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The Piezoelectric Properties of (Na<sub>0.5</sub>K<sub>0.5</sub>)NbO<sub>3</sub>-K<sub>4</sub>CuNb<sub>8</sub>O<sub>23</sub> Ceramics with Various K<sub>4</sub>CuNb<sub>8</sub>O<sub>23</sub> Doping and Sintering Temperatures
The Piezoelectric Properties of (Na0.5K0.5)NbO3-K4CuNb8O23 Ceramics with Various K4CuNb8O23 Doping and Sintering Temperatures
Transactions on Electrical and Electronic Materials. 2010. Jun, 11(3): 126-129
Copyright ©2010, The Korean Institute of Electrical and Electronic Material Engineers
  • Received : January 01, 2010
  • Accepted : April 04, 2010
  • Published : June 25, 2010
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About the Authors
Jung-Rag Yoon
yoonjungrag@samwha.com
Chang-Bae Lee
Kyung-Min Lee
Heun-Young Lee
Serk-Won Lee
Abstract
(1-X) (Na 0.5 K 0.5 )NbO 3 - X K 4 CuNb 8 O 23 (NKN-X KCN) ceramics were produced using the conventional solid state sintering method, and their sinterability and electric properties were investigated. The density, dielectric constant (ε r ), piezoelectric constant d 33 , electromechanical coupling factor k p and mechanical quality factor Q m value of the NKN ceramics depended upon the KCN content and the sintering temperature. In particular, the KCN addition to the NKN greatly improved the mechanical quality factor Q m value. The ceramic with X = 2.0 mol% sintered at 1,150℃ possesses the optimum properties (ε r = 241, d 33 = 78, k p = 0.34 and Q m = 1,121). These results indicate that the ceramic is a promising candidate material for applications in lead free piezoelectric transformer and filter materials.
Keywords
1. INTRODUCTION
Lead-based piezoelectrics, such as Pb(Zr,Ti)O 3 (PZT), ceramics have excellent piezoelectric properties and have been applied to many piezoelectric devices, such as actuators, sensors, and transformers [1 , 2] . However, these materials may be restricted because of various environmental problems. Therefore, lead-free piezoelectric materials are being extensively investigated as a replacement for PZT-based ceramics. From among several candidates for lead-free piezoelectric materials, alkali niobate-based materials, such as potassium sodium niobate, are well-known harmless materials and are promising candidates for PZT-based alternative materials due to their excellent piezoelectric properties. The Na x K 1-x NbO 3 system has a perovskite structure in its composition (x < 0.093). Among the alkali niobate compounds, (Na 0.5 K 0.5 )NbO 3 (NKN) has a high Curie temperature of more than 400℃ and excellent piezoelectric properties [3] . In the case of NKN, it is difficult to achieve high density NKN ceramics because of the volatility of the Na 2 O and K 2 O components and its high reactivity to moisture, and so the piezoelectric properties are poor. In order to improve the densification and piezoelectric properties of NKN ceramics, many binary systems have been studied, including NKN-(Ba,Sr)TiO 3 , NKNKTaO 3 , NKN-LiNbO 3 , NKN-LiSbO 3 , and NKN-K 5.4 Cu 1.3 Ta 10 O 29 [3 - 5] . Although many binary systems have been studied, the NKNK 4 CuNb 8 O 23 (KCN) binary system has rarely been done [4] . This paper describes the effect of the KCN addition and the sintering temperature on the phase structure and piezoelectric properties of the NKN ceramics. The optimum sintering temperature, density and microstructure of NKN ceramics with KCN have also been evaluated.
2. EXPERIMENTS
Conventional mixed oxide processing was used to prepare the (1-X) (Na 0.5 K 0.5 )NbO 3 -X K 4 CuNb 8 O 23 (NKN- X KCN) composition. The NKN powder was fabricated with high purity oxide powder, Na 2 CO 3 (Kojundo Chemical, 99.9%), K 2 CO 3 (Kojundo Chemical, 99.9%), and Nb 2 O 5 (MCP Inc., 99.9). The powders were weighed to achieve the desired compositions and mixed by ball milling in an anhydrous ethanol solution for 24 hours. To enhance the homogeneity of the composition, the mixtures were calcined at 850℃ for 2 hours. The KCN powder was also prepared by using the solid state reaction method using K 2 CO 3 , CuO (Kojundo Chemical, 99.9%) and Nb 2 O 5 . The initial materials were weighed and mixed for 24 hours in an anhydrous ethanol solution. The mixture was calcined at 850℃ for 5 hours. The mixture of NKN and KCN powders was ground using ball milling in an anhydrous ethanol solution for 24 hours, and then granulated with polyvinyl alcohol as a binder. The granulation was then pressed into ceramic disks, 16 mm in diameter, at 1,500 kg/cm 2 . The green disks were sintered at the optimum sintering temperatures of 1,100- 1,175℃ for 2 hours at atmospheric pressure. The sintered disks were polished, supplied with silver electrodes on the sides, and poled in a silicon bath at 120℃ under 3 kV/mm for 30 minutes. The bulk densities of the sintered ceramics were measured by the Archimedes method. The crystal structures were determined by X-ray diffraction (XRD, D-max 2200; Rikaku) measurements that were utilized to determine the resultant phase. The sample microstructures were examined using scanning electron microscopy (SEM, JSM-6360; Jeol) and the compositional analysis of the selected areas was determined by using an attached X-ray energy dispersive spectroscopy (EDS, Oxford ISIS). The dielectric properties at the frequency of 1 kHz were measured by an impedance gain phase analyzer (HP-4194A; Agilent Technologies, Santa Clara, CA, USA). The electromechanical coupling factor (k p ) and mechanical quality factor (Q m ) were measured using the resonance-antiresonance method with an impedance gain phase analyzer (HP-4194A, Agilent Technologies). The planar mode electromechanical coupling factor (k p ) and mechanical quality factor (Q m ) were calculated using:
Lager Image
and
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(f R : resonance frequency, f A : antiresonance frequency, R 1 : resonance impedance, C f : capacitance at 1 kHz)
3. RESULTS AND DISCUSSION
Figure 1 shows the XRD patterns of the (1-X) (Na 0.5 K 0.5 )NbO 3 - X K 4 CuNb 8 O 23 (NKN-X KCN) ceramics, sintered at 1,150℃ for 2 hours. The position of the (111) peak was shifted to lower angles with an increasing X. It was thought that the geometrical distortion of the ceramics was induced by the substitution of part of the KCN for the NKN. In the composition of 0.5 ≤ X ≤ 2.0 mol%, a homogenous orthorhombic NKN phase was well developed without a secondary phase. This would indicate that only a small amount of the Cu 2+ in the KCN entered the NKN ceramic matrix. The radius of the Cu 2+ (~0.72 Å) ion is similar to that of the Nb 5+ (~0.68 Å) ion, suggesting that the Cu 2+ ion entered the B site of the perovskite unit cell and replaced the Nb 5+ ion. However, when X exceed the 2.0 mol%, a peak for the KCN (K 4 CuNb 8 O 23 [P4/mbn, a = b = 12.64 Å, c = 3.99 Å]) phase, indicated by circle symbol, was observed.
Lager Image
The X-ray patterns of the (1-X) (Na0.5K0.5)NbO3-X K4CuNb8O23 ceramics sintered at 1,150℃ for 2 hours with (a) X = 0.5, (b) X = 1.0, (c) X = 2.0, and (d) X = 3.0.
Lager Image
The dependence of the densities of the (1-X) (Na0.5K0.5)NbO3- X K4CuNb8O23 ceramics and sintered temperatures.
Figure 2 shows the density of the ceramics of the (1-X) (Na 0.5 K 0.5 ) NbO 3 -X K 4 CuNb 8 O 23 (NKN-X KCN) ceramics, sintered at various temperatures. The density of the pure NKN ceramics was very low (4.2 g/cm 3 at 1,150℃) and increased with the addition of NKN- 1.0 mol% KCN to a peak 4.43 g/cm 3 at 1,125℃ for 2 hours. However, the density decreased with a further increase of X and the sintering temperature, which was due to the volatility of the K and Na in the ceramics with a high sintering temperature.
Figure 3 shows the microstructure of the (1-X) (Na 0.5 K 0.5 ) NbO 3 -X K 4 CuNb 8 O 23 (NKN- X KCN) ceramics, sintered at 1,150℃ for 2 hours. A characteristic quasicubic morphology of the grain with a clear grain boundary was observed. The change in the microstructure may be because of the low melting point of Cu 2+ in KCN, which was formed during the sintering process. With the addition of higher amounts of KCN, the optimum sintering temperature decreased and abnormal growth started. The average grain size increased upon increase of the KCN content up to approximately 8 μm for the 1.0 mol% KCN. It is observed that there are three types of grains in Figs. 3(c) and (d) , the first one is the large grains (~5 μm), the second is the needle-like grain and the third is the small grain (<1 μm). The NKN-3.0 mol% KCN ceramics shown in Fig. 3(d) was subjected to EDS analysis to identify these three phases. The EDS analysis results are shown of the compositional analysis listed in Table 1. The large and small grains contained Na, K, Cu, and Nb ions at a ratio similar to that of NKN-1.0 mol% KCN. Na, K, Cu, and Nb ions were found in the needle-like grains, but the amount of Cu ions was very large, suggesting that the liquid phase was a K 4 CuNb 8 O 23 phase.
Lager Image
The scanning electron microscopy images of the (1-X) (Na0.5K0.5) NbO3-X K4CuNb8O23 ceramics sintered at 1,150℃ for 2 hours with (a) X = 0.5, (b) X = 1.0, (c) X = 2.0, and (d) X = 3.0.
The chemical composition of the grains in the (1-X) (Na0.5K0.5) NbO3-c K4CuNb8O23ceramics sintered at 1,150℃ for 2 hours with X = 2.0.
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The chemical composition of the grains in the (1-X) (Na0.5K0.5) NbO3-c K4CuNb8O23 ceramics sintered at 1,150℃ for 2 hours with X = 2.0.
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The dependence of the dielectric constant of the (1-X) (Na0.5K0.5) NbO3-X K4CuNb8O23 ceramics with the sintered temperature.
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The dependence of the piezoelectric constant d33 of the (1-X) (Na0.5K0.5)NbO3- X K4CuNb8O23 ceramics with the sintered temperature.
Figure 4 shows the dielectric constant of the (1-X) (Na 0.5 K 0.5 ) NbO 3 -K 4 CuNb 8 O 23 (NKN-X KCN) ceramics, sintered at various temperatures. The dielectric constant of the ceramics increased with an increase of the KCN. The sintering temperature, reaches a maximum at X = 2.0 mol% at 1,150℃. In general, the dielectric constant is affected by not only the density but also the crystalline phase, chemical composition and microstructure [6]. The discrepancy in the dielectric constant contributes to the slightly different maxima for a mount of the KCN and sintering temperature. These behaviors are probably correlated to the crystal symmetries done by the formation of the solid solution with a small amount of KCN.
Figure 4 shows the dielectric constant of the (1-X) (Na 0.5 K 0.5 ) NbO 3 -K 4 CuNb 8 O 23 (NKN-X KCN) ceramics, sintered at various temperatures. The dielectric constant of the ceramics increased with an increase of the KCN. The sintering temperature, reaches a maximum at X = 2.0 mol% at 1,150℃. In general, the dielectric constant is affected by not only the density but also the crystalline phase, chemical composition and microstructure [6]. The discrepancy in the dielectric constant contributes to the slightly different maxima for a mount of the KCN and sintering temperature. These behaviors are probably correlated to the crystal symmetries done by the formation of the solid solution with a small amount of KCN.
Figure 6 shows the electromechanical coupling factor k p of the (1-X) (Na 0.5 K 0.5 )NbO 3 - K 4 CuNb 8 O 23 (NKN-X KCN) ceramics, sintered at various temperatures. The electromechanical coupling factor k p increased with an increase in the KCN and sintering temperatures; it reaches a maximum at X = 1.0 mol% at 1,125℃ but decreased gradually with an increase in the KCN content up to 2.0 mol%.
Lager Image
The dependence of the electromechanical coupling factor kp of the (1-X) (Na0.5K0.5)NbO3- X K4CuNb8O23 ceramics and the sintered temperatures.
Lager Image
The dependence of the mechanical quality factor Qm of the (1- X) (Na0.5K0.5)NbO3- X K4CuNb8O23 ceramics with the sintered temperatures.
Figure 7 shows the mechanical quality factor Q m of the (1-X) (Na 0.5 K 0.5 )NbO 3 - K 4 CuNb 8 O 23 (NKN-X KCN) ceramics, sintered at various temperatures. In the view point of practical application, it is important to reduce the dielectric dissipation factor tanδ and enhance the mechanical quality factor Q m as much as possible in order to suppress the generation of heat during operation [3] .
It was found that the addition of KCN was effective in increasing the Q m . We believe that the enhancement of the Q m is attributed to the acceptor doping effect of CuO in the KCN composition. As a hard dopant, the solution of Cu 2+ ion into the B site of the perovskite unit cell of the NKN-KCN ceramics will lead to the creation of oxygen vacancies and results in the enhancement of the Q m . When the KCN addition exceeds 3.0 mol%, however, the Q m tends to decrease, which may be the reason for the secondary phase, as affirmed by XRD and SEM observations.
4. CONCLUSIONS
A small amount of KCN was added to NKN ceramics to increase their sinterability and to improve their piezoelectric properties. The Q m value increased when a small amount of KCN was added. The hardening effect of the Cu 2+ ions was also considered to influence the Q m improvement. However, when the KCN content exceeds 3.0 mol?%, the d 33 , k p and Q m values decrease due to the formation of the KCN second phase. The ceramic having X = 2.0 mol% sintered at 1,150℃ for 2 hours exhibited the high piezoelectric properties of ε r = 241, d 33 = 78, k p = 0.34, and Q m = 1,121. These results show that the (1-X) NKN-XKCN ceramics are a promising lead-free piezoelectric material for piezoelectric applications.
References
Li E , Kakemoto H , Wada S , Tsurumi T 2007 J Am Ceram Soc 90 1787 -
Zeng J , Zhang Y , Zheng L , Li G , Yin Q 2009 J Am Ceram Soc 92 752 -
Shirane G , Newnham R , Pepinsky R 1954 Phys Rev 96 581 -
Matsubara M , Yamaguchi T , Kikuta K , Hirano S. I 2004 Japan J Appl Phys 43 7159 -
Yoon J. R , Lee C. B , Lee K. M , Lee H. Y , Rhie D. H 2009 J KIEEME 22 665 -
Lee I. H , Yoo J. H 2008 J KIEEME 21 906 -