Synthesis & Characterization of Lead Free Piezoelectric NBT-BT Ceramics by Solid State Processing Route Method

Synthesis & Characterization of Lead Free Piezoelectric NBT-BT Ceramics by Solid State Processing Route Method A thesis submitted in partial fulfilment of the requirement For the degree of MASTER OF SCIENCE IN PHYSICS By ArchanaShubhadarshaniPadhi Roll-410ph2134 Under guidance of Prof. Pawan Kumar Department of Physics NIT Rourkela, 2008-2010 2010-2012

National Institute Of Technology, Rourkela CERTIFICATE This is to certify that the thesis entitled Synthesis& Characterization of Lead Free NBT-BT Ceramics by Solid state Processing Route Method submitted by Miss ArchanaShubhadarshaniPadhi in partial fulfilment for the requirement for the award of degree of Master of Science degree in Physics at National Institute of Technology, Rourkela is an authentic work carried out by her under my supervision and guidance in Electro ceramic Lab of Department of Physics. To the best of my knowledge, the matter embodied in the thesis has not been submitted to any other University/Institute for the award of any degree or Diploma. Date: Prof. Pawan Kumar Dept. of Physics National Institute of Technology, Rourkela

ACKNOWLEDGEMENT On the submission of my thesis report titled Synthesis& Characterization of Lead Free sodium bismuth titanate-barium titanate Piezoelectric Ceramics by Solid State Processing Route Method I would like to acknowledge and extend my heartfelt gratitude to my guide Dr. PAWAN KUMAR for his vital encouragement and support. I was privileged to experience a sustained enthusiastic and involved interest from his side. This fuelled my enthusiasm even further and encouraged me to boldly step into a project which was a totally new and unexplored topic for me. I am indebted to him for having helped me, shape the problem and providing insights towards the solution. I also thanks to all PhD and M.Tech Research scholars for assisting the collection of my project topics and help while doing project work. I would also like to thank the ELECTROCERAMIC lab members and the National Institute Of Technology, Rourkela, in general, for extending a helping hand and liberal co-operation whenever needed. Date: M.Sc. Physics, NIT Rourkela ArchanaShubhadarshaniPadhi Roll.No-410PH2134

ABSTRACT This project deals with the preparation of Lead-free piezoelectric ceramics (1-x) Na 0.5 Bi 0.5 TiO 3 -xbatio 3 that has prepared by solid state processing route method for three different composition of NBT-BT in which the x has values 0.07, 0.06, and 0.05.These ceramics exhibits a strong piezoelectric property at MPB and an optimum dielectric property due to the addition of BaTiO₃ into Na.₅Bi.₅TiO₃.The phases of the material of different composition can be known by X-Ray Diffraction analysis. The dielectric measurement can be carried out for different composition. The samples are poled at a voltage 3-4 KV where the piezoelectric measurement were carried out. Scanning Electron Microscope is used for micro-structural characterization. The P-E loop shows that the remnant polarization is high at room temperature for NBT.

CONTENTS CHAPTER 1 1.1 Introduction 1.1.1 Sodium Bismuth Titanate (NBT) 1.1.2 Structure of NBT 1.1.3 Doping in NBT System CHAPTER 2 2.1 Experimental Procedure 2.1.1 Precursors 2.1.2 Mixing and Milling 2.1.3 Calcination 2.1.4 Binder Addition 2.1.5 Shaping 2.1.6 Sintering CHAPTER 3 3.1 Characterization Techniques for BCT and BLT systems 3.1.1 X-Ray Diffraction 3.1.2 Density Measurements 3.1.3 Scanning Electron Microscopy 3.1.4 Dielectric Property 3.1.4.1 Dielectric Constant measurement 3.1.4.2 Dielectric loss 3.1.5 P-E Hysteresis loop CHAPTER 4 4.1 Results and Discussion 4.2 Conclusions References

CHAPTER-1 1. INTRODUCTION The word piezoelectricity means electricity produced by pressure. Piezo, it is a Greek word which means to squeeze or press. Piezoelectricity is the ability of some materials (crystals and certain ceramics) to generate an electric field or electric potential in response to applied mechanical stress [1]. The effect is closely related to a change of polarization density within the material's volume. A voltage will induced due to applied stress across the material if the material is not short-circuited. The piezoelectric effect is reversible in that materials exhibiting the direct piezoelectric effect (the production of an electric potential when stress is applied) also exhibit the reverse piezoelectric effect (the production of stress or strain when an electric field is applied). For example, lead zirconate titanate crystals will exhibit a maximum shape change of about 0.1% of the original dimension. Production and detection of sound, generation of high voltage, ultrafine focussing of optical assemblies, microbalances and electronic frequency generation all these applications is based on the piezoelectric effect. It is also basis of many scientific instrumental techniques with atomic resolution like scanning probe microscopies such as AFM, STM, MTA, SNOM etc. It is also acting as ignition source for the cigarette lighters.. Lead-based piezoelectric ceramics with perovskite structure based on lead zirconatetitanate (PZT) are widely used in actuators, sensors as well as microelectronic devices because of their high piezoelectric properties and low transition temperature. But, the lead-based devices were high toxic in nature. Because of high toxic nature of these devices, it causes serious environmental problem and lead pollution. To avoid the toxicity in the lead-containing device there has been compositional development of lead-free piezoelectric materials.

Among all lead-free piezoelectric materials NBT is one of them about which I will go to discuss in this paper. 1.1 SODIUM BISMUTH TITANATE: People attempted to reduce the size of all communicative devices as small as and as light as possible for which high dielectric constant ceramic materials is important. As NBT is a dielectric material with high temperature dielectric constant and lead-free, so it is widely used now a day. The Bi3+ and Na+ of Na₀.₅Bi₀.₅TiOз (NBT) have standard effective charge of +1 and -1 respectively of (NBT) on A-site of the ABOз perovskite structure which is a ferroelectric complex with rhombohedral symmetry [2]. Because the average effective charge on A-site is 2+. It has a large remnant polarisation at room temperature. So it is considered as one of a good candidate for lead-free piezoelectric ceramic [3]. NBT ceramic usually exhibits high dielectric loss, weak piezoelectric properties, high coercive field and difficult to polarise. Due to high coercive field the poling of the ceramic is difficult [4]. To improve the piezoelectric properties of the material doping of some materials are used like NBT-BaTiOз, NBT- Bi 0.5 K 0.5 TiO 3 [5, 6], NBT-SrTiOз, NBT-BiFeOз, NBT-PbTiOз and NBT-NaNbOз [7]. In my report the piezoelectric properties of NBT-BaTiOз (NBT-BT) is frequently reported as NBT is noted as classical based system [8-10]. The electrical properties of NBT-BT is temperature dependent, so the temperature dependence of electrical property and depolarisation temperature has been discussed in my report.in my work, (1-x) Na₀.₅Bi₀.₅TiOз-x BaTiOз piezoelectric ceramics are synthesised by convectional solid state processing method and characterised. Their structures, densification properties, electrical properties and optical properties are discussed systematically.

1.2 STRUCTURE OF SODIUM BISMUTH TITANATE: The structure of sodium bismuth titanate is like the ABO₃ distorted perovskite with rhombohedral R3c structure at room temperature [11]. In standard form NBT can be represented as (Na₀.₅Bi₀.₅)TiO₃. An ABO₃ perovskite structure can be represented in two ways. In first way the sodium (Na+) and bismuth (Bi 3+ ) cations are in the corner of the cubic unit cell, the oxygen (O²ˉ) cations are occupying in the face centre and the Titanium (Ti⁴+) cation occupies the centre of oxygen octahedral that is formed. In the second way, the TiO₆ octahedra is at the centre of the cube which shares the 8-corners of the cube formed by the octahedral with sodium and bismuth cations in three-dimension [12]. -O²ˉ Oxygen -B⁴+ -A²+ Figure.1- Perovskite structure of cubic NBT

Figure-1 shows the typical ABO₃ perovskite structure of cubic NBT system. In order to show the stoichiometry present in the ideal mixed system, the sodium and bismuth cations are ordered on A-site of the structure which is shown in the figure. But the real material does not exhibit long range ordering which is discussed later in text. 1.3 Doping in Sodium Bismuth Titanate: To increase the electrical and structural properties of NBT ceramic materials it is subjected to doping. How the dopants affect the electrical and structural properties of material that can be determined by performing many studies on NBT. Some studies focus on dielectric properties, some on electrical properties and some others on piezoelectric properties of the material. In ABO₃ perovskite structure both the A-site and B-site dopant have been studied to determine they affect different properties of NBT material. Ba, Zr, Bi, La, Sr, K are examples of some dopant which affects different properties of NBT ceramics [13-17].

2.1 Experimental procedure: CHAPTER-2 The composite NBT-BT having general formula (1-x) Na0.5Bi0.5TiO3 - xbatio 3 (x=0.07, 0.06, 0.05) were synthesized through solid state reaction synthesis route. The preparation and characterization of the sample follows the following sequences Figure-2: Flow Chart for the Preparation of Na 0.5 Bi 0.5 TiO 3 - BaTiO 3 Na 2 CO 3 + Bi 2 O 3 + TiO 2 + BaCO 3 Mixing and grinding g Drying and calcination Grinding powder XRD ANALYSIS OF CALCINED POWDER Binder addition Preparation of pallets Sintering at 1150 0 C SEM ANALYSIS OF SINTERED SAMLE Electroding P-E HYSTERESIS LOOP Dielectric measurement

Preparation of NBT-BT Samples: 1. for 10 gms of 0.93NBT- 0.07BT Sample- Na 2 Co 3 = 1.37029 Bi 2 O 3 = 6.02415 TiO 2 = 2.2214 BaCO 3 = 0.38408 2. for 10 gms of 0.94 NBT- 0.06 BT sample- Na 2 Co 3 = 1.3816 Bi 2 O 3 = 6.07454 TiO 2 = 2.2162 BaCO 3 = 0.3287 3. for 10 gms of 0.95 NBT- 0.05 BT sample- Na 2 Co 3 = 1.3932 Bi 2 O 3 = 6.1237 TiO 2 = 2.2107 BaCO 3 = 0.11052 By adding all these compounds and mixing with acetone by following the above procedure we got the desired composition.

2.1.1 Raw Materials used for synthesis of NBT-BT: 1) Sodium carbonate (Na 2 CO 3 ) 2) Bismuth oxide (Bi 2 O 3 ) Titanium dioxide (TiO 2 ) Barium carbonate (BaCO 3 ) 2.1.2 Mixing and Ball Milling of Raw Materials: For powder preparation bismuth oxide (Bi 2 O 3 ) powder, sodium carbonate (Na 2 CO 3 ) powder, titanium dioxide (TiO 2 ) powder, barium carbonate (BaCO 3 ) powders were mixed together in an agate mortar after weighing stochiometrically. After mixing in dry condition acetone was added and mixed and again grinding was done and leaves it till it became dry. Then this mixture in acetone solution was subjected to ball milling for 6 hr maintained the powder to ball ratio at 1:4. The ball milling was done for the homogenous mixing of powder and to reduce the particle size. Then the powder was dried and grinding has been done for homogenous mixing. 2.1.3 Calcination of powder: The dried and mixed powders were calcined at a temperature of 1000 0 C for 2 hr. in an alumina crucible by an indigenous programmable furnace. Calcination is used to know about the phase formation and reaction mechanism of sample. T hen the calcined powders were grinded in the agate motor to avoid agglomerizetion of the particle. The density and the electromechanical properties of the product have been influenced by the calcined temperature. The solid phase reaction takes place between the constituents during calcinations. 2.1.4 Binder Addition: Binder is generally used to give mechanical support to the particles of the sample. In my sample poly vinyl alcohol (PVA) is used as binder. Here 2wt% PVA was mixed in

the sample and then left it for dry. Since PVA is an organic binder so it can be vaporized during sintering. 2.1.5 Shaping: After drying it was grinded in an agate mortar to produce fine powder. Now compositions of powder were separately packed after being weighed (around 0.4 gms). By uniaxial compaction with load of 6 ton the powder was pressed into pellets 2.1.6 Sintering of pellets: The compacted pellets were sintered in an indigenous programmable conventional furnace at 1150 0 C for 2 hours at rate 5 o C the heating per minute and then cooled in the furnace. In the sintering processes the densification or reduction in the porosity of the body and joining of the particles occur due to atomic diffusion. The driving force for the solid state sintering process is the reduction in the surface energy which accomplishes by the atomic diffusion process that leads to densification of the body. 2.1.7 Electroding: A layer of metallic silver paste with thinner liquid has been applied to the sintered pallets of (1-x) Na 0.5 Bi 0.5 TiO 3 -xbatio 3 for silver coating. Before silver coating the pallets should be polished by the emery paper. The silver paste is used in the pallet as it adheres strongly to the ceramic sample. But it should be zero resistance and very thin.

CHAPTER-3 3.1 Characterisation of NBT-BT SYSTEM: 3.1.1 XRD (X-RAY DIFFRACTION) ANALYSIS- The calcined powders of different composition were subjected to x-ray diffraction using Philips Analytical XRD machine to know the phase analysis and crystal structure of the sample. In XRD, when a beam of x-ray strikes an array of electrons then each electron scatters some radiation in all direction. The radiation scattered by adjacent electrons are not in phase. So the beams are in phase when reinforcement occurs and a diffracted beam is observed. The diffraction beam sometimes behaves as if it were reflected from the electron layer. The diffracted beam is called as reflection as a small portion of incident radiation is reflected and the angle between the beam and the plane which is called as Bragg angle. The x-ray diffraction depends on Bragg s law i.e. 2dsinƟ = n λ. The angle range was from 20 0 to 80 0. 3.1.2 Density measurement- The density of the sintered sample can be measured by Archimedes principle. First the dry weight of the sample should be measured in the weighing machine. Then the soak weight and suspended weight were measured by using kerosene oil. During the soak weight measurement all the samples were soaked in water by evacuating the chamber so that all the bubbles of the sample come out. By using suspension arrangements suspended weight can be calculated. The densities and apparent porosities of the pallets can be calculated by formula: Density (ρ) = Dry Wight Soaked weight suspended weight

Apparent porosity = Soaked weight Dry weight Soaked weight suspended weight 3.1.3 SEM (Scanning Electron Microscope): The sintered pallets were taken for micro structural analysis by SEM. In present work Jeol T-330 Scanning Electron Microscope has been used. Before SEM, platinum coating of 20 m was done for 0 seconds by JEOL JFC- 1600 auto fine coater. sthis analysis helps us to know the microstructure of the sintered pallets. It was also analyzed the topographies of specimens at high magnifications. SEM magnification can exceed 300,000. In SEM, a beam of electrons i.e. the primary electrons is focused on a spot volume of the specimen and transfer energy to the spot. Dislodge electrons called as secondary electrons are attracted by the positively biased grid or detector then translated into a signal. The electron beam is swept across an area being scanned produces many signals which are further amplified, analyzed and translate into image of topography. On the CRT (cathode ray tube) the final image has been seen. 3.1.4 Dielectric Property: 3.1.4.1 Dielectric Constant Measurement- Dielectric materials are insulator at room temperature when field is applied then charge separation occurs and molecules are get polarised. But the ferroelectric ceramics are dielectric whose electrons are bound to the nucleus by strong forces and hence they are not free under the influence of an external field. The molecules may be behaves as nuclei of positive charge +q surrounded by the electron cloud of negative charge q. In the absence of an applied field the centres of gravity of the positive and

negative charge distributions coincide, but when an external electric field is applied then the positive and negative charges experience electric forces tending to move them apart in the field direction. Now the centres of positive and negative charge no longer coincide with each other and molecules are said to be polarised.. Each molecule forms a dipole having moment µ which can be represented as µ = q dx, where dx is distance between the two centres of the charges and is a vector pointing from the negative to the positive charges. In ferroelectric materials spontaneous polarization can exist even in the absence of an applied electric field. Thus ferroelectric can be used as a capacitor. Generally ferroelectric ceramics have higher dielectric constants. It can be calculated from the capacitance values which have already been measured. Formula for dielectric constant measurement: C =ε 0 A /d when the medium is air C = K ε 0 A /d for any medium Where, C = capacitance of the sample ε 0 = permittivity of free space K = dielectric constant of material A = area of the electrode d = thickness of the pallet In present work the dielectric measurement were done by the instrument HIOKI 3532-50LCR HiTester. By plotting temperature on x-axis and dielectric constant on y- axis the temperature vs. Dielectric graph was obtained.

3.1.4.2 Dielectric loss: When a dielectric material is subjected to an alternating field the orientation of the dipole changes and hence the polarization will tend to reverse every time the polarity of the field changes. As long as the frequency remains low (<10 6 c/sec), the polarization follows the alternations of the field without any significant lag and the permittivity is independent of frequency and has the same magnitude as in a static field. When the frequency is increased the dipoles will no longer be able to rotate sufficiently so that their oscillations will begin to lag behind those of the field. As the frequency is further increased and if the permanent dipoles present in the medium, then they will be completely unable to follow the field and the contribution to the static permittivity from this molecular process i.e. orientation polarization ceases. This usually occurs in the ratio frequency range (10 6 10 11 Hz) of the electromagnetic spectrum. At still higher frequencies, usually in the infra-red (10 11 10 14 Hz) the relatively heavy positive and negative ions cannot follow the field variation so that the contribution to the permittivity from the atomic or ionic polarization ceases and only the electronic polarization remains. The above effects lead to fall in the permittivity of a dielectric material with increasing frequency. When the period of the applied voltage is much larger than the relaxation time of a polarization process, polarization is essentially complete at any instant during each cycle. The charging current is 90 degree advance in relation to the voltage so that no electrical energy is lost during charging. When the period of the applied voltage is much shorter than the relaxation time for a polarization process, then there will no polarization at all. Here again, the charging current is 90 degree advanced of the applied voltage. When the period is in the same range as the relaxation time, resonance occurs. At resonance, current leads the voltage by (90-δ) where δ is loss angle and tan δ is a measure of the electrical loss due to resonance. At lower frequencies the electrical energy loss is due to d.c. resistivity, but at higher frequencies the electrical loss is mostly due to dipole rotations or due to ionic transitions from the lower energy states. The energy is absorbed because of the upward transition from the applied field. The losses which

fall on the infrared region are referred to as infra-red absorption and in the optical region are known as optical absorption. With alternating voltage, the charge stored on a dielectric has both real (in phase) and imaginary (out of phase) components, caused by either resistive leakage or dielectric absorption. The loss is expressed by the ratio of out of phase component to the in phase component. This is D, the dissipation factor of the dielectric loss, also frequently called loss tangent tan δ. It is measured directly using HIOKI 3532-50LCR Hi tester. 3.1.5 P-E Hysteresis loop Ferroelectric crystal possesses regions with uniform polarization called ferroelectric domain where all the electric dipoles are aligned in the same direction. There may be many domains in a crystal separated by interfaces called domain walls. A ferroelectric single crystal, when grown has multiple ferroelectric domains. A single domain can be obtained by domain wall motion made possible by the application of an appropriate electric field. A very strong field could lead to the reversal of the polarization in the domain, known as domain switching [18, 19]. The direction of the spontaneous polarization in ferroelectrics can be switched by an applied electric field. The reversal can be observed as ferroelectric hysteresis. As the electric field strength is increased, the domain starts to align in the field direction giving rise to a rapid increase in the polarization (OB) as shown in Fig. 3. At very high field levels, the polarization reaches a saturation value (P sat ).The polarization does not fall to zero when the external field is removed. At zero external fields, some of the domain remains aligned in the positive direction, hence the crystal will show a remnant polarization P r. The crystal cannot be completely depolarized until a field of magnitude OF is applied in the negative direction. A field is said to be coercive field strength E c,, when the field needed to reduce the polarization to zero. If the field is increased to a more negative value, then it flips the direction of polarisation and hence a hysteresis loop is obtained. The value of the spontaneous polarization P s (OE) is obtained by extrapolating the curve onto the polarization axes (CE). Hysteresis loops of ferroelectric material were obtained by using Sawyer- Tower circuit. It is a practical circuit to characterize the ferroelectrics and study

fundamental phenomenon such as spontaneous polarization, coercive field and remnant polarisation mechanisms [20] Fig.3 Polarization vs. Electric Field (P-E) hysteresis loop for a typical ferroelectric crystal.

intensity (a.u.) CHAPTER 4 4.1 RESULTS AND DISCUSSIONS: 4.1.2 Structure analysis from XRD peaks- 95 96 97 20 30 40 50 60 70 80 Angle (2 ) Fig-4 XRD peaks ofna 0.5 Bi 0.5 TiO 3 -BaTiO 3 (x=0.07, 0.06, 0.05) Calcined at 1000 0 C for 2hrs.

Fig.4 shows the XRD patterns of thena 0.5 Bi 0.5 TiO 3 -BaTiO 3 (x=0.07, 0.06, 0.05) sample prepared by convectional solid state synthesis route calcined at 1000 0 C for 2hrs. The XRD patterns confirm the single perovskite phase formation and also show that the sample does not contain any impurity or secondary phase. If the BaTIO 3 content is higher then there were no impurity phase and also the peaks were got broaden. Table- 1 represents the type of structures corresponding to different compositions of NBT- BT samples. Table.1 structures of 1-x(Na 0.5 Bi 0. 5)TiO3-x(BaTiO 3 ) where(x = 0.05, 0.06,0.07) SYSTEM 0.95(Na 0.5 Bi 0. 5)TiO3-0.05(BaTiO 3 ) 0.94(Na 0.5 Bi 0.5 TiO 3 )-0.06(BaTiO 3 ) 0.93(Na 0.5 Bi 0.5 TiO 3 )-0.07(BaTiO 3 ) STUCTURE Rhombohedral Rhombohedral Tetragonal From XRD analysis we found there was existence of MPB. Pure NBT forms rhombohedral structure whereas BaTiO 3 forms tetragonal structure. So there will be existence of MPB. In solid solution of NBT-BT when x < 0.06, then XRD peak shows the rhombohedral structure but when x >= 0.10 then the phase structure will tetragonal. So the MPB of rhombohedral phase and tetragonal phase resides at 0.06 < x < 0.10. So from XRD analysis it is observed that the (202) peak of (1-x) NBT-x BT ceramics has been splits into (002) and (200) peaks [21, 22, 23]

4.1.3 Density measurements: Densities and apparent porosity of the sintered sample1-x (Na 0.5 Bi 0.5 ) TiO3-x (BaTiO 3 ) for (x = 0.05, 0.06, 0.07) by convectional solid route method were measured using Archimedes principle. The values are as shown in the given table-2: sintered density in g/cm 3 Apparent Porosity samples (Conventional) (Conventional) 0.95(Na 0.5 Bi 0. 5)TiO3-0.05(BaTiO 3 ) 0.94(Na 0.5 Bi 0. 5)TiO3-0.06(BaTiO 3 ) 5.7763 0.001477 5.7992 0.001562 0.93(Na 0.5 Bi 0. 5)TiO3-0.07(BaTiO 3 ) 5.8519 0.001468 Table.2 density measurement of 1-x(Na 0.5 Bi 0. 5)TiO3-x(BaTiO 3 ) where(x = 0.05, 0.06,0.07)

4.1.3 SEM Analysis of NBT-BT Samples: The SEM images of different compositions of NBT-BT system is as shown in the figures. a 0.93 NBT 0.07 BT

b c 0.94 NBT- 0.06 BT 0.95 NBT 0.05 BT Fig-5 shows the SEM images of different composition of NBT-BT. Figure (a), (b), (c) show the SEM image of the sintered sample of solid solution of NBT with BT. It also helps to determine the grain size the sample. Table-3 shows grain size for different composition of NBT-BT. SYSTEM GRAIN SIZE 0.95(Na 0.5 Bi 0.5 )TiO3-0.05(BaTiO 3 ) 0.975 µm 0.95(Na 0.5 Bi 0.5 )TiO3-0.05(BaTiO 3 ) 1.882 µm 0.95(Na 0.5 Bi 0.5 )TiO3-0.05(BaTiO 3 ) 2.506 µm Table.2 grain size measurement of 1-x(Na 0.5 Bi 0. 5)TiO3-x(BaTiO 3 ) where(x = 0.05, 0.06,0.07)

4.1.4 Polarization Mechanisms: 20 15 P r -8.378 C/cm 2 E c -11.3535kV/cm 10 Polarisation in C/cm 2 5 0-5 -10-15 -20-30 -20-10 0 10 20 30 Electric field in kv/cm Fig-6(a) P-E Loop for 0.94NBT-0.06BT

Polarisation in C/cm 2 Polarisation in C/cm 2 10 P r -6.1125 C/cm 2 E c -14.6266kV/cm 5 0-5 -10-30 -20-10 0 10 20 Electric field in kv/cm Fig-6(b) P-E Loop 0.95NBT-0.05BT 20 15 P r -7.7685 C/cm 2 E C -11.3548 Kv/CM 10 5 0-5 -10-15 -20-30 -20-10 0 10 20 Electric field in kv/cm Fig-6(c) P-E Loop for 0.93NBT-0.07BT Fig.6 Hysteresis loops of 1-x(Na 0.5 Bi 0. 5)TiO3-x(BaTiO 3 ) where(x = 0.05, 0.06, 0.07)

Dielectric constant In the absence of electric field the dipoles are randomly oriented, but when field is applied the orientation of the domains increases along the field direction which leads to the poling of sample. Before dielectric constant measurement the poling should be done. Polarization mechanism studies the spontaneous polarization P s, coercive field E c and remnant polarization P r which decreases with increase in concentration in BT as observed from the above Fig. 4.1.5 Dielectric Measurements: Dielectric constant & dielectric loss vs. Temperature graph is measured by HIOKI LCR 3532-50 Hi Tester for the 1-x (Na 0.5 Bi 0.5 )TiO 3 x (BaTiO 3 ) for ( x = 0.05, 0.06, 0.07) systems synthesized by conventional solid routeprocessing. Dielectric constant and dielectric loss vs. temperature of some of the samples of the NBT-BT systems are shown in Figs 7& 8: 5500 1kHz 5000 10kHz 100kHz 4500 1MHz 4000 3500 3000 2500 2000 1500 1000 500 0-500 50 100 150 200 250 300 350 400 450 Temperature( O C) Fig7 (a)-dielectric constant vs. Temperature for 0.95NBT 0.05BT system

Dielectric constant Dielectric constant 6000 5500 5000 4500 1kHz 10kHz 100kHz 1MHz 4000 3500 3000 2500 2000 1500 1000 500 0 50 100 150 200 250 300 350 400 450 Temperature( O C) Fig-7 (b) dielectric constant vs. Temperature for 0.94NBT 0.06BT system 6000 5500 5000 1kHz 10kHz 100kHz 1MHz 4500 4000 3500 3000 2500 2000 1500 50 100 150 200 250 300 350 400 450 Temperature( O C) Fig-7(c) dielectric constant vs. Temperature for 0.93NBT 0.07BT system

tan tan Figures for Dielectric loss vs. Temperature for different NBT-BT system: 6 5 1kHz 10kHz 100kHz 1MHz 4 3 2 1 0 50 100 150 200 250 300 350 400 450 Temperature( O C) 5.5 5.0 4.5 4.0 1kHz 10kHz 100kHz 1MHz 3.5 3.0 2.5 2.0 1.5 1.0 0.5 0.0-0.5 50 100 150 200 250 300 350 400 450 Temperature( O C) Fig-8(b) dielectric loss vs. Temperature for 0.94NBT 0.06BT system

tan 1.2 1.0 0.8 0.6 0.4 1kHz 10kHz 100kHz 1MHz 0.2 0.0 50 100 150 200 250 300 350 400 450 Temperature( O C) Fig-8(c) dielectric loss vs. Temperature for 0.93NBT 0.07BT system Dielectric constant increases with temperature but decreases with frequency. The decrease or fall in the dielectric constant value isdue to the fact that polarization does not occur instantaneously with the application of the external electric field, which is further due to the inertia of the dipoles and the delay in response towards the alternating electric field leads to dielectric loss and decline in the dielectric constant value. At lower frequencies ε r is maximum because the contributions from the space charge polarization is large.

CONCLUSION 1-x(Na 0.5 Bi 0.5 )TiO3 x(batio 3 ) where (x=0.05,0.06,0.07) ceramics were synthesized by convectional solid state processing route method. For different compositions of NBT-BT XRD, analysis has done at a calcined temperature 1000 0 C for 2 hrs. It is concluded from XRD analysis that there were no impurity phases in the system with tetragonal structure. The density and porosity of sintered sample has been determined by using Archimedes principle. The density of NBT-BT system increases with increase in the BT content which was observed by density measurement. Grain size of samples also decreases with increase in BT content which was observed during SEM analysis. The piezoelectric property of the material increases with increase in BT concentration. But the dielectric loss factor (tanδ) decreases with increase in the BT concentration. Dielectric constant increases with increase in temperature but decreases with frequency.

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