SciELO - Scientific Electronic Library Online

 
vol.62 issue364Preparation of soda-lime glass using rock wool wasteStudy of the effect of dilution on the microstructural and magnetic properties of Mn0.65Zn0.35Fe2O4 ferrites by combustion reaction author indexsubject indexarticles search
Home Pagealphabetic serial listing  

Services on Demand

Journal

Article

Indicators

Related links

Share


Cerâmica

Print version ISSN 0366-6913On-line version ISSN 1678-4553

Cerâmica vol.62 no.364 São Paulo Oct./Dec. 2016

http://dx.doi.org/10.1590/0366-69132016623642006 

Articles

Magnetic properties and potential barrier between crystallites model of MgGa2-xFexO4 ceramics

Propriedades magnéticas e modelo de barreiras de potencial entre cristalitos de cerâmicas de MgGa2-xFexO4

V. A. dos S. Ribeiro*  1 

R. M. Rubinger1 

A. F. Oliveira1 

C. S. P. Mendonça1 

M. R. da Silva1 

1 Instituto de Física e Química, Universidade Federal de Itajubá, Itajubá, MG, Brazil 37500-903. rero@unifei.edu.br, adhimarflavio@unifei.edu.br, sales.claudiney21@gmail.com, mrsilva@unifei.edu.br

Abstract

The aim of this work was to investigate the magnetic properties and the electrical conductivity temperature dependence associated to the potential barrier between the crystallites model. Gallium and magnesium containing spinel ceramic has low magnetic coercivity and high electrical resistivity. MgGa2-xFexO4 samples (x= 0.01, 0.05, 0.15, 0.25, 0.35) were prepared by solid-state method and sintered at 800 °C for 8 h. X-ray diffraction analysis confirmed the formation of a single phase with compact cubic spinel structure. The magnetic measurements show that the saturation magnetization and remanence of all samples increased with increasing iron concentration. The coercive field decreased up to the concentration x= 0.15, and above x= 0.25 it was observed an increase in the coercive field. Through electrical characterization it was found that the samples presented highly insulating behavior for x= 0.01, and further increase in x above 0.15 gives a semiconductor behavior compatible with the potential barrier between the crystallites model, i.e. fulfills the condition L/2 > LD (crystallite size L in comparison with the Debye length LD), and the conduction is limited by potential barriers between the crystallites.

Keywords: spinel; magnetic properties; potential barrier

Resumo

O objetivo deste trabalho foi investigar as propriedades magnéticas e a dependência da condutividade elétrica com a temperatura associada ao modelo de barreiras de potencial entre os cristalitos. A cerâmica de espinélio de gálio e magnésio possui baixa coercividade magnética e alta resistividade elétrica. As amostras de MgGa2-xFexO4 (x= 0,01, 0,05, 0,15, 0,25, 0,35) foram preparadas pelo método de estado sólido e sinterizada a 800 °C durante 8 h. A análise de difração de raio X confirmou a formação de única fase com estrutura de espinélio cúbico compacto. As medições magnéticas mostraram que a magnetização de saturação e remanescência de todas as amostras aumentaram com a concentração de ferro. O campo coercitivo diminuiu até a concentração x= 0,15 e acima de x= 0,25 observou-se um aumento no campo coercivo. Através da caracterização eléctrica verificou-se que as amostras apresentaram comportamento isolante para x= 0,01 e acima de x= 0,15 observou-se um comportamento semicondutor compatível com o modelo de barreira de potencial entre cristalitos, ou seja, preenche a condição de L/2 > LD (tamanho de cristalito L em comparação com o comprimento de Debye) e a condução é limitada por barreiras de potencial entre os cristalitos.

Palavras-chave: espinélio; propriedades magnéticas; barreira de potencial

INTRODUCTION

In recent years, the study of the spinel MGa2O4 (M= Zn, Mg) has attracted much attention due to its high electrical resistivity and interesting magnetic properties such as low coercivity, low magnetic losses, low remanence, low saturation magnetization, and low coercive field 1), (2. In normal spinel the oxygen ions are positioned in a face-centered cubic closed-packed arrangement with metal ions occupying the interstices. The unitary cell contains 32 oxygen atoms with 96 interstices (32 B3+ octahedral sites and 64 tetrahedrally coordinated A2+ sites) 3), (4. The MgGa2O4 has a partially inverted spinel structure belonging to the space group Fd3m with cell parameter a= 8.2733 Å 4), (5. In the inverted spinel, the B3+ cations occupy tetrahedral sites while A2+ and B3+ cations are distributed randomly on octahedral sites.

The magnetic properties, such as magnetic permeability, coercivity and magnetic losses are strongly correlate to the microstructure, chemical composition, and crystal structure 6)-(8. In addition, the electrical properties are mainly controlled when the traps states in the region between the crystallites are present, and the conductivity of material changes due to the capture of free carriers. Polycrystalline materials are made of small crystallites usually joined at their surfaces via grain-boundaries 9), (10. Therefore, the conductivity of polycrystalline materials is related to the potential barrier between the crystallites. According to potential barrier between the crystallites model, in a polycrystal, the region between the crystallites presents a large number of defects, which act as effective carrier traps 9), (10. This model states that, when the trapping states in crystallite region are unoccupied, they create a depletion region in the crystallite and a potential barrier at the interface 9), (10. This reduces the number of free carriers available for electrical conduction. In this work, the investigations are extended by studying magnetic properties and the temperature dependent conductivity of these ceramic materials in terms of potential barrier between the crystallites model.

EXPERIMENTAL

MgGa2-xFexO4 samples with stoichiometry x= 0.01, 0.05, 0.15, 0.25 and 0.35 were prepared by solid-state method using MgO, Ga2O3 and Fe2O3 (99.9% purity, Sigma-Aldrich). Initially, the oxides were weighed, taking into account the stoichiometry x and mixed and ground in an agate mortar for about 1 h. Using a uniaxial press, the samples were compacted up to a pressure of 293 MPa and finally sintered at 800 °C for 8 h in ambient atmosphere.

X-ray diffraction analyzes were performed using a diffractometer (URD 65, Seifert & Com. ID 3000) using CuKa radiation in the 2q range of 10° to 70° with a step size of 0.02° and counting time of 2 s. The identification of the phases was carried out using the PDF2-ICDD database of software High Score Plus. The average crystallite size of the particles was determined by using the Debye-Scherrer formula. Magnetic hysteresis loops M (H) were measured using a Lakeshore 7404 vibrating sample magnetometer (VSM) in the magnetic field range of 10 kG at room temperature. The magnetization was measured as a function of the temperature using a high temperature attachment from Princeton Applied Research, 151 M, from room temperature to 1000 °C. The DC resistivity (ρ) of the samples was measured by two-probe as a function of temperature. Due to high resistivity of ferrite samples, two probe method is useful for ceramics; the measurements were taken in the range of temperature between 300 to 725 K. The real part (Z') and imaginary part (-Z") of the complex impedance of the samples were obtained by the impedance analyzer. The permittivity was calculated from the values of Z, obtained by fitting the complex impedance plots and the sample dimensions. The capacitance was measured using Novo Control Technologies, Apha A High Performance Frequency Analyzer, at room temperature and then the dielectric permittivity was calculated within frequency range of 1 Hz to 40 MHz.

RESULTS AND DISCUSSION

Fig. 1 shows the X-ray diffraction patterns obtained using CuKα radiation. The diffraction peaks clearly provide evidence for the formation of series of solid solution between MgGa2O4 (JCPDF 01-072-1520) and MgFe2O4 (JCPDF 01-088-1943). Diffraction patterns of these compounds show the typical diffraction peaks of the same basic structure, as the MgGa2O4 - MgFe2O4. It was observed in all iron concentration range the development of a compact single-phase cubic spinel type structure.

Figure 1: X-ray diffraction patterns of MgGa2-xFexO4 samples. 

Figura 1: Difratogramas de raios X de amostras de MgGa2-xFexO4

Fig. 2 shows magnetic hysteresis loops of MgGa2-xFexO4. It was possible to determine the values of some parameters such as coercive field (Hc), remanent magnetization (Mr), and saturation magnetization (Ms). Through the magnetic hysteresis loops, it can be seen that the samples did not reach the magnetic saturation at low fields, same behavior presented by Ga-substituted MnFe2O411.

Figure 2: Hysteresis loops for the MgGa2-xFexO4 samples. 

Figura 2: Ciclo de histerese para as amostras de MgGa2-xFexO4

The temperature dependence of the magnetization for all samples of MgGa2-xFexO4 is shown in Fig. 3. It can be seen from this figure that all samples studied have ferromagnetic ordering below Curie temperature (Tc) while the spontaneous magnetization increases with increasing the Fe3+ concentration (x). It is clear that the magnetization decreased with the increases in temperature, as would be expected from a system with ferromagnetic coupling below Tc. It is also clear that Tc increase with increasing x. This is the expected behavior since the paramagnetic part of the Ga3+ ions was replaced by the ferromagnetic Fe3+ ions. This change on the cation distribution implies that the magnetic interactions between the magnetic ions on the octahedral sites are increased. Two slopes are observed indicating a two-step decay of the magnetization. All samples present a change in the decay slope of the magnetization close to 400 K and Curie temperature above 700 K that are listed in Table I, except for the sample with x= 0.01 that shows diamagnetic behavior, so it does not present Curie temperature 12. Gilleo 13 indicated that the Curie temperature depends primarily upon the dominant [Fe3+-O2--Fe3+] linkages at tetrahedral and octahedral sites. The gallium ion, being diamagnetic, does not directly participate in the exchange interaction 14. Probably the change in the decay slope is associated with the paramagnetic Ga3+ ions role and the Tc is due to the Fe3+ ions role on the magnetization of the samples 11), (12. From the sample with x= 0.05 it was observed a change in concavity of the curve with paramagnetic material characteristics.

Figure 3: Magnetization temperature dependences measured for all MgGa2-xFexO4 samples. 

Figura 3: Dependência da magnetização com a temperatura medida para todas as amostras de MgGa2-xFexO4

Table I - Remanent magnetization (MR), coercivity (HC), saturation magnetization (MS), and Curie temperature (Tc) for all MgGa2-xFexO4 samples. 

Tabela I - Magnetização remanente (MR), coercividade (HC), magnetização de saturação (MS) e temperatura de Curie (Tc) para todas as amostras de MgGa2- xFexO4

Sample MR (emu/g) HC (G) MS (emu/g) Tc (K)
x=0.01 0.004 ------ 0.016 ---------
x=0.05 0.015 288.15 0.105 733.38
x=0.15 0.020 254.56 0.275 735.97
x=0.25 0.025 256.13 0.425 736.61
x=0.35 0.028 277.57 0.495 753.39

Table I shows the results of the magnetic parameters, remanent magnetization (MR), coercivity (HC), saturation magnetization (MS) and Curie temperature (Tc), of all samples obtained from the hysteresis and the magnetization-temperature curves. It can be seen that the values of saturation magnetization and remanence increased with increasing iron concentration. If the Ga3+ ions were supposed to enter only into the tetrahedral sites, even for small Ga concentration, the Ga3+ ions will cause Fe3+ ions to displace from tetrahedral to octahedral sites leading to an increase in magnetization which is observed in Table I 11. The coercive field was unable to be determined for sample with x= 0.01, and from x= 0.05 to 0.15 it decreased with the concentration. From x= 0.25 is observed an increase in the coercive field with x.

Samples with x up to 0.15 were highly insulating and, for this reason, electrical measurements were only possible to be obtained in a.c. Samples with x= 0.25 and x= 0.35 presented a semiconductor behavior which can be interpreted in the framework of the potential barrier between the crystallites model. Potential barrier between the crystallites model considers the electrical transport resistivity (ρ) of thermally activated band conduction, expressed by Equation A 9), (10:

(A)

where, e is the electron charge, n is the electron concentration in neutral region of the crystallites, L is the mean size of the crystallites, kB is the Boltzmann's constant, m* is the effective mass of charge carriers, and Eb is the energy barrier height between the crystallites, which can be expressed by Equation B 9), (10:

(B)

where, ε is the low frequency relative dielectric permittivity, and Nd is the donor density. This effect can be verified by evaluation of the Debye screening length (LD) in comparison with the crystallites size (L). LD is given by 9), (10:

(C)

where, ε 0 is the vacuum dielectric constant. If LD < L/2, charge carriers remain confined to the grains and potential barriers between the crystallites region due to interface trap states. If, however, LD > L/2, the barrier limited conductivity mechanism dominates and the electrons are transported with negligible grain boundary scattering 9), (10. It was examined the plots of ln(ρT−1/2) vs. 103/T for all samples. The large linear temperature region of the plots observed in Fig. 4 reveals that, for the studied domain of the temperature, is an evidence that the crystallites scattering of the charge carriers dominates in the investigated samples 9.

Figure 4: Inverse temperature dependence of the resistivity [ln(ρT-1/2)]. 

Figura 4: Dependência da resistividade [ln(ρT-1/2)] com o inverso da temperatura. 

In order to complete verification of the potential barrier between the crystallites model, it is necessary to measure the dielectric permittivity for all samples. The dielectric permittivity of all samples have been calculated considering a.c. capacitance measurements in the frequency range of 1 Hz to 40 MHz and Equation D. In this equation, C is the capacitance of the pellet, d is the thickness of the pellet, A is the cross-sectional area of the flat surface of the pellet, and ε 0 is the permittivity constant of free space.

(D)

The frequency dependence of dielectric permittivity of all samples is shown in Fig. 5. It is observed that the dielectric permittivity of all samples decreases with increasing frequency. The dielectric permittivity of these samples may be related to the space-charge polarization since higher conductivity grains are separated by insulating grain boundaries which produces localized accumulation of charge under the influence of an alternated electric field 15. According to Maxwell and Wagner two-layer model, space-charge polarization is due to the inhomogeneous dielectric structure of the material 15), (16. A similar variation of the dielectric constant with frequency was observed in the case of ZnFe2O, MnFe2O417, ZnxCu1-xFe2O4 and MnxCu1-xFe2O418 ferrite systems. Koops 19 proposed that the effect of grain boundaries is predominant at low frequencies; the thinner the grain boundary, the value of dielectric constant is higher. It is seen that the value of the dielectric constant is very high at low frequencies and decreases with increasing frequency, and then at higher frequency they become almost constant. The decrease in dielectric constant value with increasing frequency is attributed to the fact that the electron exchange between Fe2+ and Fe3+ ions cannot follow the change of the external applied field beyond certain frequency 16), (20. At low frequencies, grain boundaries are more effective than grain electrical conduction. The higher value of dielectric constant at low frequency is due to voids, dislocations and other defects 16), (20. In the high frequency range, which corresponds to low resistivity due to the grains, a small energy is needed for electron transfer between Fe2+ and Fe3+ ions in grains and accompanied by a small eddy current and hence a decrease in the energy loss in all samples 16), (20.

Figure 5: Frequency dependence of dielectric permittivity for all samples. 

Figura 5: Dependência da permissividade dielétrica com a frequência para todas as amostras. 

The complex-plane impedance spectrum of samples measured at room temperature is shown in Fig. 6. The impedance spectroscopy is widely used to characterize the electrical properties of materials and interfaces present in these materials. The impedance measurements data gives both resistive (real) and reactive (imaginary) components for a material. To separate the grain and grain boundary contributions of the samples, complex impedance plane plots have been drawn in the frequency range at room temperature. It is clear from Fig. 6 that all the samples show one incomplete arc due to grain boundary conduction. The incomplete circular arc in low frequency region shows that grain boundary resistance is out of measurement scale or presence of some additional relaxation phenomena which occur outside the measured frequency range.

Figure 6: Complex impedance spectra for all samples. 

Figura 6: Espectro de impedância complexa para todas as amostras. 

Now, considering the static permittivity e as the lowest frequency mean value at the flattest part of the results of Fig. 5, it can be proceeded to the potential barrier between the crystallites model. From the curves of Fig. 4, the values of Eb were calculated from the slopes of the linear dependences and their values are shown in Table II. Then, it was determined the concentration of donors (Nd ) values using the Equation B. Identifying the ND values, the values of the Debye length (LD ) was calculated using Equation C, which values are given in Table II. Applying the potential barrier between the crystallites model in the samples with x= 0.25 and 0.35 it was found that the barriers defined the conduction mechanism since for both samples LD < L/2. The Eb value for both samples was, however, small, which agrees with the small difference between L/2 and LD , meaning that further increase in x would lead to a sample with no barrier between the crystallites.

Table II - Values of barrier height (EB), dielectric permittivity (ε), donor concentration (Nd), average crystallite size (L), and Debye screening length (LD). 

Tabela II - Valores de altura da barreira (EB), permissividade dieléctrica (ε), concentração dos doadores (Nd), tamanho médio de cristalito (L) e comprimento de Debye (LD). 

Sample Eb (meV) ε Nd (m-3) LD (nm) L (nm)
0.25 15.53 186.81 6.31 x 1022 28.90 142.5
0.35 19.63 23.67 1.01 x 1022 23.43 142.4

CONCLUSIONS

The XRD patterns of the samples showed the same diffraction peaks typical of basic structure, as the MgGa2O4 - MgFe2O4 and confirmed the formation of a single phase cubic spinel structure. Through the hysteresis loops, the samples showed characteristics of a soft magnetic material. From the data, it is observed that the saturation magnetization and remanence of the samples increase with increasing iron concentration. The coercive field decreases to the concentration with x= 0.15, and from x= 0.25 is observed an increase in the coercive field. The samples studied have ferromagnetic ordering below Curie temperature (Tc) while the spontaneous magnetization increases with increasing the Fe3+ concentration (x). Magnetization decreases with the increase in temperature, as would be expected from a system with ferromagnetic coupling below Tc. The resistivity for the samples with x= 0.25 and 0.35 decreases with the increase in temperature showing a semiconductor behavior, and the samples with x= 0.01 to 0.25 showed the behavior of an insulating material. Applying the potential barrier between the crystallites model in the samples with x= 0.25 and 0.35, it was found that energy barriers between the crystallites limits the conduction of the samples with energies lower than 20 meV.

ACKNOWLEDGMENTS

The authors are thankful to CNPq, CAPES and FAPEMIG for the financing support of this research work.

REFERENCES

1 S. Wu, J. Xue, R. Wang, J. Li, J. Alloys Compd. 585, 5 (2014) 542-548. [ Links ]

2 D.R. Askeland, P.P. Fulay, W.J. Wright, The Science and Engineering of Materials, Publisher CL Engineering (2010). [ Links ]

3 Q.M. Wei, J.B. Li, Y.J. Chen, Y.S. Han, Mater. Charac. 47, 3-4 (2001) 247-252. [ Links ]

4 L.P. Sosman, R.J.M. da Fonseca, A. Dias Tavares Jr., T. Abritta. Cerâmica 52, 322 (2006) 200-204. [ Links ]

5 G.K.B. Costa, L.P. Sosman, A. López, N. Cella, R.B. Barthem, J. Alloys Compd. 534, 5 (2012) 110-114. [ Links ]

6 A.C.F.M. Costa, M.R. Morelli, R.H.G.A. Kiminami, Cerâmica 49, 311 (2003) 168-173. [ Links ]

7 O. Mirzaee, A. Shafyeia, M.A. Golozara, H. Shokrollahib, J. Alloys Compd. 461, 1-2 (2008) 312-315. [ Links ]

8 O. Mirzaee, J. King Saud University - Eng. Sci. 26, 2 (2013) 1-7. [ Links ]

9 D. Mardare, N. Iftimie, M. Crişan, M. Răileanu, A. Yildiz, T. Coman, K. Pomoni, A. Vomvas, J. Non-Cryst. Solids 357, 7 (2011) 1774-1779. [ Links ]

10 A. Yildiz, N. Serin, M. Kasap, T. Serin, D. Mardare, J. Alloys Compd. 493, 1-2 (2010) 227-232. [ Links ]

11 A.A. Sattar, Egypt. J. Sol. 27, 1 (2004) 99-110. [ Links ]

12 A. Franco, Jr. M. S. Silva, J. Appl. Phys. 107, 07B505 (2011) 109-11. [ Links ]

13 M.A. Gilleo, Phys. Chem. Solids 13 (1960) 33. [ Links ]

14 M. Kaiser, S.S. Ata-Allah, Phys. Status Solidi B 242, 15 (2005) 3138-3148. [ Links ]

15 H. Farooq, M.R. Ahmad, Y. Jamil, A. Hafeez, Z. Mahmood, T. Mahmood, J. Basic Appl. Sci. 8, 2 (2012) 597-601. [ Links ]

16 R. Sridhar, D. Ravinder, K.V. Kumar, Int. J. Eng. Res. Appl. 3, 5 (2013) 2021-2024. [ Links ]

17 K. Iwauchi, Japanese J. Appl. Phys. 10, 11 (1971) 1520-1528. [ Links ]

18 N. Rezlescu, E. Rezlescu, Phys. Status Solidi A 23, 2 (1974) 575-582. [ Links ]

19 C.G. Koops, Phys. Rev. 83, 121 (1951) 121-124. [ Links ]

20 S.S. Karande, B.R. Karche, Int. J. Emerging Techn. Adv. Eng. 4, 10 (2014) 602-608. [ Links ]

Received: November 02, 2015; Revised: January 29, 2016; Accepted: May 09, 2016

Creative Commons License This is an open-access article distributed under the terms of the Creative Commons Attribution License