RSS
E-mail Alert
Search Advanced
Article navigation > Materials Lab > 2024 > 3, 230019
Next Article Previous Article

Haitao Li, Mingyang Li, Xiaoxue Jiang, Changda Zhu, Hongguang Wang, Aowei Deng, Guozhong Zang, Yongjun Gu. Enhanced piezoelectric properties for potassium sodium niobate lead-free piezoelectric ceramics prepared by microwave technology[J]. Materials Lab, 2024, 3(1): 230019. doi: 10.54227/mlab.20230019
Citation: Haitao Li, Mingyang Li, Xiaoxue Jiang, Changda Zhu, Hongguang Wang, Aowei Deng, Guozhong Zang, Yongjun Gu. Enhanced piezoelectric properties for potassium sodium niobate lead-free piezoelectric ceramics prepared by microwave technology[J]. Materials Lab, 2024, 3(1): 230019. doi: 10.54227/mlab.20230019
shu

RESEARCH ARTICLE

Enhanced piezoelectric properties for potassium sodium niobate lead-free piezoelectric ceramics prepared by microwave technology

More Information
  • 1.

    School of Materials Science and Engineering, Henan University of Science and Technology, Luoyang 471023, PR China

  • 2.

    School of physics and Engineering, Henan University of Science and Technology, Luoyang 471023, PR China

  • Corresponding author: listone@163.com
    Abstract

  • Potassium-sodium niobate (Na, K)NbO3 (NKN) powder was synthesized at low temperature via microwave-assisted hydrothermal solovthermal method (MHSM). The resultant powder was characterized by X-ray diffraction (XRD) and scanning electron microscope (SEM). XRD results showed that pure (Na, K)NbO3 powder with a single perovskite structure was successfully synthesized when the concentration of mineralization exceeded 1 M. In order to reduce the volatilization of alkaline elements, NKN ceramics derived from 5M-powder were prepared in a microwave furnace. Microstructure, stoichiometry, and electrical properties of the obtained ceramics were investigated. The piezoelectric coefficient (d33), electromechanical coupling coefficient (kp) and remnant polarization (Pr) of the sample sintered at 1050 °C show optimal values of 132 pC/N, 38% and 26.3 µC cm-2, respectively. The results indicate that the microwave heating is a promising method for synthesizing and sintering NKN-based ceramics.


    • FullText(HTML)

  • Although PbZr1-xTixO3 (PZT)-based piezoelectric ceramics have dominated the market of piezoelectric devices for more than half a century because of their superior piezoelectric properties, they will be replaced in the near future due to the toxicity of lead. Therefore, it is urgent to find environment-friendly alternative materials to meet the growing environmental awareness. Among lead-free piezoelectric compositions, potassium-sodium niobate ((Na, K)NbO3, NKN) is considered to be one of the promising candidate owing to its high curie temperature and good piezoelectricity[1-6]. However, the high-temperature sintering of traditional solid-state method makes alkali metal volatilize seriously, which causes the stoichiometric ratio deviation and affects the density of KNN ceramics, thereby damaging their piezoelectric properties[7-8]. Therefore, the piezoelectric coefficient of pure NKN ceramics fabricated by traditional solid-state method was no more than 80 pC/N[3, 9].

    Special techniques like hot pressing and spark plasma sintering[10-11] are reported to be effective means for getting dense NKN ceramics, but the complex process and high fabricating cost make them unsuitable for industrial production. Therefore, sintering aids such as ZnO, CuO, and MgO have been applied to lower the sintering temperature and improve the density of NKN ceramics[5,12-15].

    Another efficacious solution to obtain dense NKN ceramics is to manufacture them with ultrafine powders, based on the idea that the driving force of sintering is inversely proportional to the particle size of powders[16]. Several wet-chemical methods, such as sol-gel, hydrothermal method and pechini method, have been studied to synthesize ultrafine NKN powder[17-19]. Among them hydrothermal method is promising because it requires low temperature and delivers pure ultrafine powders without further heat treatment. Nevertheless, this method usually require dense mineralization and spend a long aging time[19]. Microwave-assisted hydrothermal solovthermal method (MHSM), as a modified hydrothermal method, has attracted more attention due to its thin mineralization concentration and short synthesis time. Bai et al. have successfully synthesized NKN powders through MHSM, reducing the concentration of mineralization from 10 M to 2 M[20]. In our previous study[21], ultrafine NKN powders have been fabricated using MHSM at 200 °C for only 30 min.

    For NKN based ceramics, sintering temperature and holding time are two important factors that affect the volatilization of alkali metals. Due to the large particle size and uneven distribution of the powder synthesized by traditional solid-state method, ceramics often requires higher temperatures and longer holding times to density, which inevitably exacerbates the volatilization of alkali metals. On the contrary, the powder synthesized by wet chemical method can achieve densification by sintering at lower temperatures due to its fine particle size and uniform distribution. Wu et al. synthesized NKN ceramic powder using traditional solid-state method and sintered it at a temperature of 1120 °C for 2 h, with a relative density of 92.5% and a d33 of 125 pC/N[9]. Zhou et al. sintered NKN powder synthesized by microwave hydrothermal method at 1000 °C for 2 h, with a d33 of 126 pC/N[22]. Microwave sintering is known to be adequate for shorting sintering time due to its fast heating rate. According to the report of Mahdi[23], KNN ceramics prepared by microwave sintering (total heating time of 36 min without soaking time) showed nearly the same density, dielectric, piezoelectric and ferroelectric behavior as those obtained in conventionally sintered ceramics (with a heating rate of 5 °C min-1 and soaking time of 2 h).

    In the present study, microwave-assisted hydrothermal solovthermal method (MHSM) was utilized to synthesize NKN powder, and the influence of the mineralization concentration on the synthesized powder was characterized. Also, the electrical properties of NKN ceramics (from as-MHSMed powder) sintered in microwave furnace were investigated with special emphasis on sintering temperature. The d33 of 132 pC/N and Pr of 26.3 µC cm-2 can be achieved by microwave sintering at 1050 °C for only 30 min, which better than that of the ceramics prepared by traditional sintering at 1120 °C for 2 h[9]. The results show that the microwave solvothermal synthesis and microwave sintering have great potential for preparing KNN-based ceramics.

    Preparation process

    Analytical-grade potassium hydroxide (KOH), sodium hydroxide (NaOH), niobiumpentoxide (Nb2O5) and isopropanol were used as starting materials. All of these chemicals were obtained from Sinopharm Chemical Reagent Co., Ltd, China. First, a mixed solution of KOH and NaOH with a KOH/NaOH ratio of 3:1 was adjusted to 1.0-8.0 mol L−1. Then appropriate amounts of Nb2O5 and isopropanol were dispersed in the mixed hydroxide solution, and stirred for 30 min. The slurry was poured into a 100 ml teflon lined reactor with 60% filling ratio. The reactor was placed in a microwave synthesizer (XH-800G, BJXH, China) and the reaction was operated at 2.45 GHz. According to our previous study, MHSM temperature was set at 200 °C and hold time to 90 min. After the reaction was completed, the precipitates were filtered and washed several times with deionized water and dried at 100 °C for 6 h.

    The as-MHSMed powder was mixed with 5 wt.% polyvinyl alcohol(PVA) solution, and then uniaxially pressed into pellets of 10 mm in diameter and 1.0 mm in thickness under a pressure of 80 MPa. After burning out PVA, the green disks were sintered in microwave furnace at selected temperatures between 1000 °C and 1080 °C for 30 min in air to get dense ceramics. For electrical characterization, synthetic ceramics were polished and coated with Ag paste on both parallel surfaces, and then fired at 550 °C for 30 min. Subsequently, the ceramics were polarized along the thickness direction by applying a direct current electric field of 3 kV mm−1 at 120 °C for 30 min.

    Performance testing

    Density of ceramics was determined by the Archimedes method. Phase structure was determined using x-ray powder diffraction with a Cu K radiation (λ=1.5416 Å) filtered through a Ni foil (Rigaku; RAD-B system, Tokyo, Japan). The morphology of as-MHSMed powders and ceramics was observed using a scanning electron microscope (SEM, S-450, HITACHI, Tokyo, Japan). After ultrasonic distribution for 10 min, the mean particle size and particle size distribution of as-MHSMed powders were measured by a laser particle size analyzer (Horiba LA-960, Japan). The concentrations of K and Na were determined by energy dispersive X-ray (EDS) analysis on SEM. Dielectric properties were examined using a precision impedance analyzer (Agilent, 4294A). The piezoelectric constant d33 was measured using a quasi-static piezoelectric coefficient testing meter (ZJ-3A, Institute of Acoustics, Chinese Academy of Sciences, Beijing, China). A precision impedance analyzer (Agilent, 4294A) was used to calculate the planar electromechanical coupling coefficient kp on the basis of IEEE standards by resonance–antiresonance method. Ferroelectric hysteresis loops were measured at 100 Hz using a ferroelectric tester (RT6000HVA, Radiant Technologies, Inc., Albuquerque, NM).

    The influence of the concentration of mineralizer

    Fig. 1 shows the XRD patterns of NKN powders synthesized by MHSM at 200 °C for 90 min with different concentration of mineralizer. It can be seen that the samples show a single phase perovskite structure without any detectable secondary phases when the concentration of mineralizer is greater than 1 M. For the sample with 1 M, a minute amount of second phase Nb2O5 (PDF32-0710) is formed due to too thin alkaline concentration. As the alkaline concentration increases from 3 M to 8 M, a splitting peak of (202)/(020) occurs at 2θ = 45-47°, which indicates the formation of a single phase orthorhombic perovskite structure. It is interesting that as the alkaline concentration increases from 1 M to 5 M, the 2θ of diffraction peak in (110) space shifts to a lower angle, and almost no changes as it further increases to 8 M. This may be attributed to the fact that NaOH is more reactive than KOH, and thus there are more Na+ ions react with Nb2O5 at low alkaline concentration, even though the K+/Na+ molar ratio is constant in the detected alkaline solution[24]. With increasing alkaline concentration, there are more K+ ions will enter into the lattice of NKN, which leads to the diffraction peak of (110) shift to a low angle owing to that K+ (1.64 Å) radius is larger than Na+ (1.39 Å) radius. However, when the alkaline concentration exceeds 5 M, the angle of diffraction peak in (110) remains nearly unchanged, indicating that the solid solubility of K+ in NKN lattice will no longer increase.

    Fig. 1  XRD patterns of NKN powders synthesized by MHSM with different mineralizer concentrations.
    DownLoad: Full-Size Img PowerPoint

    The SEM images of as-MHSMed powders with different concentration of mineralizer are shown in Fig. 2. It is observed that as-MHSMed powders exhibit a typical quadrate-like morphology, except that a few smaller crystals adhere to the larger ones for the sample with 3 M concentration, which leads to slight agglomeration, as shown in Fig. 2a. When the concentration of mineralizer exceeds 3 M, the crystal presents a stepwise growth mode, as shown by the arrows in Fig. 2b and Fig. 2c, in addition, obvious small holes appear on the crystal surface of the sample with 8 M concentration.

    Fig. 2  SEM images of NKN powders with different mineralizer concentrations: a 3 M; b 5 M; c 8 M.
    DownLoad: Full-Size Img PowerPoint

    The corresponding particle size distribution of as-MHSMed powders are shown in Fig. 3. It can be observed that as the concentration of mineralizer increases from 3 M to 8 M, the average particle size (da) and cutting particle size (d50) increase from 2.56 μm and 2.12 μm to 5.92 μm and 3.62 μm, respectively. In addition, compared to the samples with 3M and 8M concentration, the powder with 5 M concentration has a fine morphology and a narrow distribution.

    Fig. 3  Particle size distribution of NKN powders with different mineralizer concentrations: a 3 M; b 5 M; c 8 M.
    DownLoad: Full-Size Img PowerPoint

    Microstructure and EDS spectra

    To evaluate the microwave sintering of NKN ceramics, the as-MHSMed powder with 5 M concentration was pelletized and sintered at 1000-1080 °C in microwave furnace (with a heating rate of 25 °C min−1 and soaking time of 0.5 h). Fig. 4 shows the SEM images of the fracture surface of NKN ceramics sintered at different temperatures. As shown in Fig. 4, the sample sintered at 1000 °C has a blurry microstructure with small grains, indicating insufficient grain growth. The samples sintered at higher temperature exhibit rectangular grains, and the grain size increases with the increase of sintering temperature. The average grain sizes of the samples sintered at 1000 °C, 1020 °C, 1050 °C and 1080 °C are 0.60, 0.96, 1.31 and 1.76 μm, respectively, and the corresponding densities are 4.21, 4.28, 4.30 and 4.25 g cm−3, respectively. The reason for the decrease in density of the sample sintered at 1080 °C may be due to the severe volatilization of alkali metals at high temperature.

    Fig. 4  SEM images of the fracture surface of NKN ceramics sintered at different temperatures: a 1000 °C; b 1020 °C; c 1050 °C; d 1080 °C.
    DownLoad: Full-Size Img PowerPoint

    The EDS spectra of NKN ceramics sintered at different temperatures are shown in Fig. 5. It is observed that as the sintering temperature increases from 1000 °C to 1080 °C, the K+/(Na++K+) molar ratio increases from 0.454 to 0.502 , all of which are less than that of the precursor solution 0.75. On the one hand, it is because Na+ reacts more readily with Nb2O5 than K+ to form NKN. On the other hand, the volatilization of sodium is more severe than that of potassium, resulting an increase in K+/(Na++K+) molar ratios with increasing sintering temperature, which is also reported by Wang [25].

    Fig. 5  EDS spectra of NKN ceramics sintered at different temperatures: a 1000 °C; b 1020 °C; c 1050 °C; d 1080 °C.
    DownLoad: Full-Size Img PowerPoint

    Density and electrical properties

    P-E hysteresis loops of NKN ceramics sintered at different temperatures are depicted in Fig. 6. The samples sintered at 1000 °C, 1020 °C, 1050 °C and 1080 °C present remnant polarization (Pr) values of 16.2, 18.9, 26.3 and 20.8 µC cm−2 as well as coercive field (Ec) values of 12.8, 11.1, 9.6 and 9.3 KV cm−1, respectively. Pr first increases and then decreases and Ec decreases monotonically with increasing sintering temperature. As reported by Jin[26], the value of Pr is manly affected by grain size and density. On the one hand, as domain size is proportional to the square root of grain size, a larger grain is conducive to its polarization, thus increasing its Pr. On the other hand, a higher density is beneficial for increasing the polarization voltage, thereby enhancing its Pr. As mentioned above, the optimal value of 26.3 µC cm−2 may be the result of the synergistic effect of grain size and density. Compared to Pr, the influencing factors of Ec are more complicated, mainly including composition, grain size, defect concentration, crystallinity, and phase structure. The variation of Ec may be the result of the synergistic effect of these factors, and its detailed mechanism still needs further research.

    Fig. 6  P-E hysteresis loops of NKN ceramics sintered at different temperatures.
    DownLoad: Full-Size Img PowerPoint

    For NKN-based piezoelectric ceramics, samples with good piezoelectric and ferroelectric properties should have high Pr and low Ec. Zuo et al. have reported a remnant polarization of 15 µC cm−2 in NKN[27]. Mahdi et al. obtained a Pr = 18 µC cm-2 in NKN prepared by microwave technology[23], and Gu et al. measured a Pr = 22.9 µC cm−2 in Ta doped NKN[19]. All these reported values are less than 26.3 µC cm−2 determined in this work, indicating that the sample sintered at 1050 °C exhibits an excellent ferroelectricity.

    Density and electrical properties of NKN ceramics sintered at different temperatures are summarized in Table 1. It can be seen that as the sintering temperature increases from 1000 °C to 1080 °C, the piezoelectric coefficient (d33), electromechanical (kp), density (ρ), and remnant polarization (Pr) first increase and then reduce, and reach their maximum values of 132 pC/N, 38%, 4.30 g cm−3 and 26.3µC cm−2, respectively, at the densification sintering temperature of 1050 °C. It is reported that, for NKN-based piezoceramics, piezoelectric properties are closely related to the morphtropic phase boundary (MPB) between two orthorhombic phases, as well as densification[27]. Although some researchers carried out MPB on pure NKN or NKN-based piezoceramics with the Na/K ratio of 0.5/0.5[28-30], while others believe that the composition of MPB should be approximated to 0.525/0.475 Na/K ratio[31-32], which can be determined by the phase diagram of NaNbO3-KNbO3, as reported by Tennery and Hang[33]. On the other hand, it has been reported that d33 is due in part to the combined effect of εr and Pr in NKN-based ceramics, which could be illuminated by the equation of d33 ~ αεrPr[34]. It can be seen from Fig. 5 and Table 1, the sample sintered at 1050 °C has a K+/(Na++K+) molar ratio of 0.481, indicating that whose composition is relatively close to MPB, and posses large εrPr value of 13729 µC cm−2. All these suggest that the sample sintered at 1050 °C exhibits excellent piezoelectricl properties.

    Table 1.  Summary of physical and electrical properties of NKN ceramics sintered at different temperatures.
    ST
    (°C)    		d33
    (pC/N)    		kp
    (% )    		ρ
    (g. cm−3 )    		pr
    (µC. cm−2 )    		tanδ
    (@10 KHz)    		εr
    (@10 KHz)    		εrpr
    (µC. cm−2 )
    100086254.2116.20.0424106642
    1200125354.2818.90.0314588656
    1500132384.3026.30.02852213729
    1800120324.2520.80.01853111045
     | Show Table
    DownLoad: CSV

    In addition, it can also be observed from Table 1 that the relative dielectric constant (εr) monotonically increase, while the dielectric loss (tanδ) monotonically decreases with the the increase of sintering temperature. The tanδ drops from 0.042 to 0.018, while εr raises from 410 to 531, as the sintering temperature increases from 1000 °C to 1080 °C. The variations of tanδ and εr may be due to the increases of density and/or grain size. It has been reported that the tanδ and the εr are highly dependent on the density (ρ) and grain size for NKN-based ceramics[35-36].

    A single phase orthorhombic perovskite NKN powder has been successfully synthesized using MHSM with a thin concentration of alkali liquor above 1 M. In order to avoid severe volatilization of alkali metals during high-temperature sintering process, as-MHSMed powder with 5 M concentration was pelleted and sintered in a microwave furnace. Enhanced electrical properties of d33 ~132 pC/N, kp ~38%, Pr ~ 26.3µC cm−2, and εr ~522 are obtained in the ceramic sintered at an optimal temperature of 1050 °C. Compared with the sample prepared by traditional synthesis method, the d33 has increased by 65%, indicating that the microwave heating is a promising method for synthesizing and sintering NKN-based ceramics.

    Haitao Li conducted the research; Mingyang Li wrote the results and discussion; Xiaoxue Jiang wrote the introduction; Changda Zhu organized the data; Hongguang Wang wrote the experimental; Aowei Deng wrote the conclusion; Guozhong Zang reviewed & edited; Yongjun Gu draw charts.

  • This work was supported by the Higher Education Key Project of Henan Province (Grant No. 15A430005), the PhD Start-up Fund of Henan University of Science and Technology (Grant No. 09001542).

  • The authors declare no conflict of interest.

    • References
  • 1. Y. Saito, H. Takao, T. Tani, T. Nonoyama, K. Takatori, T. Homma, T. Nagaya, M. Nakamura, Nature, 2004, 432, 84

    CrossRef Google Scholar

    2. T. Q. Shao, H. L. Du, H. Ma, S. Qu, J. Wang, J. Wang, X. Wei, Z. Xu, J. Mater. Chem. A, 2017, 5, 554

    CrossRef Google Scholar

    3. H. T. Li, Q. Cao, F. Wang, M. H. Zhang, Q. Yu, R. Y. Dong, J. Alloys Comp., 2015, 634, 163

    CrossRef Google Scholar

    4. J. Ma, B. Wu, W. J. Wu, J. Mater. Sci.-Mater. Electron., 2017, 28, 4458

    CrossRef Google Scholar

    5. H. T. Li, B. P. Zhang, Q. Zhang, P. P. Shang, G. L. Zhao, Int. J. Miner. Metall. Mater., 2010, 17, 340

    CrossRef Google Scholar

    6. H. T. Li, B. P. Zhang, J. B. Wen, R. H. Xu, Q. Li, J. Inorg. Mater., 2012, 27, 385

    CrossRef Google Scholar

    7. S. R. Kim, J. H. Yoo, J. H. Kim, Y. S. Cho, J. W. Park, Nano Energy, 2021, 79, 105445

    CrossRef Google Scholar

    8. Y. W. Liu, Y. P. Pu, Q. Jin, Sci. Adv. Mater., 2018, 10, 257

    CrossRef Google Scholar

    9. L. Wu, J. L. Zhang, C. L. Wang, J. C. Li, J. Appl. Phys., 2008, 103, 084116

    CrossRef Google Scholar

    10. Y. L. Su, X. M. Chen, Z. D. Yu, J. Mater. Sci., 2017, 52, 2934

    CrossRef Google Scholar

    11. B. P. Zhang, J. F. Li, K. Wang, H. L. Zhang, J. Am. Chem. Soc., 2006, 89, 1605

    CrossRef Google Scholar

    12. H. T. Li, B. P. Zhang, M. Cui, W. G. Yang, N. Ma, J. F. Li, Curr. Appl. Phys., 2011, 11, 184

    CrossRef Google Scholar

    13. H. T. Li, Q. Li, Y. F. Yan, R. H. Xu, J. Inorg. Mater., 2015, 30, 369

    CrossRef Google Scholar

    14. Y. Lu, H. T. Li, Q. Li, B. P. Zhang, Rare metals, 2010, 29, 243

    CrossRef Google Scholar

    15. H. Y. Park, C. W. Ahn, K. H. Cho, S. Nahm, H. G. Lee, H. W. Kang, D. H. Kim, K. S. Park, J. Am. Ceram. Soc., 2007, 90, 4066

    CrossRef Google Scholar

    16. M. R. Bafandeh, J. S. Lee, H. S. Han, J. Electroceram., 2014, 33, 128

    CrossRef Google Scholar

    17. A. Chowdhury, J. Bould, Y. Zhang, C. James, S. J. Milne, J. Nanopart. Res., 2010, 12, 209

    CrossRef Google Scholar

    18. C. Pithan, Y. Shiratori, J. Dornseiffer, F. H. Haegel, A. Magrez, R. Waser, J. Cryst. Growth, 2005, 280, 191

    CrossRef Google Scholar

    19. H. Gu, K. Zhu, X. Pang, B. Shao, J. Qiu, H. Ji, Ceram. Int., 2012, 38, 1807

    CrossRef Google Scholar

    20. L. Bai, K. Zhu, L. Su, J. Qiu, H. Ji, Mater. Lett., 2010, 64, 77

    CrossRef Google Scholar

    21. H. T. Li, Y. F. Yan, G. X. Wang, Q. Li, Y. J. Gu, J. Mater. Sci: Mater. Electron, 2018, 29, 746

    CrossRef Google Scholar

    22. Y. Zhou, J. L. Yu, M. Guo, M. Zhang, Ferroelectrics, 2010, 404, 69

    CrossRef Google Scholar

    23. M. Feizpour, H. Barzegar Bafrooei, R. Hayati, T. Ebadzadeh, Ceram. Int., 2014, 40, 871

    CrossRef Google Scholar

    24. R. López-Juárez, R. Castañeda-Guzmán, M. E. Villafuerte-Castrejón, Ceram. Int., 2014, 40, 14757

    CrossRef Google Scholar

    25. K. Wang, J. F. Li, N. Liu, Appl. Phys. Lett., 2008, 93, 092904

    CrossRef Google Scholar

    26. L. Jin, F. Li, S. J. Zhang, J. Am. Chem. Soc., 2014, 97, 1

    CrossRef Google Scholar

    27. R. Zuo, J. Rodel, R. Chen, L. Li, J. Am. Ceram. Soc., 2006, 89, 2010

    CrossRef Google Scholar

    28. H. Evelyn, D. Matthew, D. Dragan, S. Nava, Appl. Phys. Lett., 2005, 87, 182905

    CrossRef Google Scholar

    29. P. Kumar, P. Palei, Ceram. Int., 2010, 36, 1725

    CrossRef Google Scholar

    30. H. Birol, D. Damjanovic, N. Setter, J. Eur. Ceram. Soc., 2006, 26, 861

    CrossRef Google Scholar

    31. P. Zhao, B.P. Zhang, J. F. Li, Appl. Phys. Lett., 2007, 90, 242909

    CrossRef Google Scholar

    32. H. T. Li, B. P. Zhang, P. P. Shang, Y. Fan, Q. Zhang, J. Am. Ceram. Soc., 2011, 94, 628

    CrossRef Google Scholar

    33. V. J. Tennery, K. W. Hang, J. Appl. Phys., 1968, 39, 4749

    CrossRef Google Scholar

    34. P. Li, Y. Huan, W. W. Yang, Acta Mater., 2019, 165, 486

    CrossRef Google Scholar

    35. D. K. Liu, X. C. Zhang, W. B. Su, J. Alloy. Compd., 2019, 779, 800

    CrossRef Google Scholar

    36. X. Y. Gao, Z. X. Cheng, Z. B. Chen, Nat. Commun., 2021, 12, 881

    CrossRef Google Scholar

    • Rights and permissions

  • This is an open access article under the terms of the Creative Commons Attribution License, which permits use, distribution and reproduction in any medium, provided the original work is properly cited.

    • Relative Articles

  • Related articles

    1. Ruanbin Wang, Feng Gu, Shuhao Yan, Yonggang Zhao, Li-Qian Cheng. Preparation and properties of artificial bone with lead-free piezoelectric materials. Materials Lab, 2023, 2(3): 230005. doi: 10.54227/mlab.20230005
    2. Qixin Chen, Mingyuan Zhao, Jing Wang, Lei Zhao. Enhanced energy storage performance in Gd/Mn co-doped AgNbO3 lead-free antiferroelectric ceramics via tape casting. Materials Lab, 2023, 2(3): 230014. doi: 10.54227/mlab.20230014
    3. Chaofeng Wu, Wen Gong, Jinfeng Geng, Jianye Cui, Lipeng Mi, Zhixiang Zhu, Jingkai Nie, Qiang He, Zhongshang Dou, Xuting Qiu, Fang-Zhou Yao, Ke Wang. Additive manufacturing: pushing the boundaries of piezoelectric materials. Materials Lab, 2023, 2(2): 230002. doi: 10.54227/mlab.20230002
    4. Håvard Mølnås, Michael R. Scimeca, Ayaskanta Sahu. Harnessing high power factors with enhanced stability in heavy metal-free solution-processed thermoelectric copper sulfoselenide thin films. Materials Lab, 2023, 2(1): 220040. doi: 10.54227/mlab.20220040
    5. Ju Li, Renzhe Jin, Mengyuan He, Qiang Zhao, Zhengyu Wei, Panfei Sun, Dehai Ping, Xiaomei Yu, Songjie Li. Preparation and anti-corrosion properties of 8-HQ@SiO2@AK/EP composite materials. Materials Lab, 2024, 3(1): 230018. doi: 10.54227/mlab.20230018
    6. Wang-Qi Bao, Xing Yang, Tian-En Shi, Ze Li, Yi-Xin Zhang, Jing Feng, Zhen-Hua Ge. The role of Ag8GeS6 addition in p-type SnSe with enhanced thermoelectric properties. Materials Lab, 2024, 3(3): 240011. doi: 10.54227/mlab.20240011
    7. Xinyue Han, Yuyang Qiu, Bin Zhang, Yunzhu Huang, Yusong Wang, Pan Feng, Xin Gao, Qian Zhu, Menghui Liao, Yangnan Hu, Renjie Chai. Advances in Organ-on-a-chip Technologies for Biomedical Research and Applications. Materials Lab, 2025, 4(1): 240006. doi: 10.54227/mlab.20240006
    8. Xiang-Xi He, Jia-Hua Zhao, Wei-Hong Lai, Zhuo Yang, Yun Gao, Hang Zhang, Yun Qiao, Li Li, Shu-Lei Chou. Challenges and Applications of Flexible Sodium Ion Batteries. Materials Lab, 2022, 1(1): 210001. doi: 10.54227/mlab.20210001
    • Cited by
  • 1.  Masson, K., Shahni, S., Shukla, A.K. Lead-Free Piezoelectric Materials and Their Applications. Piezoelectric Materials: Design and Applications, 2025.
    2.  Amiri, O., Ahmed, M.H., Salavati-Niasari, M. et al. Exploring innovative approaches for enhanced performance of piezo catalysts. Journal of Cleaner Production, 2024.
    • Supplements
通讯作者: 陈斌, bchen63@163.com
  • 1. 

    沈阳化工大学材料科学与工程学院 沈阳 110142

  1. 本站搜索
  2. 百度学术搜索
  3. 万方数据库搜索
  4. CNKI搜索
Export Citation
PDF view
DownLoad PDF 2079KB
XML

Figures(7)

Tables(1)

Information

Received Date:  08 April 2023
Revised Date:  18 May 2023
Accepted Date:  28 May 2023
Available Online:  13 June 2023
Publish Date:  12 April 2024

Article Metrics

Article views(1686) PDF downloads(509) Citation(2)

Other Articles By Authors

2024 Vol. 3, No. 1
Article Contents
Abstract
Experimental
Results and discussion
Conclusion
AUTHOR’S CONTRIBUTION
ACKNOWLEDGEMENTS
CONFLICT OF INTEREST
References
Related articles
Cited By

Catalog

Abstract
FullText(HTML)

  • Preparation process

  • Performance testing

  • The influence of the concentration of mineralizer

  • Microstructure and EDS spectra

  • Density and electrical properties

References
Rights and permissions
Relative Articles
Cited by
Supplements

/

DownLoad:  Full-Size Img  PowerPoint
Return
  • Table 1.  Summary of physical and electrical properties of NKN ceramics sintered at different temperatures.
    ST
    (°C)    		d33
    (pC/N)    		kp
    (% )    		ρ
    (g. cm−3 )    		pr
    (µC. cm−2 )    		tanδ
    (@10 KHz)    		εr
    (@10 KHz)    		εrpr
    (µC. cm−2 )
    100086254.2116.20.0424106642
    1200125354.2818.90.0314588656
    1500132384.3026.30.02852213729
    1800120324.2520.80.01853111045
     | Show Table
    DownLoad: CSV
qrcode