Solid-state electrothermal energy interconversion utilising the electrocaloric effect is currently being considered as a viable source of applications alternative to contemporary cooling and heating technologies. Electrocaloric performance of a dielectric system is critically dependent on the number of uncorrelated polar states, or ‘entropy channels’ present within the system phase space. Exact physical origins of these states are currently unclear and practical methodologies for controlling their number and creating additional ones are not firmly established. Here we employ a multiscale computational approach to investigate the electrocaloric response of an artificial layered-oxide material that exhibits Goldstone-like polar excitations. We demonstrate that in the low-electric-field poling regime, the number of independent polar states in this system is proportional to the number of grown layers, and that the resulting electrocaloric properties are tuneable in the whole range of temperatures below TC by application of electric fields and elastic strain.
Electrocaloric (EC) effect is defined as the variation of the dielectric material
entropy as a function of the electric field at a given temperature, which results in
an adiabatic temperature change. Recently, there has been significant
The magnitude of the EC ΔT is proportional to a
logarithm of the number of possible polar states, or independent
‘entropy channels’ in the system.3,19 Therefore,
it is highly desirable to acquire precise understanding of physical phenomena
underpinning the emergence of these states and develop practical methods for
engineering additional entropy channels into dielectrics. Moreover, since entropic
changes involving evolution of other ferroic order parameters can be cumulative with
the EC effect, more advanced multicaloric materials concepts blending polar,
magnetic and elastic energy-interconversion functionalities, are also being
Here we use a multiscale computational approach that combines ab
initio quantum mechanical simulations, phenomenological Landau theory
and thermodynamical evaluations to investigate the EC response of a
‘material template’ based on a quasi-two-dimensional system
that exhibits polar Goldstone-like25,
The most interesting predicted feature of this system is that under biaxial
basal-plane strains ranging from slight tensions (up to 0.2%) to modest compressions
(up to 2%) it loses crystalline anisotropy with respect to the direction of its
Py),32 whereas rocksalt-type SrO–SrO inserts
in between perovskite slabs prevent any polarisation in the out-of-plane direction
z. The system free-energy density landscape
Py) is shown in Figure 1b and has a distinctive sombrero-hat
shape characteristic of a presence of a Goldstone-like or phason
This path, shown in greater detail in Figure 1c for zero biaxial strain, is only approximately circular—hence the ‘-like’ suffix above, as for the true Goldstone excitation it has to be a perfect circle. Here the absolute energy minima (at −6.26 meV per structural unit, or s.u.) are located along the , θ=0°, and three symmetrically equivalent crystallographic directions, and separated by saddle points (at −6.01 meV/s.u.) located along , θ=45°, and symmetrically equivalent directions. The competition between the - and -oriented sets of energy extrema can be controlled by applied strain; e.g., a small amount of tension can shift the minima to the  set of directions and saddle points to the  set.
We have developed Landau-type polynomial expansions for f from ab initio calculations,32 including couplings to elastic strain and applied electric field E. Since RP structure does not support out-of-plane polar distortions,32,33 only the in-plane polarisation components were included. Also, only planar biaxial strain–tensor components , accounting for the epitaxial misfit strain on a square substrate, were considered in the expansion. Both linear and quadratic couplings involving ε were included to reproduce polarisation locking–unlocking phase transition under changing strain. With all the simplifications, this quasi-two-dimensional free-energy function is
The estimated system TC≃120 K, while the rest of the expression coefficients are given in Supplementary Information.
The equilibrium state of the system at a given temperature T and strain ε is determined by minimising f with respect to the polarisation vector components Px, Py. System excess heat capacity34 ΔC and pyroelectric coefficients , , can be obtained from the equilibrium values of polarisation (P0) and energy density f0≡f(P0) as
Then the adiabatic change in the system temperature ΔT under the influence of varying applied electric field E is35 where , , are changes in the x and y components of E during the poling procedure, and C(T) is the system heat capacity. Equations (1)–(4) were then used to study polarisation switching and the resulting temperature change ΔT in PSTO under applied field E. More details on the evaluation of both heat capacity terms and their influence on the magnitude of ΔT are provided in the Materials and Methods section below and in Supplementary Information.
Remarkably different types of the system polarisation behaviour are observed under conditions of either high-, or low-field poling. In the former case, i.e., for (depending on the value of ε), energy landscape shown in Figure 1 is deformed away from its original sombrero-hat shape. Application of a large electric field (Ex,a, Ey,b) creates a deep energy minimum along its direction, locking the polar vector P0 inside this minimum and destroying the Goldstone-like excitation. Poling field (ΔEx, ΔEy) then preserves the locked state of the polarisation. If the direction of E remains fixed during the poling, polarisation azimuthal angle θ stays constant, while only the amplitude changes value. Such amplitudon mode of polarisation switching is usually seen in conventional EC materials,5,6,34,35 where the largest variations in and thus the largest changes in and ΔT occur near TC.
In Figure 2a, we present the versus T dependence at different values of ε (see Supplementary Figure 1 for more details). This includes , where even at zero field the Goldstone-like excitation disappears in favor of a localised minimum along . These results display transitional behaviour typical for a generic perovskite ferroelectric around TC.36 Curves for a number of different applied fields Ex,a=Ey,a are also shown for and, as expected, show a persistence of the polar phase beyond the zero-field TC. For the poling field , we obtain the values of ΔT in the range of 1–2 K (Supplementary Figure 2), which is similar to the performance of conventional EC materials undergoing amplitudon-polarisation switching.5,6,34,35
In the case of low-field poling, i.e., for and , the sombrero-hat energy landscape is only slightly perturbed. If the  state of Figures 1b and c is taken as a starting point, applying noncollinear E induces a rotation of the polar vector along the minimum-energy groove until . During this rotation process, which we refer to as phason polarisation switching, its azimuthal angle θ changes while its amplitude remains approximately constant.
The θ(T) dependence for a number of different magnitudes of E is shown in Figure 2b and Figure 2c for symmetric, Ex,a≡Ey,a, and asymmetric, Ex,a≠Ey,a, static applied fields, respectively. Here, the polarisation is initially pointing towards the nearest energy minimum, so that, e.g., θ=0°, while the angle is <45°. In the both cases, it is observed that P can align with E only if sufficient energy is provided to the system in the form of heat. The temperature value at which the alignment happens (Tlock) can be adjusted by changing the magnitude of E throughout the whole temperature interval (0→TC), similarly to how the value of TC can be attuned by the applied strain ε during the amplitudon switching. However, for asymmetrically applied fields, the alignment of P with E always happens smoothly (see Figure 2c), not resulting in an emergence of large in the vicinity of Tlock. On the other hand, for symmetrically applied fields, polarisation alignment occurs abruptly (see Figure 2b; Supplementary Figure 3) and produces large pyroelectric response, which is strikingly similar to the behaviour of near TC during the high-field poling. The application of sufficiently large E—which is dependent on T—along  lowers the energy of the associated saddle point until it becomes the new energy minimum, while simultaneously raising the energy of the original minima along  and . This creates a strong bias for locking P along the saddle-point direction, while such an incentive would be missing in the case of asymmetrically applied fields.
Since passage of the applied field through the saddle-point direction is accompanied by an emergence of large pyroelectric coefficients, which should in turn result in large EC ΔT, the following simple poling scenario can be considered. Starting with the polarisation along the x direction, θ=0°, a static field is applied, i.e., ΔEx=0 which eliminates one of the two integrals in Equation (4). Then, the field along the y direction is changed from to . This situation is illustrated step by step in Figure 3, which suggests that even for modest poling-field ramps ΔEy, bracketing the value of , it is possible to trigger rotation of P by an angle close to 90°, e.g., from the  energy minimum, through the saddle point along  and into the  energy minimum. The θ(T) plot in Figure 3b shows that initiates a smooth alignment of P with E, while only results in an abrupt switching of P between the two neighbouring basins within the energy landscape, after which it again smoothly aligns with E as T is raised above Tlock.
Figure 3c shows that abrupt changes in θ translate into large negative values of EC ΔT. As illustrated by the two different switching cases, the position of the phason EC peak on the temperature axis, as well as its width, can both be controlled purely by means of applied electric field—specifically by setting the values of and ΔEy, respectively. For example, changing from 5 to 13 kV/cm moves the center of the phason EC peak down from 60 to 30 K. Such precise tuning of the shape and location of the phason-induced EC response can be accomplished for all temperatures below TC. Typical maximum entropy changes achieved in this poling scenario are 0.5–1 J/kg/K (Supplementary Figure 4), similar to values observed by others for low-field switching.37
The negative sign of the phason-switching induced ΔT originates from the following consideration: as T→Tlock and polarisation rotation occurs, the angle is always diminished. Naturally, polarisation component after the rotation is always larger than component before the rotation, where γ is the direction along the field. Thus, the associated is positive, which results in negative ΔT according to Equation (4).
As shown in Figure 3c, abrupt changes of θ, each occurring under a specific fixed value of , result in an emergence of sharp bumps in the EC ΔT response. Furthermore, by choosing the values of the stationary field and the bracketing ΔEy poling interval, these peaks can be shifted to lower or higher temperatures on demand. When during the poling procedure Ey is swept continuously from to , individual peaks in the ΔT curve merge into an envelope that is presented in Figure 4 for different values of ε (see also Supplementary Figure 5). Remarkably, the variation of ε by ⩽1% can result in the system EC response changing from cooling (phason contribution) to heating (amplitudon contribution) at the same operating temperature.
The EC temperature changes in PSTO in the low-field poling regime range from −50 to −100 mK, i.e., they are two orders of magnitude smaller compared to the (positive) ΔT values produced during the conventional, high-field poling. However, since, without the loss of generality, the quasi-two-dimensional form of f can describe the behaviour of a single slab whose polarisation is decoupled from those of its neighbours, cumulative EC ΔT in a multi-slab system should look very different for the high- and low-field poling cases. It is noteworthy that the approximation of electrically decoupled polar slabs is already quite good for bulk PSTO, as illustrated by an absence of phonon-band dispersion for polar modes in the direction perpendicular to the slab planes; see Figure 2 in reference 32.
In the high-field regime, individual slab polarisations are switched ‘all
at once,’ being forcefully correlated by the applied field. That is, the
multi-slab system possesses only one entropy channel and the value of
ΔT≃1–2 K quoted
above for PSTO should represent its aggregate EC response. In the low-field regime,
applied fields are insufficient to correlate the directions of (disordered) polar
vectors in different slabs and, therefore, polarisation rotations under the cycling
of the field should occur independently in each slab. In such a case, each slab acts
as a separate entropy channel and the aggregate EC response of the whole system
should be proportional to the logarithm of the number of slabs. Then, even with
individual slab contributions being low (~100 mK for PSTO),
a system comprised of a large number of slabs should possess an aggregate
ΔT that is at least comparable with other
state-of-the-art negative EC materials.15,
The estimate of one entropy channel per slab is conservative, as in the model presented here any influence of polar domain-wall dynamics on the EC response is not taken into account, i.e., each slab is considered to be in a monodomain state. An investigation of polarisation-closure patterns in PSTO nanostructures predicted that these patterns are likely to form and their behaviour sensitively depends on the applied strain,38 suggesting that multiple entropy channels may be created (or destroyed, if needed) in each slab by distorting its shape. Alternatively, a nano-island device geometry, where polar states of individual islands uncorrelated from each other, can be used instead of a continuous-film one.
In summary, we have shown that layered polar systems with Goldstone-like instabilities should exhibit attractive EC properties that are highly tunable by applying electric fields and elastic distortions over a wide range of operating temperatures below TC, which may even include on-demand switching between cooling and heating. By virtue of operating at low electric fields, device applications of actual materials will require modest power consumption, compared with most other known EC compounds, where fields of upwards of 500 kV/cm are needed for best performance. Furthermore, in such model systems the mechanisms behind the emergence of independent entropy channels can be clearly established allowing for an easy up- or down-scaling of the system entropy-flow and EC characteristics by growing an appropriate number of layers. Although for the specific example of PSTO, a single monodomain-slab EC response in the low-field operation is only around 0.1 K, it should be possible to employ ‘materials by design’ principles to develop new compounds with improved EC properties. The competition between the - and -oriented sets of energy minima in polar-perovskite layers, leading to Goldstone-like excitations, appears to be a generic geometrical feature of such systems, rather than a peculiar trait distinctive to PSTO. We have recently identified other layered-oxide structures that should possess similar properties.39
Materials and methods
Ab initio calculations were performed with the density-functional theory code Quantum Espresso40 utilising local-density approximation in the Perdew–Zunger parametrisation41 and Vanderbilt ultrasoft pseudopotentials.42 Vibrational frequencies, ionic displacement patterns and system vibrational density of states, were obtained using density-functional perturbation theory approach within Quantum Espresso.43 The system total heat capacity C(T), used in Equation (4) above, was evaluated from the vibrational density of states44,45 computed for the non-polar system configuration (see Supplementary Information and Supplementary Figure 6 for more details).
Ionic forces were relaxed to less than 0.2×10−5 Ry/bohr (~0.5×10−4 eV/Å) and the appropriate stress tensor components (α and β are Cartesian directions x, y and z) were converged to values below 0.2 kbar. Epitaxial thin-film constraint on a cubic (001)-oriented substrate was simulated by varying the in-plane lattice constant a of the tetragonal cell and allowing the out-of-plane lattice constant c to relax (by converging the normal stress in this direction to a small value), while preserving the imposed tetragonal unit-cell symmetry. The biaxial misfit strain ε is defined as (a−a0)/a0, where a0 is the in-plane lattice parameter of the free standing PSTO structure with all the normal stress tensor components relaxed to <0.2 kbar.
Ionic Born effective-charge tensors , where i is the ion number, and high-frequency dielectric permittivity tensor were calculated by utilising the density-functional perturbation theory approach. The system polarisation was evaluated with a linearised approximation46 involving products of and ionic displacements away from centrosymmetric positions. The value of TC (~120 K) was estimated from energy differences between the non-polar I4/mmm and polarised , and  states of the system.
We should point out that due to the purely analytical nature of our approach it does
not account for spatial inhomogeneities of the polarisation P and
variables. Such inhomogeneities can be present in epitaxially clamped thin films
producing additional contributions to the aggregate ΔT
that stem from, e.g., elastocaloric effects and polydomain behaviour. Although we
have not yet studied piezoelectric response of PSTO in detail, we expect most of its
piezoelectric coefficients to be low—with the same being true about the
magnitude of the intrinsic elastocaloric effect—as polarisation rotation
in this material is not accompanied by large elastic distortions. Instead of
utilising the Maxwell relation (3), a number of approaches involving combinations of
effective-Hamiltonian techniques with molecular dynamics or Monte Carlo simulations
have been used to directly compute field-induced temperature and entropy changes in
S.N., K.C.P. and J.M. are grateful to the National Science Foundation (DMR 1309114) for partial funding of this project. S.N. also thanks Olle Heinonen and Joseph Mantese for illuminating discussions.
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