Commercial lead-based piezoelectric materials raised worldwide environmental concerns in the past decade. Bi0.5Na0.5TiO3-based solid solution is among the most promising lead-free piezoelectric candidates; however, depolarization of these solid solutions is a longstanding obstacle for their practical applications. Here we use a strategy to defer the thermal depolarization, even render depolarization-free Bi0.5Na0.5TiO3-based 0–3-type composites. This is achieved by introducing semiconducting ZnO particles into the relaxor ferroelectric 0.94Bi0.5Na0.5TiO3–0.06BaTiO3 matrix. The depolarization temperature increases with increasing ZnO concentration until depolarization disappears at 30 mol% ZnO. The semiconducting nature of ZnO provides charges to partially compensate the ferroelectric depolarization field. These results not only pave the way for applications of Bi0.5Na0.5TiO3-based piezoceramics, but also have great impact on the understanding of the mechanism of depolarization so as to provide a new design to optimize the performance of lead-free piezoelectrics.
Piezoelectric materials are indispensable in daily life because they have wide applications in electromechanical devices such as sensors, actuators and so on. Up to now, the most dominantly commercialized piezoelectric materials contain lead exemplified by lead–zirconate–titanate-based materials, but lead is toxic to human health and the environment. Therefore, with the enforcement of regulations on the restriction of the use of hazardous substances in electronic devices1,2, intensive efforts have been continuously devoted to the search for lead-free replacement and to the understanding of the enhancement mechanisms for piezoelectric behaviour3,4,5,6,7,8. There has been a steady progress on the development of lead-free piezoelectrics. Many lead-free piezoelectric materials have been reported, consisting mostly of solid solutions with morphotropic phase boundary compositions based on BaTiO3 (BT), K0.5Na0.5NbO3 (KNN) and Bi0.5Na0.5TiO3 (BNT). However, it is still not possible to completely replace lead–zirconate–titanate materials due to a common drawback concerning the phase transition of these lead-free materials. The BT-based solid solutions are limited due to the low Curie temperature (Tc), which is around 120 °C. KNN-based solid solutions also have a similar problem, its giant piezoelectric property happens at the transition between orthorhombic and tetragonal structure (TO–T). This transition is composition sensitive and the transition temperature can be tuned down to near room temperature (RT). These drawbacks, limiting the working temperature and affecting the property’s temperature stability, are difficult to overcome. Thus they hinder the application of BT- and KNN-based lead-free materials6,9,10,11. As one of the most feasible lead-free candidates, BNT-based solid solutions have good piezoelectric property, excellent reproducibility and high maximum dielectric constant temperature (Tm~300 °C)4,5,6. However, its most noticeable drawback is the depolarization at around 100 °C (Td), which is much lower than the Tm (300 °C)4,6,12,13,14. This thermal depolarization leads to the disappearance of macroscopic piezoelectric behaviour so that the Td determines the upper-limit working temperature. If the thermal depolarization could be suppressed or eliminated, the path to application of these lead-free piezoceramics would be open.
A large amount of attempts using conventional methods based on solid solution or chemical doping have been explored, but failed to suppress or eliminate the depolarization of BNT-based solid solutions. Such methods generally lead to decreased Td towards RT to enhance RT piezoelectric properties12,15,16,17, while the increase on Td is at the expense of reduced piezoelectric properties. Up to now, it is still a challenge to increase Td and enhance piezoelectric properties simultaneously. Therefore, an alternative method must be developed to resolve this problem.
Here we report the composites of 0.94Bi0.5Na0.5TiO3–0.06BaTiO3:xZnO (BNT–6BT:xZnO), which show excellent piezoelectric properties without depolarization and enhanced temperature stability. The parameter x (0~0.4) represents the mole ratio of ZnO over BNT–6BT. Perovskite BNT–6BT ceramic is well known to have a rhombohedral-tetragonal morphotropic phase boundary and demonstrates good electromechanical properties18. Wurtzite ZnO is a polar semiconductor with piezoelectricity19,20,21. BNT–6BT and ZnO have only limited solid solution and hence afford the formation of composites. To highlight the specific nature of ZnO, composites formed by the same matrix BNT–6BT, but different oxide ZrO2 (a typical dielectric insulator22) are prepared and investigated.
Phase and microstructure analysis
The X-ray diffraction (XRD) patterns (Supplementary Fig. 1) reveal that the samples with x=0.2, 0.3 and 0.4 have two sets of diffractions peaks from BNT–6BT and ZnO, which indicate that these samples are composites instead of solid solutions. XRD measurements on both unpoled and poled samples (Supplementary Fig. 2a,b) reveal that composites with higher ZnO content retain the poled state, as confirmed by the poling-induced tetragonal structure, indicated by splitting of the diffraction peak around 2θ~46.5° (ref. 23). Further temperature-dependent XRD patterns on poled samples with x=0.3 (Supplementary Fig. 2c) and 0.4 prove that such a poled state is stable up to ~240 °C, which is close to the Tm. It indicates the absence of thermal depolarization, as will be discussed in more detail below. Furthermore, different grain ensembles in the compositions with x=0.3 and 0.4 also indicate the composite structure (Supplementary Fig. 3). To reveal the composition visually, a typical two-dimensional element mapping of x=0.3 is demonstrated in Fig. 1a. Three features are noticeable. First, there are two sets of grains corresponding to BNT–6BT and ZnO, respectively. We suggest that there is limited cation diffusion between BNT–6BT and ZnO, since the solution limit is very low24,25. Some Zn ions have entered into the lattice as the sintering is enhanced and the grain size becomes larger with increasing ZnO content (Supplementary Fig. 3). Second, the initially nano-sized ZnO (25 nm) has grown into larger ZnO particles with the average size of ~500 nm. Most of the irregular ZnO particles are located at boundaries between BNT–6BT grains. Third, 0–3-type composites have been formed, in which the BNT–6BT grains form a three-dimensional network, while the ZnO particles are isolated. Note that each BNT–6BT grain has several neighbouring and independent ZnO particles. For further confirmation, the detailed element distribution and the energy-dispersive spectrum recorded from the same area are provided in Fig. 1b. Obvious chemical inhomogeneity is observed: the Ba, Ti and Na cations occupy the same areas and these areas connect with each other, whereas Zn cations occupy the remaining and isolated areas.
The theoretical volume fraction of ZnO in the composite of BNT–6BT:xZnO can be calculated by considering the theoretical densities of BNT–6BT and ZnO. The theoretical volume fractions of ZnO are calculated to be 5.3%, 11.9%, 20.5% and 31.9% for the compositions with x=0.1, 0.2, 0.3 and 0.4, respectively. The experimental volume fraction of ZnO can be basically quantified according to the area ratio of different components provided in the scanning electron micrograph (SEM) (Fig. 1a). For compositions with small amount of ZnO (x=0.1 and 0.2), the volume fraction cannot be experimentally determined from SEM because no clear ZnO particles can be observed. For x=0.3 and 0.4, the volume fractions of ZnO are calculated to be ~13% and 24%, respectively. The relatively lower experimental volume fraction values of ZnO compared with theoretical values could be attributed to the fact that not all initial 25-nm-sized ZnO particles have grown into large particles.
Such an 0–3-type composite structure has also been confirmed by micro-Raman measurements, which were carried out on the four grains labelled as grain 1, grain 2, grain 3 and grain 4 (Supplementary Fig. 4a). The Raman spectrum of each grain is plotted in Supplementary Fig. 4b. The mode at ~439 cm−1 coming from ZnO (ref. 26) can only be observed in grain 1, grain 2 and grain 3. The other modes at ~286, ~534 and ~608 cm−1 attributed to BNT–6BT13,27 are not dependent on the ZnO concentration, indicating that the introduction of ZnO has not changed the crystal structure of the BNT–6BT matrix. Hence, ZnO and BNT–6BT are independent of each other in forming the 0–3-type composite structure, which is further confirmed by the two-dimensional Raman spectrum mapping with the fixed mode of 286 cm−1, as depicted in Supplementary Fig. 4c.
Temperature-dependent dielectric constant and loss
The temperature-dependent dielectric constant (εr) and loss (tanδ) of all compositions measured at 1 kHz are contrasted in Fig. 2a,b, respectively. The curves of the composition with x=0 are consistent with previous reports13,26. The first anomaly of dielectric constant or the sharp decrease of dielectric loss around 100 °C is attributed to the depolarization behaviour, which is an indication for Td5,13,26,27,28. As can be seen, with increasing ZnO concentration from 0 to 0.2, the Td increases from ~98 °C for x=0 to ~130 °C for x=0.1, and to ~150 °C for x=0.2, indicating the progressively suppressed thermal depolarization. More interestingly, with further increasing ZnO concentration to 0.3 and 0.4, the first anomaly of dielectric constant and the sharp decrease of dielectric loss disappear, indicating the completely eliminated thermal depolarization. At the same time, the peak of dielectric loss for both compositions appears around 245 °C, close to Tm (~280 °C). The peak temperature determined from dielectric loss is slightly lower than that from the dielectric constant, which is attributed to the relaxor nature in the BNT system29. Note that the absence of the depolarization in the present composites has not been reported in any BNT-based or other lead-free materials. One may bear in mind that the possibility of an increase in Td by forming solid solution between Zn cations and the BNT–BT lattice could be excluded due to the fact that Td is reduced by the chemical Zn substitution25. For a succinct mechanistic understanding, the compositional dependence of permittivity on composition may be of interest. However, we are not only contemplating a complex rule of mixtures, but also expect that the domain structure responds to the altered local electric fields, which complicates a further discussion.
For more detailed information on dielectric property, the temperature-dependent εr and tanδ of all unpoled compositions are measured at different frequencies. Typical results of the x=0.3 composition are plotted in Fig. 2c. The most noticeable feature is that the well-known anomalies of εr and tanδ corresponding to Td disappear at all measuring frequencies. For example, there is only one anomaly of εr around 280 °C, indicating the absence of depolarization in this composition. The frequency-dependent εr points to the relaxor nature of the composition, due to the coexistence of R3c and P4bm phases of BNT–6BT30,31. The dielectric property measured on the poled composition of x=0.3 is plotted in Fig. 2d for comparison. For BNT-based solid solutions, if the temperature-dependent εr and tanδ are measured on poled samples, the εr and tanδ peaks corresponding to Td should be observed31; however, such peaks are absent in Fig. 2d, which further confirms the absence of depolarization in the composite.
Composition-dependent ferro- and piezoelectric properties at RT
To optimize the property, the compositions of BNT–6BT:xZnO with the x-value of 0–0.6 were prepared. It has been found that the resistivity decreased significantly when the ZnO content was greater than 0.4, especially for x=0.6. RT polarization–electric-field (P–E) loops, bipolar and unipolar strain–electric-field (S–E) curves of the BNT–6BT:xZnO (x=0~0.4) are plotted in Fig. 3a–e. The corresponding composition-dependent saturated polarization (Ps) and remnant polarization (Pr), and piezoelectric coefficient (d33) of x=0~0.5 are depicted in Fig. 3f. Three important features are emphasized as follows. (1) All compositions have well-shaped P–E loops and butterfly-shaped bipolar S–E curves, indicating a typical ferroelectric nature at RT. The Ps, Pr and d33 values increase with increasing x. Note that the Ps, Pr and d33 values of the composites are larger than other reported values of pure BNT–6BT ceramics27,32, but lower than corresponding values in single crystals33. This is related to the charge-compensating effect of ZnO as discussed below. A further confirmation is provided by the fact that the P–E loops provide a more rectangular shape with limited back-switching, when the electric field is removed, particularly with x=0.3 and 0.4. (2) For each composition, the applied electric field is close to the electric breakdown field. For example, for the BNT–6BT:0.3ZnO, the measuring field is 12 kV mm−1. The ceramic will feature dielectric breakdown if the field is increased further. So, the breakdown field is 6, 10, 10, 12, 17 and 12 kV mm−1 for x=0~0.5, respectively. It is interesting to observe that the breakdown field of BNT–6BT:0.4ZnO composite is ~3 times higher than that of single-phase BNT–6BT. So, the breakdown strength has been greatly improved by the introduction of ZnO. The increase of breakdown strength as ZnO content increases is mainly due to ZnO-improved relative density or the reduction of porosity (Supplementary Fig. 3). Furthermore, we suggest that the ZnO partially compensates the depolarization field and therefore smoothens the intrinsic electric field distribution. (3) The electric properties degrade when x reaches 0.5, where wide-scale percolation of the ZnO is reached.
It should be emphasized that the P–E loops provided in Fig. 3 are measured with different applied electrical fields. This is required as the coercive field is enhanced with increasing ZnO content. If measured with the same electric field, for example, 6 kV mm−1, the Ps and Pr decrease from x=0 to 0.2, then increase for x=0.3 and 0.4 (Supplementary Fig. 5). We hypothesize that there are two competing effects of ZnO on the measured values of ferroelectric parameters: one is that ZnO and BNT–6BT obey polarization (connection in series) and strain (connection in parallel) coupling34; this leads to a reduced local electric field in the BNT–6BT and to overall decreased Ps and Pr values. The other is that ZnO bolsters ferroelectricity by retaining the tetragonal phase after poling (Supplementary Fig. 2), which could increase Ps and Pr values. Accordingly, the reduction of Ps and Pr in x=0.1 and 0.2 samples is attributed to the fact that the positive effects of ZnO to enhance Ps and Pr is less dominant, whereas it becomes predominant in the compositions with higher Zn content (x=0.3 and 0.4).
Temperature-dependent ferro- and piezoelectric properties
Figure. 4a–e plots the temperature-dependent P–E loops and current–electric-field (J–E) curves of the BNT–6BT:0.3ZnO composite, while Fig. 4f demonstrates the temperature-dependent Ps, Pr and Ec. The two peaks in the J–E curves are due to the polarization-switching current. From 25 to 125 °C, the well-shaped ferroelectric P–E loops and J–E curves confirm the ferroelectric nature. Furthermore, Ps and Pr are almost temperature independent, except for a strong increase around 125 °C arising from thermally induced leakage. The Ec decreases monotonously with increasing temperature. For comparison, temperature-dependent P–E loops and J–E curves of BNT–6BT without the addition of ZnO are provided in Fig. 5a–e. The slightly pinched P–E loops and four-peak J–E curves indicate that this solid solution tends to depolarize near 50 °C, consistent with previous reports27,30. In such case, the Ps is almost temperature independent, whereas the Pr decreases sharply above 50 °C (Fig. 5f). By comparing the results plotted in Figs 4 and 5, it is reasonable to conclude that the BNT–6BT:0.3ZnO composite is free from depolarization and exhibits improved ferroelectric property and thermal stability of the composite. A key to further discussions may be that the switching currents of the composite materials have a narrower distribution as compared with the materials without the ZnO. Note that the composite of BNT–6BT:0.4ZnO has similar temperature-independent P–E and J–E curves as that of BNT–6BT:0.3ZnO, but has increased leakage (Supplementary Fig. 6).
The bipolar and unipolar S–E curves of BNT–6BT:0.3ZnO were also measured at different temperatures (Fig. 6a–e). If we define the total strain as the difference between positive and negative maximum strain, and define the negative strain as the difference between the zero-field strain and the lowest strain, then the temperature-dependent total strain, negative strain, maximum unipolar strain, and maximum unipolar strain/maximum electric field (Smax/Emax), which is the large signal d33 (d33*) (ref. 6), are plotted in Fig. 6f. The comparative results of BNT–6BT are provided in Fig. 7. It has been reported that at around Td, the negative strain tends to be zero in the bipolar S–E curves, while the unipolar S–E curves tend to have large recoverable strain with large hysteresis because of the loss of ferroelectric order14,15,27,34, which is consistent with the results near 75 °C (see Fig. 7). However, it is not the case in the BNT–6BT:0.3ZnO composite (Fig. 6). Accordingly, two experimental aspects about BNT–6BT:0.3ZnO should be emphasized. One is that the butterfly-shaped bipolar S–E curves and the non-zero negative strain confirm the ferroelectric nature, that is, there is no depolarization of this composite up to 125 °C, consistent with the ferroelectric results provided in Fig. 4. The other is the temperature-independent unipolar strain value and the Smax/Emax: for the BNT–6BT:0.3ZnO, the unipolar strain increases from 0.11% at RT to 0.12% at 125 °C, and the corresponding Smax/Emax increases from 157 pm V−1 at RT to 171 pm V−1 at 125 °C. However, for the BNT–6BT, the unipolar strain changes significantly from 0.11% at RT, 0.43% at 75 °C, to 0.26% at 125 °C, and the Smax/Emax changes from 180 pm V−1 at RT, 715 pm V−1 at 75 °C, to 500 pm V−1 at 125 °C. Clearly, the thermal stability of piezoelectric property of the BNT–6BT:0.3ZnO composite has been improved. This will provide opportunities for industrial application in the form of sensors and transformers, where device manufacture often entails temperature treatment around 100 °C, which would lead to depolarization of the BNT–6BT piezoceramics. Again, the BNT–6BT:0.4ZnO composite has similar bipolar and unipolar S–E curves with BNT–6BT:0.3ZnO (Supplementary Fig. 7).
To further confirm the elimination of thermal depolarization in the composites, the retained d33 after thermal annealing of the BNT–6BT, BNT–6BT:0.3ZnO and BNT–6BT:0.4ZnO are depicted in Fig. 8. The d33 of the BNT–6BT decreases sharply from 110 pC N−1 at RT to 5 pC N−1 after exposure to 125 °C due to the well-known thermal depoling effect. However, this is not the case for the other two composites. For example, after exposure to 125 °C, BNT–6BT is almost thermally depoled, while the composites of BNT–6BT:0.3ZnO and BNT–6BT:0.4ZnO can well maintain their piezoelectric property. Here, the retained d33 values are as high as 80 and 75 pC N−1, respectively.
Although the origin of depolarization is still somewhat unclear, it is commonly believed that the size and charge disorder in BNT-based solid solutions decreases the ferroelectric order. BNT–6BT is classified as a nonergodic relaxor, which assumes long-range ferroelectric order after poling. Upon heating, it transits from an aligned domain structure to a randomized domain structure to an ergodic relaxor with polar nanoregions when it depolarizes28. Depolarization can be suppressed by an external poling field34,35: as the domains at the grain boundaries carry a misfit polarization, a depolarization field develops36 (Fig. 9a). This depolarization field is at a maximum at pore surfaces and is considered to be 0.1 Pr at grain boundaries in average37. After removing the poling field, this depolarization field leads to complete back-switching of the domains at Td (Fig. 9b). According to Jo et al.28, at zero electric field there exists a randomized domain structure. This mechanism is also consistent with the following fact: pure BNT–6BT and other BNT-based solid solutions always demonstrate the well-known pinched P–E loops with non-zero remnant polarization four-peak J–E curves, and zero negative-strain bipolar S–E curves above Td, as typical for relaxors (see Figs 5 and 7).
The mechanism in the BNT–6BT:0.3ZnO composite is a very novel one. We therefore can only provide the following hypothesis: An external poling field leads to the alignment of ferroelectric domains in BNT–6BT grains and unbound misfit compensation charges at BNT–6BT/BNT–6BT grain boundaries. It further provides mobile electronic charges from semiconductor ZnO to distribute at the BNT–6BT/ZnO grain boundaries, as schematically depicted in Fig. 9c, in which the depolarization field is partially compensated by the charges stemming from ZnO. Therefore, even after removing the poling field, the BNT–6BT grains can still keep the poled states and will provide reduced back-switching as noted in Figs 3 and 9d. Useful computations on related effects in the fields of aging and fatigue have recently been advanced37. If we contemplate a full compensation of local polarization mismatch at grain boundaries, a charge separation h in ZnO grains would be required as: . Here, is the elemental charge, is the misfit polarization at grain boundaries37 and is a concentration of electronic carriers in ZnO. If we take (ref. 38), then we arrive at . As the ZnO grain size was ascribed to be ~0.5 μm, partial charge compensation and hence, reduction of the local depolarization field is feasible. At the same time, the equation offers opportunities for future microstructural tailoring of ferroelectric composites to adjust the local depolarization fields.
Further evidence that the depolarizing field hinders domain switching is afforded by studies on a comparison of electrical and mechanical domain switching. It is demonstrated that electrical switching requires substantially higher energies as compared with mechanical switching where depolarization fields are not created39. Here it must be emphasized that the 0–3-type composite microstructure is an important ingredient because if ZnO particles form a network path throughout the BNT–6BT matrix, the composite will demonstrate semiconductor behaviour and the sample will provide too high a conductivity. The above domain evolution process is consistent with the XRD results measured on unpoled and poled samples (Supplementary Fig. 2). The poled BNT–6BT:xZnO composites help to retain the tetragonal structure, revealing that domains in composites are not relaxed completely after removing the poling field, which is not the case for pure BNT–6BT.
As far as the role of ZnO is concerned, we believe that ZnO offers one clear advantage: its semiconductor nature ensures that it can act as a charge pool, so it provides charges to form a field to partially compensate the depolarization field. If a dielectric insulator is introduced to form a composite with BNT–6BT, the depolarization behaviour cannot be suppressed since insulators cannot provide enough charges to form a local field to compensate the local depolarization field. To verify this idea, BNT–6BT:xZrO2 (x=0~0.4) composites were also prepared and investigated. All electrical measurements confirm that BNT–6BT:xZrO2 composites depict depolarization behaviour like BNT-based solid solutions. The typical temperature-dependent εr and tanδ are plotted in Supplementary Fig. 8. There are two anomalies of εr that correspond to Td and Tm, respectively, and the sharp decrease of tanδ around 150 °C corresponds to Td. These experimental results support our model.
In summary, we have designed and prepared semiconductor/relaxor 0–3-type composites BNT–6BT:xZnO. Detailed microstructure analysis substantiates that ZnO particles are isolated from each other and occupy the grain boundaries of the BNT–6BT matrix. The composites exhibit excellent piezoelectric properties: first, the Td increases with increasing x, and the depolarization disappears around x=0.3. This is experimentally confirmed by systematical temperature-dependent dielectric, ferroelectric, piezoelectric measurements and temperature-dependent XRD measurements. Second, the introduction of ZnO can enhance electric properties and improve thermal stability, both of which are advantages for practical applications, particularly for sensors and transformers. Third, by further comparing with BNT–6BT:xZrO2 composites, the mechanism for the observations in BNT–6BT:xZnO composites are rationalized based on the charge-order model. We believe that these results can provide a simple and effective way to defer the thermal depolarization to higher temperature, improve electrical property and thermal stability of conventional BNT-based and other lead-free piezoceramics, which may pave the way for applications. Furthermore, this work provides a referential method to develop novel piezoceramics with designed microstructures and optimized physical properties. We therefore expect innovative work in composites in the field of in situ diffraction, modelling of electric-field distributions and synthesis to optimize second-phase distribution and microstructure in general. Depolarization in single crystals versus polycrystalline materials may also highlight the role of the depolarization field.
BNT–6BT was prepared independently. Stoichiometric Bi2O3 (99.8%), BaCO3 (99.0%), Na2CO3 (99.8%) and TiO2 (99.0%, all from Alfa Aesar), were weighed and ball milled in ethanol for 24 h. The dried slurries were calcined at 900 °C for 3 h with an increasing and decreasing ramp rate of 5 °C min−1, ground by hand for 0.5 h, ball milled again in ethanol for 24 h, followed by a drying process. The powders were sintered in covered alumina crucibles at 1,100 °C for 3 h and then ground by hand for 1.0 h. In this way, single-phase BNT–6BT powders were obtained.
Afterwards, both the prepared BNT–6BT powders and the commercial ZnO nanoparticles with the size of 25 nm (PlasmaChem, Germany) were weighed according to the formula of BNT–6BT:xZnO with x=0.1, 0.2, 0.3 and 0.4. Each mixture was ball milled again in ethanol for 24 h, dried and subsequently pressed into green disks with a diameter of 10 mm under 40 MPa. Sintering was carried out in covered alumina crucibles at 1,000–1,050 °C for 1.0 h with a rapid increasing and decreasing temperature rate of 9 °C min−1 The relatively low sintering temperature, short sintering time and rapid increasing/decreasing ramp rate were adopted to prevent the diffusion between ZnO and BNT–6BT and to suppress the growth of ZnO nanoparticles. For the x=0 composition, that is, BNT–6BT disks were sintered at 1,050 °C for 1.0 h with the heating and cooling rate of 9 °C min−1 for comparative investigations. The BNT–6BT:xZrO2 composites were prepared in the same way, and ZrO2 (99.9%, Alfa Aesar) was used as the raw material.
Crystal structure analysis
The crystal structure of the composites was characterized by powder XRD with Cu Kα1 source. RT XRD measurements on unpoled and poled (6.0 kV mm−1 for x=0 and 7.0 kV mm−1 for others, 20 min, RT) were carried out using Rigaku Ultima III, while temperature-dependent XRD measurements were performed using PANalytical, PW 3040-X’Pert Pro. The microstructures and element distribution were analysed by SEM (FEI Quanta 200 and Zeiss Ultra 55). Two-dimensional micro-Raman measurements (Horiba Jobin Yvon HR800) were carried out to confirm the composite microstructure.
Electrical property measurements
For electrical measurements, the circular surfaces of the ground disks with the diameter of ~8.5 mm and the thickness of ~0.5 mm were covered by a thin layer of silver paste and fired at 550 °C for 30 min. Dielectric constant (εr) and loss factor (tanδ) were measured using an impedance analyzer (HP4294A) at several frequencies in a temperature range from 30 to 320 °C on unpoled and poled samples. The P–E loops, J–E curves and S–E curves were measured at 1 Hz using the TF analyzer 1000 (AixACCT) in silicone oil with controllable temperature from RT (~25 °C) to 125 °C. The RT piezoelectric coefficient (d33) was measured on poled ceramics by a Berlincourt-d33-meter (ZJ-6A). To measure the effect of thermal annealing on d33, the ceramics were poled at RT (6.0 kV mm−1 for x=0 and 7.0 kV mm−1 for other compositions, 20 min) and annealed at different temperatures (25–125 °C with step of 25 °C) for 10 min and then the retained d33 was determined after the poled ceramics were cooled down to RT. These crucial experiments were repeated several times.
How to cite this article: Zhang, J. et al. Semiconductor/relaxor 0–3-type composites without thermal depolarization in Bi0.5Na0.5TiO3-based lead-free piezoceramics. Nat. Commun. 6:6615 doi: 10.1038/ncomms7615 (2015).
This work was supported by the State Key Program for Basic Research of China (2013CB632900 and 2015CB921203) and the National Nature Science Foundation of China (U1432112 and 21322102). We are indebted to Y.A. Genenko for insightful discussions on compensation of depolarization fields.
Supplementary Figures 1-8
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Materials Science and Engineering: R: Reports (2019)