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ISRN Materials Science
Volume 2013 (2013), Article ID 490798, 8 pages
Magnetotransport Behaviour of Nanocrystalline ()
1Department of Physics, National Institute of Technology, Kurukshetra 136119, India
2Department of Applied Physics, Delhi Technological University, Delhi 110042, India
3National Physical Laboratory, Dr. K.S. Krishnan Marg, New Delhi 110012, India
4Centre of Nanotechnology, Indian Institute of Technology, Roorkee 247667, India
Received 16 July 2013; Accepted 1 September 2013
Academic Editors: D. M. Chipara and C. Carbonaro
Copyright © 2013 Neelam Maikhuri et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.
The nanocrystalline samples of (PSMO) (, 0.50, 0.55, and 0.60) were synthesized by wet-chemical sol-gel route. Structural, magnetic, and magnetotransport properties have been studied systematically. It is found that samples with Sr content and 0.50 show paramagnetic to ferromagnetic (PM-FM) transition at K with no trace of FM-AFM transition within the temperature range of 77–350 K. However, interestingly a second transition is observed at 273 and 255 K, respectively, for samples and 0.60 correspond to an A-AFM magnetic structure. This indicates that samples and 0.50 are ferromagnetic below , while other samples ( and 0.60) have a mixed phase consisting of FM and A-type AFM phases. Resistivity versus temperature (ρ-T) curve shows that the resistivity of all the samples is much larger than the single crystals of corresponding compositions due to large contribution of grain boundaries in the present nanocrystalline samples. Moreover, the decrease in metallic component at higher Sr concentration is also evidenced by the successive reduction in magnetoresistance (MR) with increasing Sr content from to 0.60.
Several experimental and theoretical studies have focused on the exploration of grain size effect on the structural, magnetic, and electrical transport properties of alkaline-earth doped rare earth perovskite manganites chemically represented by (RE = rare earth cation and AE = alkaline earth cation) because of their unusual magnetic and electronic properties like colossal magnetoresistance (CMR), charge ordering, orbital ordering, and phase separation [1–10]. These studies focus on and clearly highlight the significance of broken Mn–O–Mn exchange bonds at the grain surface and their likely impact on the magnetic and electrical transport properties. Since size reduction leads to increased contribution from the surface regions, the broken Mn–O–Mn bonds are indeed expected to have a definite impact on magnetoelectrical properties in manganites. However, in view of the fact that manganites exhibit a strong competition and correlation between various structural and electronic degrees of freedom even more intriguing and complex phenomena are expected. It has been shown that in nanomanganites, size reduction below ~100 nm renders the charge and orbitally ordered (CO–OO) ground state with unstable antiferromagnetic (AFM) spin order, giving rise to a ferromagnetic (FM) ground state [3, 11]. Size induced transition from the AFM/CO to the weak ferromagnetic (WFM) state was observed in both nanowires  and nanoparticles . It has been shown by Lu et al.  that destabilization of the AFM-CO state and formation of an FM order can result in an enhancement of magnetization by two orders of magnitude. The WFM ground state in nanomanganites resulting from the destabilization of AFM ground state has been regarded as a direct consequence of size reduction because when the size is small enough (e.g., 20 nm), the effect of surface spin disordering would become more evident. However, WFM induced by the destabilization of the AFM order has been also reported in single crystals [12, 13] as well as epitaxial thin films . This suggests that the evolution of WFM out of the AFM-CO state cannot be a consequence of material downsizing to nanometric scale alone and that some additional effects such as orbital disordering may also be equally important [13–17].
The effect of material downsizing can have more dramatic effect in the vicinity of compositions that possess strong magnetic phase coexistence and hence show bicritical/multicritical points. Among the manganites, (PSMO) has larger bandwidth than (NSMO) and exhibits PM-FM at K for –0.40 [15, 17, 18]. In single crystals, epitaxial thin films, and large grain polycrystalline bulk, insulator to metal (I-M) transition is also observed to be simultaneous with the PM-FM transition. At higher Sr concentrations (), it transforms into an A-type AFM metal and when exceeds 0.75 the magnetic structure becomes C-type AFM insulator. Therefore, it is interesting to study the behavior of this compound in this critical range, to 0.60, for its nanocrystalline particles.
In view of the above, we have tried to understand the magnetic and magnetotransport behaviour of nanocrystalline in this critical range, to 0.60. The (, 0.50, 0.55, and 0.60) nanoparticles are prepared by wet-chemical sol-gel route and their magnetic and magnetotransport properties for their nanometric size (~40 nm) grains are studied.
2. Experimental Procedure
The wet-chemical sol-gel route has been adopted to synthesize (with , 0.50, 0.55, and 0.60) nanosized particles at a significantly lower sintering temperature as compared to conventional solid-state reaction method. In this technique, the aqueous solution of high purity Pr(NO3)3·6H2O, Sr(NO3)2·4H2O, and Mn(NO3)2·4H2O has been taken in the desired stoichiometric proportions. An equal amount of ethylene glycol has been added to this solution with continuous stirring. This solution is then heated on a hot plate at a temperature of ~100–140°C till a dry thick brown colour sol is formed. At this temperature ethylene glycol polymerizes into polyethylene glycol, which disperses the cations homogeneously forming a cation polymer network. The polymerized ethylene glycol assists in forming a close network of cations from the precursor solution and helps the reaction in enabling the phase formation at low temperatures as compared to that in bulk synthesis via solid state route. The gel forms a resin and the high viscosity of the resin prevents different cations from segregating and ensures a high level of homogeneity. This has been further decomposed in an oven at a temperature of ~250°C to get a polymeric precursor in the form of a black resin-like material. This material was then finely ground into powder. The same procedure was used to synthesize all the samples and then pellets were made for each sample. A pellet from each sample was finally sintered at ~900°C for about 12 hrs. All the synthesized samples have been subjected to phase identification and structural characterizations using a powder X-ray diffractometer [XRD, Philips PW1710] using CuKα radiation at room temperature and microstructural characterization by the scanning electron microscopic technique [SEM, Philips XL20]. The magnetotransport measurements have been performed by standard dc four-probe technique in the temperature range of 300–77 K at an applied magnetic field of 3 kG. The magnetic characterizations have been carried out by temperature dependent ac susceptibility measurements in the temperature range of 77–350 K.
3. Results and Discussion
3.1. Structural and Microstructural Characterization
The powder X-ray diffraction (XRD) patterns of (PSMO) (, 0.50, 0.55, and 0.60) samples are shown in Figure 1. All the samples are single phase polycrystalline and possess orthorhombic structure (space group Pbnm). The degree of crystallinity remains almost unaffected by the value of (Sr content). In all the samples, the most intense diffraction maxima corresponds to the (112) plane followed by (312)/(132), (220), and so forth. The lattice parameters of all the PSMO samples were evaluated from the XRD data and are listed in Table 1. For clarity, the variation of the lattice parameters and unit cell volume with Sr content () is plotted in Figures 2 and 3, respectively. From the XRD data of Table 1 and Figure 2, it is clear that as the Sr content increases, the in-plane lattice parameters, namely, and , come closer, and the structure becomes nearly tetragonal. The out-of-plane lattice parameter first decreases and then again increases slightly. This variation in the lattice parameters is in agreement with the previously reported results [15, 17]. However, in the present case, the in-plane lattice parameters are slightly larger than the previously reported values. This could be due to the nanocrystalline nature of the present samples where strain is expected to be more dominant than in microcrystalline samples.
The average crystallite size (CS) of the samples is obtained by the X-ray line width using Scherer formula, , where is the shape factor, is the wavelength of X-rays, is the actual FWHM due to CS only, and is the angle of diffraction. The average CS of samples having Sr content , 0.50, 0.55, and 0.60 is found to be approximately equal to ~19 nm, 18 nm, 17 nm, and 15 nm, respectively. This suggests that Sr concentration () also affects the crystallite size. The variation of CS is plotted in Figure 4. The CSs, lattice parameters, and unit cell volumes obtained for the different samples are listed in Table 1.
The surface microstructure of the samples, as revealed by scanning electron microscopy (SEM), was found to consist of nanometric grains. The average grain size is found to be ~40 nm in all the samples. This grain size is larger than the crystallite size calculated from the XRD data. This difference is due to the fact that grains are composed of several crystallites, probably due to the internal stress or defects in the structure. A representative typical micrograph showing the surface morphology of the fractured portion of sample is shown in Figure 5. The crystallite size was also determined by TEM. All the samples were observed to consist of nanocrystalline crystallites of average size ~40 nm and in majority of cases these nanocrystals were found to be present in the form of clusters. The TEM investigations also revealed that the crystallite size was not uniform and in some areas crystals as large as 60–70 nm were also observed. However, the density of such crystals was relatively small. A representative TEM micrograph unraveling local area microstructure and the corresponding selected area electron diffraction pattern showing the presence of nanocrystals and nanocrystalline cluster are shown in Figure 6.
3.2. Magnetic Characterization
The magnetic phase characterization was carried out by the temperature dependent AC susceptibility () which was measured using the lock-in technique. The variation of AC susceptibility with temperature is shown in Figure 7 (left panels). The paramagnetic to ferromagnetic (PM-FM) phase transition temperature () was determined from the first-order temperature derivative () of the data, which is plotted in the right panel of Figure 7. The has been defined as the temperature corresponding to the peak in the curve. The sample with Sr content shows onset of transition around 315 K and a sharp PM-FM transition at K (value corresponding to the peak in the first-order derivative of ). This value is nearly equal to the values reported for single crystals of similar composition  and similar to the bulk samples. There is no trace of FM-AFM transition within the temperature range of 77–350 K. The half doped sample with Sr content also shows transition from PM-FM state at around 308 K, but, in this case, the transition width has slightly larger value, as shown by relatively broader peak in the . On the lower temperature side, the susceptibility decreases around K. This could be due to appearance of A-type AFM ordering. In samples with Sr content and 0.60, the FM transition temperature is found to decrease slightly to K and the transition width also increases. But the most interesting observation is the occurrence of a second transition for the samples with Sr content and 0.60 that generally corresponds to an A-AFM magnetic structure. The PM-FM transition is followed by a kink and change in the slope of the curve (marked by double arrow in Figure 7). The smaller peak, which occurs at and 255 K, respectively, for sample and 0.60, in the curve corresponds to this transition. This is due to the presence of a second magnetic phase that has a lower magnetic moment, such as the A-AFM phase that consists of two-dimensional ferromagnetic sheets coupled in an antiferromagnetic manner. In samples having Sr concentration and 0.60, the presence of the AFM phase is also evidenced by sharp decrease in the susceptibility in the lower temperature regime. Thus, the present results show that at and 0.50 samples are ferromagnetic below , while other samples ( and 0.60) have a mixed phase consisting of FM and A-type AFM phases. In nanomanganites with an AFM ground state, the superexchange interaction drives AFM, which is diluted by the surface disorder [6, 16, 19, 20]. This induces a reorganization of the disordered surface spins and has been explained in terms of the core-shell model [19, 20].
3.3. Electrical Transport Characterization
Electrical transport characterization of all samples was performed by resistance measurements in zero magnetic field as well as a DC magnetic field kOe by four-probe technique. The resistivity was calculated from the formula , where is the resistance, is the resistivity, is the distance between the voltage probes, and is the cross-sectional area of the sample. Percentage magnetoresistance/magnetoresistivity (MR) was calculated by , where is the resistivity at zero magnetic field and is the resistivity at kOe. The temperature dependence of resistivity (in the temperature range of 4.2–350 K) and MR (in the temperature range of 77–300 K) is plotted in Figure 8. The resistivity of all the samples is much larger (~few Ω-cm) than the single crystals of corresponding composition [15, 18] which is of the order mΩ-cm or even smaller. This is due to large contribution of the grain boundaries in the present nanocrystalline samples. Because of the increased surface area which leads to increased grain boundary disorder as discussed in a previous section, the carrier scattering is strongly enhanced in the GB region. As seen in the - curves plotted in Figure 8, for the sample the resistivity first increases on lowering the temperature up to 165 K and then shows an insulator to metal (I-M) transition, which is much lower than the PM-FM transition temperature . In case of sample, the resistivity first increases on lowering the temperature and then shows a hump- or plateau-like region. However, no I-M transition is seen in this case and, in fact below the humped region, the resistivity shows a very strong enhancement. Nearly similar trend is showing samples having higher Sr concentration ( and 0.60). Disappearance of the I-M transition at or higher is indicative of the fact that in these samples metallic component is reduced. In the composition range –0.60, the electrical characteristic is determined by competing metallic and insulating phases. The metallic phases are generally contributed by FM and A-AFM phases, while the insulating characteristics are mainly due to the presence of grain boundaries. The absence of I-M transition shows that the contribution of grain boundaries is rather dominant in these samples (–0.60) and one possible scenario is that the induced FM phase is not metallic but insulating or has relatively lower conductivity. This can be attributed to the nanocrystalline nature of the sample. Because of the small grain/crystallite size the electrical transport is dominated by the contribution from the grain boundaries. The grain boundary contribution envelopes the I-M transition, which occurs in the vicinity of in single crystalline materials.
The decrease in the metallic component at higher Sr concentration is also evidenced by the successive reduction in the magnetoresistance (MR) as Sr content increases from to 0.60. As seen in the right panel of Figure 8, sample shows the highest MR ~12% at 77 K and kOe. The MR values are measured to be ~8, 4.5, and 3.5% for , 0.55, and 0.60, respectively. This gradual and systematic decrease in MR magnitude confirms the conjecture that induced FM phase in the present nanocrystalline samples may not be metallic.
We have synthesized (, 0.50, 0.55, and 0.60) nanocrystalline samples by wet-chemical sol-gel route and studied their structural, magnetic, and electrical transport properties. All the samples are single phase and possess orthorhombic structure with space group Pbnm. The samples with and 0.50 show a paramagnetic to ferromagnetic (PM-FM) transition at K. However, interestingly, a second transition is observed at and 255 K, respectively, for samples and 0.60 correspond to an A-AFM phase which indicates that, below , samples with –0.60 have a mixed phase consisting of FM and A-type AFM phases. In these nanocrystalline samples, the resistivity is much larger than the single crystals of corresponding compositions due to large contribution of grain boundaries. Moreover, the gradual decrease in the MR from ~12 to 3.5% is observed with increasing the Sr content from to 0.60 which also indicates the decrease in the metallic component at higher Sr concentrations.
- Y. Tokura and Y. Tomioka, “Colossal magnetoresistive manganites,” Journal of Magnetism and Magnetic Materials, vol. 200, no. 1, pp. 1–23, 1999.
- F. Chen, H. W. Liu, K. F. Wang et al., “Synthesis and characterization of La0.825Sr0.175MnO3 nanowires,” Journal of Physics, vol. 17, no. 44, pp. L467–L475, 2005.
- S. S. Rao, K. N. Anuradha, S. Sarangi, and S. V. Bhat, “Weakening of charge order and antiferromagnetic to ferromagnetic switch over in Pr0.5Ca0.5MnO3 nanowires,” Applied Physics Letters, vol. 87, no. 18, Article ID 182503, 3 pages, 2005.
- S. S. Rao, S. Tripathi, D. Pandey, and S. V. Bhat, “Suppression of charge order, disappearance of antiferromagnetism, and emergence of ferromagnetism in Nd0.5Ca0.5MnO3 nanoparticles,” Physical Review B, vol. 74, no. 14, Article ID 144416, 5 pages, 2006.
- Z. Q. Wang, F. Gao, K. F. Wang, H. Yu, Z. F. Ren, and J.-M. Liu, “Synthesis and magnetic properties of Pr0.57Ca0.43MnO3 nanoparticles,” Materials Science and Engineering B, vol. 136, no. 1, pp. 96–100, 2007.
- A. Biswas and I. Das, “Experimental observation of charge ordering in nanocrystalline Pr0.65Ca0.35MnO3,” Physical Review B, vol. 74, no. 17, Article ID 172405, 4 pages, 2006.
- A. Biswas, I. Das, and C. Majumdar, “Modification of the charge ordering in Pr1/2Sr1/2MnO3 nanoparticles,” Journal of Applied Physics, vol. 98, no. 12, Article ID 124310, 5 pages, 2005.
- K. S. Shankar, S. Kar, G. N. Subbanna, and A. K. Raychaudhuri, “Enhanced ferromagnetic transition temperature in nanocrystalline lanthanum calcium manganese oxide (La0.67Ca0.33MnO3),” Solid State Communications, vol. 129, no. 7, pp. 479–483, 2004.
- T. Zhang, C. G. Jin, T. Qian, X. L. Lu, J. M. Bai, and X. G. Li, “Hydrothermal synthesis of single-crystalline La0.5Ca0.5MnO3 nanowires at low temperature,” Journal of Materials Chemistry, vol. 14, pp. 2787–2789, 2004.
- S. Dong, F. Gao, Z. Q. Wang, J.-M. Liu, and Z. F. Ren, “Surface phase separation in nanosized charge-ordered manganites,” Applied Physics Letters, vol. 90, no. 8, Article ID 082508, 3 pages, 2007.
- C. L. Lu, S. Dong, K. F. Wang et al., “Charge-order breaking and ferromagnetism in La0.4Ca0.6MnO3 nanoparticles,” Applied Physics Letters, vol. 91, no. 3, Article ID 032502, 3 pages, 2007.
- M. Nagao, T. Asaka, D. Akahoshi et al., “Nanostructural evidence at the phase boundary of A-and C-type antiferromagnetic phases in Nd1-xSrxMnO3 crystals,” Journal of Physics, vol. 19, no. 49, Article ID 492201, 2007.
- D. Akahoshi, R. Hatakeyama, M. Nagao, T. Asaka, Y. Matsui, and H. Kuwahara, “Anomalous ferromagnetic behavior and large magnetoresistance induced by orbital fluctuation in heavily doped Nd1-xSrxMnO3 (0.57 ≤ x ≤ 0.75),” Physical Review B, vol. 77, no. 5, Article ID 054404, 5 pages, 2008.
- R. Prasad, M. M. Singh, P. K. Siwach, P. Fournier, and H. K. Singh, “Anomalous insulator-metal transition and weak ferromagnetism in Nd0.37Sr0.63MnO3 thin films,” Europhysics Letters, vol. 84, no. 2, Article ID 27003, 2008.
- Y. Tokura, “Critical features of colossal magnetoresistive manganites,” Reports on Progress in Physics, vol. 69, no. 3, p. 797, 2006.
- Y. Moritomo, T. Akimoto, A. Nakamura, K. Ohoyama, and M. Ohashi, “Antiferromagnetic metallic state in the heavily doped region of perovskite manganites,” Physical Review B, vol. 58, no. 9, pp. 5544–5549, 1998.
- H. Kawano, R. Kajimoto, H. Yoshizawa, Y. Tomioka, H. Kuwahara, and Y. Tokura, “Magnetic ordering and relation to the metal-insulator transition in Pr1-xSrxMnO3 and Nd1-xSrxMnO3 with x~ 1/2,” Physical Review Letters, vol. 78, no. 22, pp. 4253–4256, 1997.
- J. A. Fernandez-Baca, P. Dai, H. Y. Hwang, C. Kloc, and S.-W. Cheong, “Evolution of the low-frequency spin dynamics in ferromagnetic manganites,” Physical Review Letters, vol. 80, no. 18, pp. 4012–4015, 1998.
- R. N. Bhowmik, R. Nagarajan, and R. Ranganathan, “Magnetic enhancement in antiferromagnetic nanoparticle of CoRh2O4,” Physical Review B, vol. 69, Article ID 054430, 5 pages, 2004.
- T. Zhang, T. F. Zhou, T. Qian, and X. G. Li, “Particle size effects on interplay between charge ordering and magnetic properties in nanosized La0.25Ca0.75MnO3,” Physical Review B, vol. 76, no. 17, Article ID 174415, 7 pages, 2007.