# Synthesis and Characterization ofCaxSryBa1-x-yFe12-zLazO19 by Standard Ceramic Method

Authors: Rohit K. Mahadule; Purushottam R. Arjunwadkar; Megha P. Mahabole
Journal: International Journal of Metals
 (2013)

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## Abstract

The polycrystalline compounds with chemical formulaCaxSryBa1-x-yFe12-zLazO19 (CSBFLO) were synthesized via standard ceramic method. The chemical phase analysis was carried out by X-ray powder diffraction (XRD) method, which confirmed the formation of the magnetoplumbite phase belonging to ferrite structure. The frequency dependence of AC conductivity and dielectric constant was studied in the frequency range of 10 Hz to 2 MHz. The experimental results revealed that AC conductivity increases with increasing frequency, which is in agreement with Koop’s phenomenological theory. However, variation in dielectric constant required explanation in light of dielectric polarization. Magnetic characterization included studies of parameters such as Ms, Mr, Hc, and Tc, and results were explained via magnetic dilution and canting spin structure.


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## Body

## 1. Introduction

M-hexaferrite is a hard ferrimagnetic material possessing magnetoplumbite phase of hexagonal structure which is widely used in various industrial applications. Along with M-hexaferrites, various other members like W, Z, Y, X, and U belong to this family and they can be distinguished as per their stoichiometry. However, M-hexaferrites have gained more attention because of their special characteristic of being magnetoplumbite in nature which leads to greater structural stability compared to other members. The general chemical formula by which M-hexaferrites are represented is MeFe12O19 where Me is the divalent alkaline metal cations and can be replaced by a suitable cation or their combinations. Among various hexaferrites, M-hexaferrite is preferred as permanent magnetic material due to its cost effectiveness, reasonable magnetic performances, and wide availability of raw materials needed for synthesis [1].It finds numerous applications in diverse fields like high-density magnetic recording, microwave absorption devices, high power transmitters, high permeability ferrite components for digital switching equipment for the telecom requirement, high frequency microwave ferrites for VHF/UHF communication sets, defense radar requirement, and transmitter and receiver application in railway projects and can be used as building blocks for hexaferrite isolators [2–4]. The ferrimagnetic oxides with hexagonal crystal structure were first synthesized at the Philips laboratory in 1950 and were called hexagonal ferrites in order to distinguish them from the ferrimagnetic oxides with Spinel and Garnet structure [5]. The basic crystallographic and magnetic properties of the main hexagonal ferrites have been reviewed by Smit and Wijn [6]. The literature survey shows that a lot of works on various combinations of Sr2+, Ca2+, Ba2+, Pb2+, and La3+ as alkali earth metals cations have been carried out, which revealed the evolution of the uniaxial anisotropy in M-hexaferrite [7–17]. Furthermore, combination of Sr-La is found to be affecting positively the magnetic properties of the M-hexaferrites in comparison to Ba-La and Ca-La combination [18–21].In addition to magnetic properties, the exhaustive work on dielectric properties of M-hexaferrites has also been reported by various researchers. Perieria and his group have shown that combined substitution of Sr2+ and Ba2+ in M-hexaferrite possesses high value of dielectric constant with low loss in radio frequency range [22, 23]. High values of complex relative permittivity and low loss tangent for pure Ba-M hexaferrites have been reported by Mallick [24]. Debnath et al. have studied dielectric properties of Sr, La-M hexaferrite wherein high value of loss tangent is observed at lower frequency side [25].From the literature review, it is depicted that very meager work is carried out on the simultaneous combinational effect of these cations, namely, Ca2+, Ba2+, Sr2+, and La3+, on electric, magnetic, and dielectric properties of the M-hexaferrites. Hence, attempt has been made to study the electric, dielectric, and magnetic properties of M-type hexaferrite with combined substitution of divalent ions Ca, Sr, and Ba (CSB) along with trivalent La with compositional formula CaxSryBa1-x-yFe12-zLazO19 synthesized using standard ceramic method.


## 2. Experimental Details

### 2.1. Synthesis

The preparation of polycrystalline compounds with chemical formulaCaxSryBa1-x-yFe12-zLazO19 (CSBFLO) (with x=0.1,0.25,0.4; z=0.1,0.2,0.3, and y=0.2,0.4,0.6) was carried out via standard ceramic method. The molecular concentration (x and y) of substituted cations in the chemical formula was chosen that the stoichiometry of the compound remains unaffected. The AR grade oxides Fe2O3, La2O3, CaO, SrO, and BaO (Merck grade) were used as starting precursors for the synthesis of present series of compounds. The preparation process involved the mixing of oxides with respective stoichiometry and grounded together in agate mortar in an acetone medium. The synthesis was divided into two steps. Initially the mixture was calcined at 773 K for 8 h in air followed by further mixing and rigorous grinding and final thermal treatment at 1430 K for 72 hr. The compounds, thus formed, were coded as R-1 to R-10 concerning different combination of substituted cations (Table 1), were characterized by XRD technique, and were used as sample to carry out further studies.Table 1
The structural properties of mixed M-hexaferrite samples.
Code
x, z
a (Å)
c (Å)
V
D
x
D
M
Mol. Wt.
Porosity
a/c
Ca
Sr
Ba
R1
0.1
0.2
0.7
5.8569
23.1070
686.45
5.32
4.13
1100.09
22.33
0.25
R2
0.1
0.4
0.5
5.8157
22.7836
667.35
5.42
4.02
1090.14
25.85
0.25
R3
0.1
0.6
0.3
5.8170
22.7823
667.61
5.37
3.99
1080.20
25.66
0.25
R4
0.25
0.2
0.55
5.8278
22.7442
668.97
5.43
3.96
1093.80
27.01
0.25
R5
0.25
0.4
0.35
5.8158
22.7633
666.78
5.39
3.87
1083.85
28.13
0.25
R6
0.25
0.6
0.15
5.8079
22.7410
664.32
5.36
3.83
1073.92
28.57
0.25
R7
0.4
0.2
0.4
5.8959
23.0741
694.63
5.19
3.97
1087.52
23.57
0.25
R9
0.4
0.6
0.0
5.8956
23.1369
696.45
5.09
3.87
1067.64
23.88
0.25
R8
0.4
0.4
0.2
5.8958
23.1108
695.71
5.14
3.81
1077.58
25.91
0.25
R10
0.4
0
0.6
5.9028
23.0910
696.76
5.23
3.89
1097.47
25.63
0.25


### 2.2. Characterization

X-ray diffraction patterns ofCaxSryBa1-x-yFe12-zLazO19 hexagonal ferrites, under investigation, were obtained using Cu-Kα radiation on a Philips X-ray diffractometer (Model PW1732) within scanning range from 10° to 90°. Dielectric parameters were measured by using samples in the pellet form (13 mm diameter) with the help of QuadTech LCR meter in the frequency range of 10 Hz–2 MHz. The study on magnetic behavior at room temperature of the prepared M-hexaferrite samples was carried out at magnetic field of 1T with the help of vibrating sample magnetometer (VSM).


## 2.1. Synthesis

The preparation of polycrystalline compounds with chemical formulaCaxSryBa1-x-yFe12-zLazO19 (CSBFLO) (with x=0.1,0.25,0.4; z=0.1,0.2,0.3, and y=0.2,0.4,0.6) was carried out via standard ceramic method. The molecular concentration (x and y) of substituted cations in the chemical formula was chosen that the stoichiometry of the compound remains unaffected. The AR grade oxides Fe2O3, La2O3, CaO, SrO, and BaO (Merck grade) were used as starting precursors for the synthesis of present series of compounds. The preparation process involved the mixing of oxides with respective stoichiometry and grounded together in agate mortar in an acetone medium. The synthesis was divided into two steps. Initially the mixture was calcined at 773 K for 8 h in air followed by further mixing and rigorous grinding and final thermal treatment at 1430 K for 72 hr. The compounds, thus formed, were coded as R-1 to R-10 concerning different combination of substituted cations (Table 1), were characterized by XRD technique, and were used as sample to carry out further studies.Table 1
The structural properties of mixed M-hexaferrite samples.
Code
x, z
a (Å)
c (Å)
V
D
x
D
M
Mol. Wt.
Porosity
a/c
Ca
Sr
Ba
R1
0.1
0.2
0.7
5.8569
23.1070
686.45
5.32
4.13
1100.09
22.33
0.25
R2
0.1
0.4
0.5
5.8157
22.7836
667.35
5.42
4.02
1090.14
25.85
0.25
R3
0.1
0.6
0.3
5.8170
22.7823
667.61
5.37
3.99
1080.20
25.66
0.25
R4
0.25
0.2
0.55
5.8278
22.7442
668.97
5.43
3.96
1093.80
27.01
0.25
R5
0.25
0.4
0.35
5.8158
22.7633
666.78
5.39
3.87
1083.85
28.13
0.25
R6
0.25
0.6
0.15
5.8079
22.7410
664.32
5.36
3.83
1073.92
28.57
0.25
R7
0.4
0.2
0.4
5.8959
23.0741
694.63
5.19
3.97
1087.52
23.57
0.25
R9
0.4
0.6
0.0
5.8956
23.1369
696.45
5.09
3.87
1067.64
23.88
0.25
R8
0.4
0.4
0.2
5.8958
23.1108
695.71
5.14
3.81
1077.58
25.91
0.25
R10
0.4
0
0.6
5.9028
23.0910
696.76
5.23
3.89
1097.47
25.63
0.25


## 2.2. Characterization

X-ray diffraction patterns ofCaxSryBa1-x-yFe12-zLazO19 hexagonal ferrites, under investigation, were obtained using Cu-Kα radiation on a Philips X-ray diffractometer (Model PW1732) within scanning range from 10° to 90°. Dielectric parameters were measured by using samples in the pellet form (13 mm diameter) with the help of QuadTech LCR meter in the frequency range of 10 Hz–2 MHz. The study on magnetic behavior at room temperature of the prepared M-hexaferrite samples was carried out at magnetic field of 1T with the help of vibrating sample magnetometer (VSM).


## 3. Results and Discussion

### 3.1. Structural Analysis

The lattice parameters, X-ray density, bulk density, and porosity are calculated for each sample and are presented in Table1. It is observed that not only the values of lattice parameter a vary from 5.8079 to 5.9208 Å but also the lattice parameter c changes from 22.7442 to 23.2143 Å. The XRD profiles of the standard M-hexaferrite are presented in Figure 1 along with the recorded X-ray diffraction patterns of all the samples. In comparison, the presence of reflection planes (006), (107), (114), (201), (108), (220), and (304) corresponding to pure magnetoplumbite phase of hexaferrite family which belongs to the space group P63/mmc was found (no. 194) [14]. The recorded values of lattice parameters also strengthen the results, as the values lie within the lattice parameter range (a = 5.8−5.9 Å and c = 22-23 Å) of pure magnetoplumbite phase of hexaferrite. Moreover, due to high sintering temperature, the intensity of the peaks becomes stronger and narrower, indicating a better structural quality of materials.XRD pattern for the samples belonging to different composition (sample code).However, it seems that substitution of La3+ for Sr2+ ion leads to decreasing lattice parameters “a,” since La3+ ion (1.13 Å) has ionic radii less than those of Sr2+ (1.27 Å) ion. Hence, it was concluded that the lattice expansion is higher for the sample having lowest amount of La3+ ion. Whereas overall variations of lattice parameter can be attributed to average ionic radius of substituted cations, as the ratio of a/c has remained fairly constant. Similar behavior was reported in La3+ substituted M-type strontium ferrites [15–17]. Hence, the behavior confirmed that interaction and solubility between Sr2+ ion and La3+ ion is higher than other divalent ions with La3+ ion in the compounds.The variation in the densities shows general behavior; that is, the X-ray density is higher than the apparent density. The densification of samples depends on oxygen ions which diffuse through the material during sintering process. The variation in porosity attributes to function of lattice parameters; it is reported that variation in porosity is inverse to variation in effective cross sectional area of grain-to-grain contact. This concludes that if densification increases, the volume of unit cell and lattice constant ultimately decreases and vice-versa [23, 26]. This showed a good agreement with our results.


### 3.2. Compositional Variation of Electrical Conductivity and Dielectric Constant

Electrical conductivity and dielectric constant, both are basically electrical properties and it has been recognized that the same mechanism, namely, exchange of electron between Fe2+  ↔  Fe3+, is responsible for variation in both properties. Figure 2 represents variation in electrical conductivity and dielectric constant with respect to compositions or sample codes (R-1 to R-10). An increase is observed along with the increasing substitution of Sr2+ and La3+ ion till compound R-7, which is further followed by a decrease up to R-10. The maximum value is obtained for electrical conductivity and dielectric constant for sample R7 (Table 2) having proportion of Ca2+ = 0.4, Sr2+ = 0.2, Ba2+ = 0.4, and La3+ = 0.3.Table 2
Electric, dielectric, and magnetic parameters of mixed M-hexaferrite samples.
Code
x, z
E
A (eV)
σ
DC (Ω m)−1
σ
AC
×
10
-
3
ε
Ms (emu/g)
Mr (emu/g)
Hc (G)
Tc (K)
Ca
Sr
Ba
R1
0.1
0.2
0.7
0.34
0.05537
2.5
8.54 k
49.298
24.339
2307.5
700–750
R2
0.1
0.4
0.5
0.31
0.04442
1.11
5.15 k
57.88
30.440
2427.3
700–750
R3
0.1
0.6
0.3
0.35
0.07205
1.49
7.36 k
68.471
35.569
2904.6
700–750
R4
0.25
0.2
0.55
0.279
0.32859
3.89
13.50 k
55.610
23.671
1170.8
670–700
R5
0.25
0.4
0.35
0.262
0.44474
2.59
12.27 k
48.143
23.043
2074.14
670–700
R6
0.25
0.6
0.15
0.268
0.70824
4.48
12.45 k
52.98
23.297
2327.67
670–700
R7
0.4
0.2
0.4
0.31
0.73797
6.58
18.02 k
54.811
22.200
1074.9
650–670
R8
0.4
0.4
0.2
0.248
0.64729
7.54
17.47 k
54.140
26.934
2101.8
650–670
R9
0.4
0.6
0.0
0.244
0.32852
5.31
14.26 k
43.381
19.910
1657.1
650–670
R10
0.4
0.0
0.6
0.265
0.1369
4.76
17.47 k
52.350
21.670
1091.1
650–670Variation of electrical conductivity and dielectric constant as a function of composition (sample code).
(a)
(b)These results can be explained with small polaron hopping mechanism and Maxwell Wagner interfacial polarization. Both of the mechanisms deal with the production of Fe2+ ions resulting from the partial substitution of Fe2+  ↔  Fe3+ at octahedral site 4f1 or 2b and volatilization of substituted ions during sintering process. As the structure possesing cations and anions separately in tetrahedral site and octahedral site surrounded by oxygen ions (excluding only trigonal bipyramidal site) can be treated isolated from each other. Thus the localized electron model, namely, hopping mechanism, is more appropriate to discuss the condition mechanism rather than the band model. It is expected that till R7 the interaction and solubility of Sr2+  ↔  La3+ ion dominate semiconducting phenomenon, to compensate the charge neutrality at 4f1 or 2b site and produce electron transfer between Fe2+ and Fe3+ [27]. Moreover, in compound R-7, high value of electrical conductivity reflects transfer of maximum number of Fe2+ ions which are involved in the phenomenon of exchange interaction between Fe2+ and Fe3+, giving rise to maximum conduction process. It may be due to high activation energy (EA = 0.31 eV) among the compounds having the high concentration of La3+ ion along with Ba2+ and  Sr2+. As reported, the transition energy between Fe2+ and Fe3+ is 0.2 eV and if the activation energy of resistivity is greater than 0.28 eV, the energy is mainly utilized in moving the charges, not for the production of further charge carriers [26]. Hence, higher concentration of La3+ ion, which resides at the grain boundaries, results in high mobility of charges and the decrease of Fe3+ ion concentration, which ultimately enhances conductivity and reflects semiconducting behavior [28, 29]. However, further decrease in conductivity can be attributed to migration of Fe3+ ions to 12k site due to higher substitution of Ba2+ and Sr2+, separately, along with La3+ ion in M-hexaferrites, resulting in weakening the hopping mechanism and increasing resistivity [30]. Whereas, the high value of dielectric constant for the series of synthesized compounds is due to high conductivity. As it was already reported that sintered ferrites with high conductivity at low frequencies have a high dielectric constant [30].


### 3.3. Magnetic Measurements

#### 3.3.1. Compositional Variation of Magnetic Parameters

In general magnetic moment found in the range between 43 and 70 emu/g, retentivity between 19 and 36 emu/g, and the coercivity between 1074 and 2905 G for all the samples confirming the good quality of samples are shown in Figure3 and Table 2.Figure 3
Variation in M-H curve for the samples.Taking these results into account, we can conclude that sample code R3 (having composition Ca = 0.1, Sr = 0.6, Ba = 0.3, and La = 0.1) has shown the maximum value for magnetic saturation (Ms), retentivity (Mr), and coercivity (Hc). The observed increase in saturation magnetic moment, retentivity, and coercivity showed high solubility and interaction between La3+ and Sr2+ as compared to Ba2+ among the substitution. The increase in value of magnetization reflects the substitution of ions at spin down—sublattice at octahedral site [31, 32]. Whereas increase in coercivity can be explained by the loss of magnetocrystalline anisotropy and growth of large shape anisotropy in the magnetic particles [33]. However, substitution of nonmagnetic ion La3 increases for further samples having Sr2+ contents constant, reflecting the decrease in magnetic parameters. This variation concerned with phenomenon known as canting spin structure plays its role, when there is the substitution of divalent ion by trivalent ion associates with a valency change of one Fe3+ to Fe2+ which reduces the strength of interaction. This results into the shift from collinear to non-collinear of magnetically hard axis, for example, c-axis in spin structure. This showed a relevant support to our results and also led to strengthening the assumption that exchange of Fe3+ to Fe2+ referred to octahedral sites and Fe2+ anisotropy on the octahedral site could be dominant in all M-hexaferrites.


#### 3.3.2. Curie Temperature

The variation of the Curie temperature Tc (K) with composition for all the samples is shown in Table2. It is observed that the Curie temperature Tc (K) was higher in sample having lower amount of La3+ ion. This trend may be attributed to the exchange interactions between different magnetic ions, concentration of these ions, and their magnetic moments. It is therefore expected that a greater amount of energy will be required to offset the effects of exchange interactions in the material having a larger number of magnetic ions. As the magnetic moment of La3+ ion is 2.78 μB compared to the magnetic moment of 10 μB for the two Fe3+ ions [34], this concludes that the replacement of Fe3+ ions by lower amount of La3+ ion and Sr2+ is likely to increase hard magnetic properties and the Curie temperature. However, lower values for other samples can be explained on the basis of the number of magnetic ions present in the two sublattices and their mutual contraction. As Fe3+ ions are gradually replaced by rare earth La3+ ions, the number of magnetic ions begins to decrease at both sites, thus leading to a decrease of exchange interaction of the type Fe3+-O2−-Fe3+ [35]. As the Curie temperature Tc (K) is determined by the overall strength of the exchange interactions, the weakening of exchange interactions results in a decrease in the Curie temperature [29], which is in good agreement with our result.


## 3.1. Structural Analysis

The lattice parameters, X-ray density, bulk density, and porosity are calculated for each sample and are presented in Table1. It is observed that not only the values of lattice parameter a vary from 5.8079 to 5.9208 Å but also the lattice parameter c changes from 22.7442 to 23.2143 Å. The XRD profiles of the standard M-hexaferrite are presented in Figure 1 along with the recorded X-ray diffraction patterns of all the samples. In comparison, the presence of reflection planes (006), (107), (114), (201), (108), (220), and (304) corresponding to pure magnetoplumbite phase of hexaferrite family which belongs to the space group P63/mmc was found (no. 194) [14]. The recorded values of lattice parameters also strengthen the results, as the values lie within the lattice parameter range (a = 5.8−5.9 Å and c = 22-23 Å) of pure magnetoplumbite phase of hexaferrite. Moreover, due to high sintering temperature, the intensity of the peaks becomes stronger and narrower, indicating a better structural quality of materials.XRD pattern for the samples belonging to different composition (sample code).However, it seems that substitution of La3+ for Sr2+ ion leads to decreasing lattice parameters “a,” since La3+ ion (1.13 Å) has ionic radii less than those of Sr2+ (1.27 Å) ion. Hence, it was concluded that the lattice expansion is higher for the sample having lowest amount of La3+ ion. Whereas overall variations of lattice parameter can be attributed to average ionic radius of substituted cations, as the ratio of a/c has remained fairly constant. Similar behavior was reported in La3+ substituted M-type strontium ferrites [15–17]. Hence, the behavior confirmed that interaction and solubility between Sr2+ ion and La3+ ion is higher than other divalent ions with La3+ ion in the compounds.The variation in the densities shows general behavior; that is, the X-ray density is higher than the apparent density. The densification of samples depends on oxygen ions which diffuse through the material during sintering process. The variation in porosity attributes to function of lattice parameters; it is reported that variation in porosity is inverse to variation in effective cross sectional area of grain-to-grain contact. This concludes that if densification increases, the volume of unit cell and lattice constant ultimately decreases and vice-versa [23, 26]. This showed a good agreement with our results.


## 3.2. Compositional Variation of Electrical Conductivity and Dielectric Constant

Electrical conductivity and dielectric constant, both are basically electrical properties and it has been recognized that the same mechanism, namely, exchange of electron between Fe2+  ↔  Fe3+, is responsible for variation in both properties. Figure 2 represents variation in electrical conductivity and dielectric constant with respect to compositions or sample codes (R-1 to R-10). An increase is observed along with the increasing substitution of Sr2+ and La3+ ion till compound R-7, which is further followed by a decrease up to R-10. The maximum value is obtained for electrical conductivity and dielectric constant for sample R7 (Table 2) having proportion of Ca2+ = 0.4, Sr2+ = 0.2, Ba2+ = 0.4, and La3+ = 0.3.Table 2
Electric, dielectric, and magnetic parameters of mixed M-hexaferrite samples.
Code
x, z
E
A (eV)
σ
DC (Ω m)−1
σ
AC
×
10
-
3
ε
Ms (emu/g)
Mr (emu/g)
Hc (G)
Tc (K)
Ca
Sr
Ba
R1
0.1
0.2
0.7
0.34
0.05537
2.5
8.54 k
49.298
24.339
2307.5
700–750
R2
0.1
0.4
0.5
0.31
0.04442
1.11
5.15 k
57.88
30.440
2427.3
700–750
R3
0.1
0.6
0.3
0.35
0.07205
1.49
7.36 k
68.471
35.569
2904.6
700–750
R4
0.25
0.2
0.55
0.279
0.32859
3.89
13.50 k
55.610
23.671
1170.8
670–700
R5
0.25
0.4
0.35
0.262
0.44474
2.59
12.27 k
48.143
23.043
2074.14
670–700
R6
0.25
0.6
0.15
0.268
0.70824
4.48
12.45 k
52.98
23.297
2327.67
670–700
R7
0.4
0.2
0.4
0.31
0.73797
6.58
18.02 k
54.811
22.200
1074.9
650–670
R8
0.4
0.4
0.2
0.248
0.64729
7.54
17.47 k
54.140
26.934
2101.8
650–670
R9
0.4
0.6
0.0
0.244
0.32852
5.31
14.26 k
43.381
19.910
1657.1
650–670
R10
0.4
0.0
0.6
0.265
0.1369
4.76
17.47 k
52.350
21.670
1091.1
650–670Variation of electrical conductivity and dielectric constant as a function of composition (sample code).
(a)
(b)These results can be explained with small polaron hopping mechanism and Maxwell Wagner interfacial polarization. Both of the mechanisms deal with the production of Fe2+ ions resulting from the partial substitution of Fe2+  ↔  Fe3+ at octahedral site 4f1 or 2b and volatilization of substituted ions during sintering process. As the structure possesing cations and anions separately in tetrahedral site and octahedral site surrounded by oxygen ions (excluding only trigonal bipyramidal site) can be treated isolated from each other. Thus the localized electron model, namely, hopping mechanism, is more appropriate to discuss the condition mechanism rather than the band model. It is expected that till R7 the interaction and solubility of Sr2+  ↔  La3+ ion dominate semiconducting phenomenon, to compensate the charge neutrality at 4f1 or 2b site and produce electron transfer between Fe2+ and Fe3+ [27]. Moreover, in compound R-7, high value of electrical conductivity reflects transfer of maximum number of Fe2+ ions which are involved in the phenomenon of exchange interaction between Fe2+ and Fe3+, giving rise to maximum conduction process. It may be due to high activation energy (EA = 0.31 eV) among the compounds having the high concentration of La3+ ion along with Ba2+ and  Sr2+. As reported, the transition energy between Fe2+ and Fe3+ is 0.2 eV and if the activation energy of resistivity is greater than 0.28 eV, the energy is mainly utilized in moving the charges, not for the production of further charge carriers [26]. Hence, higher concentration of La3+ ion, which resides at the grain boundaries, results in high mobility of charges and the decrease of Fe3+ ion concentration, which ultimately enhances conductivity and reflects semiconducting behavior [28, 29]. However, further decrease in conductivity can be attributed to migration of Fe3+ ions to 12k site due to higher substitution of Ba2+ and Sr2+, separately, along with La3+ ion in M-hexaferrites, resulting in weakening the hopping mechanism and increasing resistivity [30]. Whereas, the high value of dielectric constant for the series of synthesized compounds is due to high conductivity. As it was already reported that sintered ferrites with high conductivity at low frequencies have a high dielectric constant [30].


## 3.3. Magnetic Measurements

### 3.3.1. Compositional Variation of Magnetic Parameters

In general magnetic moment found in the range between 43 and 70 emu/g, retentivity between 19 and 36 emu/g, and the coercivity between 1074 and 2905 G for all the samples confirming the good quality of samples are shown in Figure3 and Table 2.Figure 3
Variation in M-H curve for the samples.Taking these results into account, we can conclude that sample code R3 (having composition Ca = 0.1, Sr = 0.6, Ba = 0.3, and La = 0.1) has shown the maximum value for magnetic saturation (Ms), retentivity (Mr), and coercivity (Hc). The observed increase in saturation magnetic moment, retentivity, and coercivity showed high solubility and interaction between La3+ and Sr2+ as compared to Ba2+ among the substitution. The increase in value of magnetization reflects the substitution of ions at spin down—sublattice at octahedral site [31, 32]. Whereas increase in coercivity can be explained by the loss of magnetocrystalline anisotropy and growth of large shape anisotropy in the magnetic particles [33]. However, substitution of nonmagnetic ion La3 increases for further samples having Sr2+ contents constant, reflecting the decrease in magnetic parameters. This variation concerned with phenomenon known as canting spin structure plays its role, when there is the substitution of divalent ion by trivalent ion associates with a valency change of one Fe3+ to Fe2+ which reduces the strength of interaction. This results into the shift from collinear to non-collinear of magnetically hard axis, for example, c-axis in spin structure. This showed a relevant support to our results and also led to strengthening the assumption that exchange of Fe3+ to Fe2+ referred to octahedral sites and Fe2+ anisotropy on the octahedral site could be dominant in all M-hexaferrites.


### 3.3.2. Curie Temperature

The variation of the Curie temperature Tc (K) with composition for all the samples is shown in Table2. It is observed that the Curie temperature Tc (K) was higher in sample having lower amount of La3+ ion. This trend may be attributed to the exchange interactions between different magnetic ions, concentration of these ions, and their magnetic moments. It is therefore expected that a greater amount of energy will be required to offset the effects of exchange interactions in the material having a larger number of magnetic ions. As the magnetic moment of La3+ ion is 2.78 μB compared to the magnetic moment of 10 μB for the two Fe3+ ions [34], this concludes that the replacement of Fe3+ ions by lower amount of La3+ ion and Sr2+ is likely to increase hard magnetic properties and the Curie temperature. However, lower values for other samples can be explained on the basis of the number of magnetic ions present in the two sublattices and their mutual contraction. As Fe3+ ions are gradually replaced by rare earth La3+ ions, the number of magnetic ions begins to decrease at both sites, thus leading to a decrease of exchange interaction of the type Fe3+-O2−-Fe3+ [35]. As the Curie temperature Tc (K) is determined by the overall strength of the exchange interactions, the weakening of exchange interactions results in a decrease in the Curie temperature [29], which is in good agreement with our result.


## 3.3.1. Compositional Variation of Magnetic Parameters

In general magnetic moment found in the range between 43 and 70 emu/g, retentivity between 19 and 36 emu/g, and the coercivity between 1074 and 2905 G for all the samples confirming the good quality of samples are shown in Figure3 and Table 2.Figure 3
Variation in M-H curve for the samples.Taking these results into account, we can conclude that sample code R3 (having composition Ca = 0.1, Sr = 0.6, Ba = 0.3, and La = 0.1) has shown the maximum value for magnetic saturation (Ms), retentivity (Mr), and coercivity (Hc). The observed increase in saturation magnetic moment, retentivity, and coercivity showed high solubility and interaction between La3+ and Sr2+ as compared to Ba2+ among the substitution. The increase in value of magnetization reflects the substitution of ions at spin down—sublattice at octahedral site [31, 32]. Whereas increase in coercivity can be explained by the loss of magnetocrystalline anisotropy and growth of large shape anisotropy in the magnetic particles [33]. However, substitution of nonmagnetic ion La3 increases for further samples having Sr2+ contents constant, reflecting the decrease in magnetic parameters. This variation concerned with phenomenon known as canting spin structure plays its role, when there is the substitution of divalent ion by trivalent ion associates with a valency change of one Fe3+ to Fe2+ which reduces the strength of interaction. This results into the shift from collinear to non-collinear of magnetically hard axis, for example, c-axis in spin structure. This showed a relevant support to our results and also led to strengthening the assumption that exchange of Fe3+ to Fe2+ referred to octahedral sites and Fe2+ anisotropy on the octahedral site could be dominant in all M-hexaferrites.


## 3.3.2. Curie Temperature

The variation of the Curie temperature Tc (K) with composition for all the samples is shown in Table2. It is observed that the Curie temperature Tc (K) was higher in sample having lower amount of La3+ ion. This trend may be attributed to the exchange interactions between different magnetic ions, concentration of these ions, and their magnetic moments. It is therefore expected that a greater amount of energy will be required to offset the effects of exchange interactions in the material having a larger number of magnetic ions. As the magnetic moment of La3+ ion is 2.78 μB compared to the magnetic moment of 10 μB for the two Fe3+ ions [34], this concludes that the replacement of Fe3+ ions by lower amount of La3+ ion and Sr2+ is likely to increase hard magnetic properties and the Curie temperature. However, lower values for other samples can be explained on the basis of the number of magnetic ions present in the two sublattices and their mutual contraction. As Fe3+ ions are gradually replaced by rare earth La3+ ions, the number of magnetic ions begins to decrease at both sites, thus leading to a decrease of exchange interaction of the type Fe3+-O2−-Fe3+ [35]. As the Curie temperature Tc (K) is determined by the overall strength of the exchange interactions, the weakening of exchange interactions results in a decrease in the Curie temperature [29], which is in good agreement with our result.


## 4. Conclusions

The structural study of samples reveals that Ca2+ does not replace Ba2+ in proper quantity as compared to Sr2+ and Fe ions. The substitution of La3+ for Ba2+ and Sr2+ in M-type hexaferrite is associated with a valance change of Fe2+  ↔  Fe3+ at octahedral 2a or 4f2 site. Among the samples having higher concentration of Sr2+ with suitable concentration of La3+ in M-hexaferrite shows largest variation in AC. Conductivity and dielectric polarization along with conduction enable us to conclude excess formation of  Fe2+ ion and dually supported by negative value of thermoelectric power. Due to such a high value of dielectric parameters, it can be very useful for application discussed like RAMs. Furthermore, in the magnetic studies we observed high values of magnetic parameters for La-substituted Ca, Sr, Ba, and M-hexaferrite (R3) are concerned with high interaction between La3+ and Sr2+ ions and also support the formation of single domain particles as the magnetization process takes place by spin rotation instead of domain wall displacement. These samples can be selected for the production of permanent magnets.



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*Source: 198970-2013-12-08.xml*