# Crystal Defects and Cation Redistribution Study on Nanocrystalline Cobalt-Ferri-Chromites by Positron Annihilation Spectroscopy

Authors: Kunal B. Modi; Nimish H. Vasoya; Vinay K. Lakhani; Tushar K. Pathak; P. M. G. Nambissan
Journal: International Journal of Spectroscopy
 (2013)

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## Abstract

Positron lifetime and Doppler broadening measurements were carried out on nanocrystalline (grain size ~60–65 nm) samples of the Cr3+-substituted cobalt ferrite system with general chemical formula CoCrxFe2−xO4 (x=0.0−2.0) synthesized by the coprecipitation technique. The results indicated selective trapping of positrons in large vacancy clusters initially at the tetrahedral (A-) sites and then with Cr3+-substitution up to concentration (x)=0.7, at the octahedral (B-) sites. The results are consistent with the cation distribution determined from X-ray diffraction line intensity calculations, which indicated partial inversion of the inverse spinel ferrite, subsequent stabilization over a range of substitution (x=0.7 to 1.7), and finally the full inversion to the normal spinel chromite (CoCr2O4, x=2.0). In the intermediate range of substitution, lattice contraction prevented a fraction of Co2+ ions released from the (B-) sites from entering the tetrahedral sites, and these vacancies at the (A-) sites trapped positrons. Although the samples were composed of nanocrystalline grains, only an insignificant fraction of positrons were diffused and annihilated at the grain surfaces, since the grain sizes and the thermal diffusion length of positrons nearly overlapped.


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## Body

## 1. Introduction

Crystalline materials with the characteristic spinel structure, comprising of well-designated tetrahedral (A-) and octahedral (B-) sites, constitute a very interesting class of condensed matter systems evoking interest even from the very fundamental science viewpoint [1, 2]. Cobalt ferrite (CoFe2O4), Cobalt chromite (CoCr2O4), and their solid solutions with a typical crystalline structure XY2O4 are candidate materials in this class, where X is normally a divalent and Y is a trivalent ion. These materials have attracted a large number of chemists, physicists, and metallurgists to study their different aspects, including the structure and properties, using both theoretical modeling and wide variety of experimental tools [3–5]. Ferrites composed of nanometer-sized particles elevate this interest to new dimensions as the very large network of interfaces will then play a decisive role in controlling the atomic transport and spatial rearrangement of atoms within the structure. So far as the tools for investigating such details are concerned, conventional experimental methods such as X-ray diffraction (XRD) and transmission electron microscopy (TEM) have helped to obtain substantial information on a macroscopic scale. But defect-specific probes such as positron annihilation spectroscopy are needed to pinpoint their role in the postsynthesis and characterization treatments such materials have to undergo. We present in this paper the results of our investigation carried out on CoFe2O4, both on the nascent mother sample and samples in which the Fe3+ ions are replaced by Cr+3 ions, that is, CoCrxFe2−xO4, x = 0.0–2.0. The purpose of the work is double sided. Initially we will present the important observations which were obtained from more conventional experimental tools such as XRD, TEM, and energy dispersive analysis of X-rays (EDAX) and highlight the changes occurring at the different stages of Cr3+-substitution. The emphasis will be thereafter diverted to demonstrate the ability of positron annihilation techniques to sense such changes. The latter is of importance since such works are scarcely available in the literature so far, and secondly it offers a viable investigative probe for such studies which are highly essential in the current scenario of novel materials and arising challenges in their understanding.According to the existing literature, cobalt ferrite (CoFe2O4) is an inverse spinel and taken to be collinear ferrimagnet [6], while cobalt chromite, CoCr2O4, is a normal spinel with a canted ferromagnetic structure, and its Curie temperature is 97 K [7]. Previous studies of magnetic properties and Mossbauer spectroscopy on mixed cobalt-ferri-chromites, CoCrxFe2−xO4, of coarse-grain composition indicated that canting of magnetic structure is observed when Co2+ is present at the tetrahedral (A-) site [8, 9]. While magnetization measurements on the same system could be explained by Neel’s model as far as the series remained inverse spinel, they deviated significantly when they began to have normal spinel structure [10]. Recently, structural and magnetic properties of nanocrystalline CoCrxFe2−xO4 (0 ≤ x ≤ 1.0) system prepared by the sol-gel autocombustion route have been studied by Tolesha et al. [11].The redistribution of cations when one species is replaced by ions of neighboring elements in the periodic table has been of tremendous significance in modifying the properties as well as in giving rise to new phenomena and processes [6, 8, 9]. The transformation of a nearly complete inverse spinel ferrite, CoFe2O4, to a normal spinel chromite, CoCr2O4, through successive replacement of the Fe3+ ions by Cr3+ ions has been found to generate drastic changes in the cationic distribution in the structure, owing to lattice contraction as well as the likely presence of vacancy-type structural defects. Although substitution effects generally prompt such redistributions, concomitant lattice contraction or expansion can also influence it, and quite often it will result in the generation of structural defects in the form of unoccupied lattice sites. The latter are potential sites for investigation by positron annihilation experiments. Such a defect-sensitive spectroscopic probe will be of immense benefit as it can pinpoint the origin and evolution of such defects and their dominating role over the redistribution of ions in the lattice. As is popularly known, the positron lifetimes and Doppler broadening of the electron-positron annihilation gamma ray spectrum are directly related to the electron density and momentum distribution in a material, and hence, the information carried by the signals of annihilation can unravel the material properties in the atomic scale [12].


## 2. Experimental Procedure

The spinel ferrite system, CoCrxFe2−xO4, with variable compositions with the range of  x = 0.0, 0.1, 0.3, 0.7, 1.1, 1.3, 1.5, 1.7, 1.8, 1.9, and 2.0 were prepared by air oxidation of an aqueous suspension containing Co2+, Fe2+, and Cr3+ cations in stoichiometric proportions. The starting solutions was prepared by mixing 50 mL of aqueous solutions of CoSO4·7H2O, FeSO4·7H2O, and Cr2(SO4)3·6H2O in proper proportions. A 2 M solution of NaOH was prepared as a precipitant. The starting solution (pH ~ 3.5) was added into the precipitant so that the solubility product constants for the hydroxides of the cation are exceeded and their sequential precipitation can be avoided. The suspension (pH = 10.5) thus formed, containing dark green intermediate precipitates, was then heated and kept at 333 K for 1 hour. During the heating, oxygen gas was bubbled uniformly into the suspension to stir it and to promote oxidation reaction until all the intermediate precipitates changed into dark brownish precipitates of the spinel ferrite. The samples were filtered, washed by acetone several times, and dried at 473 K under vacuum.The formation of the ferrite powders by the oxidation method consists of oxidation by air (O2) bubbling through an aqueous solution containing ferrous ions (Fe2+) and other divalent ions (M2+) after an alkaline solution (ROH) has been added. This is according to the chemical reaction Fe2+ + M2+ + ROH + O2 → M2+(Fe3+)2O4 where ROH is NaOH, KOH, NH4OH, and so forth. Ferrite powder of high homogeneity and purity and with sufficient control over the particle size can be achieved by this method.The stoichiometry of the powdered samples was confirmed from EDAX measurements. The compositional values were determined within an accuracy of 1%. X-ray diffraction data were collected using a Philips (PW 1710) automated X-ray powder diffractometer with Cu Kα radiation, graphite monochromator, and Xe-filled proportional counter. Data were collected in the angle range 5°–80°. TEM images of the samples were taken using a TECNAIK 20 (Philips) microscope operated at 200 kV. For the TEM observations, the powder was first dispersed in amyl acetate by ultrasonication, and then the suspensions were dropped on a copper grid with a carbon film. The grain sizes and shapes were determined from the TEM pictures.Positron annihilation studies of the powdered samples were performed in the conventional way. The radioactive isotope22Na in the form of 22NaCl dissolved in dilute HCl was deposited and dried on a thin (~2 μm) Ni foil and folded to form the source of positrons. It was kept immersed in the volume of the sample taken in a glass tube. Care was taken to ensure that the powdered sample surrounded the source from all sides sufficiently enough to ensure annihilation of positrons within it. Further, the sample with the source embedded in it was maintained under dry vacuum conditions during the experiments. This is done to eliminate the possibility of the trapping of positrons and quenching of positronium (the metastable bound state of the positron and an electron) by the air and gases otherwise getting trapped within the powdered sample [13]. The positron lifetime measurements were carried out using a slow-fast coincidence spectrometer, having a time resolution (FWHM) of 200 ps for the gamma rays from 60Co source under experimental conditions. For Doppler broadening measurements, a high pure germanium (HPGe) detector with resolution 1.14 keV at 511 keV was used. This and another detector with identical resolution were used on either side of the source-sample assembly for coincidence Doppler broadening spectroscopy (CDBS) studies. The CDBS experiments helped to identify the elemental environment around the positron trapping sites in materials by virtue of the ability to record the gamma ray energy distribution spectra of positron annihilation with the high momentum core electrons, without the nuclear background. The details about these measurements and the methods of data analysis to extract the relevant information can be seen in the paper by Asoka-Kumar et al. [14].


## 3. Results and Discussion

### 3.1. Characterization of the Samples

After obtaining the final products, it was essential to check the chemical composition of each sample. The reason for making EDAX characterization was to ratify the purity and surety of the chemical composition. Two representative EDAX patterns, namely, ofx = 0.3 and 1.8 compositions are shown in Figure 1. The results of EDAX confirm the expected stoichiometry with small deficiencies of Cr3+ ions. Further, the incorporation of Cr3+ in the place of Fe3+ was indicated by the intensities of the respective peaks in the two patterns. No traces of impurities were found. The EDAX results suggested that the precursors had fully undergone the chemical reaction to form ferrite material of the expected composition.The EDAX spectrum of the Cr3+-substituted samples, at concentrations x=0.3 and 1.8.
(a)
(b)The particle size and morphology of all the compositions were studied by means of transmission electron microscopy. Typical images forx = 0.0, 1.0, and 1.6 compositions are shown in Figure 2. It can be seen that the average particle size is in the range 60–65 nm.Transmission electron micrographs of CoCrxFe2−xO4 system for (a) x=0.0, (b) 1.0, and (c) 1.6 compositions. The insets show the enlarged images of grains in each case.
(a)
(b)
(c)The CoCrxFe2−xO4 samples were characterized by XRD to ascertain the single-phase structure formation and to deduce cell edgeparameter and cation distribution and grain size verification. Typical XRD patterns of CoCrxFe2−xO4 samples with x = 0.0, 0.7, 1.1, 1.3, 1.7, and 2.0 are shown in Figure 3. The background noise and the broadness of the peaks are characteristics of particles with nanometer dimensions since there is not a sufficient number of crystallographic planes to result in sharp diffraction lines. The XRD patterns also showed that all the samples have the monophase spinel structure. No extra lines corresponding to any other phase or nonreacted ingredients were detected. The diffraction patterns could be indexed for a face centered cubic (fcc) structure [15]. The lattice constant for each composition was determined by using the “Powder-X” software [16]. The concentration dependence of the lattice constant (a) determined from the X-ray data is presented in Figure 4. The lattice constant remains more or less constant initially but rapidly decreases for higher concentrations of Cr3+. The observed change in lattice constant value with Cr3+-content (x) is attributed to the small difference in the ionic radii of the constituent cations, Fe3+ (0.640 Å) and Cr3+ (0.630 Å), and the change in the distribution of cations among the available (A-) and (B-) sites of the spinel lattice.Typical X-ray diffraction patterns of the CoCrxFe2−xO4 system for different Cr3+ concentration (x).
(a)
(b)
(c)
(d)
(e)
(f)The lattice constant (a) and the radii of the tetrahedral (rA) and octahedral (rB) sites versus Cr3+ concentration (x).
(a)
(b)
(c)In order to determine the cation distribution, the XRD line intensity calculations were made using the formula suggested by Buerger [17]:
(1)Ihkl=|Fhkl|2PL.
Here, Ihkl is the relative integrated intensity, Fhkl is the structure factor, P is the multiplicity factor, and L = (1 + cos22θ)/(sin2θ cos θ) is the Lorentz polarization factor.According to Ohnish and Teranishi [18], the intensity ratios of planes I220/I440 and I400/I422 are considered to be sensitive to the cation distribution. There exists distinct contrast in the atomic scattering factors of Cr3+ or Fe3+ and Co2+ cations present in the system. This makes the determination of the cation distribution quite reliable. Any alteration in the distribution of cations causes a significant change in the XRD intensity ratios. Therefore, in the process of arriving at the final cation distribution, the site occupancy of all the cations was varied for many combinations, and those that agreed with the experimental intensity ratios are shown in Table 1. The final cation distributions were deduced simultaneously by considering the Bragg plane ratios, the fitting of the magnetization data at 80 K, and the ion distribution parameters of Fe3+ among the (A-) and (B-) sites of spinel lattice derived from Mossbauer spectral analysis [19].Table 1
The cationic distribution in the samples at different Cr3+ concentrations (x).
x
Cation distribution
0.0
(Fe3+0.9Co2+0.1)A [Co2+0.9Fe3+1.1]B  O42-
0.1
(Fe3+0.8Co2+0.2)A [Co2+0.8Cr3+0.1Fe3+1.1]B  O42-
0.3
(Fe3+0.6Co2+0.4)A [Co2+0.6Cr3+0.3Fe3+1.1]B  O42-
0.7
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+0.7Fe3+1.0]B  O42-
1.1
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.1Fe3+0.6]B  O42-
1.3
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.3Fe3+0.4]B  O42-
1.5
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.5Fe3+0.2]B  O42-
1.7
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.7]B  O42-
1.8
(Co2+1.0)A [Cr3+1.8Fe3+0.2]B  O42-
1.9
(Co2+1.0)A [Cr3+1.9Fe3+0.1]B  O42-
2.0
(Co2+1.0)A [Cr3+2.0]B  O42-


### 3.2. Positron Lifetimes in the Unsubstituted Sample, CoFe2O4 (x = 0.0)

The positron lifetime spectra were analyzed using the PALSfit computer program developed by the Risoe group [20]. The spectra of all the samples were fitted to obtain variances of fit within satisfactory limits (1.07±0.12). The fits yielded three distinct lifetimes τ1, τ2, and τ3 in all the cases, and their magnitudes, as discussed below, were the characteristics of positron trapping in specific sites within the spinel structure or positronium formation within the grain boundaries. In the CoFe2O4 (x = 0.0) sample, the intermediate lifetime τ2 was found as high as 356 ps with relative intensity I2 = 48.2%. The normal interpretation for the observation of such a well-resolved longer lifetime with appreciable intensity is the presence of vacancy-type crystalline defects within the material since positrons get trapped in such lower-than-average-electron-density sites. This is a reasonable assumption since it is nearly impossible to synthesize ferrites with fully occupied crystalline structure. Besides, those positrons managing to diffuse out to the vacancies on the nanocrystalline grain interfaces may also contribute to this component. The reason is that the thermal diffusion lengths of positrons in oxide materials are typically about 50–60 nm [21, 22]. Hence, a small fraction of positrons would inevitably diffuse and migrate to the surfaces of the nanocrystals (which are of sizes about 60–65 nm) before their annihilation. Despite prolonged heating, the grain dimensions could not be increased to more than the above limit. On the other hand, the diffusion lengths in the present case could be shortened due to the trapping of positrons by vacancy clusters if present within the nanoparticles. The positron lifetime in the perfect crystalline sample (τf, for which no theoretical value is available) can be calculated using the trapping model equation [23]:
(2)1τf=I1τ1+I2τ2+I3τ3.
Substituting the experimental values of the positron lifetimes and their intensities of the CoFe2O4 sample in the above equation, we obtain τf=199 ps. The shorter lifetime component τ1 is obviously less than this value in all the cases due to admixing with the Bloch state residence time of trapped positrons [12]. A small contribution coming to τ1 from parapositronium atoms of lifetime 125 ps is ignored as the intensity of this component, one-third that of the orthopositronium intensity I3, is negligibly small.The annihilation characteristics of positrons diffusing out to the grain surfaces are also reflected in the variation of the longest lifetimeτ3 and its intensity I3. The magnitude of this lifetime (1.8–2.1 ns) is typical of the “pick-off” annihilation of orthopositronium atoms formed at the interfacial regions of the grains [12]. Although positronium formation is not significant enough to alter the interpretations in metallic oxides, it has been found still relevant enough to force a three-component analysis of the positron lifetime spectra of nanocrystalline materials [24–26], and the intensity I3, despite being relatively small (0.8–1.4%), indicates the presence of large free volume regions in the intergranular regions of materials when composed by nanometer-sized particles or grains.


### 3.3. Results of Cr3+ Substitution

Figures5 and 6 describe the changes occurring in the positron annihilation parameters as a result of Cr3+ substitution for Fe3+ in CoFe2O4. A close look into the trends of variation helps to identify three distinct stages of defects evolution and/or structural variations. In the first stage spreading over the concentration x = 0.1 to 0.7, the two positron lifetimes τ1 and τ2 show remarkable increase in the initial stage and attain saturation. The longer lifetime τ3 and its intensity I3 show characteristic decrease that will be discussed later. The second stage of variation is marked for x > 0.7 till 1.7 during which the lifetimes decrease and the intensity sharply rises. All these trends are just reversed once again in the last stage from x = 1.8 to 2.0.The positron lifetimes,τ1 and τ2, and intensity I2 versus Cr3+ concentration (x).
(a)
(b)
(c)The orthopositronium lifetimeτ3 and intensity I3 versus Cr3+ content (x).
(a)
(b)The variation of the different positron annihilation parameters with Cr3+-substitution is thus highly complex in nature, as the potential trapping centers might have changed during the different stages of substitution, due to not only the arrival of a new element but also the relative displacement they may cause in the positioning of the other ions already present in the crystalline structure. Certain information in this direction is available from the results of CDBS measurements shown in Figures 7(a) and 7(b). The data has been analyzed using the usual quotient spectral method in which the projected one-dimensional spectra on the ((E1-E2)/2) axis of the counts in the window ((E1+E2)/2) = 511±1.2 keV are peak normalized and divided by that of a pure reference sample (Si single crystals) [14, 27]. The choice of Si to serve as a reference is not unjustified since it is not a constituent of the material at any stage in this investigation, and the purpose is to magnify the differences in shapes of the momentum distribution curves for easy understanding and interpretation. In Figure 7(a), the ratio curves of the samples with the two extreme compositions, CoFe2O4 (x = 0.0) and CoCr2O4 (x = 2.0), are shown together with the identical curves obtained for the constituent elemental samples. Figure 7(b) illustrates the curves obtained similarly for the Cr3+-substituted samples of a few representative concentrations. The ratio curves of the samples are found having a characteristic peaks at pL = 10.3 × 10−3 m0c (where m0 is the electron mass and c is the velocity of light). The peaks of the ratio curves of the three constituent metals, that is, Co, Fe, and Cr, appear at 15.0 × 10−3 m0c, 12.2 × 10−3 m0c, and 11.3 × 10−3 m0c, respectively, but with decreasing amplitudes. This observation is consistent with the decreasing number of d-electrons and decreasing radius of the 3d-shell. Thus the peak of the ratio curve of either the pure or any of the Cr3+-substituted samples does not coincide with those of the elemental curves as an ample proof to suggest that positrons are not trapped in oxygen vacancies, a fact even otherwise vindicated by their positive charge that will repel positrons. On the other hand, trapping takes place in the cationic vacancies, and the peak at pL = 10.3 × 10−3 m0c common to all the samples and irrespective of the Cr+ concentration (x) indicates the encirclement of the defects by oxygen ions. In several of our recent studies on nanocrystalline oxide semiconductors, we have similarly obtained the peak due to annihilation with oxygen electrons at pL = 10.3 × 10−3 m0c [28–30].The ratio curves generated from the coincidence Doppler broadening spectra of the different samples—(a) elements Co, Fe, and Cr besides CoCrxFe2−xO4 of x=0.0 and 2.0; (b) CoCrxFe2−xO4 of x = 0.0, 0.3, 0.7, 1.7, and 1.9. All the spectra had been peak normalized and then divided by that of a pure reference Si sample in order to generate the ratio curves.
(a)
(b)The identical elemental environment around the positron trapping sites at all concentrations of Cr3+ substitution is further verified from the S versus W plot shown in Figure 8 that is normally used to identify the changes in the predominant type of positron trapping defects at different stages of variation of the experimental parameters. The S and W parameters have been derived from the CDB spectra as the counts falling under segments, respectively, from 0 to 3.75 × 10−3 m0c and from 7.5 × 10−3 m0c to 12.25 × 10−3 m0c normalized by the total counts accumulated under 0 to 37.5 × 10−3 m0c. The S-W plot is linear, and all the points lie essentially on a straight line. This indicates that positrons essentially encounter similar elemental environments irrespective of the cationic redistribution. This is a further credence to the argument that the defects which trap positrons are surrounded by oxygen ions, and therefore, the traps are none other than the cationic vacancies. But there are variations in the intensity of annihilation with the oxygen electrons, as indicated by the individual variations of the S and W parameters with Cr3+ concentration (x) shown in Figures 9(a) and 9(b). (For the sake of clarity, the curves of not all the samples are shown in Figure 7(a) or Figure 7(b), but the peak coordinates of all the curves are shown in Figure 8). From Figures 9(a) and 9(b) also, we can distinguish from one another basically three regions, the demarcation being identical to that mentioned in the case of the positron lifetime results. The first two regions (x = 0.0–0.7 and x = 0.7–1.7) are characterized by a fall and a rise of the peaks of the curves, and the last stage is marked by again a fall. It can be argued that although the annihilation environment of positrons essentially remains identical, they are trapped at different stages of Cr3+ substitution by the defects situated at different sites in the lattice structure. These points are further discussed in detail afterwards.Figure 8
TheS-W plot of the Cr3+-substituted samples.TheS and W parameters versus Cr3+ concentration (x).
(a)
(b)The insensitivity of the CDB spectra to the oxygen vacancies can be explained on the basis of the results of positron lifetime measurements as well. The difference between the lifetime characteristic of defects (i.e.,τ2) and the bulk lifetime τf is normally considered as an indication of the size of the defect. The enhancement in the positron lifetime due to trapping in monovacancies is ~40–80 ps in typical metals and alloys [31]. Assuming that τ2 = 356 ps is an upper limit of the positron lifetime in vacancy clusters in the unsubstituted sample, τ2 − τf = 356 − 199 = 157 ps will correspond to defects much larger than monovacancies. Theoretical estimations in Fe, which is normally bcc in structure but a constituent of the present samples, have shown the enhancement of positron lifetime in a neutral vacancy cluster composed of 4-5 neighboring monovacancies as 152 ps [32]. Considering these facts, the positron trapping site in the undoped alloy can be conceived to be a vacancy cluster composed of the monovacancy created by the absence of a doubly ionized cation and four of its coordinated oxygen ions. Based on X-ray diffraction, magnetization and Mossbauer results, Mohan et al. [10] have shown that the CoFe2O4 (x = 0.0) is a nearly complete inverse spinel and the ionic distribution in it is of the form (Fe3+0.9Co2+0.1)A[Co2+0.9Fe3+1.1]BO42-. The absence of a Co2+ ion with four oxygen neighbor ions will give rise to a neutral pentavacancy cluster in which positrons can be trapped and annihilated. The other possibility of the absence of a trivalent cation with four neighboring oxygen ions cannot be ruled out as it would have enhanced positron trapping due to surplus negative charge, and hence, it is necessary to point out whether the said vacancy cluster is centered at the (A-) site or at the (B-) site. This can be answered by looking at the effects of Cr3+ substitution on the cationic redistribution. A schematic diagram showing the two neighboring octants of a normal spinel structure is shown in Figure 10. At the very onset of substitution, a drastic drop in the intensity of the peak in the CDB spectra (represented by the W parameter) is observed (Figures 7(b) and 9(b)), and it indicates the diminishing positron annihilation probability with oxygen electrons. The ionic distributions obtained from the X-ray diffraction peak intensity analysis for samples with the different concentrations of the Cr3+ ions are given in Table 1. Thus, for example, the distribution is (Fe3+0.8Co2+0.2)A[Co2+0.8Cr3+0.1Fe3+1.1]BO42- for x = 0.1. This implies that the substituted Cr3+ ions initially replace an equal number of Fe3+ ions from the (B-) sites, but simultaneously an equal number of Fe3+ ions from the (A-) sites move over to the (B-) sites in exchange of Co2+ ions from the (B-) sites to the (A-) sites. In effect, an inversion of the spinel structure is prompted as a result of the substitution process. Hence, as shown in Table 1, the number of Fe3+ ions at the (A-) sites decreases whereas that at the (B-) sites remains unaltered till x = 0.7 compositions. Since CDB spectra indicate diminishing annihilation with oxygen electrons and the positron lifetime τ2 increases from 356 ps to 374 ps, it is reasonable to argue that the defects in the sample with x=0.1 are larger in size and increasingly deficient in oxygen ions than those in the unsubstituted (x=0.0) sample. In other words, the defects were centered at the (A-) sites in the unsubstituted sample and at the (B-) sites in the substituted samples. We attribute the second positron lifetime component τ2 to such large vacancy clusters.Figure 10
Schematic representation of the two neighboring octants of a normal spinel structure. The large circles represent oxygen ions. The small solid and open circles represent the cations at the tetrahedral and octahedral sites, respectively, as illustrated in [33].As already stated, the substitution or doping resulted in sharp rises in the two lifetimes,τ1 and τ2. The intensity I2, however, did not show any change. It is, therefore, a local effect in which the vacancy cluster has undergone an increase in size. From EDAX studies, we have estimated the actual concentration of the Cr3+ ions effectively substituted in the crystallites (Figure 1). It has been found that the (B-) sites suffered from nonstoichiometric deficiencies of Cr3+ ions, and hence, the Co2+ ions transferred to the (A-) sites are also less in number than that predicted by the formula (Fe3+0.9-xCo2+0.1+x)A[Co2+0.9-xCr3+xFe3+1.1]BO42-. The result is that the vacancies so created will add to the existing vacancy clusters, resulting in further increase in their size and thereby enhancing the positron lifetimes. However, the deficiency decreases on subsequent doping, and therefore, the lifetime τ2 and intensity I2 remain rather unchanged in the range of concentration from 0.1 to 0.7.On the other hand, the concentration of Fe3+ ions at the (B-) sites does not change despite the substitution by Cr3+ ions till x = 0.7 due to the simultaneous inversion process in which the Co2+ ions migrate to the (A-) sites [10]. This means that, the Cr3+ ions occupy the (B-) sites. The Cr3+ substitution (x) above this value does not indicate further inversion, and hence, the effective number of Fe3+ ions at the (B-) sites starts decreasing (Table 1), whereas at x = 0.7 the peak in the CDB spectrum appears the sharpest, and the positron lifetimes start decreasing above this concentration, indicating a reduction in the size of the vacancy clusters. The intensity I2 increases (Figure 5). The fact that positrons are now annihilating at sites which are smaller in size can be understood as follows. The lattice constant of the CoCrxFe2−xO4 samples steeply reduces in samples with increased Cr3+ concentration (Figure 4). The contraction of the lattice can be attributed to the slightly smaller ionic radius of Cr3+ (0.630 Å) compared to that of Fe3+ (0.640 Å). Using the experimentally found values of the lattice constant (a) and the oxygen positional parameter (u) [1], it is possible to calculate the radii of the tetrahedral and octahedral sites, rA and rB, respectively, using the relations [1](3a)
r
A
=
3
(
u
-
1
4
)
a
-
R
0
,
(3b)
r
B
=
(
5
8
-
u
)
a
-
R
0
.Here,R0 is the radius of the oxygen ion (taken as 1.32 Å), and u is taken as = 0.379 considering that CoCrxFe2−xO4 is fully inverse at x=0.0 composition [1, 2]. The site radii for the different compositions estimated from the above equations are also shown in Figure 4. Increasing the concentration of Cr3+ will result in filling the vacancies at the octahedral sites, and, owing to the positive charge, positrons are trapped in a reducing number in the Cr3+-vacancy complexes so formed. On the other hand, while the octahedral sites were large enough to accommodate the Co2+ ions, the radii of the tetrahedral sites are magnitude-wise smaller than its ionic radius (0.740 Å), and hence, it is likely that a fraction of the tetrahedral sites are unoccupied during the inversion of the spinel structure at concentrations x < 0.7. As a result, positrons now that are no more trapped at the octahedral vacancies will move over to the vacancies at the tetrahedral sites and get trapped there. The fast decreasing positron lifetimes support this argument since the tetrahedral vacancy clusters are smaller than the octahedral ones. The availability of additional trapping sites expectedly increases the intensity I2 as well. Considering that positrons are now getting trapped in the vacancy clusters present at the tetrahedral sites, the lattice contraction would directly influence their lifetime, and the observations in the range mentioned above are in accordance with the same. A careful study of the ionic distribution shown in Table 1 makes us realize that from x = 0.7 onwards till x = 1.7, the occupancies of Fe3+ and Co2+ at the (A-) sites remain unchanged, whereas the Cr3+ ions directly replace the Fe3+ ions at the (B-) sites. At x=1.7, all the Fe3+ ions at the (B-) sites are replaced by Cr3+ ions (Table 1).The last stage in the variation of the positron annihilation parameters versus the Cr3+ concentration (x) is observed between x = 1.8 and 2.0. During x = 0.7 to 1.7, the cation distribution at the (A-) sites remained unaltered as Fe3+0.3Co2+0.7, while Cr3+ ions monotonically replaced the Fe3+ ions at the (B-) sites with the Co2+ concentration at the (B-) sites remaining unaltered as 0.3. As the lattice contraction continues, the transformation of the spinel structure from the inverse to the normal configuration that had started during x = 0.1–0.7 and discontinued during x = 0.7–1.7 gets completed. From octahedral site stabilization energy considerations, it is known that cobaltchromite (CoCr2O4) is a normal spinel [10]. In earlier positron annihilation studies of nanocrystalline ZnFe2O4 [24] and NiFe2O4 [25, 33], the positron lifetimes had been observed to decrease when a normal spinel ferrite transforms to an inverse spinel, and conversely they increase when the transformation is just the opposite. These observations had been verified through Mossbauer spectroscopic studies too [25, 33]. Since the two positron lifetimes, τ1 and τ2, drastically increase during x=1.8 and 2.0 (Figure 5), this stage is attributed to the total transformation of the partly inverse CoCrxFe2−xO4 to the fully normal CoCr2O4. Note further that unlike during x = 0.1–0.7 when the intensity I2 did not show any change, it decreases in the final stage of inversion indicating the full occupancy of the (A-) sites by Co2+ ions. The fact remains that the spinel structures normally suffer from nonstoichiometric disorders, and therefore, vacancy clusters are inherently in-built in the structure. The large value of τ2 with still an appreciable intensity I2 supports this argument.As has been already pointed out, the longest lifetimeτ3 and its intensity I3 are due to the nanocrystalline dimensions of the samples, and they result from positronium atoms annihilating at the intergranular region. Hence, they need not necessarily reflect the effects of any change in the vacancy cluster dynamics within the grains. Yet τ3 shows a sudden decrease during the initial stage x=0.1 to 0.7 and then remains constant (Figure 6). The intensity I3 gradually falls during this stage but shows a characteristic rise during the second stage x=0.7 to 1.7 and then remains constant (Figure 6). The initial fall can be attributed to small traces of Cr3+ ions, unsuccessful in being incorporated into the spinel structure and hence left to remain in trace amounts within the intergranular region. EDAX analysis also indicated frustration even within the lattice due to the failure in the complete substitution of Fe3+ by the Cr3+ ions in the system. In the latter stage (i.e., x>0.7), the lattice contraction has expectedly resulted in a decrease by 0.3% in the grain size, and thereby, the number of positrons reaching out on the grain surfaces has slightly increased.Although it is known that the magnetic properties of the samples undergo rapid and interesting changes during the Cr3+ substitution, correlating such changes to the behavior of positron annihilation parameters is never straightforward and is not attempted here. The structural properties and their changes, as depicted by the positron annihilation parameters and their variations, may influence the magnetic properties, which need to be investigated by appropriate experimental methods.


## 3.1. Characterization of the Samples

After obtaining the final products, it was essential to check the chemical composition of each sample. The reason for making EDAX characterization was to ratify the purity and surety of the chemical composition. Two representative EDAX patterns, namely, ofx = 0.3 and 1.8 compositions are shown in Figure 1. The results of EDAX confirm the expected stoichiometry with small deficiencies of Cr3+ ions. Further, the incorporation of Cr3+ in the place of Fe3+ was indicated by the intensities of the respective peaks in the two patterns. No traces of impurities were found. The EDAX results suggested that the precursors had fully undergone the chemical reaction to form ferrite material of the expected composition.The EDAX spectrum of the Cr3+-substituted samples, at concentrations x=0.3 and 1.8.
(a)
(b)The particle size and morphology of all the compositions were studied by means of transmission electron microscopy. Typical images forx = 0.0, 1.0, and 1.6 compositions are shown in Figure 2. It can be seen that the average particle size is in the range 60–65 nm.Transmission electron micrographs of CoCrxFe2−xO4 system for (a) x=0.0, (b) 1.0, and (c) 1.6 compositions. The insets show the enlarged images of grains in each case.
(a)
(b)
(c)The CoCrxFe2−xO4 samples were characterized by XRD to ascertain the single-phase structure formation and to deduce cell edgeparameter and cation distribution and grain size verification. Typical XRD patterns of CoCrxFe2−xO4 samples with x = 0.0, 0.7, 1.1, 1.3, 1.7, and 2.0 are shown in Figure 3. The background noise and the broadness of the peaks are characteristics of particles with nanometer dimensions since there is not a sufficient number of crystallographic planes to result in sharp diffraction lines. The XRD patterns also showed that all the samples have the monophase spinel structure. No extra lines corresponding to any other phase or nonreacted ingredients were detected. The diffraction patterns could be indexed for a face centered cubic (fcc) structure [15]. The lattice constant for each composition was determined by using the “Powder-X” software [16]. The concentration dependence of the lattice constant (a) determined from the X-ray data is presented in Figure 4. The lattice constant remains more or less constant initially but rapidly decreases for higher concentrations of Cr3+. The observed change in lattice constant value with Cr3+-content (x) is attributed to the small difference in the ionic radii of the constituent cations, Fe3+ (0.640 Å) and Cr3+ (0.630 Å), and the change in the distribution of cations among the available (A-) and (B-) sites of the spinel lattice.Typical X-ray diffraction patterns of the CoCrxFe2−xO4 system for different Cr3+ concentration (x).
(a)
(b)
(c)
(d)
(e)
(f)The lattice constant (a) and the radii of the tetrahedral (rA) and octahedral (rB) sites versus Cr3+ concentration (x).
(a)
(b)
(c)In order to determine the cation distribution, the XRD line intensity calculations were made using the formula suggested by Buerger [17]:
(1)Ihkl=|Fhkl|2PL.
Here, Ihkl is the relative integrated intensity, Fhkl is the structure factor, P is the multiplicity factor, and L = (1 + cos22θ)/(sin2θ cos θ) is the Lorentz polarization factor.According to Ohnish and Teranishi [18], the intensity ratios of planes I220/I440 and I400/I422 are considered to be sensitive to the cation distribution. There exists distinct contrast in the atomic scattering factors of Cr3+ or Fe3+ and Co2+ cations present in the system. This makes the determination of the cation distribution quite reliable. Any alteration in the distribution of cations causes a significant change in the XRD intensity ratios. Therefore, in the process of arriving at the final cation distribution, the site occupancy of all the cations was varied for many combinations, and those that agreed with the experimental intensity ratios are shown in Table 1. The final cation distributions were deduced simultaneously by considering the Bragg plane ratios, the fitting of the magnetization data at 80 K, and the ion distribution parameters of Fe3+ among the (A-) and (B-) sites of spinel lattice derived from Mossbauer spectral analysis [19].Table 1
The cationic distribution in the samples at different Cr3+ concentrations (x).
x
Cation distribution
0.0
(Fe3+0.9Co2+0.1)A [Co2+0.9Fe3+1.1]B  O42-
0.1
(Fe3+0.8Co2+0.2)A [Co2+0.8Cr3+0.1Fe3+1.1]B  O42-
0.3
(Fe3+0.6Co2+0.4)A [Co2+0.6Cr3+0.3Fe3+1.1]B  O42-
0.7
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+0.7Fe3+1.0]B  O42-
1.1
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.1Fe3+0.6]B  O42-
1.3
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.3Fe3+0.4]B  O42-
1.5
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.5Fe3+0.2]B  O42-
1.7
(Fe3+0.3Co2+0.7)A [Co2+0.3Cr3+1.7]B  O42-
1.8
(Co2+1.0)A [Cr3+1.8Fe3+0.2]B  O42-
1.9
(Co2+1.0)A [Cr3+1.9Fe3+0.1]B  O42-
2.0
(Co2+1.0)A [Cr3+2.0]B  O42-


## 3.2. Positron Lifetimes in the Unsubstituted Sample, CoFe2O4 (x = 0.0)

The positron lifetime spectra were analyzed using the PALSfit computer program developed by the Risoe group [20]. The spectra of all the samples were fitted to obtain variances of fit within satisfactory limits (1.07±0.12). The fits yielded three distinct lifetimes τ1, τ2, and τ3 in all the cases, and their magnitudes, as discussed below, were the characteristics of positron trapping in specific sites within the spinel structure or positronium formation within the grain boundaries. In the CoFe2O4 (x = 0.0) sample, the intermediate lifetime τ2 was found as high as 356 ps with relative intensity I2 = 48.2%. The normal interpretation for the observation of such a well-resolved longer lifetime with appreciable intensity is the presence of vacancy-type crystalline defects within the material since positrons get trapped in such lower-than-average-electron-density sites. This is a reasonable assumption since it is nearly impossible to synthesize ferrites with fully occupied crystalline structure. Besides, those positrons managing to diffuse out to the vacancies on the nanocrystalline grain interfaces may also contribute to this component. The reason is that the thermal diffusion lengths of positrons in oxide materials are typically about 50–60 nm [21, 22]. Hence, a small fraction of positrons would inevitably diffuse and migrate to the surfaces of the nanocrystals (which are of sizes about 60–65 nm) before their annihilation. Despite prolonged heating, the grain dimensions could not be increased to more than the above limit. On the other hand, the diffusion lengths in the present case could be shortened due to the trapping of positrons by vacancy clusters if present within the nanoparticles. The positron lifetime in the perfect crystalline sample (τf, for which no theoretical value is available) can be calculated using the trapping model equation [23]:
(2)1τf=I1τ1+I2τ2+I3τ3.
Substituting the experimental values of the positron lifetimes and their intensities of the CoFe2O4 sample in the above equation, we obtain τf=199 ps. The shorter lifetime component τ1 is obviously less than this value in all the cases due to admixing with the Bloch state residence time of trapped positrons [12]. A small contribution coming to τ1 from parapositronium atoms of lifetime 125 ps is ignored as the intensity of this component, one-third that of the orthopositronium intensity I3, is negligibly small.The annihilation characteristics of positrons diffusing out to the grain surfaces are also reflected in the variation of the longest lifetimeτ3 and its intensity I3. The magnitude of this lifetime (1.8–2.1 ns) is typical of the “pick-off” annihilation of orthopositronium atoms formed at the interfacial regions of the grains [12]. Although positronium formation is not significant enough to alter the interpretations in metallic oxides, it has been found still relevant enough to force a three-component analysis of the positron lifetime spectra of nanocrystalline materials [24–26], and the intensity I3, despite being relatively small (0.8–1.4%), indicates the presence of large free volume regions in the intergranular regions of materials when composed by nanometer-sized particles or grains.


## 3.3. Results of Cr3+ Substitution

Figures5 and 6 describe the changes occurring in the positron annihilation parameters as a result of Cr3+ substitution for Fe3+ in CoFe2O4. A close look into the trends of variation helps to identify three distinct stages of defects evolution and/or structural variations. In the first stage spreading over the concentration x = 0.1 to 0.7, the two positron lifetimes τ1 and τ2 show remarkable increase in the initial stage and attain saturation. The longer lifetime τ3 and its intensity I3 show characteristic decrease that will be discussed later. The second stage of variation is marked for x > 0.7 till 1.7 during which the lifetimes decrease and the intensity sharply rises. All these trends are just reversed once again in the last stage from x = 1.8 to 2.0.The positron lifetimes,τ1 and τ2, and intensity I2 versus Cr3+ concentration (x).
(a)
(b)
(c)The orthopositronium lifetimeτ3 and intensity I3 versus Cr3+ content (x).
(a)
(b)The variation of the different positron annihilation parameters with Cr3+-substitution is thus highly complex in nature, as the potential trapping centers might have changed during the different stages of substitution, due to not only the arrival of a new element but also the relative displacement they may cause in the positioning of the other ions already present in the crystalline structure. Certain information in this direction is available from the results of CDBS measurements shown in Figures 7(a) and 7(b). The data has been analyzed using the usual quotient spectral method in which the projected one-dimensional spectra on the ((E1-E2)/2) axis of the counts in the window ((E1+E2)/2) = 511±1.2 keV are peak normalized and divided by that of a pure reference sample (Si single crystals) [14, 27]. The choice of Si to serve as a reference is not unjustified since it is not a constituent of the material at any stage in this investigation, and the purpose is to magnify the differences in shapes of the momentum distribution curves for easy understanding and interpretation. In Figure 7(a), the ratio curves of the samples with the two extreme compositions, CoFe2O4 (x = 0.0) and CoCr2O4 (x = 2.0), are shown together with the identical curves obtained for the constituent elemental samples. Figure 7(b) illustrates the curves obtained similarly for the Cr3+-substituted samples of a few representative concentrations. The ratio curves of the samples are found having a characteristic peaks at pL = 10.3 × 10−3 m0c (where m0 is the electron mass and c is the velocity of light). The peaks of the ratio curves of the three constituent metals, that is, Co, Fe, and Cr, appear at 15.0 × 10−3 m0c, 12.2 × 10−3 m0c, and 11.3 × 10−3 m0c, respectively, but with decreasing amplitudes. This observation is consistent with the decreasing number of d-electrons and decreasing radius of the 3d-shell. Thus the peak of the ratio curve of either the pure or any of the Cr3+-substituted samples does not coincide with those of the elemental curves as an ample proof to suggest that positrons are not trapped in oxygen vacancies, a fact even otherwise vindicated by their positive charge that will repel positrons. On the other hand, trapping takes place in the cationic vacancies, and the peak at pL = 10.3 × 10−3 m0c common to all the samples and irrespective of the Cr+ concentration (x) indicates the encirclement of the defects by oxygen ions. In several of our recent studies on nanocrystalline oxide semiconductors, we have similarly obtained the peak due to annihilation with oxygen electrons at pL = 10.3 × 10−3 m0c [28–30].The ratio curves generated from the coincidence Doppler broadening spectra of the different samples—(a) elements Co, Fe, and Cr besides CoCrxFe2−xO4 of x=0.0 and 2.0; (b) CoCrxFe2−xO4 of x = 0.0, 0.3, 0.7, 1.7, and 1.9. All the spectra had been peak normalized and then divided by that of a pure reference Si sample in order to generate the ratio curves.
(a)
(b)The identical elemental environment around the positron trapping sites at all concentrations of Cr3+ substitution is further verified from the S versus W plot shown in Figure 8 that is normally used to identify the changes in the predominant type of positron trapping defects at different stages of variation of the experimental parameters. The S and W parameters have been derived from the CDB spectra as the counts falling under segments, respectively, from 0 to 3.75 × 10−3 m0c and from 7.5 × 10−3 m0c to 12.25 × 10−3 m0c normalized by the total counts accumulated under 0 to 37.5 × 10−3 m0c. The S-W plot is linear, and all the points lie essentially on a straight line. This indicates that positrons essentially encounter similar elemental environments irrespective of the cationic redistribution. This is a further credence to the argument that the defects which trap positrons are surrounded by oxygen ions, and therefore, the traps are none other than the cationic vacancies. But there are variations in the intensity of annihilation with the oxygen electrons, as indicated by the individual variations of the S and W parameters with Cr3+ concentration (x) shown in Figures 9(a) and 9(b). (For the sake of clarity, the curves of not all the samples are shown in Figure 7(a) or Figure 7(b), but the peak coordinates of all the curves are shown in Figure 8). From Figures 9(a) and 9(b) also, we can distinguish from one another basically three regions, the demarcation being identical to that mentioned in the case of the positron lifetime results. The first two regions (x = 0.0–0.7 and x = 0.7–1.7) are characterized by a fall and a rise of the peaks of the curves, and the last stage is marked by again a fall. It can be argued that although the annihilation environment of positrons essentially remains identical, they are trapped at different stages of Cr3+ substitution by the defects situated at different sites in the lattice structure. These points are further discussed in detail afterwards.Figure 8
TheS-W plot of the Cr3+-substituted samples.TheS and W parameters versus Cr3+ concentration (x).
(a)
(b)The insensitivity of the CDB spectra to the oxygen vacancies can be explained on the basis of the results of positron lifetime measurements as well. The difference between the lifetime characteristic of defects (i.e.,τ2) and the bulk lifetime τf is normally considered as an indication of the size of the defect. The enhancement in the positron lifetime due to trapping in monovacancies is ~40–80 ps in typical metals and alloys [31]. Assuming that τ2 = 356 ps is an upper limit of the positron lifetime in vacancy clusters in the unsubstituted sample, τ2 − τf = 356 − 199 = 157 ps will correspond to defects much larger than monovacancies. Theoretical estimations in Fe, which is normally bcc in structure but a constituent of the present samples, have shown the enhancement of positron lifetime in a neutral vacancy cluster composed of 4-5 neighboring monovacancies as 152 ps [32]. Considering these facts, the positron trapping site in the undoped alloy can be conceived to be a vacancy cluster composed of the monovacancy created by the absence of a doubly ionized cation and four of its coordinated oxygen ions. Based on X-ray diffraction, magnetization and Mossbauer results, Mohan et al. [10] have shown that the CoFe2O4 (x = 0.0) is a nearly complete inverse spinel and the ionic distribution in it is of the form (Fe3+0.9Co2+0.1)A[Co2+0.9Fe3+1.1]BO42-. The absence of a Co2+ ion with four oxygen neighbor ions will give rise to a neutral pentavacancy cluster in which positrons can be trapped and annihilated. The other possibility of the absence of a trivalent cation with four neighboring oxygen ions cannot be ruled out as it would have enhanced positron trapping due to surplus negative charge, and hence, it is necessary to point out whether the said vacancy cluster is centered at the (A-) site or at the (B-) site. This can be answered by looking at the effects of Cr3+ substitution on the cationic redistribution. A schematic diagram showing the two neighboring octants of a normal spinel structure is shown in Figure 10. At the very onset of substitution, a drastic drop in the intensity of the peak in the CDB spectra (represented by the W parameter) is observed (Figures 7(b) and 9(b)), and it indicates the diminishing positron annihilation probability with oxygen electrons. The ionic distributions obtained from the X-ray diffraction peak intensity analysis for samples with the different concentrations of the Cr3+ ions are given in Table 1. Thus, for example, the distribution is (Fe3+0.8Co2+0.2)A[Co2+0.8Cr3+0.1Fe3+1.1]BO42- for x = 0.1. This implies that the substituted Cr3+ ions initially replace an equal number of Fe3+ ions from the (B-) sites, but simultaneously an equal number of Fe3+ ions from the (A-) sites move over to the (B-) sites in exchange of Co2+ ions from the (B-) sites to the (A-) sites. In effect, an inversion of the spinel structure is prompted as a result of the substitution process. Hence, as shown in Table 1, the number of Fe3+ ions at the (A-) sites decreases whereas that at the (B-) sites remains unaltered till x = 0.7 compositions. Since CDB spectra indicate diminishing annihilation with oxygen electrons and the positron lifetime τ2 increases from 356 ps to 374 ps, it is reasonable to argue that the defects in the sample with x=0.1 are larger in size and increasingly deficient in oxygen ions than those in the unsubstituted (x=0.0) sample. In other words, the defects were centered at the (A-) sites in the unsubstituted sample and at the (B-) sites in the substituted samples. We attribute the second positron lifetime component τ2 to such large vacancy clusters.Figure 10
Schematic representation of the two neighboring octants of a normal spinel structure. The large circles represent oxygen ions. The small solid and open circles represent the cations at the tetrahedral and octahedral sites, respectively, as illustrated in [33].As already stated, the substitution or doping resulted in sharp rises in the two lifetimes,τ1 and τ2. The intensity I2, however, did not show any change. It is, therefore, a local effect in which the vacancy cluster has undergone an increase in size. From EDAX studies, we have estimated the actual concentration of the Cr3+ ions effectively substituted in the crystallites (Figure 1). It has been found that the (B-) sites suffered from nonstoichiometric deficiencies of Cr3+ ions, and hence, the Co2+ ions transferred to the (A-) sites are also less in number than that predicted by the formula (Fe3+0.9-xCo2+0.1+x)A[Co2+0.9-xCr3+xFe3+1.1]BO42-. The result is that the vacancies so created will add to the existing vacancy clusters, resulting in further increase in their size and thereby enhancing the positron lifetimes. However, the deficiency decreases on subsequent doping, and therefore, the lifetime τ2 and intensity I2 remain rather unchanged in the range of concentration from 0.1 to 0.7.On the other hand, the concentration of Fe3+ ions at the (B-) sites does not change despite the substitution by Cr3+ ions till x = 0.7 due to the simultaneous inversion process in which the Co2+ ions migrate to the (A-) sites [10]. This means that, the Cr3+ ions occupy the (B-) sites. The Cr3+ substitution (x) above this value does not indicate further inversion, and hence, the effective number of Fe3+ ions at the (B-) sites starts decreasing (Table 1), whereas at x = 0.7 the peak in the CDB spectrum appears the sharpest, and the positron lifetimes start decreasing above this concentration, indicating a reduction in the size of the vacancy clusters. The intensity I2 increases (Figure 5). The fact that positrons are now annihilating at sites which are smaller in size can be understood as follows. The lattice constant of the CoCrxFe2−xO4 samples steeply reduces in samples with increased Cr3+ concentration (Figure 4). The contraction of the lattice can be attributed to the slightly smaller ionic radius of Cr3+ (0.630 Å) compared to that of Fe3+ (0.640 Å). Using the experimentally found values of the lattice constant (a) and the oxygen positional parameter (u) [1], it is possible to calculate the radii of the tetrahedral and octahedral sites, rA and rB, respectively, using the relations [1](3a)
r
A
=
3
(
u
-
1
4
)
a
-
R
0
,
(3b)
r
B
=
(
5
8
-
u
)
a
-
R
0
.Here,R0 is the radius of the oxygen ion (taken as 1.32 Å), and u is taken as = 0.379 considering that CoCrxFe2−xO4 is fully inverse at x=0.0 composition [1, 2]. The site radii for the different compositions estimated from the above equations are also shown in Figure 4. Increasing the concentration of Cr3+ will result in filling the vacancies at the octahedral sites, and, owing to the positive charge, positrons are trapped in a reducing number in the Cr3+-vacancy complexes so formed. On the other hand, while the octahedral sites were large enough to accommodate the Co2+ ions, the radii of the tetrahedral sites are magnitude-wise smaller than its ionic radius (0.740 Å), and hence, it is likely that a fraction of the tetrahedral sites are unoccupied during the inversion of the spinel structure at concentrations x < 0.7. As a result, positrons now that are no more trapped at the octahedral vacancies will move over to the vacancies at the tetrahedral sites and get trapped there. The fast decreasing positron lifetimes support this argument since the tetrahedral vacancy clusters are smaller than the octahedral ones. The availability of additional trapping sites expectedly increases the intensity I2 as well. Considering that positrons are now getting trapped in the vacancy clusters present at the tetrahedral sites, the lattice contraction would directly influence their lifetime, and the observations in the range mentioned above are in accordance with the same. A careful study of the ionic distribution shown in Table 1 makes us realize that from x = 0.7 onwards till x = 1.7, the occupancies of Fe3+ and Co2+ at the (A-) sites remain unchanged, whereas the Cr3+ ions directly replace the Fe3+ ions at the (B-) sites. At x=1.7, all the Fe3+ ions at the (B-) sites are replaced by Cr3+ ions (Table 1).The last stage in the variation of the positron annihilation parameters versus the Cr3+ concentration (x) is observed between x = 1.8 and 2.0. During x = 0.7 to 1.7, the cation distribution at the (A-) sites remained unaltered as Fe3+0.3Co2+0.7, while Cr3+ ions monotonically replaced the Fe3+ ions at the (B-) sites with the Co2+ concentration at the (B-) sites remaining unaltered as 0.3. As the lattice contraction continues, the transformation of the spinel structure from the inverse to the normal configuration that had started during x = 0.1–0.7 and discontinued during x = 0.7–1.7 gets completed. From octahedral site stabilization energy considerations, it is known that cobaltchromite (CoCr2O4) is a normal spinel [10]. In earlier positron annihilation studies of nanocrystalline ZnFe2O4 [24] and NiFe2O4 [25, 33], the positron lifetimes had been observed to decrease when a normal spinel ferrite transforms to an inverse spinel, and conversely they increase when the transformation is just the opposite. These observations had been verified through Mossbauer spectroscopic studies too [25, 33]. Since the two positron lifetimes, τ1 and τ2, drastically increase during x=1.8 and 2.0 (Figure 5), this stage is attributed to the total transformation of the partly inverse CoCrxFe2−xO4 to the fully normal CoCr2O4. Note further that unlike during x = 0.1–0.7 when the intensity I2 did not show any change, it decreases in the final stage of inversion indicating the full occupancy of the (A-) sites by Co2+ ions. The fact remains that the spinel structures normally suffer from nonstoichiometric disorders, and therefore, vacancy clusters are inherently in-built in the structure. The large value of τ2 with still an appreciable intensity I2 supports this argument.As has been already pointed out, the longest lifetimeτ3 and its intensity I3 are due to the nanocrystalline dimensions of the samples, and they result from positronium atoms annihilating at the intergranular region. Hence, they need not necessarily reflect the effects of any change in the vacancy cluster dynamics within the grains. Yet τ3 shows a sudden decrease during the initial stage x=0.1 to 0.7 and then remains constant (Figure 6). The intensity I3 gradually falls during this stage but shows a characteristic rise during the second stage x=0.7 to 1.7 and then remains constant (Figure 6). The initial fall can be attributed to small traces of Cr3+ ions, unsuccessful in being incorporated into the spinel structure and hence left to remain in trace amounts within the intergranular region. EDAX analysis also indicated frustration even within the lattice due to the failure in the complete substitution of Fe3+ by the Cr3+ ions in the system. In the latter stage (i.e., x>0.7), the lattice contraction has expectedly resulted in a decrease by 0.3% in the grain size, and thereby, the number of positrons reaching out on the grain surfaces has slightly increased.Although it is known that the magnetic properties of the samples undergo rapid and interesting changes during the Cr3+ substitution, correlating such changes to the behavior of positron annihilation parameters is never straightforward and is not attempted here. The structural properties and their changes, as depicted by the positron annihilation parameters and their variations, may influence the magnetic properties, which need to be investigated by appropriate experimental methods.


## 4. Conclusions

In understanding the effects of Cr3+-substitution in place of Fe3+ in CoFe2O4 studied by positron annihilation spectroscopy, we have offered the physical interpretation of the results in terms of three distinct stages of defect evolution and interaction. First, the unsubstituted ferrite (CoFe2O4, x=0.0) itself was found to contain large vacancy clusters. These clusters are identified as being present at the (A-) sites with the divalent Co2+ ion and four of its coordinated oxygen ions making way for such very strong trapping centers for positrons. At the onset of Cr3+-substitution (x), the positron lifetimes increased due to the transfer of positron trapping into defects to the (B-) sites. In the second stage from x=0.7 to x=1.7, a concomitant lattice contraction influenced the positron annihilation characteristics. This contraction is attributed to the slightly smaller ionic radius of Cr3+ than that of Fe3+. There is also a change in the positron trapping sites from the vacancy clusters at the (B-) sites back to those at the (A-) sites. The last stage is marked by a full inversion of the structure to that of a normal spinel chromite, and the positron annihilation parameters depicted this stage with a characteristic reversal of the trend of variation with the Cr3+ concentration.Finally, we conclude that the positron lifetime measurements complemented by results from coincidence Doppler broadening spectroscopy can be a viable alternative experimental tool to monitor the generation and evolution of structural disorders in XY2O4 (where X and Y are divalent and trivalent metals, resp.) systems during physical treatments like doping and grain size reduction. Positron annihilation parameters are seen to sense, directly or indirectly, physical phenomena of different kinds and implications like the redistribution of cations, lattice contraction or expansion, and structural transformations in certain cases [24–26].



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*Source: 272846-2013-06-11.xml*