a rapid combustion synthesis of mgo stabilized sr- and ba-β-alumina and their microwave sintering
TRANSCRIPT
A rapid combustion synthesis of MgO stabilized Sr- and
Ba-h-alumina and their microwave sintering
Tom Mathews, R. Subasri, O.M. Sreedharan*
Materials Characterization Group, Thermodynamics and Kinetics Division, Indira Gandhi Centre for Atomic Research,
Kalpakkam, Tamil Nadu 603 102, India
Received 5 June 2001; received in revised form 11 February 2002; accepted 18 February 2002
Abstract
MgO stabilized Sr- and Ba-h-alumina powders corresponding to the composition MMgAl10O17 (M=Sr or Ba) were
synthesized through a rapid solution combustion route using stoichiometric amounts of metal nitrates and urea. The products
were characterized by powder X-ray diffraction (XRD). The powders were compacted and sintered using microwaves as the
energy source. Dense MgO stabilized Sr- and Ba-h-aluminas of 94% and 91%, respectively, were obtained within a short period
of 30 min. AC impedance measurements on the microwave-sintered samples performed as a function of temperature yielded
activation energies lower than that reported for the samples sintered through conventional routes. This paper reports of a novel
method for synthesizing phase-pure powders of MgO stabilized Sr- and Ba-h-alumina and sintering of the powder compacts
into dense membranes ( > 90% theoretical density) which materials are used as solid electrolytes in chemical sensors and molten
metal processing. D 2002 Elsevier Science B.V. All rights reserved.
PACS: 81.20.Ka; 81.20.Ev; 81.05.Je; 78.70.G
Keywords: h-Alumina; Microwave sintering; Solid electrolyte; Chemical sensor; Solution combustion synthesis
1. Introduction
Since the discovery of Na-h-alumina more than
three decades ago by Yao and Kummer [1], there has
been a sustained interest in the synthesis and character-
ization of other monovalent (K + , Cs + ), divalent
(Ba + 2, Sr + 2, Pb + 2) and trivalent (La + 3, Sc + 3) ion-
substituted analogs of Na-h-alumina [2–8]. This is
due to the wide variety of applications of the h-alumina family of compounds [9–11]. A recent review
on multivalent cation conduction in solids (Ref. [12]
and references therein) give a detailed account of the
multivalent ion conducting h-aluminas. The ion-sub-
stituted h-aluminas are usually synthesized by the ion
exchange of Na-h-alumina with the respective ions
[5]. There are, however, only few reports on the direct
synthesis of ion-substituted h-aluminas because of the
limited thermal stability of such substituted com-
pounds [13,14].
Alkaline earth hexa-aluminates, which possess h-alumina or magnetoplumbite type structure, show
interesting optical and electrical properties. Among
the two above-mentioned structures, materials with h-alumina type structure exhibit very good ionic con-
0167-2738/02/$ - see front matter D 2002 Elsevier Science B.V. All rights reserved.
PII: S0167 -2738 (02 )00105 -4
* Corresponding author. Tel.: +91-4114-80116; fax: +91-4114-
80081.
E-mail address: [email protected] (O.M. Sreedharan).
www.elsevier.com/locate/ssi
Solid State Ionics 148 (2002) 135–143
ductivity. The hexa-aluminates with composition
MAl12O19 and MAl11O17 crystallize in magnetoplum-
bite and h-alumina type structures, respectively.
Depending on the ionic size of the M + 2 ion in
MAl12O19, it is possible to transform alkaline earth
and similar hexa-aluminates with magnetoplumbite
type structure into h-alumina type structure when
Al + 3 is replaced by Mg + 2 resulting in MMgAl10O17
[15]. This change is observed for M=Sr, Eu and Pb
but not for Ca. Thus, hexa-aluminates containing a
large cation (Ba + 2) possess h-alumina type structure,
whereas for those with smaller cations (Ca + 2), the
structure is magnetoplumbite. The hexa-aluminates
containing cations with intermediate size switch
between both structure types. In the system SrO–
Al2O3, the compound SrAl12O19 is of magnetoplum-
bite type, whereas the MgO stabilized compound,
SrMgAl10O17 is of h-alumina type [16]. In the system
BaO–Al2O3, the two phases Ba1.21Al11O17.71 with
collapsed h-alumina structure and Ba0.75Al11O17.25
with h-alumina structure containing defects are
reported [17]. The MgO substituted analog BaM-
gAl10O17 has h-alumina structure [17,18].
Sr- and Ba-h-aluminas corresponding to the gen-
eral formula MMgAl10O17 (M= Sr or Ba) are syn-
thesized through the conventional ceramic route
[19–21]. Synthesis through ceramic routes require
prolonged heat treatments for several hours at high
temperatures, often with repetitive grinding, compac-
tion and annealing. Besides, the material prepared
contains a second glassy phase, which segregates at
the grain boundaries on sintering and is deleterious to
ionic conductivity. Single phase Ba- and Sr-h-alumina
are reported to be obtained at 1523 and 1573 K, res-
pectively, in 12 h by a conventional ceramic technique
[19,20]. Recently, synthesis through soft chemistry
routes has been of interest. In this technique, homo-
geneous mixing of several components at atomic level
is achieved. This allows a low processing temperature
and a morphological control of uniform crystallite par-
ticle size at superfine dimensions resulting in very high
reactivity. In order to obtain dense membranes, the
phase-pure Ba- and Sr-h-aluminas have to be sintered
at f 2000 K [19,20]. For Ba- and Sr-h-alumina, the
highest relative density of 91% and 94%, respectively,
was obtained by sintering at around 2038 K [19,20].
Sintering at such high temperatures is cost- and
energy-intensive. Besides, it may lead to grain growth,
which is deleterious to mechanical strength and ionic
conductivity. This problem can be circumvented using
microwaves as energy source for sintering [22]. The
use of microwaves for sintering of h-aluminas are
scarce [23–25]. Recently, a direct microwave synthe-
sis cum sintering of MgO stabilized Na-hW-alumina
was reported by Subasri et al. [26,27]. However, there
are no reliable reports on the use of microwaves for the
Fig. 1. Flow chart for the rapid solution combustion synthesis.
T. Mathews et al. / Solid State Ionics 148 (2002) 135–143136
sintering of substituted h-aluminas. Certain ceramics,
like alumina and stabilized zirconia, which require
high temperatures and longer soaking times for sinter-
ing, could easily be sintered to high densities in a
short time using microwaves as energy source [28,29].
In light of the aforementioned factors, the employ-
ment of a solution combustion technique for the rapid
synthesis of fine powders of SrMgAl10O17 and BaM-
gAl10O17 and the subsequent successful application of
microwaves for sintering of such h-aluminas are re-
ported here.
2. Experimental
2.1. Synthesis
All reagents used were of purity greater than 99.9%.
Appropriate amounts of aluminum nitrate, strontium
nitrate or barium nitrate and magnesium nitrate (mag-
nesium nitrate solution was prepared by dissolving
appropriate amount of Mg(CH3COO)2�4H2O in dilute
nitric acid and boiling off excess nitric acid on a hot
plate) were dissolved in distilled water, in such a mole-
ratio with respect to cations to make SrMgAl10O17 and
BaMgAl10O17 as the final products. An aqueous
solution of urea was added as the complexant and
reducer. The amount of urea added was that required
to consume completely the excess oxygen in the
nitrate mixture and is called the stoichiometric amount
[30]. This solution was then refluxed for 10 min and
introduced into an open muffle furnace maintained at
773 K. At this temperature, excess water is removed
from the solution resulting in the formation of a gel
and its simultaneous combustion. The as-combusted
product was obtained as a fine powder. A flow chart
for the steps involved in the combustion synthesis is
given in Fig. 1. The powder X-ray diffraction (XRD)
pattern was collected for the as-combusted product.
XRD patterns were obtained using a Rigaku model
diffractometer with CuKa as the target. The com-
busted product was compacted into disks of dimen-
sions 10-mm diameter and 2–3-mm thickness at a
pressure of 300 MPa and subjected to microwave
radiation (for a period of 20 min) using a domestic
microwave oven.
2.2. Description of the microwave set-up
A domestic microwave oven (2450 MHz, BPL,
India) with a power rating of 800 W was used for
the present study. The compacted disks were placed in
a ceramic crucible embedded in powder bearing the
same composition. This crucible in turn was sur-
rounded by an insulating sheath made up of fibrous
alumina, housed in a larger silica container with a lid.
The silica container was once again enshrouded by a
2-cm-thick layer of fibrous alumina inserted into a
cylindrical recrystallized alumina tube. The schematic
sketch of the set-up is shown in Fig. 2. The entire set-
Fig. 2. Schematic of the set up for microwave sintering, (a) microwave cavity, (b) outer ceramic tube, (c) quartz crucible with lid, (d) alumina
fibre (insulation), (e) ceramic crucible and (f) sample.
T. Mathews et al. / Solid State Ionics 148 (2002) 135–143 137
up was positioned inside the microwave oven followed
by gradual rising of power. The heating was carried out
in air at 175-W power for 5 min, at 455 W for 5 min
and then at 800 W for 30 min. The sample got heated
to very high temperatures in f 15 min time. No
efforts were made to measure the actual temperature
of the sample.
2.3. Characterization of the samples
The powder X-ray diffraction (XRD) pattern was
collected for the as-combusted product as well as for
the microwave-sintered material. The pycnometric
densities of the sintered disks were measured using
dibutyl phthalate as the medium of immersion. For AC
impedance measurements, a thin adherent layer of Pt
was applied over the parallel surface of the disks,
which served as the electrodes. A frequency range of 1
MHz–1 Hz was used with 10 mV as the amplitude of
the applied voltage. The impedance was measured as a
function of temperature using a Frequency Response
Analyser supplied by M/s Autolab, Netherlands.
Impedance measurements were made in a purified
Helium atmosphere. The microstructural analysis
was done using a scanning electron microscope
(model Philip XL 30) on the polished surface of the
sintered disks with an accelerating voltage of 20.0 kV.
3. Results and discussion
3.1. Synthesis
Assuming that the combustion reaction occurs with
the stoichiometric quantity of the reductant (urea), the
balanced combustion reaction can be written as
MðNO3Þ2ðaq:ÞðM ¼ Sr=BaÞ þMgððNO3Þ2ðaq:Þþ 10AlððNO3Þ3ðaq:Þ þ 28:33COðNH2Þ2ðaq:Þ! MMgAl10O17 þ 56:66H2Oþ 28:33CO2
þ 45:33N2 ð1Þ
The product of rapid combustion resulted in very
fine powders due to the large amount of gases that
evolved during the reaction. Approximately 130 mol
of gases are evolved for each mole of h-alumina.
Single phase Sr- and Ba-h-alumina were obtained at
Tf 773 K. The XRD pattern of the as-combusted
products showed them to be pure Sr- and Ba-h-
Fig. 3. X-ray diffraction pattern of the microwave-treated precursor confirming it to be pure Sr-h-alumina.
T. Mathews et al. / Solid State Ionics 148 (2002) 135–143138
aluminas. The reason for the substantial lowering of
the processing temperature, when the synthesis was
carried out through a rapid solution combustion tech-
nique, could be attributed to the removal of excess
water, formation of metal–urea complex and its
simultaneous ignition so that the homogeneous dis-
tribution of cations (achieved in the solution) is
retained until ignition. Moreover, though the furnace
temperature was maintained at f 773 K, the particles
could have attained higher temperatures during igni-
tion. The as-combusted powder after compaction
followed by exposure to microwave radiation, got
Fig. 4. X-ray diffraction pattern of the microwave-treated precursor confirming it to be pure Ba-h-alumina.
Fig. 5. �ZW against ZV for the microwave sintered Sr-h-alumina at 873 K.
T. Mathews et al. / Solid State Ionics 148 (2002) 135–143 139
heated up to high temperatures resulting in sintering to
high densities in 30 min. The XRD patterns shown in
Figs. 3 and 4 confirmed them to exhibit the h-alumina
structure. The densities measured were 94% and 91%
of the theoretical for SrMgAl10O17 and BaM-
gAl10O17, respectively. A compacted disk of Ba-h-alumina powder was conventionally sintered at 1773
K for 6 h. This disk on immersion into dibutyl
phthalate for density measurements showed the evo-
lution of air bubbles, indicating the presence of open
pores. The measured pycnometric density was f 81%
of theoretical. In the case of microwave-sintered
samples, no such evolution of air bubbles was ob-
served. In addition, there was no change in density
when measurements were repeated few times after
sufficient intervals of time and adequate drying under
vacuum. It should be mentioned here that this is the
first attempt reported in the literature for a microwave
assisted sintering for making dense membranes of Sr-
and Ba-h-aluminas. This is novel in that the method
of obtaining fine powders of SrMgAl10O17 and BaM-
gAl10O17 using combustion synthesis technique has
not so far been reported in the literature. Though there
are several soft chemistry routes already published in
the literature to obtain Na-h-alumina, all of them re-
quire temperatures in excess of 1273 K to form the
final product. The urea combustion technique offers
the advantage of directly obtaining fine powders of
the desired product in a very short time (30 min), com-
pared to the conventional ceramic route that requires
Fig. 6. Comparison of conductivity data of microwave-sintered Sr-h-alumina with those reported in the literature for the samples sintered using
conventional techniques.
Fig. 7. �ZW against ZV for the microwave-sintered Ba-h-alumina at
973 K.
T. Mathews et al. / Solid State Ionics 148 (2002) 135–143140
higher temperature heat-treatments for long periods.
As mentioned earlier, high temperatures (2000 K) are
also required to obtain dense membranes of Sr- and
Ba-h-aluminas. The product obtained after the micro-
wave sintering of the disks for 30 min were of high
density comparable with the samples conventionally
sintered around 2000 K.
3.2. Conductivity measurements
The impedance spectrum obtained in the case of Sr-
h-alumina showed the presence of two semicircles at
lower temperatures and is shown in Fig. 5 (T= 873 K).
The two semicircles can be assigned to the bulk and
the grain boundary resistances occurring at high and
the low frequency regions, respectively. The con-
ductivity was calculated by fitting the results with a
semicircle and the resistance was determined by the
intersection of the earlier circle with the X-axis, which
gives the real part of the impedance. No corrections
Fig. 8. Comparison of conductivity data of microwave-sintered Ba-h-alumina with those reported in the literature for the samples sintered using
conventional techniques.
Table 1
Comparison of coefficients of linear fit of conductivity data for Sr-
and Ba-h-alumina
Authors Sr-h-alumina Ba-h-alumina Ref.
A B Ea
(eV)
A B Ea
(eV)
He et al. 4.758 � 4.989 0.990 6.297 � 9.239 1.830 [21]
Yamaguchi
et al.
4.898 � 4.588 0.911 5.316 � 8.689 1.724 [32]
Schafer et al. 3.872 � 5.400 1.071 [31]
Present work 3.683 � 3.990 0.792 1.114 � 2.679 0.532Fig. 9. Scanning electron micrograph of microwave-sintered Sr-h-alumina.
T. Mathews et al. / Solid State Ionics 148 (2002) 135–143 141
were made for the resistance of the leads (Pt in this
case) as the bulk resistance due to the sample itself was
very high. The impedance was measured as a function
of temperature in the range of 750–1200 K. The bulk
conductivities were plotted as a function of inverse
temperature and are shown in Fig. 6. The activation
energy determined from the conductivity results is
0.79 eV. The conductivity values of conventionally
sintered samples reported by other workers are com-
pared in Fig. 6. In the case of Ba-h-alumina, the
impedance spectrum as presented in Fig. 7 showed
the presence of only one semicircle, which is indica-
tive of bulk resistance. The conductivities in this case
are also calculated as in the case of Sr-h-alumina and
are plotted as a function of inverse temperature in Fig.
8. The activation energy in this case was determined to
be 0.53 eV, valid over the temperature range 1000–
1250 K. The conductivity values of conventionally
sintered samples reported by other workers are also
compared in Fig. 8. Table 1 presents the coefficients
of the linear fit of the conductivity as a function of
inverse temperature for Sr- and Ba-h-aluminas. The
conductivity studies on the microwave-sintered sam-
ples showed that the activation energy for electrical
conduction in these samples is lower than the liter-
ature values for the samples otherwise sintered. The
scanning electron micrographs of the microwave-
sintered Sr- and Ba-h-alumina samples are shown in
Figs. 9 and 10. The grain size from the micrographs
could be calculated to be ranging from 0.5 to 2 Am in
the case of Sr-beta alumina and from 1 to 2.5 Am for
the Ba-analog.
4. Conclusions
An attempt to synthesize MgO stabilized Sr- and
Ba-h-alumina powders by urea combustion technique
and sintering of the product so synthesized using
microwave radiation is reported here for the first time.
AC impedance measurements performed on the
microwave-sintered disks showed the Ea (eV) to be
0.79 and 0.53, valid over the ranges 750–1200 and
1000–1250 K for Sr- and Ba-h-alumina, respectively.
It was also demonstrated that a soft chemistry route, to
obtain fine powders of the desired material when
combined with use of microwaves for sintering,
would yield a dense material with improved micro-
structure in a much shorter time compared to the
conventional processes. This technique of fabrication
of dense membranes of the divalent substituted beta
aluminas could be cost-effective and time-saving from
a technological point of view.
Acknowledgements
The authors are grateful to Dr.Baldev Raj, Director,
MCRG, and Dr. V.S. Raghunathan, Associate Direc-
tor, MCG, IGCAR, Kalpakkam for their keen interest
and constant encouragement throughout the course of
this investigation. The authors are also thankful to Dr.
C. Mallika, Scientific Officer (SO/F), TKD, IGCAR
for her help in impedance measurements.
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