The Piezoelectric Effect in Ceramics

Jaffe, Bernard

doi:10.1016/b978-0-12-379550-2.50006-5

Cited by 801 publications

(1,200 citation statements)

References 16 publications

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“…This negative thermal expansion is, therefore, a unique characteristic of the FE RH phase, which has been confirmed to exist for other zirconia-rich compositions (without Nb modifications). 1 In addition, the thermally stable phase range for the FE RH phase in the PSZT (~97°C) is considerably smaller than the PZT95/5(1.8Nb) (~183°C); and the negative CTE for PSZT (-5.112 X 10 -6 /°C) in this phase region is greater than observed for PZT95/5(1.8Nb) ceramics (-3.345 X 10 -6 /°C). This suggests that the change of spontaneous polarization with respect to temperature in the PSZT could be greater than that in PZT95/5(1.8Nb) ceramics in the FE RH region.…”

Section: Resultsmentioning

confidence: 94%

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Thermal properties of PZT95/5(1.8Nb) and PSZT ceramics.

Rae¹,

Corelis²,

Yang³

et al. 2006

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Thermal properties of niobium-modified PZT95/5(1.8Nb) and PSZT ceramics used for the ferroelectric power supply have been studied from -100 °C to 375°C. Within this temperature range, these materials exhibit ferroelectric-ferroelectric and ferroelectric-paraelectric phase transformations. The thermal expansion coefficient, heat capacity, and thermal diffusivity of different phases were measured. Thermal conductivity and Grüneisen constant were calculated at several selected temperatures between -60°C and 100°C. Results show that thermal properties of these two solid solutions are very similar. Phase transformations in these ceramics possess first order transformation characteristics including thermal hysteresis, transformational strain, and enthalpy change. The thermal strain in the high temperature rhombohedral phase region is extremely anisotropic. The heat capacity for both materials approaches to 3R (or 5.938 cal/(g-mole*K)) near room temperature. The thermal diffusivity and the thermal conductivity are quite low in comparison to common oxide ceramics, and are comparable to amorphous silicate glass. Furthermore, the thermal conductivity of these materials between -60°C and 100°C becomes independent of temperature and is sensitive to the structural phase transformation. These phenomena suggest that the phonon mean free path governing the thermal conductivity in this temperature range is limited by the lattice dimensions, which is in good agreement with calculated values. Effects of small compositional changes and density/porosity variations in these ceramics on their thermal properties are also discussed. The implications of these transformation characteristics and unusual thermal properties are important in guiding processing and handling procedures for these materials.

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Section: Resultsmentioning

confidence: 94%

“…1 1 near the phase boundary between FE and antiferroelectric (AFE) phases. Above the Curie temperature, the paraelectric phase (PE) for both compositions has the ideal cubic perovskite (Pm3m) structure.…”

Section: Introductionmentioning

confidence: 99%

Thermal properties of PZT95/5(1.8Nb) and PSZT ceramics.

Rae¹,

Corelis²,

Yang³

et al. 2006

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“…This might be the result of a slight decrease of the Curie temperature. In fact all these experimental results can be explained by the assumption that the presence of the dopants gives rise to A vacancies into the PZT lattice with the direct consequence of rising the dielectric constant, the piezoelectric coupling factor and the charge constant 15 . This is consistent with the ionic 16 , where the piezoelectric properties are subsequently enhanced because of the increased easy of reorientation during poling 17 .…”

Section: Resultsmentioning

confidence: 99%

Effect of iron and nickel substitution on the piezoelectric properties of PZT type ceramics

Tănăsoiu

Miclea

Amarande

et al. 2005

Journal of the European Ceramic Society

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The effect of Fe and Ni doping on piezoelectric properties of a soft type piezoelectric material was investigated. The materials composition was as follows: Pb 0.95 Bi 0.03 Nb 0.02 Zr 0.51 Ti 0.49-x M x O 3 , where M stands for the transitional metals Fe or Ni and x=0; 0.02; 0.04; 0.06; 0.08; 0.10. The materials were prepared by the conventional ceramic technique, using high purity oxides, mixed in a planetary ball mill for 3 hours and double calcined at 850 o C and 900 o C for 2 hours, with an intermediate milling of 4 hours and a final milling of 48 hours in order to get a final powder with crystallites in the nanometric range. X-ray diffractograms showed that compounds were completely formed and they were situated in the nanometric range with an average crystallite size of about 95 nm. The pressed and sintered samples of these materials showed maximum densification of about 98.5 % of TD at an optimum sintering temperature of 1200 o C for both types of materials. The optimum amounts of doping for both types of transitional elements were situated somewhere around x=0.06 with better results for nickel doped samples. Thus the maximum density for 0.06 nickel doped material was 7.87 g/cm 3 while for iron doped one it was only 7.80 g/cm 3 . The piezoelectric properties followed consequently the same trend. Thus the electromechanical coupling factor k p for 0.06 nickel doped samples was 0.665 while for the correspondingly iron doped ones it was 0.638. The relative dielectric constant was about 4050 for nickel doped samples and 3400 for iron doped ones. The corresponding values for the charge constant d 33 were 625 pm/V and 530 pm/V respectively. These results were discussed in terms of the positions occupied by Ni and Fe into the lattice, the type of vacancies created by this and the shift of the morphotropic phase boundary.

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“…Acceptor dopants at the B-site can induce oxygen vacancies in the lattice to maintain charge neutrality 1 …”

Section: Introductionmentioning

confidence: 99%

Evolution of dielectric and ferroelectric relaxor states in Al3+-doped BaTiO3

Vani

Kumar

2015

AIP Advances

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In ferroelectric BaTiO3, we report the evolution of the Dielectric Relaxor and Ferroelectric Relaxor states as a function of B-site doped Al3+ concentration. The relaxor states occur after the paraelectric-ferroelectric phase transition upon cooling. Two different mechanisms are proposed; one based on migration of oxygen vacancies for symmetry-confirmation and the other based on disruption of long-range ferroelectric order by high concentrations of Al3+ ions at the B-site.

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The Piezoelectric Effect in Ceramics

Cited by 801 publications

References 16 publications

Thermal properties of PZT95/5(1.8Nb) and PSZT ceramics.

Thermal properties of PZT95/5(1.8Nb) and PSZT ceramics.

Effect of iron and nickel substitution on the piezoelectric properties of PZT type ceramics

Evolution of dielectric and ferroelectric relaxor states in Al3+-doped BaTiO3

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