % in N2 (4 h), respectively. This demonstrates that
more Fe ions are maintained at ?3 valence in the O2 sin-
tered samples than that in N2 sintered samples and more
evaporation of Bi will happen in N2 sintered samples.
Therefore, the leakage in 8BF–BT ceramics is likely
induced by the existence of Fe2? and oxygen vacancies,
which both are detrimental for characterizing the intrinsic
properties of 8BF–BT. It can be expected that Bi was
extracted from the original perovskite lattice when sinter-
ing. However, the remained Bi constructed a defective
perovskite with many oxygen and Bi vacancies. This may
induce an oxygen deficient and reducing environment in
the material, which contributes to Fe valence transition and
therefore high leakage current for N2 sintered ceramics. As
analysized above, the samples sintered in O2 should
Fig. 5 P-E loop behavior for 8BF–BT ceramics sintered for 2–4 h in various atmospheres till to breakdown
4980 J Mater Sci: Mater Electron (2014) 25:4975–4982
123
achieve lower leakage current and higher resistivity than
that sintered in N2. However, the result is just the opposite.
As seen from Figs. 4, 5, the N2 sintered ceramics exhibits
greatly reduced current densities and can be poled effec-
tively while not for O2 sintered ceramics. It can be deduced
that these defects mentioned above should not be respon-
sible for leakage current.
Many studies on BiFeO3-based materials have been
interested in eliminating secondary impurities and oxygen
vacancies to reduce leakage and increase resistivity,
thereby improving ferroelectric properties. As in BiFeO3,
the ferroelectricity has been observed with a giant swit-
ched polarization of 110–136 lC/cm2 grown by physical/
chemical deposition [44–46] and theoretically predicted
with the polarization of 90–110 lC/cm2 [47]. This indi-
cates that the intrinsic ferroelectric property of BiFeO3-
based system should theoretically be very high when
poling completely. As shown in Fig. 5, the values of
remnant polarization (Pr) and coercive field (Ec) at the
same field of 80 kV/cm are about 12.6 lC/cm2 (52.6 kV/
cm), 4.7 lC/cm2 (34.4 kV/cm) and 4.5 lC/cm2 (34.5 kV/
cm) for air (2 h), N2 (2 h), and N2 (4 h) sintered samples,
respectively. It can be observed that more Fe2? ions in
8BF–BT ceramics can deteriorate the ferroelectric prop-
erties while obviously decrease coercive field. Greatly
reduction of coercive field can be ascribed to slight dis-
tortion of the lattice (FeO6 octahedra) due to different
ionic radii between Fe3? (0.645 A) and Fe2? (0.78 A).
Although Fe2? ions in O2 sintered composition are rather
low, the intrinsic breakdown strength of pure 8BF–BT is
limited which leads to incomplete poling. So, there must
be another factor which contributes to the enhancement of
breakdown strength. Here, we have demonstrated that
secondary Bi-containing phase appears in N2 sintered
ceramics during processing owing to the thermodynamic
stability of the phase while no any secondary phase
observed in other atmospheres. It is well-known that the
impurity phase can increase resistivity due to its non-
ferroelectric activity. Therefore, one possible explanation
for the observed behavior for the samples sintered in N2
may be related to the existence of secondary phases
which exhibit high resistivity and that greatly reduce the
leakage currents.
4 Conclusions
In summary, the structure, electrical properties, and defect
mechanism of 8BF–BT composition sintered in O2, air, and
N2 were intensively investigated. XRD results indicated the
appearance of secondary phases for the samples sintered in
N2 while not observed in other atmospheres. The charged
defects by Fe2? ions, which will reduce the electrical
resistivity of the samples and give rise to high leakage
currents, were more in the samples sintered in N2 than that
sintered in other atmospheres by XPS spectra. However,
greatly improved leakage currents were achieved in N2
sintered compositions and the samples sintered in other
atmospheres exhibited large leakage currents. One possible
explanation for the observed behavior for the samples
sintered in N2 may be related to the existence of secondary
phases which greatly improve the leakage currents. The
largest polarization and lowest leakage current were
obtained in the sample sintered in N2 (2 h), which
owned the optimal ferroelectric, piezoelectric, and elec-
tromechanical properties with piezoelectric constant
d33 = 98 pC/N, planar electromechanical coupling factors
kp = 26.1 %, remnant polarization Pr = 25.7 lC/cm2,
coercive field Ec = 74.6 kV/cm, and a high Curie tem-
perature Tc = 632 �C, respectively. It is expected that the
BF–BT system will form the basis of an important family
Fig. 6 The deconvolution of XPS Fe 2p3/2 spectra of BF–BT
ceramics sintered in different atmospheres
J Mater Sci: Mater Electron (2014) 25:4975–4982 4981
123
of high-performance lead free piezoelectric ceramics by the
improvement of sintering techniques.
Acknowledgments The authors would like to thank the support
of the International Technology Cooperation Project from the Min-
istry of Science and Technology of China (2011DFA52680), Natural
Science Foundation of China (No. 51372191 and No. 51102189), the
Fundamental Research Funds for the Central Universities (No.
2012-IV-006), and State Key Laboratory of New Ceramic and Fine
Processing Tsinghua University (KF201314).
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