Abstract: Two-dimensional (2D) lead-free (K, Na)NbO3 (KNN) micro/nano structures with controllable K/Na ratio were successfully fabricated via a two-step molten salt synthesis (MSS). In this work, the reaction factors, including the proportion of molten salts, the types of carbonates, the sintering temperature, and the sintering time, were discussed in detail and the optimized condition was identified. The microstructure of KNN was confirmed by confocal Raman spectroscopy, while piezoresponse force microscopy (PFM) was applied to measure three-dimensional (3D) morphology and piezoelectric properties of KNN particles. The as-synthesized KNN platelets apparently possess anisotropic morphology and uniform structure, the size of which reaches 5–20 µm in length/width and 0.5–1 µm in thickness. It should be noted that the K/Na ratios of the KNN crystals are basically consistent while the proportion of salts changes within a certain range. The enrichment of Na element in the products is also observed, which owes to the smaller ionic radius of Na comparing to that ofK . This result provides a reference for the further preparation of textured ceramics and flexible piezoelectric generators.
Keywords: (K, Na)NbO3 (KNN); lead-free; two-dimensional (2D) structure; piezoelectric propert
1 Introduction
Piezoelectric materials are functional materials which can interconvert mechanical and electrical energies. Such smart materials can be fabricated as sensors, actuators, transducers, etc., which are widely applied in the fields of electronic communications, smart homes, and medical imaging [1–8]. Although lead zirconate titanate (Pb(Zr,Ti)O3, abbreviated as PZT) has excellent electromechanical performance, lead-based materials have been gradually replaced by lead-free materials due to the toxic nature of lead. Among all the lead-free material candidates, alkali niobate ceramics based materials have made a breakthrough in 2004. Saito et al. [9] prepared textured (K, Na)NbO3 (KNN) based ceramics with a high piezoelectric coefficient d33 of 416 pC/N, which is comparable to that of PZT. This work has ignited worldwide interest in exploring leadfree KNN based piezomaterials. More and more studies on KNN materials concentrate on the improvement of piezoelectricity [10–15].
Driven by an increasing demand for the textured ceramics and the flexible piezoelectric generators, the research on low dimensional lead-free niobate based micro/nano-structures have made great progress [16–18]. For instance, the well-textured KNN ceramics are considered to possess high piezoelectric response [9,19]. Yan et al. [20] fabricated grain-oriented PbTiO3 ceramic with 95% <001> texture, which has an extremely large g33. Thus, the textured lead-free ceramics with high piezoelectric performance are also expected according to the work reposted by Saito et al. [9]. In order to obtain the textured KNN materials with high piezoelectric response, one of the challenges is the fabrication of plate-like particles as templates [21]. As is known, the reactive template grain growth (RTGG) is a texturing technique, which uses plate-like or needle-like particles as templates for oriented growth of crystals. The resultant samples would obtain the anisotropic structures with improved physical and mechanical properties [9,22]. During the process, the required characteristics of the templates are crucial, such as uniform structure, complete crystal morphology, and stable chemical properties [23–27]. Furthermore, the plate-like KNN particles are expected to inherit the morphology and structure of the precursor [28–30].
There are many studies on the preparation of single-crystal NaNbO3 structures through the plate-like precursors [9,31–33], while the reports on KNN structures are relatively few. Ishii and Tashiro [34] reported the orientation control of KNN ceramics using NaNbO3 templates, and the sinterability of the textured ceramics, together with the diffusivity of K atoms into the templates was investigated. Li et al. [35] studied the synthesis of mechanism of KNN plate-like particles. Lee et al. [36] found that the salt contributed to the conversion reaction from plate-like precursor to KNN or NaNbO3 platelets. Zhu et al. [37] fabricated Li-doped KNN thick film by employing NaNbO3 as template. Compared to NaNbO3 two-dimensional (2D) templates, KNN plate-like crystals are expected to possess high piezoelectric properties, and might be much similar to the ceramic matrix [35,36]. Moreover, the enhanced performance is reasonably expected when the K/Na ratios of KNN materials are tailored at an optimal
composition. Thus, the preparation of the KNN micro/ nano-plates would be beneficial to the piezoelectric composite and ceramics. However, it would be a challenge for synthesizing KNN materials with controlled compositions at the micro/nano-scale. For instance, the type of molten salt, together with the ratio of K2CO3/ BNN5, would lead to the deviated structures results [35,36]. Besides, it should be stressed that the cationic sizes of K and Na differ from that of Bi3 , thus it is difficult to predict the practical amount of cations entering the lattice.
In this work, the plate-like KNN platelets were fabricated via topochemical micro-crystal conversion (TMC). During the preparation procedure, the bismuth layered-perovskite Bi2.5Na3.5Nb5O18 (BNN5) precursors were initially prepared by molten salt synthesis. Then, the KNN crystals were obtained by cations substitution of the BNN5 structures. The reaction conditions including molten salts, the carbonates, the sintering temperature, and the sintering time were also investigated. Furthermore,
the microstructure and piezoresponses of the KNN micro/nano-structures were addressed by Raman and piezoresponse force microscopy (PFM), respectively.
2 Experimental
2. 1 Synthesis of the plate-like KNN crystals via TMC
The BNN5 precursors were synthesized by the molten salt synthesis (MSS). Realgent-grade Bi2O3 (99.99%), Nb2O5 (99.99%), and Na2CO3 (99.8%) were weighed according to the stoichiometric ratio and mixed together with the same weight of NaCl (99.5%). The mixtures were fully milled in the mortar for 2 h. Then, the mixture of reactants was calcined at 1100 ℃ for 2 h in the Al2O3 crucible. The as-prepared products were washed several times with hot deionized water to remove the residual salts. Finally, the BNN5 particles were obtained as precursors. The plate-like KNN structures were fabricated via TMC. The BNN5 precursors reacted with Na2CO3 or
K2CO3 (99.0%) in a molten salt flux. The carbonate and KCl/NaCl (99.5%) salts were milled for ~1 h, and then the BNN5 particles were added and milled for another
1 h. The mixtures were kept at 970–1020 ℃ for different hours. The reaction products were washed several times with hot deionized water and HCl solution alternately to remove the NaCl salts and the Bi2O3, respectively.
2. 2 Characterization of KNN structures
The crystalline structures of the platelets were characterized by X-ray diffraction (XRD Rigaku, D/Max2500, Japan) using Cu Kα radiation. The morphologies of the particles were observed by scanning electron microscope (SEM, JEOL JSM-7001F, Japan). The elemental analysis was carried out by energy dispersive spectroscope (EDS, Oxford, Japan). The phase structure of the products was examined by Raman spectroscopy (LabRAM HR, HORIBA Jobin Yvon, France) with an excitation wavelength of 488 nm. The microscopies of 2D KNN structures were observed by atomic force microscope (AFM, Asylum Research MPF-3D, USA) with a Cr/Pt coated tip at tapping mode, while the piezoelectric responses were measured using switching spectroscopy piezoresponse force microscopy (SS-PFM).
3 Results and discussion
The XRD patterns of the BNN5 particles synthesized by molten salt synthesis at 1100 ℃ for 2 h with a heating rate of 10 ℃/min are shown in Fig. 1(a). Almost all of the diffraction peaks could be assigned to the BNN5 phase. The intensities of (0012), (0014), (0018), and (0024) peaks in the diffraction pattern are stronger than those in the PDF#42-0399, indicating that the BNN5 structures tend to orientate along (001) crystallographic plane direction. Although there are a few of BNN2 and BNN4 phases as marked in Fig. 1(a), it has no significant effect on the TMC due to their similar structures to that of the BNN5 crystals. As shown in Fig. 1(b), the BNN5 products are plate-like with relatively smooth surface and quite complete rectangle section. A typical particle of the BNN5 crystal is presented in the inset of Fig. 1(b), revealing that the
BNN5 particles are high-aspect-ratio. According to the statistics of sample sizes, the BNN5 samples possess an average size of 5–20 µm in length/width and 0.5–1 µm in thickness. Hence, the BNN5 platelets with anisotropic morphology would be suitable precursors to fabricate the KNN crystals.
Fig. 1 (a) XRD patterns and (b) SEM images of BNN5 products.
In order to fully investigate the KNN crystals, the NaNbO3 particles were first prepared as comparison. Figure 2(a) shows the XRD patterns of NaNbO3 crystals produced in NaCl salt at 950 ℃ for 4 h. All the peaks can be indexed to the perovskite phase well, identified by PDF#33-1270. Moreover, the surfaces of the NaNbO3 crystals are parallel to (00l) since the intensities of the (001) and (002) are much stronger than those in the PDF#33-1270. Figure 2(b) shows the SEM images of the plate-like NaNbO3 platelets. The morphology of the NaNbO3 crystals has inherited that of BNN5 precursors according to the similarity between Figs. 1(b) and 2(b). Moreover, a representative NaNbO3 particle is shown in the inset of Fig. 2(b), the morphology of which is also in accordance with that of BNN5 particle. Whereas, there are a few of fragments perhaps due to the structure reconstruction during the reaction.
Fig. 2 (a) XRD patterns and (b) SEM images of NaNbO3 platelets.
The XRD patterns of the KNN particles prepared at 1020 ℃ for 10 h with K2CO3 and different ratios of KCl/NaCl are shown in Fig. 3(a). Although there are a tiny amount of BNN5 structures, the KNN particles mainly possess perovskite phases when the ratios of KCl/NaCl are set at 2/1 and 4/1. However, a certain amount of BNN5 phase emerges with the increasing KCl/NaCl ratio, and the XRD results of the resultant product with the salts ratio of 8/1 is also presented. As is known, the cation radius of Na
(1.02 Å ) is much close to that of Bi3 (1.03 Å ). Moreover, the cation radius of K is 1.38 Å , thus Na is considered easier to incorporate into the BNN5 structures. However, the concentration of Na is considerably low in the reaction solution when the salts ratio of KCl/NaCl is 8/1 with K2CO3 as carbonate. Hence, the Na cations
would be insufficient to replace Bi3 , and the BNN5 precursor was retained. In addition, there is a small shift of diffraction peaks to a lower angle ~46° with the increase of the salts ratio, illustrating that a certain amount of K incorporate into the structures. It could be inferred that the KNN particles with high K concentration would be rather difficult to be obtained only with the high ratio of KCl in the salts due to the remnant BNN5 and big radius of K . In order to confirm the effect of carbonate on the KNN particles, further comparative experiments were carried out. Figure 3(b) shows the XRD patterns of the KNN particles synthesized with K2CO3 and Na2CO3 when
the salts ratio of KCl/NaCl is 4/1, respectively. The samples with perovskite structure can be identified by PDF#33-1270. The types of carbonates have no significant influence on the final products, which is in good agreement with Ref. [35]. During the TMC process, the CO32–could mainly contribute to removing the weak network [Bi2O2]2 . In addition, some peaks at 22° and 45° indexed by PDF#32-0822 reveal the existence of KNN phase.
Fig. 3 XRD patterns of KNN platelets synthesized with (a) different ratios of KCl/NaCl and (b) carbonates.
Moreover, the synthesis factors such as reaction temperature, together with the sintering time, should also be emphasized, and the results are shown in Fig. 4. Figure 4(a) shows the KNN structures prepared at 970 ℃ for various sintering time. The BNN5 structures are clearly observed in the KNN particles synthesized for 6 h. It was decided to extend the sintering time from 6 to 10 h for the purpose of promoting more complete reaction. As shown in Fig. 4(a), the BNN5 phases obviously decrease, and there are mainly perovskite phases in the KNN particles assigned by PDF#33-1270. Thus, it is revealed that extending the sintering time helps K /Na to replace the Bi3 completely. In order to further control the KNN structures, the reaction temperatures varied from 970 to 1020 ℃. It can be seen from Fig. 4(b) that the intensities of BNN5 phase are weaker at 1020 ℃ comparing to that at 970 ℃, indicating that increasing sintering temperature helps the fabrication of KNN structures with less impurity.
Fig. 4 XRD patterns of KNN platelets fabricated with different (a) sintering time and (b) sintering temperatures.
The morphology and EDS images of the KNN particles are shown in Fig. 5. The morphology of the KNN platelets synthesized with the KCl/NaCl ratio of 2/1 and 4/1 is basically consistent with that of BNN5 structures. The length/width of the KNN samples reaches 5–20 µm, while the thickness is close to 1 μm. The morphology of the KNN particles prepared with the salts ratio of 2/1 is quite complete in edge as shown in Fig. 5(a); when the samples are broken, more obvious sample fragments can be seen in Fig. 5(c). The reason might be that the perovskite structures would be crashed to some extent when the considerable K incorporates into the structures during the TMC procedure. The EDS spectra of the KNN particles with different molten salt ratios are shown in Figs. 5(b) and 5(d). There are Na , K , Nb5 , and O2– detected in the KNN particles, and the atomic ratios are also listed. The enrichment of Na cations is also observed in the EDS results, and the quantity of K cations entered the crystal structures rises to some extent with the increase of the KCl/NaCl ratio. Thus, the chemical formulas of the KNN structures synthesized with the KCl/NaCl ratio of 2/1 and 4/1 are roughly considered as (K0.08Na0.92)NbO3 and (K0.15Na0.85)NbO3, respectively. According to the experimental results, the K/Na ratio of the KNN
particles could be mainly attributed to the salt ratio and the sintering condition, while the types of carbonates seem do not play a critical role on the KNN template
synthesis. As a result, the content of Na in the product is much higher than that of K element, and the change of K atomic ratio is not so obvious while the proportion of molten salts varies in the range from 2/1 to 4/1.
Fig. 5 SEM images of KNN platelets synthesized with KCl/NaCl ratios of (a) 2/1 and (c) 4/1; (b, d) EDS results corresponding to (a, c), respectively
Raman spectroscopy is very sensitive to the structure [38]. In order to figure out the effect of the salts proportion, Raman spectra of 2D NaNbO3 and KNN templates measured at ~25 ℃ are shown in Fig. 6. The structures were mechanically pressed into thin bulks as the initial step. Then, the spot of incident light was set at 1 μm and focused on the top of the thin bulk. It should be noted that the light would not raise the temperature of NaNbO3 and KNN micro/nano structures due to its low power which is small than 8 mW. As is known, there are kinds of internal vibrational modes of NbO6 octahedra. v1 and v5 modes are relatively strong and could be easily identified in the Raman spectra as shown in Fig. 6. It can be seen that some bands in the region of 180–200 cm–1 are observed as v6 modes in NaNbO3 structures, while the intensity of these bands significantly decreases in the KNN ones. Moreover, the v1 v5 mode locates at 880 cm –1 in the NaNbO3 sample and shifts to the lower frequency in the KNN sample, which is related to the change of vibration mode causing by the addition of K cations. In addition, the Raman results for the KNN templates synthesized with different salts proportions, i.e., KCl/NaCl of 2/1 and 4/1, are basically consistent. It could be concluded that there is little difference between the two components of the KNN samples, which is in accordance with the EDS results in Fig. 5. It should also be noted that random regions of the samples were selected, and the Raman scattering results remain essentially unchanged, indicating that the samples are homogeneous in composition.
Fig. 6 Raman spectra of NaNbO3 structures and KNN structures with KCl/NaCl ratios of 4/1 and 2/1.
Figure 7 shows the topography and the piezoelectric responses of the plate-like KNN structures with the KCl/NaCl ratio of 2/1. AFM at tapping mode was employed to map the topography of the KNN particles, and the 3D and 2D images of the KNN particles are shown in Figs. 7(a) and 7(b), respectively. A straight line was drawn across the KNN particle as marked in Fig. 7(b), and the height information of the line was gathered, indicating that the thickness of the plate is ~500 nm as shown in Fig. 7(c). Whereas, the topography of the KNN plate in Fig. 7(c) seems to be rough, and it could be attributed to the fragment of KNN samples adhered to the surface of the plate. The particle size corresponds well with the SEM analysis results (Fig. 5(a)). Furthermore, the SS-PFM was applied to measure the piezoelectric response of the KNN plates,
and three points are arranged on the surface of the particle as marked in Fig. 7(b). A sequence of DC signal with “on” and “off” states in a periodic triangle wave ranging from –30 to 30 V was applied, while an AC excitation signal of 3 V was added at intervals of increasing DC voltage to minimize electrostatic effects[39]. The amplitude butterfly curves and the phase hysteresis loops of the three points obtained during the “off” state are shown in Fig. 7(d), which represent the typical amplitude–voltage and phase–voltage hysteresis loops, respectively. The phase contrast of the three regions on the KNN structure is approximately 180°, which is a signature of domain reversal in typical ferroelectrics [40,41]. Moreover, the piezoresponses from different districts are not extensively different, indicating the uniformity of the compositions and crystal structures of the KNN plates.
Fig. 7 (a) 3D and (b) 2D AFM images of KNN structures with the KCl/NaCl ratio of 2/1; (c) height variation of the line across the KNN structure as marked in (b); (d) piezoresponse and phase information gathered from points 1–3, as marked in (b).
4 Conclusions
In conclusion, 2D plate-like lead-free KNN structures were successfully synthesized via a two-step MSS. The layered-perovskite BNN5 structures were synthesized
as precursors in the initial step, and then the high-aspect-ratio KNN crystals were prepared using the BNN5 precursors by TMC. The reaction factors were discussed in detail, and the optimized condition was confirmed. It should be emphasized that confocal Raman spectroscopy and PFM were used to characterize the microstructure and piezoelectric property of the KNN plates. Resultantly, the KNN crystals with uniform structure and anisotropic morphology were obtained, which possessed the size of 5–20 µm in length/width and 0.5–1 µm in thickness. Additionally, the enrichment of Na element in the products is also observed when compared to K element, indicating the different cation substitution in the BNN5 precursors. The 2D KNN micro/nano piezoelectric structures are expected to play an important role on the fabrication of high-performance KNN based textured ceramics.
Acknowledgements
The authors acknowledge the financial supports from the National Natural Science Foundation of China (Grant No. 51602345), the State Key Laboratory of New Ceramics
and Fine Processing Tsinghua University (Grant No. KF201512), Open Fund of State Key Laboratory of Coal Resources and Safe Mining (Grant No. SKLCRSM19KFA13), and Fundamental Research Funds for the Central Universities (Grant No. 2016QJ01).
References
[1] Cross E. Lead-free at last. Nature 2004, 432: 24–25.
[2] Rödel J, Jo W, Seifert KTP, et al. Perspective on the development of lead-free piezoceramics. J Am Ceram Soc 2009, 92: 1153–1177.
[3] Saito Y, Takao H. High performance lead-free piezoelectric ceramics in the (K, Na)NbO3-LiTaO3 solid solution system. Ferroelectrics 2006, 338: 17–32.
[4] Shrout TR, Zhang SJ. Lead-free piezoelectric ceramics: Alternatives for PZT? J Electroceram 2007, 19: 113–126.
[5] Malič B, Koruza J, Hreščak J, et al. Sintering of lead-free piezoelectric sodium potassium niobate ceramics. Materials 2015, 8: 8117–8146.
[6] Cheng LQ, Li JF. A review on one dimensional perovskite nanocrystals for piezoelectric applications. J Materiomics 2016, 2: 25–36.
[7] Koruza J, Bell AJ, Frömling T, et al. Requirements for the transfer of lead-free piezoceramics into application. J Materiomics 2018, 4: 13–26.
[8] Zhao JB, Du HL, Qu SB, et al. The effects of Bi(Mg2/3Nb1/3)O3 on piezoelectric and ferroelectric properties of K0.5Na0.5NbO3 lead-free piezoelectric ceramics. J Alloys
Compd 2011, 509: 3537–3540.
[9] Saito Y, Takao H, Tani T, et al. Lead-free piezoceramics. Nature 2004, 432: 84–87.
[10] Li JF, Wang K, Zhu FY, et al. (K, Na)NbO3-based lead-free piezoceramics: Fundamental aspects, processing technologies, and remaining challenges. J Am Ceram Soc 2013, 96:3677–3696.
[11] Wang K, Yao FZ, Jo W, et al. Temperature-insensitive (K,Na)NbO3-based lead-free piezoactuator ceramics. Adv Funct Mater 2013, 23: 4079–4086.
[12] Li Q, Zhang MH, Zhu ZX, et al. Poling engineering of (K, Na)NbO3-based lead-free piezoceramics with orthorhombic–tetragonal coexisting phases. J Mater Chem C 2017, 5: 549–556.
[13] Zhang MH, Wang K, Zhou JS, et al. Thermally stable piezoelectric properties of (K, Na)NbO3-based lead-free perovskite with rhombohedral-tetragonal coexisting phase. Acta Mater 2017, 122: 344–351.
[14] Zheng T, Wu JG, Cheng XJ, et al. New potassium–sodium niobate material system: A giant-d33 and high-TC lead-free piezoelectric. Dalton Trans 2014, 43: 11759–11766.
[15] Dai YJ, Zhang XW, Chen KP. Morphotropic phase boundary and electrical properties of K1–xNaxNbO3 lead-free ceramics. Appl Phys Lett 2009, 94: 042905.
[16] Jung JH, Lee M, Hong JI, et al. Lead-free NaNbO3 nanowires for a high output piezoelectric nanogenerator. ACS Nano 2011, 5: 10041–10046.
[17] Wang Z, Zhang YD, Yang SL, et al. (K, Na)NbO3 nanofiber-based self-powered sensors for accurate detection of dynamic strain. ACS Appl Mater Interfaces 2015, 7: 4921–4927.
[18] Tutuncu G, Chang YF, Poterala S, et al. In situ observations of templated grain growth in (Na0.5K0.5)0.98Li0.02NbO3 piezoceramics: Texture development and template-matrix interactions. J Am Ceram Soc 2012, 95: 2653–2659.
[19] Lv D, Zuo R, Su S. Reactive templated grain growth and anisotropic electrical properties of (Na0.5K0.5)NbO3 ceramics without sintering aids. J Mater Sci: Mater Electron 2012,23: 1367–1372.
[20] Yan YK, Zhou JE, Maurya D, et al. Giant piezoelectric voltage coefficient in grain-oriented modified PbTiO3 material. Nat Commun 2016, 7: 13089.
[21] Yan YK, Liu D, Zhao W, et al. Topochemical synthesis of a high-aspect-ratio platelet NaNbO3 template. J Am Ceram Soc 2007, 90: 2399–2403.
[22] Gao F, Liu LL, Xu B, et al. Phase transition and piezoelectric properties of K0.48Na0.52NbO3-LiTa0.5Nb0.5O3-NaNbO3 lead-free ceramics. J Alloys Compd 2011, 509: 6049–6055.
[23] Zhang ZQ, Yang J, Liu ZF, et al. Evolution of textured microstructure of Li-doped (K, Na)NbO3 ceramics prepared by reactive templated grain growth. J Alloys Compd 2015,624: 158–164.
[24] Yao JJ, Li JF, Viehland D, et al. Aging associated domain evolution in the orthorhombic phase of 〈001〉 textured (K0.5Na0.5)Nb0.97Sb0.03O3 ceramics. Appl Phys Lett 2012,100: 132902.
[25] Kimura T, Sakuma Y, Murata M. Texture development in piezoelectric ceramics by templated grain growth using heterotemplates. J Eur Ceram Soc 2005, 25: 2227–2230.
[26] Kimura T. Application of texture engineering to piezoelectric ceramics. J Ceram Soc Jpn 2006, 114: 15–25.
[27] Li LY, Bai WF, Zhang Y, et al. The preparation and piezoelectric property of textured KNN-based ceramics with plate-like NaNbO3 powders as template. J Alloys
Compd 2015, 622: 137–142.
[28] Messing GL, McKinstry ST, Sabolsky EM, et al. Templated grain growth of textured piezoelectric ceramics. Crit Rev Solid State Mater Sci 2004, 29: 45–96.
[29] Hussain A, Rahman JU, Ahmed F, et al. Plate-like Na0.5Bi0.5TiO3 particles synthesized by topochemical microcrystal conversion method. J Eur Ceram Soc 2015, 35: 919–925.
[30] Liu D, Yan YK, Zhou HP. Synthesis of micron-scale platelet BaTiO3. J Am Ceram Soc 2007, 90: 1323–1326.
[31] Saito Y, Takao H. Synthesis of polycrystalline platelike NaNbO3 particles by the topochemical micro-crystal conversion from K4Nb6O17 and fabrication of grain oriented (K0.5Na0.5)NbO3 ceramics. J Electroceram 2010, 24: 39–45.
[32] Hussain A, Kim JS, Song TK, et al. Fabrication of textured KNNT ceramics by reactive template grain growth using NN templates. Curr Appl Phys 2013, 13: 1055–1059.
[33] Ishii K, Tashiro S. Orientation control of (K, Na)NbO3 ceramics using NaNbO3 particles prepared by single-step molten salt synthesis. Jpn J Appl Phys 2013, 52: 09KD04.
[34] Ishii K, Tashiro S. Orientation control of (K, Na)NbO3 ceramics using platelike NaNbO3 templates prepared by single-step molten salt synthesis with mixed salt. Jpn J
Appl Phys 2016, 55: 10TD01.
[35] Li LY, Zhang Y, Bai WF, et al. Synthesis of high aspect ratio (K, Na)NbO3 plate-like particles and study on the synthesis mechanism. Dalton Trans 2015, 44: 11621–11625.
[36] Lee JS, Jeon JH, Choi SY. Role of alkali carbonate and salt in topochemical synthesis of K1/2Na1/2NbO3 and NaNbO3 templates. Met Mater Int 2013, 19: 1283–1287.
[37] Zhu BP, Zhang ZQ, Ma T, et al. (100)-Textured KNNbased thick film with enhanced piezoelectric property for intravascular ultrasound imaging. Appl Phys Lett 2015, 106:173504.
[38] Jehng JM, Wachs IE. Structural chemistry and Raman spectra of niobium oxides. Chem Mater 1991, 3: 100–107.
[39] Liu YM, Wang YJ, Chow MJ, et al. Glucose suppresses biological ferroelectricity in aortic elastin. Phys Rev Lett 2013, 110: 168101.
[40] Zhang T, Yang JO, Yang XF, et al. High performance KNN-based single crystal thick film for ultrasound application. Electron Mater Lett 2019, 15: 1–6.
[41] Yu Q, Li JF, Sun W, et al. Orientation-dependent piezoelectricity and domain characteristics of tetragonal Pb(Zr0.3, Ti0.7)0.98Nb0.02O3 thin films on Nb-doped SrTiO3 substrates. Appl Phys Lett 2014, 104: 012908.
Open Access
This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made.
The images or other third party material in this article are included in the article’s Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Commons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder.
To view a copy of this licence, visit http://creativecommons. org/licenses/by/4.0/.
