Perovskite La0.67-xLi3xTiO3 with x = 0.10, 0.11, 0.12 and 0.13 were firstly annealed at 800 oC then treated by reactive milling, followed by post-annealing at temperatures from 1100 to 1200oC. The crystalline structure of grain and grain-boundary were characterized by XRD and SEM. The impedance measurements showed that nanocrystalline La0.67-xLi3xTiO3 after being annealed at 1150 oC possessed a grain conductivity as high as 1.3×10-3 S.cm-1. The grain-boundary conductivity was enhanced one order in magnitude after annealing at temperature higher 1100oC and consists of 5.8×10-5 S.cm-1. The results have also showed the limitation of the adiabatic thermal treatment for the improvement of the grain-boundary conductivity and suggested the way to overcome the limitation by rapidly cooling the samples from the high temperature to room temperature

Dinh, Nguyen Nang

Long, Pham Duy

Trong, Le Dinh

Vietnam Academy of Science and Technology: Journals Online

Communications in Physics, Vol. 19, No. 4 (2009), pp. 235-242
EFFECT OF ANNEALING TEMPERATURE ON THE Li
+
IONIC
CONDUCTIVITY OF La0.67−xLi3xTiO3
LE DINH TRONG
Faculty of Physics, Hanoi Pedagogical University No. 2
PHAM DUY LONG
Institute of Materials Science, VAST
NGUYEN NANG DINH
College of Technology, Vietnam National University, Hanoi
Abstract. Perovskite La0.67−xLi3xTiO3 with x = 0.10, 0.11, 0.12 and 0.13 were firstly annealed
at 800 oC then treated by reactive milling, followed by post-annealing at temperatures from 1100
to 1200oC. The crystalline structure of grain and grain-boundary were characterized by XRD and
SEM. The impedance measurements showed that nanocrystalline La0.67−xLi3xTiO3 after being
annealed at 1150 oC possessed a grain conductivity as high as 1.3 × 10−3 S.cm−1. The grain-
boundary conductivity was enhanced one order in magnitude after annealing at temperature higher
1100 C˚ and consists of 5.8 × 10−5 S.cm−1. The results have also showed the limitation of the
adiabatic thermal treatment for the improvement of the grain-boundary conductivity and suggested
the way to overcome the limitation by rapidly cooling the samples from the high temperature to
room temperature.
I. INTRODUCTION
Superionic conductors or solid electrolytes are the subjects that have been con-
centrated to deal with both the theoretical and experimental researches, due to their
prospective applications in many scopes, such as microelectronics, solid lithium batteries,
electrochromic display [1-3]. Among these materials, much attention has been paid to
lithium ion conducting perovskites (ABO3). The first paper was reported by Belous et
al. [4]. Later, Inaguma et al. have shown that a high conductivity of the perovskite
lanthanum lithium titanate has been found [5]. Recently, we reported [6] on ionic con-
ductivity of perovskite La0.67−xLi3xTiO3 prepared by solid state solution reaction. The
sample with x = 0.11 had the best ionic conductivity, at room temperature it was as high
as 3,1×10−5 S.cm−1 and increased up to a value of 6×10−3 S cm−1 at 200 C˚. Though they
are not suitable for solid electrolytes of lithium batteries due to the low reduction-proof
against lithium metal, the fundamental studies are still important in the field of solid-state
ionics and solid-state chemistry. Therefore, from perovskite-type lithium ion conductors,
La0.67−xLi3xTiO3 compounds are the most attractive due to their high conductivities,
complex structures including microstructures, and have been extensively investigated con-
cerning their structures and lithium ion conductivities. In ref. [7] the authors showed
that there was a strong correlation between structure and percolative diffusion pathways
in the perovskites that was primarily referred to the ordered arrangement of La ions, and
236 EFFECT OF ANNEALING TEMPERATURE ON THE Li+ IONIC CONDUCTIVITY ...
the “bottleneck” square - surrounded by four oxygen ions determined by the distortion
and tilt of TiO6 octahedral. In addition, the 90˚-oriented micro-domain structure, which
also influences the percolative diffusion pathways in La0.67−xLi3xTiO3 was also observed.
It is seen that the grain boundaries have strongly affected to the bulk ionic conductiv-
ity (i.e. total conductivity of the conductivities of the grains and grain boundaries) of
the perovskite La0.67−xLi3xTiO3. The way to increase the bulk ionic conductivity is to
prepare samples with the grain conductivity as large as possible and to lower the grain
boundaries resistance. With this aim we have made effort to synthesize samples of the
La0.67−xLi3xTiO3compounds with different x-compounds of Li that was doped, conse-
quently annealed at different temperatures. The crystalline structure, surface morphology
and ionic conductivity of the samples have been studied.
II. EXPERIMENTAL
The La0.67−xLi3xTiO3 solid solution samples with x = 0.10; 0.11; 0.12; and 0.13,
abbreviated as M10, M11, M12 and M13, respectively were prepared from stoichiometric
amounts of TiO2(99.99%), Li2CO3, (99.99%) and freshly dehydrated La2O3 (99.9%) pur-
chased from Aldrich. These starting materials were grinded by a grinder of “Fritsch model
Pulverisette 6”, then calcinated in platinum crucibles at 800 C˚ for 10 h. After grinding
and pressing again, a second heating treatment - annealing was performed on smaller pel-
lets (φ = 12.5 mm, d = 1.4 mm, pressure of 500 MPa) at 1100, 1150, 1200 and 1250 C˚
for 4 h. The heating sweep rate is 5 C˚.min−1and the cooling is natural. The crystalline
structure has been studied by using X-ray diffraction analysis (XRD, Siemen D5000 diffrac-
tometer) and the surface morphology - by FE-SEM microscope (Model S4800, Hitachi).
The ionic conductivity of the samples was characterized on AutoLab. Potentiostat-PGS30
using FRA-2 impedance software. To characterize impedance spectroscopy (IS) the sam-
ples were mechanically polished and chemically treated in order to have clean and parallel
surfaces, then on these surfaces a metallic silver coating with 6 mm-diameter circle was
vacuum evaporated. Sintered cylindrical pellets 12.5 mm in diameter and 1.4 mm in
thick, with the evaporated silver electrodes, were used for electrical measurements. IS
measurements were recorded under normal atmosphere between room temperature (RT)
and 200 C˚, in the frequency range 0.1 Hz to 1.0 MHz. The grain and grain boundaries
conductivity was obtained by fitting experimental data with the theoretical curves using
appropriate equivalent schema.
III. RESULTS AND DISCUSSION
III.1. Crystalline structure and morphology
From XRD analysis it has been seen that after being calcinated at 800 C˚ between
La2O3, Li2CO3 and TiO2 occurred solid sate reaction to remove CO2 and to form chemical
bonding of La, Li, Ti and O atoms, consequently to create some compounds of La0,66TiO3,
Li2Ti3O7, La2Ti3O7 and La(OH)3as shown in Fig. 1.
After thermal grinding, above mentioned structure phases have disappeared, instead
a single phase structure with the compound of La0.67−xLi3xTiO3 was obtained (see XRD
patterns “a” for the as-grinded sample in Fig. 2). Moreover, the fact that XRD showed
LE DINH TRONG, PHAM DUY LONG, AND NGUYEN NANG DINH 237
Fig. 1. XRD patterns of La0.67−xLi3xTiO3 samples after calcination at 800 C˚.
Fig. 2. XRD patterns of La0.67−xLi3xTiO3 samples: as-grinded (pattern “a”),
after annealed at 1100 C˚ (pattern “b”) and at 1250 C˚ (pattern “c”).
rather small and broad peaks in the 2θ range from 30o to 60o proves the uniform distri-
bution of the nanostructured single La0.67−xLi3xTiO3 compound. Using Sherrer’s formula
one can calculate the average size of the nanostructure grains in this polycrystalline sam-
ples (it is about 30 nm).
Annealing at temperature from 1100 C˚ to 1250 C˚ enabled these samples be re-
crystallized, therefore the crystallities increased and the nanosize grains were grown up to
several micrometers (XRD patterns “b” and “c” in Fig. 2). The sample annealed at 1250
C˚ exhibited larger grains size in comparison with the sample annealed at 1100 C˚.
From all the XRD patterns in Fig. 2 one can see that by using reactive milling solid
solution mixture from stoichiometric oxides of TiO2, Li2COand La2O3 in combining with
post-annealing, the single crystalline phase of a La0.67−xLi3xTiO3 compound has been
prepared.
The clearer picture of the grain growth can be seen by using scanning electron
microscope. Figure 3 shows the FE-SEM images obtained for sample M10 which was
annealed at 1100, 1150, 1200 and 1250 C˚. Although a step of annealing temperature
was only 50 C˚, with the increase of the anneal temperature the grain size considerably
238 EFFECT OF ANNEALING TEMPERATURE ON THE Li+ IONIC CONDUCTIVITY ...
increased, from 1 µm (at 1100 C˚) to 5 µm (at 1250 C˚). In the sample annealed at 1100 C˚
there were observed large pores (Fig. 3a) and these pores were diminished by annealing
at higher temperature (Figs. 3b to 3d).
Fig. 3. FE-SEM of the sample M10 annealed at 1100 C˚ (a), 1150 C˚ (b), 1200
C˚ (c) and 1250 C˚ (d).
III.2. Ionic conductivity
For characterization of ionic conductivity it is necessary to carry-out impedance
spectra measurements throughout a large range of frequencies from 0.1 Hz to 100 MHz.
Due to this behavior of the grain, grain-boundary conductance and the contact resistance
of the electrodes can be revealed in the complex impedance diagrams (CID) of the samples.
The semicircle of impedance spectra at the higher 0.1 MHz frequencies is related to the
conducting process in crystalline grains, whereas the semicircle in the CID at average
frequencies (from 10 Hz to 1MHz) reflects the ionic conducting in the grain boundaries.
The line starting from the end of the semicircles at the frequencies lower 10Hz is related
to the diffusion process of ions in Helmholtz layer between the electrodes and the sample.
Since the semicircle of the complex impedance diagram in the high frequency range
is much smaller than that in the low frequencies range, the investigation of the grain and
grain-boundary ionic conductivity of the sample is carried-out and elaborated separately
each from other. This is demonstrated in Fig. 4. Figures 4a and 4b correspond to high
(30 MHz ÷ 0.3 MHz) and low (0.1 MHz ÷ 100 Hz) frequencies ranges, respectively for the
Nyquist complex impedance diagram measured at room temperature of sample M11, that
annealed at 1200 C˚. The ending of the first semicircle (Fig. 4a) at about Z’ = 200 Ω
LE DINH TRONG, PHAM DUY LONG, AND NGUYEN NANG DINH 239
is the starting of the second semicircle (Fig. 4b)
which has the ending at frequency of 27 Hz with a
real part of the resistance of 33 kΩ. The first semi-
circle exhibits the behavior of ionic conductance in
grains and the second one is of grain boundaries,
as described in [8-9].
In almost potentiostats like the AutoLab-PGS-
30 the frequency range is from 1.0 MHz to 0.01 Hz.
Therefore, the first semicircle obtained in the range
from 30 MHz to 300 kHz there observed several
pints with such a small value of resistance that was
not revealed together with the high resistance val-
ues of the second semicircle. Thus grain resistance
(Rg) and the total resistance (Rg+Rgb) of the sam-
ple can be evaluated, respectively from the right
ending points of the first and the second semicircles
in Fig. 4a and 4b. Qualitatively, one can compare
Rgb and Rg by the ratio of the two ending point
values in Z’ abscissa from this figure. Indeed, the
obtained ratio was found to be of 30 kΩ/200 Ω =
1.5×102, this means the grain-boundary resistance
is larger than the grain resistance in more than two
orders in magnitude. That is why to improve the
ionic conductivity is necessary to lower the grain-
boundary resistance.
Fig. 4. Complex impedance diagrams
of sample M11 anneled at 1200 C˚.
The measurements at room temper-
ature and in the range of frequences
from 30 MHz to 300 kHz (a) and from
1.0 MHz – 0.1 Hz (b).
0 100k 200k 300k
0
100k
200k
300k
1250
o
C
1200
o
C
1150
0
C
1100
0
C
Z
"
(O
h
m
)
Z' (Ohm)
(a)
0 100k 200k 300k 400k
0
100k
200k
300k
400k
1250
o
C
1200
o
C
1150
o
C
1100
o
CZ
"
(O
h
m
)
Z' (Ohm)
(b)
Fig. 5. Complex impedance diagrams vs. temperature of samples M10 (a), M11 (b).
Fig. 5 shows the CID of the samples M10 and M11 annealed at temperatures of
1100 C˚, 1150 C˚, 1200 C˚ and 1250 C˚. All the measurements were carried-out at room
temperature. From this figure one can see that all the CIDs consist of two parts: the
240 EFFECT OF ANNEALING TEMPERATURE ON THE Li+ IONIC CONDUCTIVITY ...
first part is the semicircle relating to grain-boundary conductivity and the second one is
the line obtained at low frequencies that relates to the diffusion process in the Helmholtz
layer. The fact that the increase of annealing temperature resulted in the diminishing
of the semicircles proves that the grain-boundary conductance much decreased. This is
explained by (i) with higher annealing temperature the grains were larger grown, conse-
quently the number of grain boundaries decreased and (ii) the crystalline structure of the
grains became more perfected. From the FE-SEM one can see the structure of the grains
and grain boundaries were much enhanced from the annealing temperature of 1100 C˚ to
1200 C˚.
Fig. 6. Equivalent schema used for fitting the CID data of the La0.67−xLi3xTiO3 sampes.
For the accurate determination of the ionic conductivity we used a fitting method
between experimental curves and the theoretical curves obtained from equivalent schema
to the CIDs. These CIDs of the La0.67−xLi3xTiO3 samples with Ag electrode (Ag | LLTO
| Ag) were well fitted by the equivalent schema of Rg(CgbRgb)(RcQc)(Cin[Rin(CdlW)] that
is illustrated in Fig. 6. By this schema Rg is the resistance characterizing the grain
conductivity; Rgb and Cgb are the resistance and capacity of grain boundaries, respectively;
Rin and Cin are the resistance and the capacity formed by the contact between the Ag thin
film electrode and samples surface; W and Cdl are, respectively the Waburg impedance
characterizing the charge shift and the capacity of the double charge layer; Rc and Qc are,
respectively the resistance and the constant phase component (CPE) related to electrodes.
To determine the ionic conductivity (σ) one can use the following formula:
σ =
d
R.S
where d is the thickness of the sample, S – area and R– resistance relating to ionic
conductance that is determined from equivalent schema.
Figure 7 presents the curves of grain conductivity, grain-boundary conductivity and
also the bulk ionic conductivity of samples M10, M11, M12 and M13 vs. the annealing
temperature. All the measuring data were obtained at room temperature. From these fig-
ures one can see that the grain conductivity slightly rose up with increase of the annealing
temperature and did not change more with the annealing temperatures over 1150 C˚. The
sample M12 (annealed at 1150 C˚) has the largest grain ionic conductivity, σg = 1.3×10
−3
S.cm−1. This value of the conductivity is fairly larger than the one of La0.67−xLi3xTiO3
sample that was reported by Inaguma et al. (σg = 1.0×10
−3 S.cm−1) [8]. This was
explained by the different loss of Li ions during annealing at high temperatures.
LE DINH TRONG, PHAM DUY LONG, AND NGUYEN NANG DINH 241
(a) (b)
(c)
Fig. 7. The room-temperature ionic conductivity vs. annealing temperature for
samples M10, M11, M12 and M13:(a) – Grain conductivity, (b) – Grain-boundaries
conductivity and (c) – Bulk conductivity.
In difference with the grain conductivity, the grain-boundary conductivity increased
considerably for the samples annealed at higher temperature (see Fig. 7b). It is known
that this conductivity is strongly dependent on the Li-content in the boundaries, the size
and the porosity of the boundaries [9]. At temperature higher 1000 C˚ the Li-content
was maintained unchangeably, the increase in the conductivity can be attributed to the
larger change in crystalline grains and boundaries. Among all the samples, the M10 which
was annealed at 1200 C˚ exhibits the largest grain-boundary conductivity, namely σgb =
5.8×10−5 S.cm−1. This value is one order in magnitude in comparison with the reported
ionic conductivity of Ban et al. [9]. For the other samples the grain-conductivity is as low
as 10−5 S.cm−1 (see Fig. 7c). Although the σgb was much improved, this value is still much
smaller than the σg(i.e. lower in two orders in magnitude). From our work, it is seen that
by annealing at high temperature as we did the σgb can be increased in only one order.
For enhancing bulk conductivity, the grain-boundary conductance must be more strongly
lowered or a single crystal of La0.67−xLi3xTiO3 should be grown to eliminate all grain
boundaries. But the single crystal growth is unfeasible for such a complex in compounds
of La0.67−xLi3xTiO3 and for the technological difficulty. One can suggest the other effort
242 EFFECT OF ANNEALING TEMPERATURE ON THE Li+ IONIC CONDUCTIVITY ...
in enriching the Li-content of La0.67−xLi3xTiO3 the grain boundaries by a rapid cooling
technique to quenching the samples from a high temperature to RT. The detain results of
this method will be reported in our forthcoming work.
IV. CONCLUSION
La2/3−xLi3xTiO3 with x = 0.10, 0.11, 0.12 and 0.13 were prepared by reactive milling
solid mixture from stoichiometric amounts of TiO2(99.99%), Li2CO3, (99.99%) and La2O3
(99.9%), followed by post-annealing at temperature from 1100 to 1200 C˚. The intergrain
and intragrain conductivities were evaluated by overall analyzing the XRD patterns, FE-
SEM surface morphology and impedance spectra. Because of the formation of nanocrys-
talline stoichiometic La0.67−xLi3xTiO3, after being annealed at 1150 C˚, the samples exhib-
ited a grain conductivity as high as 1.3×10−3 S.cm−1. The grain-boundary conductivity
was enhanced in one order in magnitude after annealing at temperature higher 1100 C˚
and consists of 5.8×10−5 S.cm−1. The improvement in the grain-boundaries conductivity
was explained due to the decrease of the boundary effect.
The result also showed the limitation of the adiabatic annealing, consequently sug-
gest the way to improve the bulk ionic conductivity by a rapid cooling technique for the
samples from the high temperature to room temperature.
ACKNOWLEDGEMENT
This work is supported in part by Vietnam National Foundation for Basic Scientific
Research in Physics (2006-2008), Project code: 410306.
REFERENCES
[1] C. M. Lampert and C. G. Granqvist, eds, in “Large-area Chromogenics: Materials and Devices for
Transmittance Control”, Vol. 154 (SPIE Optical Engineering Press, Bellingham, 1990)
[2] Inaguma Y., Chen L., Itoh M., Nakamura T., Uchida T., Ikuta M., and M. Wakihara, Solid State
Commun. 86 (1993) 689 - 693.
[3] Y. Inaguma, L. Chen, M. Itoh, T. Nakamura, Solid State Ionics, 70/71 (1994) 196-202.
[4] A. G. Belous, G. N. Novitskaya, S. V. Polyanetskaya, Yu. I. Gornikov, Izv. Akad. Nauk SSSR, Neorg.
Mater. 23 (1987) 470-476.
[5] Y. Inaguma, M. Itoh, Solid State Ionics 86–88 (1996) 257-260
[6] N. N. Dinh, P. D. Long, L. D. Trong, Comm. in Phys. 14 (2004) 90-96.
[7] Y. Inaguma, T. Katsumata, M. Itoh, Y. Morii, T. Tsurui, Solid State Ionics 177 (2006) 3037-3044.
[8] C. H. Chen, K. Amine, Solid State Ionics 144 (2001) 51-57.
[9] C. W. Ban, G. M. Choi, Solid State Ionics 140 (2001) 285–292.
Received 15 November 2008.


Effect of Annealing Temperature on the Li\(^{ + }\) Ionic Conductivity of La\(_{0.67 - x}\)Li\(_{3x}\)TiO\(_{3 }\)

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Vietnam Academy of Science and Technology: Journals Online

Effect of Annealing Temperature on the Li+^{ + }+ Ionic Conductivity of La0.67−x_{0.67 - x}0.67−x​Li3x_{3x}3x​TiO3_{3 }3​

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Effect of Annealing Temperature on the Li $^{ + }$ Ionic Conductivity of La $_{0.67 - x}$ Li $_{3x}$ TiO $_{3 }$