+Model JECS-10010; No. of Pages 9 ARTICLE IN PRESS Available online at www.sciencedirect.com ScienceDirect Journal of the European Ceramic Society xxx (2015) xxx–xxx Temperature stability of dielectric properties for xBiAlO3–(1 − x)BaTiO3 ceramics Mengying Liu, Hua Hao ∗ , Yichao Zhen, Ting Wang, Dongdong Zhou, Hanxing Liu ∗ , Minghe Cao, Zhonghua Yao State Key Laboratory of Advanced Technology for Materials Synthesis and Processing, School of Material Science and Engineering, Wuhan University of Technology, Wuhan 430070, People’s Republic of China Received 1 December 2014; received in revised form 12 February 2015; accepted 14 February 2015 Abstract xBiAlO3 –(1 − x)BaTiO3 [xBA–(1 − x)BT] polycrystalline ceramics were prepared by solid-state reaction method and sol–gel method, respectively. The ceramics were in tetragonal phase when x ≤ 0.1, transformed to pseudocubic at x > 0.1. The temperature stability of the dielectric constant for BA–BT was improved with BA contents increasing. Of particular interest was that the ceramics prepared by sol–gel method had less secondary phase, exhibiting much improved dielectric behavior. Among them, 0.3BA–0.7BT met the requirement of capacitance variation (C/C ≤ ±15%) in the temperature range of −55 to 440 ◦ C with moderate dielectric constant (ε = 660) and low dielectric loss (tan δ = 1.2%) at room temperature (1 kHz). Nb-doped 0.2BA–0.8BT ceramics were investigated to improve the dielectric temperature stability at high-temperature end. It is found that all samples with 0.01–0.04 mol Nb addition satisfied the X8R specification. © 2015 Elsevier Ltd. All rights reserved. Keywords: Temperature stability; Sol–gel method; Dielectric properties 1. Introduction Perovskite materials operating under harsh environments (≥200 ◦ C) are of great interest for electronic device applications [1–5]. Current researches are focused on lead-free materials in view of health and environmental concerns [6–11]. Among them, the perovskite solid solutions BiMeO3 –BaTiO3 have been extensively studied due to their high Curie temperature (Tc ) and good temperature dependent dielectric behavior [12–14]. BiMeO3 compounds, where Me can be Sc3+ , Y3+ , Al3+ , (Mg1/2 Ti1/2 )3+ or (Zn1/2 Ti1/2 )3+ , etc., will effectively improve the temperature-dependent behavior taking advantage of the combinatory substitutions of Bi3+ and Me3+ in BaTiO3 [15–22]. For example, the (1 − x)BaTiO3 –xBi(Mg1/2 Ti1/2 )O3 (BT–BMT) system was reported to possess lower dielectric maximum temperature Tm with diffused characteristics as BMT ∗ Corresponding authors. Tel.: +86 27 87885811; fax: +86 27 87885811. E-mail addresses: [email protected] (H. Hao), [email protected] (H. Liu). increased, exhibiting relaxor-like behavior [23,24]. Analog to this system, BiAlO3 was thought to be a promising lead-free ferroelectric with a Curie temperature (Tc ) of 800 K [25] and a solubility limit of BiAlO3 into BaTiO3 about 0.12 [26]. Based on the preliminary results, it was confirmed that the combined substitutions of Bi3+ and Al3+ played a dominant role to decrease the Tc and increased the relaxor behavior in xBiAlO3 –(1 − x)BaTiO3 [xBA–(1 − x)BT] system [27]. Meanwhile, it was observed the dielectric constant became flatter above the maximum dielectric constant temperature (Tm ) as BiAlO3 increased, improving the temperature-stable characteristics for capacitor applications. Furthermore, it is believed that Nb and many other oxides-doped BT systems could achieve good dielectric properties for advanced X8R capacitors with improved dielectric temperature stability at the cost of dielectric constant value [28–31]. Thus it is a key technical requirement to choose Nb as dopant in order to improve the temperature stability. Undesired phases were easily appeared in xBA–(1 − x)BT synthesized by solid state method [26,27]. However, sol–gel method was an excellent technique for offering a better http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 0955-2219/© 2015 Elsevier Ltd. All rights reserved. Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model JECS-10010; No. of Pages 9 2 ARTICLE IN PRESS M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx chemical homogeneity and low-temperature processing to produce high-purity and phase-pure powders in comparison with solid state method [32–34]. In this paper, xBA–(1 − x)BT ceramics were prepared by solid-state reaction method and sol–gel method, respectively. The phase structures, dielectric properties of BA–BT with different BA contents were investigated. Moreover, Nb-modified xBA–(1 − x)BT ceramics were also studied in an attempt to achieve low temperature coefficient of capacitance over a wide temperature range. 2. Experimental procedure 2.1. Synthesis of xBA–(1 − x)BT powders by solid-state reaction method The xBA–(1 − x)BT (x = 0.1–0.3) ceramics were synthesized using Bi2 O3 (99%), Al2 O3 (99.99%), BaCO3 (99.0%), TiO2 (99.0%) as starting materials, 5 mol% excess Bi2 O3 was added to compensate the bismuth oxide volatility. They were mixed by ball milling in alcohol for 24 h. Then, the slurry was dried, and calcined at 900 ◦ C for 2 h. 2.2. Synthesis of xBA–(1 − x)BT powders by sol–gel method The key of sol–gel method was to prepare xBA–(1 − x)BT (x = 0.1–0.3) sol. Firstly, Ti(C4 H9 O)4 was dissolved in citric acid solution with the pH value of 5–6, where the molar ratio of citric acid to Ti4+ ions was 2:1. A transparent yellow organic solution (named sol I) was obtained after water bathing at 80 ◦ C for 3 h. Then, Bi(NO3 )3 ·5H2 O(99.0%), Al(NO3 )3 ·9H2 O(99.0%) and Ba(CH3 COO)2 (99.0%) were batched stoichiometrically according to the nominal compositions of xBA–(1 − x)BT and dissolved in the acetic acid respectively. Thirdly, the solutions were mixed, followed by adding citric acid, where the molar ratio of citric acid to metallic ions was 2:1. After that, ammonia solution was added to adjust the pH value of the mixed slurry to 5.5. The mixed slurry was water bathing to achieve a transparent aqueous solution (named sol II). Finally, the sol I and sol II were mixed to obtain a stable homogeneous sol(xBA–(1 − x)BT sol). After drying, the sol turned into a gel. xBA–(1 − x)BT powders were obtained by calcining the gel at 700 ◦ C for 5 h. The detail process was illustrated in Fig. 1. Fig. 1. The processing scheme of preparing xBA–(1 − x)BT sol. 2.3. Synthesis of Nb-doped 0.2BA–0.8BT powders and ceramics For Nb-doping, firstly, the 0.2BA–0.8BT powders, prepared by sol–gel, were dispersed in isopropanol by ultrasonic treatment about 30 min to obtain 0.2BA–0.8BT slurry. Nb(OH)5 was dissolved in 0.3 mol/L oxalic acid solution to produce oxalic acid of Nb, which was added to the slurry. And then the pH value of the slurry was adjusted to 5.5 with ammonia solution. The dried powders were calcined at 550 ◦ C for 2 h to burn out the organics. The calcined powders mentioned above were subsequently granulated with the polyvinyl alcohol (PVA) binder and pressed into pellets with 12 mm in diameter and 1.5 mm in thickness. The pellets were first heated at 600 ◦ C for 2 h to drive off PVA, and then sintered at temperatures between 1050 and 1200 ◦ C for 2 h to produce xBA–(1 − x)BT ceramics or Nb-doped 0.2BA–0.8BT ceramics. 2.4. Characterization The obtained gel was characterized using thermogravimetry (TG) and differential scanning calorimetry (DSC) (STA449c/3/G, NETZSCH, Germany) in air to investigate the thermal behavior of the precursor. The chemical composition of the resulting 0.2BA–0.8BT powders synthesized by sol–gel method was analyzed by inductively coupled plasma optical emission spectrometry (ICP-OES, Optima 4300DV, PerkinElmer, USA). Phase purity and structure of the ceramics were determined using XRD (PANalytical X’ Pert PRO, Eindhoven, the Netherlands) with CuK␣ radiation (λ = 1.54056 Å), operating at 40 kV and 40 mA. In addition, the microstructures of ceramics were characterized by scanning electron microscopy (SEM, JEOL JSM-5610LV). The surfaces of the ceramics were polished and painted with fire-on silver paste as electrodes for electrical measurements. Dielectric properties were measured using an LCR meter (4980A, Agilent, Santa Clara, CA) at 1 kHz, 10 kHz, and 100 kHz in the temperature range −55 to 200 ◦ C or −55 to 500 ◦ C. 3. Results and discussions 3.1. TG–DSC and XRD for 0.2BA–0.8BT powders The TG–DSC plots for 0.2BA–0.8BT powders derived from solid-state reaction method and sol–gel method were given in Fig. 2a and b, respectively. An endothermic peak and exothermic peak were showed at about 70 ◦ C and 300 ◦ C in Fig. 2a, perhaps relating to the loss of the hydration water and the evaporation of some humidity and impurities absorbed from the atmosphere during preparation process. The main mass loss occurred at around 830 ◦ C, with a sharp endothermic peak in the DSC curve, which was due to the phase transformation ␥BaCO3 → -BaCO3 and decomposition of BaCO3 [35]. Given that no weight loss was taken places at >900 ◦ C, it is reasonable to select 900 ◦ C as the calcination temperature in solid-state reaction method. Similarly, it can be seen from Fig. 2b that two stages of weight loss occurred. The first stage (below 334 ◦ C) Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model ARTICLE IN PRESS JECS-10010; No. of Pages 9 M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx 3 Fig. 2. The TG–DSC patterns of the xBA–(1 − x)BT pre-calcined powders prepared by solid-state reaction method (a) and sol–gel method (b). with a weight loss of 42.86% was consistent with the elimination of structural water and the vaporization of organic acid. The second stage (334–600 ◦ C) with a weight loss of about 32.62% and a sharp exothermic peak in the DSC curve accordingly, which may be related to the decomposition and oxidation of organic compounds. At 700 ◦ C, there was no weight loss, indicating that the powders started to crystallize and the perovskite structure can be formed at around 700 ◦ C for sol–gel method, which was a considerable decrease in the calcination temperature compared with solid-state reaction method. The X-ray diffraction patterns of 0.2BA–0.8BT powders calcined at different temperatures were used to check calcination temperature judging from TG–DSC. As seen in Fig. 3a, although the perovskite phase could be formed at temperature as low as 850 ◦ C, the crystallinity was slightly low, as indicated by the broad diffraction peaks. Instead, the sample calcined at 900 ◦ C or higher temperatures showed quite well defined diffraction peaks. Additionally, in Fig. 3b, it is easy to observe a broad peak located in the range of 25–35◦ when calcined at 600 ◦ C, as a result of incompletely crystallizing. But the perovskite phase could be observed when sample calcined at ≥700 ◦ C. Therefore, the minimum calcination temperatures of solid-state reaction method and sol–gel method were 900 ◦ C and 700 ◦ C. 3.2. Phase structure of xBA–(1 − x) BT Fig. 4a and b showed the XRD patterns of xBA–(1 − x)BT (x = 0.1–0.3) ceramics synthesized by solid-state reaction method and sol–gel method, respectively. It was observed that the samples with x = 0.1 exhibited a pure perovskite phase, while a second phase, identified as BaAl2 O4 , was detected when x > 0.1. The solubility of BiAlO3 in BaTiO3 was at about x = 0.1, in agreement with previously reported results [26]. Moreover, the split peak of the {2 0 0} diffraction gradually merged into single peak with increasing x, confirming that the sample was in tetragonal symmetry for x ≤ 0.1, transform to pseudo-cubic symmetry when x > 0.1, which was due to the smaller Al3+ ion (r = 54 pm) occupying the B-site of the Ti4+ (r = 60.5 pm) in the BT lattice, inducing a slight decrease in tolerance factor from the incorporation of BA (t = 1.016) into BT (t = 1.062), where t = 1.0571, 1.0527, and 1.0482 for x = 0.1, 0.2 and 0.3, respectively. And the decreasing tolerance factor corresponded to a lattice distortion, namely the structure transition from tetragonal into the pseudocubic phase [36]. Compared with Fig. 4a, it was obvious that the impurity peaks were much less in Fig. 3b, probably owing to the lower reaction temperature of sol–gel method helping to react easily. Actually, the finer particle size/better chemical mixing in sol–gel method accounted for improving reaction kinetics, which in turn led to a decrease in reaction temperature. Inductively coupled plasma optical emission spectroscopy (ICP-OES) testing was employed for the powders produced by sol–gel method to confirm the chemical composition of xBA–(1 − x)BT (x = 0.1–0.3) as we expected. Therefore the Bi/Al, Ba/Ti, Bi/Ba and Al/Ti molar ratios of the 0.2BA–0.8BT powders by sol–gel method, which was taken as a representative, were shown in Table 1. It was seen that the actual ratio was nearly equal to the theoretical ratio, so the sol–gel method was confirmed to produce phase-pure powders with the target chemical composition. 3.3. Density and microstructure of xBA–(1 − x) BT ceramics The densities as well as sintering temperatures of xBA–(1 − x)BT(x = 0.1–0.3) ceramics were showed in Table 2. The relative density increased with x increasing in both two methods owing to the presence of a liquid phase related to the Bi-containing compound. Notably, sol–gel method was a useful technique to obtain higher density at lower sintering temperature when comparing with solid-state reaction method. Fig. 5 showed the cross-section SEM micrographs of xBA–(1 − x)BT(x = 0.1–0.3) ceramics synthesized by solid-state reaction method and sol–gel method, respectively. All samples had spherical-like grains and rather dense microstructure, in accordance with relative density analysis. Seen from Table 2, as the BA contents increased, a significant increase in grain sizes was observed. It was because that the liquid phase made it beneficial for a faster particle dissolving and diffusion process, consequently leading to accelerated grain growth. There were a few of big oblate spheroidal grains (pointed by arrows), and the EDS result of position 2 in Fig. 5a and b both indicated that it only contained the Ba, Al and O, which were in accordance with the secondary phase BaAl2 O4 from XRD patterns. It is obvious that the secondary phase was greatly decreased in Fig. 5b, associated with the chemical uniform of the ceramics Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model ARTICLE IN PRESS JECS-10010; No. of Pages 9 4 M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx Fig. 3. X-ray diffraction patterns of the 0.2BA–0.8BT powders calcined at different temperatures; (a) solid-state reaction method, (b) and sol–gel method. Fig. 4. X-ray diffraction patterns of xBA–(1 − x)BT(x = 0.1–0.3) ceramics synthesized by solid-state reaction method (a) and sol–gel method (b). Table 1 The ICP-OES analysis of 0.2BA–0.8BT powders synthesized by sol–gel method. Element (B) W(B), wt% Bi Al Ba Ti 15.65 2.12 39.40 14.65 W(B), wt% n(B) (mol) 21.79 2.96 54.86 20.39 0.10 0.11 0.40 0.42 Ratio n(Bi):n(Al) n(Ba):n(Ti) n(Bi):n(Ba) n(Al):n(Ti) Actual ratio Theoretical ratio 0.91:1 1:1 0.95:1 1:1 0.25:1 0.25:1 0.26:1 0.25:1 Table 2 Properties for xBA–(1 − x)BT ceramics prepared by solid-state reaction method and sol–gel method. x Sintering temperature Relative density (%) Average grain size (nm) Tm (◦ C) εm (25 ◦ C) tan δ (25 ◦ C) C/C25 ◦ C ≤ ±15 (◦ C) Solid-state reaction method 0.1 0.2 0.3 1200 ◦ C-2 h 1100 ◦ C-2 h 1050 ◦ C-2 h 93.81 94.15 96.47 295 610 790 24 19 −25 3250 2303 1558 0.019 0.010 0.006 −6 to 73 −28 to 75 −55 to 124 Wet chemical method 0.1 0.2 0.3 1150 ◦ C-2 h 1050 ◦ C-2 h 1050 ◦ C-2 h 96.89 97.56 98.01 230 520 675 28 15 5 3183 1238 660 0.011 0.006 0.012 −3 to 82 −55 to 145 −55 to 440 Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model JECS-10010; No. of Pages 9 ARTICLE IN PRESS M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx 5 Fig. 5. The cross-section SEM micrographs and EDS results of xBA–(1 − x)BT ceramics synthesized by solid-state reaction method (a) and sol–gel method (b); (a1 , b1 ) x = 0.1, (a2 , b2 ) x = 0.2, (a3 , b3 ) x = 0.3; the sintering temperatures of ceramics were listed in Table 2. Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model JECS-10010; No. of Pages 9 6 ARTICLE IN PRESS M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx Fig. 6. Dielectric constant and loss as a function of temperature at frequencies from 1 kHz to 100 kHz for xBA–(1 − x)BT (a1 , b1 ) x = 0.1, (a2 , b2 ) x = 0.2, (a3 , b3 ) x = 0.3. produced by sol–gel method. Besides, the ceramics prepared by sol–gel method showed smaller grain sizes, lower porosity and more uniform grains in comparison with those by solid state reaction method, owing to the lower calcining temperature (seen from TG–DSC). 3.4. Dielectric properties of xBA–(1 − x) BT ceramics The dielectric constant and loss as a function of temperature at 1 kHz, 10 kHz, and 100 kHz for xBA–(1 − x)BT (x = 0.1–0.3) ceramics were shown in Fig. 6. As BA contents increased, the maximum dielectric constant (εm ) decreased drastically and a broad and diffuse phase transition took place in all samples, leading to smooth dielectric temperature characteristics for a relatively broad temperature range. Moreover, as seen in Fig. 6, the effect of flattening dielectric curve was enhanced in sol–gel method possibly as a result of smaller grain sizes effect. The temperature corresponding to the maximum of the diffuse phase transition (Tm ) shifted toward a lower temperature with increasing x value of the xBA–(1 − x)BT ceramics, which were consistent with the literature [26]. Dielectric properties for xBA–(1 − x) BT ceramics at 1 kHz were listed in Table 2. It is evident that the dielectric-temperature stability was improved with BA contents increasing. Besides, the ceramics prepared by sol–gel method exhibited much wider temperature range (C/C25 ◦ C ≤ ±15%) due to homogeneous grains. Of particular interest was that the 0.3BA–0.7BT ceramic by sol–gel method possessed the best dielectric property, with a moderate dielectric constant (ε = 660) and low dielectric loss (tan δ = 1.2%) at room temperature and 1 kHz, and an ultra-broad temperature range (−55 ◦ C to 440 ◦ C, C/C25 ◦ C ≤ ±15%). 3.5. Nb-doped 0.2BA–0.8BT As shown in Table 2, the temperature variation of capacitance of 0.2BA–0.8BT was within ±15% from −55 ◦ C to 145 ◦ C, which still failed to meet the requirement of X8R. Thus, Nb doping was chosen to improve the temperature Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model JECS-10010; No. of Pages 9 ARTICLE IN PRESS M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx stability. Ceramic samples with different Nb contents were prepared according to the method mentioned above. XRD patterns of 0.2BA–0.8BT–xNb (x = 0.01, 0.02, 0.03, 0.04 mol) ceramics all displayed a desired perovskite phase with little secondary phases, as shown in Fig. 7. The EDS result proved the sheet grains (position 3) only contained Ba, Bi, Ti, O and Nb, which were consistent with the speculation from XRD patterns, BaBi4 Ti4 O15 . While the secondary phase BaAl2 O4 was formed in the matrix itself, which was confirmed by the EDS result of big oblate spheroidal grains (position 2). Fig. 8 showed the cross-section SEM micrographs of 0.2BA–0.8BT–xNb ceramics. A rather dense microstructure with low porosity was detected for all samples. As showed in Table 3, the incorporation of Nb into 0.2BA–0.8BT decreased the sintering temperature and 7 Fig. 7. X-ray diffraction patterns of Nb-modified 0.2BA–0.8BT ceramic samples prepared by precipitation method. Fig. 8. The cross-section SEM micrographs and EDS results of 0.2BA–0.8BT–xNb ceramics (a) x = 0.01, (b) x = 0.02, (c) x = 0.03, (d) x = 0.04; the sintering temperatures of ceramics were listed in Table 3. Please cite this article in press as: Liu M, et al. Temperature stability of dielectric properties for xBiAlO3 –(1 − x)BaTiO3 ceramics. J Eur Ceram Soc (2015), http://dx.doi.org/10.1016/j.jeurceramsoc.2015.02.015 +Model ARTICLE IN PRESS JECS-10010; No. of Pages 9 8 M. Liu et al. / Journal of the European Ceramic Society xxx (2015) xxx–xxx Fig. 9. Dielectric constant (a) and capacitance variation as a function of temperature (b) for 0.2BA–0.8BT–xNb ceramics. Table 3 Properties for 0.2BA–0.8BT–xNb ceramics. x Sintering temperature Relative density (%) Average grain size (m) 0 0.01 0.02 0.03 0.04 1050 ◦ C-2 h 1050 ◦ C-2 h 1050 ◦ C-2 h 1030 ◦ C-2 h 1030 ◦ C-2 h 97.56 97.52 97.65 97.81 97.96 0.52 1.37 1.44 1.63 1.75 simultaneously influenced the grain growth slightly, corresponding to a denser microstructure. Table 3 showed the dielectric properties of the samples. With the increase of Nb concentration from 0 to 0.04 mol, the dielectric constant at room temperature decreased gradually from 1238 to 925, in part this may be due to secondary phase formation (Fig. 7) [37]. Fig. 9 showed the temperature dependence of dielectric constant and capacitance variation based on the capacitance at 25 ◦ C measured at 1 kHz for all samples. As Nb doping concentrations increased, the dielectric curve became more flat and the temperature stability was improved at high-temperature end, besides, all samples doped with Nb compound met the requirement of X8R. Among them, the 0.2BA–0.8BT ceramics doped with 0.04 mol Nb achieved the best dielectric property, with a moderate dielectric constant (ε = 925) and low dielectric loss(tan δ = 0.4%) at room temperature and 1 kHz, and capacitance change being on the order of ±15% over the temperature range from −55 to 178 ◦ C. 4. Conclusions xBiAlO3 –(1 − x)BaTiO3 ceramics were synthesized by solid-state reaction method and sol–gel method, respectively. The results indicated that the calcination temperature was lower in sol–gel method owing to the finer and more uniform powders. The ceramics were in tetragonal phase when x ≤ 0.1, transformed to pseudocubic at x > 0.1. With BA contents increasing, the maximum dielectric constant decreased and temperature stability of the dielectric constant was improved. The 0.3BA–0.7BT ceramic prepared by sol–gel method was found to possess a moderate dielectric constant (ε = 660) and low dielectric loss (tan δ = 1.2%) at room temperature and 1 kHz, showing flat dielectric behavior over the temperature range of −55 to 440 ◦ C. εm (25 ◦ C) 1238 1206 1122 1068 925 tan δ (25 ◦ C) C/C25 ◦ C ≤ ±15% (◦ C) 0.006 0.007 0.004 0.008 0.004 −55 to 145 −55 to 159 −55 to 167 −55 to 168 −55 to 178 Nb doped 0.2BA–0.8BT led to a more flat ε–T curve, with deteriorated dielectric constant, achieved excellent temperature stability meeting the X8R requirement. Acknowledgments This work was supported by Natural Science Foundation of China (No. 51372191, No. 51102189), the Program for New Century Excellent Talents in University (No. NCET-11-0685), International Science and Technology Cooperation Program of China (2011DFA52680), and the National Key Basic Research Program of China (973 Program) (No. 2015CB654601). References [1]. Haertling GH. 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