Open Access

Ferroelectric and magnetic properties of Nd-doped Bi4 − xFeTi3O12 nanoparticles prepared through the egg-white method

  • Khalid Mujasam Batoo1Email author,
  • Joselito Puzan Labis1,
  • Ritu Sharma2 and
  • Mahavir Singh2
Nanoscale Research Letters20127:511

DOI: 10.1186/1556-276X-7-511

Received: 25 May 2012

Accepted: 18 August 2012

Published: 18 September 2012

Abstract

Multiferroic behavior of Bi4 − xNd x FeTi3O12 (0.0 ≤ × ≤ 0.25, × = 0.05) ceramic nanoparticles prepared through the egg-white method was investigated. The dielectric properties of the samples show normal behavior and are explained in the light of space charge polarization. Room temperature polarization-electric field (P-E) curves show that the samples are not saturated with maximum remanence polarization, Pr= 0.110 μC/cm2, and a relatively low coercive field, Ec = of 7.918 kV/cm, at an applied field of 1 kV/cm was observed for 5% Nd doping. The room temperature M-H hysteresis curve shows that the samples exhibit intrinsic antiferromagnetism with a weak ferromagnetism. These properties entitle the grown nanoparticles of BNFT as one of the few multiferroic materials that exhibit decent magnetization and electric polarization.

Keywords

Nanoparticles Multiferroic Dielectric constant dc magnetization

Background

Recently, there has been an extensive study in the direction of search for the materials possessing magnetic as well as the ferroelectric properties because of the richness of physics involved in the system as well as their potential applications in memory devices and functional sensors [16]. These materials exhibit phenomena such as the control of electrical polarization by the application of an external magnetic field or vice versa, providing an additional degree of freedom for the design of new devices. Materials can be considered as multiferroic where ferroelectricity and ferromagnetism make mutually exclusive group [3] with the interaction of electric and magnetoelectric effects [4, 7] and the effect of mutual influence of the polarization and magnetization. These phenomena are of practical interest for microelectronics, magnetic memories, sensors, and nonvolatile ferroelectric random access memory applications [3, 8, 9]. In order to be used as microelectronics and sensor techniques, magnetoelectric materials should satisfy this criterion: the magnetic and electric ordering temperature must exceed the room temperature. However, up to now, multiferroic materials for room temperature applications are very few [10]. Taking into account the recent literature, most of the published articles are referring to perovskite structures as potential multiferroics [3, 11]. However, only BiFeO3 has proved multiferroic properties at room temperature [7, 12], and its complex properties are not yet well understood. Numerous studies for the search of multiferrioc properties of BiFeO3 system substituted with PbTiO3, La, Co, Nd, and Gd have been carried out in order to improve its ferroelectric and ferromagnetic properties [13, 14]. In the light of continued search for the multiferrioc materials, the substitution of Nd was used to enhance the electrical resistivity of Ba4Ti3FeO12 (BNTF) system. This paper reports the synthesization of Nd-substituted nanomaterials through the egg-white method and their dielectric, ferroelectric, and magnetic studies.

Methods

Material preparation

Nanoparticles of BNTF were prepared through egg-white method. The starting materials Bi(NO3)3·5H2O, Nd(NO3)3·6H2O, TiCl3, and FeCl3 were mixed together in proper stoichiometric proportions. Extracted egg white (60 ml), dissolved in 40 ml of double distilled water through vigorous stirring, was added to the metal mixture at room temperature. After constant stirring for 30 min, the resultant sol–gel was evaporated at 80°C until a dry precursor was obtained. The dried precursor was sintered at 700°C for 10 h. The final material obtained was ground for 1 h using mortar and pestle.

The powder samples obtained were characterized for structural phase and nanosize formation using PANalytical X'Pert Pro X-ray diffractometer (The Netherlands) with Cu Kα (λ = 1.54 Å) in the range of 20° to 80° with a sweeping rate of 2°/min.

The microstructural and morphological analysis of the samples were carried out using a field emission scanning electron microscope (FESEM, JSM 7600 F, JEOL Ltd., Akishima, Tokyo, Japan) and field emission transmission electron microscope (HRTEM, JEOL 2010 F, JEOL Ltd.) with the energy dispersive X-ray (EDX) facility attached.

For electrical measurements, a fixed amount of powder sample was taken, and a few drops of PVA were added to it. The mixture was left over night, dried at room temperature, and pressed into disc-shaped pellets (12 mm × 12 mm) with the help of hydraulic press. The pallets were heated at 500°C for 1 h, and silver paste coating was applied on opposite flat faces of the pallets to make parallel plate capacitor geometry. The dielectric measurements were performed in the frequency range 1 kHz to 1 MHz using Wayne Kerr 6500B impedance analyzer (Wayne Kerr Electronics Ltd., Woburn, MA, USA). The polarization versus electric field hysteresis measurements were carried out at 1 kV/cm field using P-E loop tracer of Marine India, New Delhi, India. Room temperature magnetic hysteresis measurements were carried out using Lake Shore VSM (Lake Shore Croyotronics Inc., OH, USA) with a field of 20 kOe.

Results and discussion

Structural and morphological studies

The powder samples of BNTF were characterized for structural and phase analysis through X-ray diffraction shown in Figure 1. The XRD patterns for annealed samples reveal the characteristic well-crystallized pattern with a few signatures of secondary phase corresponding to pure Bi4Ti3O12 compound and alpha-Fe2O3. Figure 2 shows the EDX pattern of the pure sample confirming the chemical formation of the polycrystalline BNTF nanoparticles. Figure 3a,b shows the FE-SEM microstructure of the fracture surfaces of pristine and 5% doped Nd sample. Interestingly, with Nd doping, the densification is promoted in the grown nanoparticles. Figure 4a shows the FE-TEM micrograph with inset showing the average grain size plot and selective area electron diffraction pattern for the composition x = 0.0. The micrograph shows irregular-shaped highly agglomerated nanoparticles with an average grain size of 50 nm for the composition x = 0.05. The average crystallite sizes calculated through FE-TEM show a broad size distribution from 50 to 72 nm as shown in Figure 5. A high crystalline order is observed in the grown nanoparticles. Figure 4b shows lattice pattern for the composition x = 0.05 with inset showing the d spacing value of 0.240 Å. The d value obtained collaborated well with the value obtained from X-ray diffraction pattern.
https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig1_HTML.jpg
Figure 1

XRD pattern for Bi 4 − x Nd x Ti 3 FeO 12 (0.0 ≤ × ≤ 0.25, × = 0.05) nanoparticles.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig2_HTML.jpg
Figure 2

EDX pattern for the pure ( x= 0.0) composition.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig3_HTML.jpg
Figure 3

FE-SEM images of the Bi 4 − x Nd x FeTi 3 O 12 for x= 0.0 (a) and 0.05 (b) compositions.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig4_HTML.jpg
Figure 4

FE-TEM micrograph and lattice planes. (a) FE-TEM micrograph. Lower inset, grain size distribution; upper inset, selective area electron diffraction pattern. (b) Lattice planes. Inset, lattice plane spacing for the composition x = 0.05.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig5_HTML.jpg
Figure 5

Grain size distribution with composition.

Dielectric study

The high resistivity and low dielectric loss (tanδ ≈ 1.6 at 42 Hz at RT) in Nd-substituted specimens allowed the dielectric constant (ϵ′) to be determined, as shown in Figure 6. The room temperature dielectric constant was found 515 at 1 kHz maximum for 5% Nd concentration. The obtained dielectric constant is higher than the values of thin films (≈107) [15, 16] and Nb-doped BiFeO3 ceramics [17] reported earlier. Both the dielectric constant and loss tangent (Figure 7) are found to decrease rapidly in low-frequency region and show frequency independent response above 22 kHz. These variations can be explained in the light of space charge polarization as discussed by Maxwell [18] and Wagner [19] and is in good agreement with Koop's phenomenological theory [20]. At low frequencies, the space charges are able to follow the frequency of the applied field, while at high frequencies, they may not have time to build up and undergo relaxation. The low loss values at higher frequencies show potential applications of these materials in high-frequency microwave devices. Moreover, the dielectric loss factor also depends on a number of factors, such as stoichiometry and structural homogeneity, which in turn, depend upon the composition and sintering temperature of the samples [21]. The room temperature resistivity measurements as a function of composition x are presented in Figure 8. It is seen that the resistivity of the samples increases with the increasing percentage Nd doping. The behavior may be attributed to the decreasing number of the conduction ions.
https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig6_HTML.jpg
Figure 6

Variation of dielectric constant with frequency.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig7_HTML.jpg
Figure 7

Variation of dielectric loss with frequency.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig8_HTML.jpg
Figure 8

Variation of resistivity with Nd composition.

Ferroelectric hysteresis

The ferroelectric hysteresis loop measurement is always hampered by the high leakage current. Because of low resistivity of the samples, it is difficult to apply high electric fields to the bulk samples. The ferroelectric polarization hysteresis loops at room temperature for Nd-doped Bi4 − xFeTi3O12 samples measured under an applied field (E) of about 10 kV/cm are presented in Figure 9. The loops are not really saturated and represent a partial reversal of the polarization almost elliptical-shaped [22, 23]. The Pr and E c values of the BNTF nanoparticles as a function of Nd composition are shown in Figure 10. The remanence polarization, Pr increases first and then decreases with an increasing vaue of x. The highest value of Pr = 0.110 μC/cm2 and a relatively low coercive field (Ec) of 7.918 kV/cm were observed for 5% Nd concentration. Similar behavior in Ec is also observed where it increases first and then follows a decreasing trend with increasing Nd content [24, 25]. The remnant polarization of the samples is not too high. It is well known that most magnetic materials usually have high electrical conductivity. Thus, few multiferrioc materials could exhibit the ferroelectric response properly. It is very critical for magnetic materials with high insulating resistivity to posses both ferroelectric and ferromagnetic properties simultaneously. Otherwise, an applied electric field would cause an increase in current for conducting samples rather than inducing electrical polarization.
https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig9_HTML.jpg
Figure 9

Polarization-electric field loop for Bi 4 − x Nd x Ti 3 FeO 12 nanoparticles.

https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig10_HTML.jpg
Figure 10

Variation of remanence polarization and coercive field with composition.

M-H hysteresis

Figure 11 shows the magnetization versus magnetic field (M H) hysteresis loops for the BNTF nanoparticles at room temperature for the maximum applied field (H) of 20 kOe. It is seen that all the samples show intrinsic antiferromagnetism and a weak ferromagnetism with a maximum value of remnant magnetization (Mr) of 0.00107 emu/gm for sample x = 0.05. Various authors have reported earlier similar results [2426]. The Mr value decreases with increasing Nd doping percentage. The substitution of Nd at Bi site may lead to the effective suppression of the spiral spin structure of BNTF, resulting in the appearance of magnetization. In order to verify and evaluate further the source of magnetism in the grown nanoparticles, room temperature Mossbauer spectroscopy measurements were tried on the present samples, but due to low percentage of Fe57 in the pure and doped samples, no clear Mossbauer peaks were observed.
https://static-content.springer.com/image/art%3A10.1186%2F1556-276X-7-511/MediaObjects/11671_2012_Article_966_Fig11_HTML.jpg
Figure 11

Room temperature hysteresis magnetization. With inset showing the magnified plot showing the ferromagnetic character of the grown nanoparticles.

Conclusions

In summary, a series of nanoparticles of polycrystalline system Bi4 − xNd x FeTi3O12 were prepared through the egg-white method to investigate the presence of multiferroic properties. The dielectric properties show normal behavior with respect to the frequency. Room temperature unsaturated multiferrioc properties were observed for the grown nanoparticles. All the samples show the intrinsic antiferromagnetism with very weak ferromagnetism. The remanence polarization (Pr), and remanence magnetization (Mr) values were found maximum for 5% Nd concentration. These properties entitle the grown nanoparticles of BNFT as one of the few multiferroic materials that exhibit decent magnetization and electric polarization.

Authors’ information

KMB is working as an assistant professor in King Abdullah Institute for Nanotechnology, King Saud University, Riyadh, Saudi Arabia. He obtained his Ph.D. in Applied Physics from Aligarh Muslim University, India. His field of specialization is magnetic nanomaterials. JPL is working as an assistant professor in King Abdullah Institute for Nanotechnology, King Saud University, Riyadh, Saudi Arabia. He obtained his Ph.D. in Material Sciences from the Division of Quantum Materials Physics, Okayama University, Okayama, Japan. His field of specialization is structural and morphological studies of nanomaterials. RS is at present working as Ph.D. student in the Department of Physics, Himachal Pradesh University, Summer Hill, Shimla, India. Her field of specialization is ferrite materials. MS is working as a professor in the Department of Physics, Himachal Pradesh University, Summer Hill, Shimla, India. He obtained his Ph.D. from Himachal Pradesh University in collaboration with the Indian Institute of Technology, Kanpur, India. His field of specialization is magnetic materials.

Declarations

Acknowledgment

Authors KMB and JPL are thankful to the National Plan of Science and Technology (NPST), King Saud University for providing the financial support under the project code: NANO-10-2012 for carrying this work.

Authors’ Affiliations

(1)
King Abdullah Institute for Nanotechnology, King Saud University
(2)
Department of Physics, Himachal Pradesh University

References

  1. Smolenskii GA, Chupis IE: Ferroelectromagnets. Sov Phys Uspekhi 1982, 25: 475. 10.1070/PU1982v025n07ABEH004570View Article
  2. Venevtsev Yu N, Gagulin VV: Search, design and investigation of seignettomagnetic oxides. Ferroelectrics 1994, 162: 23. 10.1080/00150199408245086View Article
  3. Hill NA: Why are there so few magnetic ferroelectrics? J Phys Chem B 2000, 104: 6694–6709. 10.1021/jp000114xView Article
  4. Spaldin NA, Fiebig M: The renaissance of magnetoelectric multiferroics. Science 2005, 309: 391–392. 10.1126/science.1113357View Article
  5. Wang J, Neaton JB, Zheng H, Nagarajan V, Ogale SB, Liu B, Viehland D, Vaithyanathan V, Schlom DG, Waghmare UV, Spaldin NA, Rabe KM, Wuttig M, Ramesh R: Epitaxial BiFeO3 multiferroic thin film heterostructures. Science 2003, 299: 1719. 10.1126/science.1080615View Article
  6. Hill NA, Filippetti A: Why are there any magnetic ferroelectrics? J Magn Magn Mater 2002, 242–245: 976–979.View Article
  7. Fiebig M: Revival of the magnetoelectric effect. J Phys D: Appl Phys 2005, 38: R123. 10.1088/0022-3727/38/8/R01View Article
  8. Scott JF, Paz de Araujo CA: Ferroelectric memories. Science 1989, 246: 1400. 10.1126/science.246.4936.1400View Article
  9. Paz de Araujo CA, Cuchiaro JD, McMillian LD, Scott MC, Scott JF: Fatigue-free ferroelectric capacitors with platinum electrodes. Nature 1995, 374: 627–629. 10.1038/374627a0View Article
  10. Takahashi K, Tonouchi M: Influence of manganese doping in multiferroic bismuth ferrite thin films. J Magn Magn Mater 2007, 310: 1174. 10.1016/j.jmmm.2006.10.280View Article
  11. Niitaka S, Azuma M, Takano M, Nishibori E, Takata M, Sakata M: Crystal structure and dielectric and magnetic properties of BiCrO3 as a ferroelectromagnet. Solid State Ionics 2004, 172: 557. 10.1016/j.ssi.2004.01.060View Article
  12. Kimura T, Goto T, Shintani H, Ishizaka K, Arima T, Tokura Y: Magnetic control of ferroelectric polarization. Nature 2003, 426: 55. 10.1038/nature02018View Article
  13. Wang DH, Goh WC, Ning M, Ong CK: Effect of Ba doping on magnetic, ferroelectric, and magnetoelectric properties in multiferroic BiFeO3 at room temperature. Appl Phys Lett 2006, 88: 212907. 10.1063/1.2208266View Article
  14. Singh K, Kotnala RK, Singh M: Study of electric and magnetic properties of (Bi0.9Pb0.1) (Fe0.9Ti0.1)O3 nanomultiferroic system. J Appl Phys 2008, 93: 212902.
  15. Singh K, Negi NS, Kotnala RK, Singh M: Dielectric and magnetic properties of (BiFeO3)1−x(PbTiO3)x ferromagnetoelectric system. J Sol Stat Commun 2008, 148: 18. 10.1016/j.ssc.2008.07.022View Article
  16. Palkar VR, Jhon J, Pinto R: Observation of saturated polarization and dielectric anomaly in magnetoelectric BiFeO3 thin films. Appl Phys Letter 2002, 80: 1628. 10.1063/1.1458695View Article
  17. Hong S-H, Horns JH, Trolier-McKinstry S, Messing GL: Dielectric and ferroelectric properties of Ta-doped bismuth titanate. J Mater Sci Lett 2000, 19: 1661. 10.1023/A:1006722312423View Article
  18. Maxwell JC: Treatise on Electricity and Magnetism. Clarendon Press, Oxford; 1873.
  19. Wagner KW: Zur Theorie der Unvolkommenen Dielektrika. Ann Physik Bd 1913, 40: 817.View Article
  20. Koop's CG: On the dispersion of resistivity and dielectric constant of some semiconductors at audio frequencies. Phys Rev 1951, 83: 121–124. 10.1103/PhysRev.83.121View Article
  21. Devan RS, Chougule BK: Effect of composition on coupled electric, magnetic, and dielectric properties of two phase particulate magnetoelectric composite. J Appl Phys 2007, 101: 014109. 10.1063/1.2404773View Article
  22. Kim WS, Jun YK, Kim KH, Hong SH: Enhanced magnetization in Co and Ta-substituted BiFeO3 ceramics. J Magn Magn Mater 2009, 321: 3262. 10.1016/j.jmmm.2009.05.059View Article
  23. Uniyal P, Yadav KL: Room temperature multiferroic properties of Eu doped BiFeO3. J Appl Phys 2009, 105: 07D914. 10.1063/1.3072087View Article
  24. Zhang X, Sui Y, Wang X, Wang Y, Wang Z: Effect of Eu substitution on the crystal structure and multiferroic properties of BiFeO3. J Alloy Compd 2010, 507: 157. 10.1016/j.jallcom.2010.07.144View Article
  25. Das S, Basu S, Mitra S, Chakravorty D, Mondal BN: Wet chemical route to transparent BiFeO3 films on SiO2 substrates. Thin Sol Films 2010, 518: 4071. 10.1016/j.tsf.2009.10.138View Article
  26. Rojac T, Kosec M, Budic B, Setter N, Damjanovic D: Strong ferroelectric domain-wall pinning in BiFeO3 ceramics. J Appl Phys 2010, 108: 074107. 10.1063/1.3490249View Article

Copyright

© Batoo et al.; licensee Springer. 2012

This article is published under license to BioMed Central Ltd. This is an Open Access article distributed under the terms of the Creative Commons Attribution License (http://creativecommons.org/licenses/by/2.0), which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.