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. 2024 Mar 12;14(1):6017.
doi: 10.1038/s41598-024-55402-0.

Titanate-based high-entropy perovskite oxides relaxor ferroelectrics

Affiliations

Titanate-based high-entropy perovskite oxides relaxor ferroelectrics

Ketkaeo Bunpang et al. Sci Rep. .

Abstract

Different combinations of monovalent and trivalent A-cations in high-entropy perovskite oxides (HEPOs) were investigated. The multicomponent (A'0.2A″0.2Ba0.2Sr0.2Ca0.2)TiO3 (A' = Na+, K+, A″ = Bi3+, La3+) perovskite compounds were successfully synthesized by solid-state reaction method persisting average cubic perovskite phase. The trivalent cation exhibited distinct effects on local structure, dielectric properties and relaxor ferroelectric behavior. Highly dense ceramics (> 95%), high dielectric constant (~ 3000), low dielectric loss (~ 0.1), and relaxor ferroelectric characteristics were obtained in the compound containing Bi3+. The La3+ containing compounds revealed lower dielectric constant, higher dielectric loss and linear dielectric behavior. The effect of monovalent cation on the dielectric properties was minimal. However, it affected relaxor ferroelectric behavior at elevated temperatures and conduction behavior at high temperatures. The (K0.2Bi0.2Ba0.2Sr0.2Ca0.2)TiO3 ceramic maintained the relaxor ferroelectric behavior with low PREM at high temperatures suggesting more stable relaxor ferroelectric characteristics than that of the (Na0.2Bi0.2Ba0.2Sr0.2Ca0.2)TiO3. Moreover, between these two compounds, the homogeneous electrical characteristics could be obtained from the compound consisting of K + and Bi + at A-site. This study suggests that tuning the chemical composition, particularly choosing appropriate combination of mono/trivalent cations in high entropy perovskite oxides, could be the effective approach to develop high-performance relaxor ferroelectrics with the desired properties.

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Conflict of interest statement

The authors declare no competing interests.

Figures

Figure 1
Figure 1
Rietveld refinement analysis of synchrotron X-ray diffraction patterns for (a) NB, (b) KB, (c) NL, and (d) KL ceramics (e) Raman spectra of NB, KB, NL, and KL ceramics.
Figure 2
Figure 2
Change in (a) linear shrinkage (%) and (b) density and (c) relative density (%) of NB, KB, NL, and KL ceramics.
Figure 3
Figure 3
SEM images of (a) NB, (b) KB, (c) NL, and (d) KL ceramics.
Figure 4
Figure 4
Temperature dependent dielectric responses at various frequencies of (a) NB, (b) KB, (c) NL, and (d) KL ceramics.
Figure 5
Figure 5
Relationship between ln(1/εr − 1/εm) and ln(T − Tm) measured at 100 kHz of (a) NB and (b) KB ceramics. The red solid lines are the fit to the Modified Curie–Weiss law.
Figure 6
Figure 6
Polarization–Electric field (P-E) hysteresis loops at different applied electric field ranging from 10 kV/cm to 80 kV/cm of (a) NB, (b) KB, (c) NL, and (d) KL ceramics.
Figure 7
Figure 7
(a) P-E hysteresis loops, (b) relation between PMAX, PREM and composition, (c) relation between EC and composition, (d) relation between WREC, WLOSS and composition, and (e) relation between ŋ and composition of NB, KB, NL, and KL ceramics at 50 kV/cm.
Figure 8
Figure 8
Temperature dependence on P-E hysteresis loops of (a) NB and (b) KB ceramics measured under an electric field of 50 kV/cm and a frequency of 1 Hz.
Figure 9
Figure 9
Complex impedance plot between the imaginary part (Z″) and the real part (Z′) of (a) NB and (b) KB ceramics in the temperature range of 400 °C–500 °C.
Figure 10
Figure 10
Frequency dependence of the imaginary part of impedance (Z″) and electrical modulus of (a) NB and (b) KB ceramics in the temperature range of 400 °C–500 °C.
Figure 11
Figure 11
Arrhenius plot of relaxation time (τ) for (a) NB and (b) KB ceramics in the temperature range of 400 °C–500 °C.

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