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Journal of Materials ScienceFull Set - Includes `Journal of MaterialsScience Letters' ISSN 0022-2461Volume 51Number 17 J Mater Sci (2016) 51:8156-8167DOI 10.1007/s10853-016-0091-5
Influence of dopants on the thermalproperties and critical behavior of theferroelectric transition in uniaxialferroelectric Sn2P2S6
V. Shvalya, A. Oleaga, A. Salazar,I. Stoika & Yu. M. Vysochanskii
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Influence of dopants on the thermal properties
and critical behavior of the ferroelectric transition
in uniaxial ferroelectric Sn2P2S6
V. Shvalya1,2, A. Oleaga1,*, A. Salazar1, I. Stoika2, and Yu. M. Vysochanskii2
1Departamento de Física Aplicada I, Escuela Técnica Superior de Ingeniería, Universidad del País Vasco, Alameda Urquijo s/n,
48013 Bilbao, Spain2 Institute for Solid State Physics and Chemistry, Uzhgorod University, Uzhgorod 88000, Ukraine
Received: 11 April 2016
Accepted: 20 May 2016
Published online:
31 May 2016
� Springer Science+Business
Media New York 2016
ABSTRACT
The thermal properties of Sn2P2S6 single crystals doped with Ge, Te, and Sb
have been studied in the neighborhood of the ferroelectric to paraelectric sec-
ond-order phase transition by means of ac photopyroelectric calorimetry, mea-
suring thermal diffusivity. A detailed study of the critical behavior of the
transitions has been undertaken using different theoretical models to study the
influence of the dopants and the physical mechanisms activated. Ge strongly
favors the stereoactivity of the material, which is revealed in the increase of the
critical temperature and the sharpening of the transition; this is due to the
strengthening of the sp2 electronic orbitals hybridization. Sb has a small influ-
ence on the stereoactivity while Te virtually none. In all cases, the ferroelectric
phases are well described using the phenomenological Landau model, while for
the paraelectric ones, a combination of two mechanisms is needed: first-order
fluctuations of the order parameter plus the presence of charged defects, ruling
out other possible mechanisms. The relative importance of the presence of these
defects increases with increasing contents of Ge and Sb, while in the case of Te,
there is only a slight increase with respect to the undoped sample.
Introduction
Sn2P2S6 is a semiconductor ferroelectric with high
electro-optic coefficients which make it promising for
its application as a photorefractive material, whose
properties can be improved by the addition of dif-
ferent dopants [1–3], specially with small percentages
of Te and Sb [4–6]. Besides, from the point of view of
solid state physics, the phase diagram is heavily
altered when S is substituted by Se, or Sn by Pb, to
form the solid state solutions Sn2P2(S1-xSex)6, (PbySn1-y)2P2S6, and (PbySn1-y)2P2Se6, modifying (even
annulling) the second-order ferroelectric transition or
provoking the appearance of incommensurate pha-
ses, first-order phase transitions, a Lifshitz point…[7]. This richness has made these families of uniaxial
Address correspondence to E-mail: [email protected]
DOI 10.1007/s10853-016-0091-5
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ferroelectrics specially attractive to study in depth the
physical mechanisms responsible for those varied
phase transitions. One tool suited to that end is the
study of the critical behavior of the transitions. The
evolution of the critical behavior of the second-order
phase transitions with doping in the three afore-
mentioned families has already been studied with
some extension [8–12] but not with any other kind of
dopants yet. Let us bear in mind that Sn2P2S6 has a
monoclinic crystalline structure, which undergoes a
second-order phase transition at about TC = 337 K
from an initial high-temperature paraelectric phase
with a point group symmetry 2/m to the low tem-
perature ferroelectric one with the point group m [1].
In this paper, we are turning our attention to the
evolution of the thermal properties and the critical
behavior of Sn2P2S6 independently doped with three
other species, each of them taking the place of each of
the three original atoms: Ge for Sn, Sb for P, and Te
for S. It is worth recalling that the critical behavior of
the pure Sn2P2S6 has been described by the combi-
nation of two physical mechanisms: first-order fluc-
tuations of the order parameter (polarization) and the
presence of charge defects [8]. Substituting S with Se
in concentrations close to the Lifshitz point turns the
critical behavior to be well described by the Lifshitz
universality class [9], while replacing Sn by Pb pro-
voked a crossover from the described behavior in the
pure sample to a mean-field model [10]. Finally, the
second-order phase transition in Sn2P2Se6 and (PbySn1-y)2P2Se6 with y\ 0.1 belongs to the 3D-XY uni-
versality class [11].
Coming back to doping with Ge, Sb, and Te, in all
cases, the single crystals can only accommodate small
percentages of these ions, it is not possible to form the
full solid solutions as it happens when Pb substitutes
Sn and Se takes the place of S. The interest of Ge lies
on the fact that it takes the place of the Sn2? ions
which play a vital role in the ferroelectricity of the
material: indeed, the mechanism of the tin cations
lone pair formation is related to the appearance of the
spontaneous polarization [13–15]. There is an anti-
bonding mixing of Sn 5s and S 3p orbitals, which in
its turn develops a bonding interaction with the Sn 5p
orbitals, generating lower-energy filled states Sn
5p ? (Sn 5s–S 3p), which are called in brief sp2. This
formation of the Sn2? lone pair electron cloud toge-
ther with the deformation of the nearest polyhedron
formed by the sulfur atoms determines the origin of
the spontaneous polarization. The sp2 hybridization
becomes stronger at the ferroelectric transition,
increasing the spontaneous polarization. Substitution
of Sn by Ge or Pb affects this hybridization,
improving or worsening the stereoactivity of the
cation sublattice. In particular, the smaller energy
distance between Ge 4s and S 3p states would
improve it while the bigger one between Pb 6s and S
3p states would make it weaker. This is revealed in
the phase transition temperature, which is first low-
ered and then frustrated as Pb concentration is
increased [7, 10], while, on the contrary, it is
increased with Ge contents [16]. A strong hybridiza-
tion of Ge states with the tin cation sublattice has
indeed been shown by Grigas et al. [17] using X-ray
photoelectron spectroscopy (XPS). In this same paper,
the influence of doping with Te on the electronic
properties of Sn2P2S6 was also studied with the result
that there is also an effective hybridization of the
tellurium impurity state with the anion (P2S6)-4
sublattice, modifying the energy zones near the top of
the valence band but without involving the Sn2?
states.
The aim of this paper is to study the thermal dif-
fusivity as a function of temperature of Sn2P2S6independently doped with Ge, Te, and Sb in the
neighborhood of the ferroelectric to paraelectric sec-
ond-order phase transition in order to check the
influence of each ion on the thermal properties of the
material and, in particular, on the critical behavior of
the ferroelectric transition compared to that of the
parent compound, already studied in detail [8]. This
will give relevant information about their different
effects on the stereoactivity of the lattice or other
mechanisms.
Experimental procedures
Single Sn2P2S6 crystals doped with Ge, Te, and Sb
ions were obtained by vapor-transport method in a
quartz tube using SnI2 as a transport agent. The
synthesis of the starting material in the polycrys-
talline form was carried out using high-purity ele-
ments Sn (99.99 %), P (99.999 %), S (99.99 %), Ge
(99.999 %), Te (99.99 %), and Sb (99.999 %) in atomic
percentage. The nominal amount of impurities was as
follows: Ge: 3 and 5 %; Te: 1 and 2 %; and Sb: 0.5, 1,
and 2 % (atomic percentages in all cases). The sam-
ples doped with Ge present a light orange color,
while Te- and Sb-doped samples have light brown
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and light red colors, respectively. The samples were
characterized by X-ray diffraction (XRD) technique
performed with DRON—4 diffractometer using Cu
Ka radiation. The diffraction lines broadening anal-
ysis confirms that the XRD pattern of the investigated
doped crystals is similar to the observed one in the
case of the nominally pure (undoped) samples. This
confirmed their good crystal quality as well as dis-
carded the presence of different phases. XRD was
also used to orient the samples before cutting them.
The incorporation of the dopants through this
method had been previously checked by the changes
in ferroelectric and optical properties already pub-
lished [4, 15, 16].
For thermal diffusivity measurements, all samples
have been prepared in the form of thin plane-parallel
slabs with thicknesses in a range of 0.500–0.530 mm
and whose faces were cut in the monoclinic symme-
try plane perpendicular to (001) crystallographic
direction. In order to carry out this kind of study, a
high resolution ac photopyroelectric calorimetry
technique in the standard back detection configura-
tion has been employed. [18, 19] In particular, its
usefulness has been well demonstrated in the thermal
diffusivity study of Sn(Pb)2P2S(Se)6 ferroelectric
mixed compounds [8–11]. In this setup, the front
surface of the sample under study is illuminated by a
modulated low power laser beam, while the rear
surface is in thermal contact with a LiTaO3 pyro-
electric sensor with metallic electrodes on both faces.
Thermal contact between the detector and sample is
guaranteed using a thin (few microns) layer of a heat-
conductive silicon thermal grease. Since the samples
are transparent, their front surfaces have been cov-
ered with a thin layer of graphite to make them
opaque and increase the absorption of the laser beam.
The photopyroelectric signal provided by the sensor
has been processed by a lock-in amplifier in the
current mode.
In order to measure as a function of temperature,
both the detector and the sample have been placed
inside a liquid nitrogen cryostat which can work in
the temperature range 78–450 K. The measurements
have been performed in two steps: first there was a
quick run with a rate of 0.1 K/min to cover a wide
temperature range and then a second one consisted
of high-resolution cooling/heating runs around the
phase transition using variations of temperature as
slow as 25–30 mK/min, with which the stability of
the shape of the phase transition was ensured to
enable the critical behavior study.
According to the experimental conditions, if the
sample is opaque and thermally thick (its thickness l
has to be larger than thermal diffusion length:
l[ l ¼ffiffiffiffiffiffiffiffiffiffiffi
D=pfp
, where f is the frequency of modula-
tion), then the phase and the natural logarithm of the
amplitude of the normalized photopyroelectric cur-
rent at a fixed temperature T have both a linear
dependence on the square root of the frequency with
the same slope m, from which the thermal diffusivity
D can be calculated [19, 20]:
D ¼ l2pm2
ð1Þ
Once the thermal diffusivity has been obtained at
some certain reference temperature Dref the temper-
ature run is performed fixing a frequency of modu-
lation belonging to the linear region explained above.
Defining the phase difference of the electric signal
with temperature as DW(T), the temperature depen-
dence of thermal diffusivity is given as follows [21]:
DðTÞ ¼ 1ffiffiffiffiffiffiffiffi
Dref
p � DW Tð Þl
ffiffiffiffiffi
pfp
" #�2
: ð2Þ
It should be pointed out that measurements have
been carried out under continuous temperature
variation and the experimental data are retrieved
every several seconds, thus obtaining curves with
thousands of experimental points. The experimental
curves shown in all graphs are the ones obtained
experimentally, without any fitting or treatment. In
the continuous runs, the relative resolution of the
points is ±0.0001 mm2/s in D and ±0.001 K in T,
retrieving the precise shape of the thermal diffusivity
as a function of temperature, especially around the
phase transition point. Depending on the thickness of
the particular sample, the modulation frequencies
used for this investigations have been in the range
1–4 Hz, always ensuring that we are working under
the proper theoretical conditions in which Eqs. 1 and
2 are fulfilled.
Experimental results
Thermal diffusivity as a function of temperature has
been measured for all samples in the (001) direction.
The experimental results are presented on Figs. 1, 2,
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and 3. To better compare and see the difference
between each doped sample and the pure one, we
have also included the previously measured thermal
diffusivity for the undoped Sn2P2S6 crystal along the
(001) direction [8]. For all samples, a dip in the tem-
perature evolution of the thermal diffusivity has been
observed, signaling the presence of the second-order
phase transition. It is clearly seen in those figures that
the added impurities have altered the shape of the
thermal diffusivity curve compared to the undoped
crystal.
Introducing Ge2? into the Sn2P2S6 cation sublattice
increases the transition temperature. From the initial
value of 336.2 K for the pure sample, it rises up to
about 349.2 K for the sample doped with 5%Ge,
while the crystal with the nominal concentration of
3%Ge reveals an intermediate value of TC = 346.1 K
(see Fig. 1). An increase in TC had already been
observed by Maior et al. [16] measuring other phys-
ical variables with less resolution. Note that the dip
becomes sharper as Ge contents is increased.
Concerning the effect of Sb, this type of dopant
should substitute P ions in the anion sublattice
(P2S6)4-. As seen from Fig. 2, the transition is slightly
shifted to lower temperatures, but the effect is much
smaller than in Ge, and the anomaly at TC is smeared
when the concentration of Sb increases. For the
samples doped with 2% of Sb, the value of TC is
almost the same as for 1 %, but the general evolution
of the thermal diffusivity curve is altered.
Finally, the impurities of Te added in Sn2P2S6 only
slightly affect the critical temperature (see Fig. 3).
Unfortunately, so far, there is no additional data
related to the influence of Sb and Te on the position of
transition temperature obtained by means of other
techniques.
It is worth noting that there is a common feature in
Figs. 1, 2, and 3. For all samples, the absolute value of
the thermal diffusivity is reduced at ‘‘low’’ dopant
concentrations while a further doping leads to a rise
in thermal diffusivity, though always smaller than in
the undoped sample. In all cases, the absolute values
of D are quite low and fall within the range of poor
thermal conductors, where heat is mainly transferred
by phonons. It is quite common that, in thermal
insulators, small additions of any dopant reduce the
phonon mean free path due to the disorder intro-
duced while from a certain percentage up there is a
relative increment, as it happens here; this has been
observed in ferroelectrics as well as in magnetic
materials. See the case of (PbxSn1-x)2P2S6 [10],
La1-xSrxMnO3 [22], or Nd1-xSrxMnO3 [23].
Critical behavior and fittings
Critical behavior theory assesses that certain physical
quantities present a singularity at the transition
temperature (critical temperature TC) whose partic-
ular mathematical form is related to the physical
mechanisms responsible for the transition; regarding
thermal properties, the most commonly theorized
physical property is specific heat. [24] Thermal dif-
fusivity and specific heat are related by the following
equation:
Figure 1 Thermal diffusivity in the (001) direction as a function
of temperature for Sn2P2S6 doped with Ge: a pure Sn2P2S6 [8];
b Sn2P2S6 ? 3%Ge; c Sn2P2S6 ? 5%Ge.
Figure 2 Thermal diffusivity in the (001) direction as a function
of temperature for Sn2P2S6 doped with Sb: a pure Sn2P2S6 [8];
b Sn2P2S6 ? 0.5%Sb; c Sn2P2S6 ? 1%Sb; d Sn2P2S6 ? 2%Sb.
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cp ¼K
qD; ð3Þ
where K is the thermal conductivity and q the den-
sity, which means that the critical behavior of specific
heat and the inverse of thermal diffusivity is the
same, provided that neither thermal conductivity nor
density have significant changes at the transition,
which is the case in Sn2P2S6 [8, 25].
Different approaches can be undertaken: the first
one is the classical approach using Landau theory
which gives a particular expression for this specific
heat which is used to fit the experimental specific
heat (or the inverse of thermal diffusivity) in the
ferroelectric phase. Taking into account the possible
coupling of polarization to strain in a uniaxial ferro-
electric such as Sn2P2S6, the thermodynamical
potential density reads [8]
F ¼ F0 þat
2P2 þ b
4P4 þ c
6P6 þ 1
2cu2 þ ruP2: ð4Þ
And the specific heat in the ferroelectric phase is
obtained by
cp ¼ �To2F
oT2
� �
P
: ð5Þ
And taking into account Eq. 3, the anomalous part of
the inverse of thermal diffusivity due to the transition
reads, after Ref. [8]
D1
D
� �
¼ p1T
ffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
1� 4p2ðT � TCÞp ; ð6Þ
where p1 ¼ a2
2b0K, p2 ¼ ca
b02, b0 ¼ b� 2r
c2
In order to fit the inverse of thermal diffusivity, the
full fitting equation that will be used is [10]
1
D¼ p3 þ p4ðT � TCÞ þ p1
Tffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
1� 4p2ðT � TCÞp ; ð7Þ
where a linear term has been added to account for a
regular contribution to the inverse of the thermal
diffusivity as a function of temperature. This allows
to obtain the values of the phenomenological coeffi-
cients b0 and c, comparing them among the doped
and undoped samples.
But Landau theory does not give a complete pic-
ture of the physics involved as it does not take into
account the fluctuations of the order parameter (po-
larization in this case) while approaching the critical
temperature, which are more and more relevant as
the so called reduced temperature t = (T - TC)/TC
decreases till they dominate the transition. Theoreti-
cal work was developed in literature to extend Lan-
dau’s approach including first-order fluctuations of
the order parameter, with the result that the singu-
larity in specific heat has the following behavior
[7, 26]
Dcp � t�1=2 ð8Þ
which, regarding the fitting of the inverse of thermal
diffusivity, will imply the use of the following
equation
1
D¼ B1 þ C1tþ A1 tj j�a; ð9Þ
with a = 0.5. But this behavior has also failed to be
proved experimentally in most cases in ferroelectrics.
In the case of uniaxial ferroelectrics, the spatially
inhomogeneous distributions of the order parameter
are necessarily associated with the appearance of a
macroscopic electric field, which can have an influ-
ence upon fluctuations. Indeed, the presence of the
dipolar–dipolar interaction attenuates the fluctua-
tions effects and a theoretical development which
takes this interaction into account leads to the fol-
lowing heat capacity anomaly [7, 26]
Dcp � ln t: ð10Þ
This logarithmic correction to the pure Landau
theory has proved extremely successful for many
uniaxial ferroelectric materials. Another possibility is
that the attenuation of fluctuations be small enough
so that Eq. 8 could nearly be of application and that
Figure 3 Thermal diffusivity in the (001) direction as a function
of temperature for Sn2P2S6 doped with Te: a pure Sn2P2S6 [8];
b Sn2P2S6 ? 1%Te; c Sn2P2S6 ? 2%Te.
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only a small logarithmic correction should be intro-
duced; hence, Eq. 8 would turn into
Dcp � t�1=2 ln tj jb ð11Þ
with 0.1\ b\ 0.33 [27, 28]. This equation is equiva-
lent to having in Eq. 8 an exponent slightly closer to
zero than -0.5. Regarding the fitting of the inverse of
thermal diffusivity, the equation to fit is
1
D¼ B2 þ C2tþ A2 tj j�0:5
ln tj jj jb: ð12Þ
Besides, the contribution of defects to the anomaly
in specific heat in ferroelectrics has also been studied.
In general, defects are simply responsible for a
rounding of the anomalies in the phase transitions
but Isaverdiyev et al. [29–31] demonstrated that in the
case of charged defects in ferroelectrics, they can give
rise to stronger anomalies as they can induce long-
range perturbations of the order parameter. The
dependence of the specific heat in this case takes the
form
Dcp � t�3=2: ð13Þ
In the particular case of Sn2P2S6, a combination of
first-order fluctuations and defects, combining Eqs. 8
and 13 was needed to fit the anomalous part of the
specific heat [8] and the resulting fitting equation of
the inverse of thermal diffusivity is [8, 10]
1
D¼ B3 þ C3tþ A3 tj j�0:5þF3 tj j�1:5: ð14Þ
Equations (8)–(14) have been frequently used in
literature to study the critical behavior of ferro-
electrics fitting the paraelectric phase while, as
already mentioned, Eq. 7 is used to fit the ferroelec-
tric phase. In the present study, the fittings of all
Figure 4 Experimental data (circles) for the inverse of thermal
diffusivity as a function of the reduced temperature for Sn2P2S6 ? 3%Ge (a1) and Sn2P2S6 ? 5%Ge (b1). Only a selection of
experimental points is shown, for the sake of clarity. The lines
marked as (1) represent the fits to Eq. 7 for the ferroelectric phases,
while the ones marked as (2) represent the fits to Eq. 14 for the
paraelectric phases. a2, b2 Deviation plots corresponding to the
fits shown above. Open circles are for T\TC and crosses for
T[TC.
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experimental curves of the inverse of the thermal
diffusivity to Eqs. 7, 9, 12, and 14 have been
performed.
Finally, it must be mentioned that if the modern
treatment of critical behavior theory were applied,
fully taking into account the contribution of fluctua-
tions till t ? 0 in its strictest sense, both branches of
the transition (paraelectric as well as ferroelectric)
should comply with the following equation [10, 32]
1
D¼ B4 þ C4tþ A�
4 tj j�a 1þ E� tj j0:5� �
; ð15Þ
where t = (T - TC)/TC is the reduced temperature.
Superscripts ? and - stand for T[TC and T\TC,
respectively. The linear term represents the regular
contribution to the inverse of the thermal diffusivity,
while the last term represents the anomalous
contribution at the second-order phase transition.
The factor under parenthesis is the correction to
scaling that represents a singular contribution to the
leading power as known from experiments and the-
ory [33, 34]. Scaling laws require that there is a
unique critical exponent a for both branches and
rigorous application states that constant B4 needs also
be the same [35]. These conditions have sometimes
been relaxed in literature due to the difficulty of
obtaining good fittings to the experimental data with
those constraints, especially in the case of ferro-
electrics. Different universality classes have been
proposed (for each of them the critical exponent a has
a particular value) taking into account different
physical scenarios in ferroelectrics; a summary can be
found in [36]. But it is worth noting that in the pre-
vious work on Sn2P2S6, it was not possible to find a
Figure 5 Experimental data (circles) for the inverse of thermal
diffusivity as a function of the reduced temperature for Sn2P2S6 ? 0.5%Sb (a1), Sn2P2S6 ? 1%Sb (b1), Sn2P2S6 ? 2%Sb
(c1). Only a selection of experimental points is shown, for the
sake of clarity. The lines marked as (1) represent the fits to Eq. 7
for the ferroelectric phases, while the ones marked as (2) represent
the fits to Eq. 14 for the paraelectric phases. a2, b2, c2 Deviation
plots corresponding to the fits shown above. Open circles are for
T\TC and crosses for T[TC.
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good fitting under these strict conditions [8]. Never-
theless, in this work, the experimental curves have
also been fitted to Eq. 15, using both paraelectric and
ferroelectric branches at the same time.
Figures 4, 5, and 6 present the inverse of the ther-
mal diffusivity in the near vicinity of the critical
temperature for the samples doped with Ge, Sb, and
Te, respectively. These measurements were per-
formed at high resolution in order to obtain the shape
of the transitions with great accuracy. In all cases, it
was not possible to fit the curves to Eq. 15, and the
fittings to Eqs. 9–11 were extremely bad as they could
not follow the experimental curvatures at all. Good
fittings were obtained for the ferroelectric phase to
Eq. 7, from where the phenomenological coefficients
in the Landau expansion were extracted and for the
paraelectric phase to Eq. 14, where the combined
effect of the first-order fluctuations of the order
parameter and the contribution of defects was nec-
essary to obtain a good fitting. The best fittings are
superimposed to the experimental points on Figs. 4,
5, and 6. Tables 1 and 2 contain the particulars of the
fittings (parameters, fitting ranges, and coefficient of
determination R2) as well as the coefficients found in
the fittings, together with the uncertainties. Figures 4,
5, and 6 also contain the deviation plots in which the
difference between the experimental and the fitted
points, normalized, are presented as a percentage, as
another proof of the quality of the fittings. It is worth
noting that, being the experimental uncertainties as
small as mentioned when describing the experimen-
tal techniques, they do not have any significant
influence on the fittings carried out.
Figure 6 Experimental data (circles) for the inverse of thermal
diffusivity as a function of the reduced temperature for Sn2P2S6 ? 1%Te (a1) and Sn2P2S6 ? 2%Te (b1). Only a selection of
experimental points is shown, for the sake of clarity. The lines
marked as (1) represent the fits to Eq. 7 for the ferroelectric phases,
while the ones marked as (2) represent the fits to Eq. 14 for the
paraelectric phases. a2, b2 Deviation plots corresponding to the
fits shown above. Open circles are for T\TC and crosses for
T[TC.
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Discussion
As explained in Experimental results section, Figs. 1,
2, and 3 show the general influence of the different
dopants on the thermal diffusivity of Sn2P2S6. Start-
ing with germanium, an increasing doping percent-
age increases the critical temperature and severely
modifies the shape, making the transition sharper.
The increase in TC is in agreement with a previous
result measuring dielectric permittivity in a 5 %
doped sample (as well as piezoelectric and pyro-
electric coefficients), [16] though our results have a
higher resolution. Both the increase in TC and in the
sharpness of the transitions in the doped samples
illustrate the fact that the ferroelectric transition is
favored with respect to the undoped one, which
suggests that the stereoactivity of the cation sublattice
has been improved with the substitution of Sn2? by
Ge2?. As the spontaneous polarization is attributed in
Sn2P2S6 to the formation of the Sn2? lone pair electron
cloud by means of the sp2 hybridization described in
the introduction [13, 14], the increase in stereoactivity
has to do with the strengthening of this hybridiza-
tion, which has been demonstrated by means of XPS
measurements [17]. Ge plays a role opposite to that of
Pb when it substitutes Sn, the effect of the latter being
a reduction in the stereoactivity of the cation sublat-
tice, lowering the phase transition temperature and
even frustrating it at high concentrations [7, 10]. The
origin of this opposed effect on the stereoactivity lies
in the energy distance between (Ge 4s–Sn 5s–Pb 6s)
and S 3p states; the smaller value in the Ge case
improves it with respect to the higher one in Pb,
favoring or disfavoring the sp2 hybridization. Con-
cerning the critical behavior of Sn2P2S6:Ge, the mod-
els which can describe it are essentially the same ones
as in the undoped Sn2P2S6 [8]: Landau classical
model for the ferroelectric phase and an added con-
tribution of the first fluctuational correction plus the
contribution of defects for the paraelectric one (see
Fig. 4), which means that the presence of Ge does not
alter the physical mechanisms responsible for the
transition but simply enhances its ferroelectric fea-
tures. There is some variation in the fitted critical
parameters obtained, though. Concerning the phe-
nomenological parameters in Landau expansion,
both b0 and c are reduced with respect to the pure
sample (see Table 1). For a second-order phase tran-
sition b0 must be positive (it is negative for a first-
order one), its decrease is due to the fact that the
shape of the transition gets sharper. For the para-
electric phase, the ratio which brings the relative
importance of the contribution of defects with respect
to the first fluctuational correction F3/A3 after Eq. 14
increases from 5.0 9 10-3 in the undoped sample [8]
to 2.3 9 10-2 and 4.6 9 10-2 in the samples doped
with 3 and 5%Ge, showing how the introduction of
Ge increases the importance of the charged defects in
the lattice.
Turning our attention to Sn2P2S6:Sb, we see from
Fig. 2 that 0.5 % gets the transition rounded and
broader but with only a slight reduction in the critical
temperature, which is further reduced up to 3 K with
higher dopings. Both the broadening and the
decrease in TC suggest a slight disfavor of the ferro-
electric transition. The origin of this small reduction
in stereoactivity is not clear, as Sb takes the place of P
in the crystalline network, which is not clearly
involved in the physical mechanism of ferroelectric-
ity. Sb will be introduced in the anion sublattice
(P2S6)4- affecting the energy levels at the top of the
valence band [17]. Unfortunately, there is no infor-
mation on how the introduction of Sb will influence
the electronic states responsible for stereoactivity.
Further studies should be undertaken in this respect.
Concerning critical behavior, again the models which
fit well the experimental curves are the same as in the
case of the pure Sn2P2S6 (see Fig. 5). With the differ-
ence, that the phenomenological coefficient in the
Landau expansion b0 is slightly decreased and c is
heavily reduced when compared to the pure sample
(see Table 1). The reduction in b0 is related to the
broadening of the transition. Regarding the para-
electric phase, the relative contribution of the two
physical mechanisms needed to describe it (first
fluctuational correction and charged defects) also
increases with respect to the undoped sample
(though the effect is less important than in the case of
Ge) as it goes to 1.3 9 10-2 for 0.5 %, 1.6 9 10-2 for
1 %, and finally 1.8 9 10-2 for 2 %.
Finally, in the case of the addition of Te, the critical
temperature is just very slightly increased, with
similar features in the shape of the transition. It could
be said that there is a very slight favoring of the
ferroelectric transition. The effect of Te on the elec-
tronic orbitals has been also studied by XPS [17] with
the conclusion that there is a strong hybridization
with P and S orbitals near the top of the valence band
but with a very slight influence on the Sn2? lone pair,
thus having very little influence on the stereoactivity,
8164 J Mater Sci (2016) 51:8156–8167
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Tab
le1
Resultsof
thefittingof
theinverseof
thermal
diffusivityusingtheLandaumod
elEq.
7
Sn 2P2S6
3%Ge
5%Ge
0.5%
Sb
1%Sb
2%Sb
1%Te
2%Te
p 1(s/m
m2)
3.3219
10-3±
49
10-6
0.0185
±0.0044
0.0111
±0.0008
0.018±
0.006
0.026±
0.008
0.017±
0.005
3.67
910
-3±
2.19
10-4
2.54
910
-3±
2.59
10-4
p 2(K
-1)
0.0512
±0.0002
10.02±
4.23
4.49
±0.45
0.0037
±0.0008
0.0015
±0.0003
0.0044
±0.0008
0.105±
0.005
0.093±
0.009
Fittedrange
3.29
10-2to
2.09
10-3
3.19
10-2to
1.49
10-3
2.79
10-2to
9.19
10-4
4.29
10-2to
1.99
10-3
6.69
10-2to
3.39
10-3
3.59
10-2to
3.09
10-3
2.89
10-2to
8.69
10-4
3.69
10-2to
1.39
10-3
R2
0.9922
0.9994
0.9994
0.9990
0.9996
0.9996
0.9999
0.9999
b0 (J
m5C-4)
6.19
108
1.69
108
2.59
107
1.69
108
1.19
108
1.79
108
7.89
108
1.19
109
c(J
m9C-6)
2.39
1010
1.69
1010
1.79
109
5.99
107
1.19
108
7.89
107
4.09
1010
7.39
1010
The
columns
show
theadjustable
parametersp 1
andp 2,thefitted
rang
ein
redu
cedtemperature
unitst=
(T-
TC)/TC,thequ
alityof
thefittingthroug
hthecoefficientof
determ
inationR2,as
wellas
thecalculated
phenom
enolog
ical
parametersin
theLandauexpansionb0
andc.
The
values
forSn 2P2S6areextractedfrom
Ref.[8]
Tab
le2
Resultsof
thefittingof
theinverseof
thermal
diffusivityusingEq.
14
Sn 2P2S6
3%Ge
5%Ge
0.5%
Sb
Fittedrang
e2.79
10-2to
6.89
10-4
2.59
10-2to
5.39
10-4
2.99
10-2to
7.29
10-4
3.29
10-2to
1.99
10-3
R2
0.98
10.96
60.98
50.98
8
A3(s/m
m2)
3.25
910
-3±
69
10-4
7.10
910
-4±
2.15
910
-4
6.15
910
-4±
1.65
910
-4
4.06
910
-3±
8.19
10-4
F3(s/m
m2)
1.62
910
-5±
19
10-7
1.60
910
-5±
29
10-7
2.83
910
-5±
29
10-7
5.45
910
-5±
1.09
10-6
F3/A
35.09
10-3
2.39
10-2
4.69
10-2
1.39
10-2
1%Sb
2%Sb
1%Te
2%Te
Fittedrang
e3.69
10-2to
1.29
10-3
3.69
10-2to
2.89
10-3
2.09
10-2to
5.89
10-4
2.39
10-2to
6.99
10-4
R2
0.95
30.98
70.96
70.95
2
A3(s/m
m2)
1.63
910
-3±
2.79
10-4
5.59
910
-3±
8.99
10-4
2.07
910
-3±
2.09
10-4
2.99
910
-3±
6.79
10-4
F3(s/m
m2)
2.52
910
-5±
39
10-7
9.95
910
-5±
1.59
10-6
1.10
910
-5±
19
10-7
1.77
910
-5±
49
10-7
F3/A
31.69
10-2
1.89
10-2
5.39
10-3
5.99
10-3
Ineach
case,therelevant
fittingparametersareshow
ntogether
withthefitted
rang
ein
redu
cedtemperature
unitst=
(T-
TC)/TCas
wellthequ
alityof
thefittingthroug
hthe
coefficientof
determ
inationR2.The
values
forSn 2P2S6areextractedfrom
Ref.[8]
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as our results show. These slight changes imply that
the values of b0 and c are very close to the ones of the
undoped sample. On the other hand, the fitting to the
paraelectric phase corresponds to the combination of
the double mechanism described above with a very
slight increase of the contribution of defects as the
ratio F3/A3 in Eq. 14 takes the value of 5.3 9 10-3 for
1%Te and 5.9 9 10-3 for 2%Te, which means that it is
very close to the one for the undoped sample
(5.0 9 10-3). In all, doping with Te affects the phase
transition very little.
Conclusions
An ac photopyroelectric calorimetry in the back con-
figuration has been used to obtain the thermal diffu-
sivity evolutionwith temperature in the neighborhood
of the second-order ferroelectric phase transition in the
uniaxial ferroelectric Sn2P2S6 dopedwith Ge, Te, or Sb.
Ge strongly favors the stereoactivity of the material,
which has been proved by the increase of the critical
temperature and the sharpening of the transition; this
is due to the strengthening of the sp2 electronic orbitals
hybridization. Sb has a small influence on the
stereoactivity, reducing it a little bit while Te has vir-
tually none. The critical behavior of all samples has
been studied through the inverse of the thermal dif-
fusivity, fitting it to different models and comparing it
with the well-known behavior of the pure sample. In
all cases, the ferroelectric phases are well described
using the phenomenological Landau model. For the
description of the paraelectric ones, the fitted model
takes into account at the same time first-order fluctu-
ations of the order parameter plus the presence of
charged defects, ruling out a mean-field description.
The relative importance of the presence of charged
defects increases with Ge and Sb doping, while in the
case of Te, it remains nearly equal with respect to the
undoped sample.
Acknowledgements
This work has been supported by Gobierno Vasco
(IT619-13), and UPV/EHU (UFI11/55). The authors
thank for technical and human support provided by
SGIker of UPV/EHU. V. Shvalya thanks the Erasmus
Mundus programme ‘‘ACTIVE’’ for his grant.
Compliance with ethical standards
Conflict of interest The authors declare that they
have no conflict of interest.
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