## Abstract

The magnetic properties of hausmannite thin films are investigated in this chapter. The Verdet constant and angle of Faraday rotation are determined. The magnetic anisotropy of Mn3O4 is explained by the measurement of the zero-field cooled (ZFC) and field cooled (FC) curves. This experiment is connected with the presentation of the ferromagnetic to superparamagnetic transition of the hausmannite.

### Keywords

- hausmannite Mn3O4
- Faraday effect
- verdet constant
- ferromagnet
- superparamagnet

## 1. Introduction

The hausmannite Mn_{3}O_{4} can be fabricated by many methods, but the spray pyrolysis method can give it the highest quality. This material is very interesting because it is a transition metal oxide and has application in semiconductor devices [1]. This oxide has two valance states on manganese—Mn^{2+} and Mn^{3+}. Thus, spinel Mn_{3}O_{4} occurs in nature as the mineral hausmannite [Mn^{2+}Mn_{2}^{3+}O^{4}]. The Mn^{2+} cations occupy the tetrahedral sites and Mn^{3+}cations occupy the octahedral sites [2]. The nanoparticles of Mn_{3}O_{4 }thin film behave as single-domain ferromagnets. However, above the blocking temperature, the particles behave as paramagnets due to the dominance of thermal fluctuations over the magnetocrystalline anisotropy energy. These nanoparticles have much higher magnetic moments than other paramagnets and are called superparamagnet.

The detailed investigation of magnetic properties of hausmannite thin film is presented in this chapter.

## 2. Method of preparation and characterization techniques

Several techniques have been used to prepare thin films of these types of transparent and conductive materials to meet the requirements of search and industries such as MOCVD (organometallic chemical vapor deposition) [3], chemical vapor transport (CVT) [4], sputtering [5] and laser ablation [6, 7], which are generally either sophisticated or expensive and hence the need for a simple, easy to meter out and less expensive technique. In addition to these techniques, spray pyrolysis [8–11] has received a little bit of extra attention because of its simplicity and cost-effectiveness as it does not require sophisticated vacuum apparatus. Furthermore, this method can be selected for film production of large area with size grain controllable by controlling the doping concentration. Also, this technique leads to a large production area and it permits also the formation of thin films with possible control of oxygen vacancy by means of the use of both appropriate precursors and postannealing treatments in air [12–15].

Thin ﬁlms of Mn_{3}O_{4} were grown at 350°C on 1 × 2 cm^{2} glass substrate using the spray pyrolysis technique. The substrate temperature was fixed using a digital temperature controller with a k-type thermocouple. The aqueous solution with a flow of about 4 ml/min contains magnesium chloride (MnCl_{2}.6H_{2}O) 0.1 M as precursor. The distance between the nozzle and the substrate was about 27 cm. Spray solutions quantity (75 ml) was kept fixed during the growth. The filtered compressed nitrogen air was used as gas carrier at a flow of 4 l/min. The total deposition time was maintained at 20 min. After deposition, the coated substrates were allowed to cool down naturally to room temperature (Figure 1).

The crystalline structure was analyzed by X-ray diffraction, using a Siemens D500 diffractometer with monochromatic CuKα radiation (* λ* = 1.54 Å) [16]. The surface morphology of the Mn

_{3}O

_{4}thin film is further analyzed using atomic force microscope (AFM) using a Veeco digital instrument 3 A microscope. The sample was probed in a tapping mode with a nanometer scale.

## 3. Magnetic study

The magneto-optic Faraday effect presents the connection between optics, magnetism and atomic physics. Faraday rotation manifests itself as a rotation of the polarization plane of the light passing through the sample in the presence of a magnetic field and is characterized by the Verdet constant (* V*) of the investigated sample (Figure 2). The rotation angle

*can be expressed by the formula [17]:*ϕ

where * A* is a constant determined from the matrix elements of the interband transitions,

*is the wavelength and*λ

λ

_{0}is the wavelength related to the interband transitions and corresponding to the natural frequency

ω

_{0}= 2

*/*π

λ

_{0}of an effective harmonic oscillator. The relationship between the rotation angle and the Verdet constant is

*= VBl, where B is the magnetic induction of the field and l is the sample thickness (Figure 3). The magneto-optic anomaly factor*ϕ

*(Figure 4) can be taken as a measure of the degree of covalency that exists in the bonds connecting the ions and atoms [18]:*γ

In the paramagnetic materials, the anomaly factors * γ* can vary with the wavelength of the incident light, even if there is only one absorption frequency contributing to dispersion. The dispersivity of the investigated crystal can be presented by the following equation:

The spectral dependence of the spin-spin exchange interaction constant * K* in the case of Mn

_{3}O

_{4}thin film is presented in Figure 5. It can be calculated by the following formula [19]:

where * V* is the Verdet constant,

*is the magnetic susceptibility of the sample (Figure 6) and*χ

λ

_{g}represents the band gap of the material. For the investigated vanadium doped crystal

λ

_{g}= 556 nm [16]. When the spin-spin exchange interaction constant has negative values, the spins align antiparallel to each other so that the net magnetization is zero. Therefore, the material is antiferromagnet and it is modeled to be made up of two sublattices [20].

The exchange interaction energy leads to the alignment of neighboring atomic moments and this forms magnetic domains. The magnetostatic interaction energy tries to break them into smaller domains oriented antiparallel to each other. The domain size depends on the relative counterbalance between both energies. The system is composed of a single domain, when the magnetostatic energy does not allow the breaking of domains into smaller parts. This condition is connected with the critical value _{c} of the radius of a spherical particle. If the rotation of the atomic magnetic moments is coherent (the structure is a single-domain one), then the particle can be characterized by its total magnetic supermoment * V* is the particle volume and

M

_{S}is saturation magnetization. The ferromagnetism and super paramagnetism are observed, respectively, below and above the blocking temperature

T

_{B}. Its origin is connected with magnetic anisotropy within particles. This anisotropy tends to orientate the particle supermoment along some preferential direction.

The spin-orbit coupling and dipolar interaction dictate preferential orientation directions of the magnetic moments because of the finite size of the particles. The magnetic anisotropy energy _{A} of the particles can be described by a simple model. This model includes two main contributions: crystalline and shape, which are connected with the core and surface atoms, respectively. When the particles are spherical and the anisotropy is uniaxial crystalline, the considered situation is the simplest [21]. If the magnetic anisotropy is proportional to the particle volume, then * K* is the effective uniaxial anisotropy constant (per unit volume) and

*particle can be written as:*i

where _{i }is the angle between the magnetic supermoment of the particle and the easy anisotropy axis (Figure 7). The moment of the particle has therefore two preferred orientations, energetically equivalent, along the easy-magnetization anisotropy axis direction. Both directions are separated by an energy barrier _{B} of height _{i}_{i}.

If the particles are magneto anisotropic, the calculation of equilibrium magnetization is complicated. The special role for nanoparticles having superficial anisotropy is the violation of local symmetry surroundings and crystal field change that acts on the magnetic ions from the surface. The simplest type of magnetic anisotropy is the easy anisotropy axis.

When external magnetic field is applied over the nanoparticles, it tries to orientate their magnetic moments in the direction of its action. Therefore, if the magnetic field is applied perpendicular of anisotropy axis and the orientation of magnetic moment of the particle is labeled with * i*, the next equation is fulfilled:

where _{A} and _{Z }are Zeeman energies.

The influence of external magnetic field in the orientation of magnetic supermoments is known as Stoner-Wohlfart model [22]. They assume that the coherent rotation of atomic magnetic moments exists and the magnetic field is applied at a certain angle _{0} with respect to the easy anisotropy axis. When the temperature effects are ignored the problem can be solved with minimal number of energetic arguments. The situation is very interesting, when we can describe the change of magnetic moments in dependence of anisotropic energy barrier and the temperature _{B}. This is the reason for the study of a simple case when the field is applied parallel to the easy anisotropy axis. It should also be noted that the particles are identical and do not interact with each other. The application of the field leads only to their arrangement in the direction of the easy anisotropy axis. Thus, the following equation can be written (Figure 8):

when * θ* = 0,

*with values*π

*= 0. The value*H

*= 0 is valid, when the moment of particles is oriented parallel to the magnetic field (*θ

*=*θ

*is fulfilled when the orientation of the moment of the particles is antiparallel to the magnetic field (*π

E

_{B}≈

*. The characteristic time of heat fluctuations of the magnetic moments can be presented by the formula [23]:*KV

where

The multiplier _{0} depends on many parameters such as temperature, gyromagnetic ratio, saturation magnetization, anisotropy constant and the size of the energy barrier. It is of the order of 10^{−9} – 10^{−13} s [24]. The formula (9) determines the characteristic time of establishing heat equilibrium in the system of noninteracting single-domain magnetic particles. At high temperatures, the following inequality is fulfilled: _{m}. In this case, the system should not appear magnetic hysteresis. When _{m }> * τ*, the system is in the super paramagnetic state and it quickly reaches equilibrium magnetization, when the temperature or the external field change. In the opposite case, when the external magnetic field changes, the system does not fail to relax in the new equilibrium state for the time

τ

_{m }and its magnetization does not change. The case when

τ

_{m}=

*is connected with the blocking temperature:*τ

Formula (10) presents the temperature _{B}, when the magnetic field is zero. This temperature decreases with the increasing of the external magnetic field by the law:

where * k* = 2 for small fields and

*= 2/3 for big fields and*k

The magnetization curve increasing to reaching saturation magnetization is measured in the study of the magnetic properties of the hausmannite Mn_{3}O_{4 }which containing nano-objects. To determine the temperature dependence of the magnetic moment Mare carried out two types of measurements—cooling in zero magnetic field (zero-field-cooling, ZFC) and cooling in a nonzero field (field-cooling, FC). The sample is cooled (to liquid helium temperature) during the method of ZFC in the absence of a magnetic field and then a small field (2–5 kOe) is included. The temperature values begin slowly to increase and the magnetic moment (_{ZFC}) values can be registered. The technique FC differs from ZFC only by the fact that a sample is cooled in a nonzero magnetic field. The curves _{ZFC}(* T*) and

M

_{FC}(

*) for the magnetic nano-objects coincide at sufficiently high temperatures, but they begin to vary below a temperature*T

T

_{H}(irreversibility temperature). The curve

M

_{ZFC}(

*) has a maximum at a certain temperature*T

T

_{max }and it increases monotonically down to very low temperatures (Figure 11). The dependence of the magnetization from the applied field at two various temperatures is shown in Figure 12(a) and (b). For an idealized system containing similar nanoparticles with uniaxial anisotropy and random orientation of easy magnetization axis, the difference of the temperature dependence

M

_{ZFC}(

*) and*T

M

_{FC}(

*) at a qualitative level follows from Eq. (8). In the case of zero field during the cooling below the blocking temperature, the magnetic moments of the particles are oriented along their axes of easy magnetization (*T

*= 0 in Eq. (8)). The total magnetic moment of the system is zero in the beginning and in the end of the cooling process. The magnetic moments for which*θ

*< 90° (see Eq. (8)) it is not necessary to overcome the energy barrier, when the external field*θ

*is included. Therefore, they turn to a position with minimum energy, creating a nonzero magnetization of the system. In contrast, the magnetic moments for which the external field is included (*H

*> 90°) are separated from the minimum energy of the potential barrier. They can overcome only this barrier for a very long time (see Eq. (9)). Therefore, in the case of ZFC measurements (*θ

*<*T

T

_{B}), the system is in a metastable state with a small total magnetic moment

At * T* =

T

_{B}, the system jumps into a stable superparamagnetic state with magnetic moment

When * T* >

T

_{B}. The sample is cooled in a nonzero magnetic field during FC measurement and the magnetization at temperatures above

T

_{B}is determined by formula (12). At

*<*T

T

_{B}, the system cannot change its magnetization during the measurement. Therefore, the magnetic moment which is determined by the FS method for

*<*T

T

_{B }is

The curves _{ZFC}(* T*) and

M

_{FC}(

*) are not separated at*T

*=*T

T

_{B }for a system consisting of a single-domain nanoparticles with dispersion of the size, the shape, etc. Their separation realizes at a higher temperature

T

_{H }>

T

_{B}, where

T

_{H}is called the irreversibility point. Another characteristic point on the curve

M

_{ZFC}(

*) is the temperature*T

T

_{max }which is often equated with the average blocking temperature of the system <

T

_{B}>. At temperatures below <

T

_{B}> we can observe the increase of

M

_{FC}(

*) that replaced section “saturation” and sometimes we can observe a maximum [25]. The value of*T

T

_{H}can be identified with the blocking temperature for the particles with a maximum size and the temperature

T

_{max }corresponds to a blocking temperature for particles with minimum size. However, all of these characteristic temperatures (as well as their relationship with the particle size distribution by volume) may depend on the cooling rate and the subsequent heating of the sample. The intensity of the interaction between the particles also influences on the characteristics temperatures. If the heating rate of the sample is much smaller than its cooling rate, a maximum may be formed on the curve

M

_{FC}(

*) at*T

*< <*T

T

_{B}> [26].

Note that the difference between the curves _{ZFC}(* T*) and

M

_{FC}(

*) is not observed only in systems of magnetic nano-objects, but also in macroscopic magnets with disorder elements (frustration of exchange bonds, topological disorder, structural defects) and even in ordered ferromagnets with a large magnetic anisotropy. The difficulties of theoretical research of the magnetic hysteresis in nano-objects consist in the fact that the phenomenon is nonlinear, nonequilibrium and nonlocal and it is caused by the existence of energy minima (due to the magnetic anisotropy) and separated barriers which have complicated dependence of the external magnetic field. The results of theoretical studies of simple models rarely give an acceptable description for real magnetic nanomaterials since their microstructure do not account, in particular, the influence of boundaries and defects on the local magnetization is not taken into account. The ferromagnetic-to-superparamagnetic transition of the hausmannite particles in the zero-field cooled (ZFC) and field cooled (FC) curves is presented in Figure 8.*T

The orientation of electron spin in the manganese ions is very interesting for study. One of the electrons of the inner shell is responsible for the magnetism and its spin is oriented upwards. If the conductivity electrons move in the same region, where there is the motion of “magnetic” electrons than their spins rotate in the opposite direction. Thus, the conductivity electrons can rotate the electron spins of the other ions. This double interaction is equivalent of the interaction between two “magnetic” electrons which are oriented in one direction. This means that the neighboring spins have to be parallel, which is a result from the action of intermediate environment. This mechanism does not require all electrons to be oriented upwards. It is sufficient that conductivity electrons can be slightly oriented downwards. Thus, the possibility for the rotation of “magnetic” electrons upwards increases.

The energy of electron spin can be presented as (Figure 13):

where * μ* = 2.8363*10

^{−4}eVT

^{−1},

*= 5700 m*λ

^{−1},

ε

_{0}= 8.8542*10

^{−12}Fm

^{−1}and

*= 8*10*c

^{8}m/s (Figure 13).

On the other hand, we can write that

where * d* = 2.2971 × 10

^{−10}m.

The magnetic moment of the electron is

where * k* = 8.6173 × 10

^{−5}eVK

^{−1}:

The energy of interaction between two electrons is expressed by the next equation (Figure 14):

## 4. Conclusions

The magneto-optic anomaly factor * γ* for the hausmannite thin films decreases with the increasing of the wave length. The spin-spin exchange interaction constant

*decreases to*K

λ

_{1}= 2172 nm (for Mn

^{2+}ions) and

λ

_{2}= 2180 nm (for Mn

^{3+}ions) and after that it begins to increase. The magnetic susceptibility of Mn

_{3}O

_{4 }has maximal value, when the intensity of applied magnetic field is 5868 Oe. The anisotropic energy barrier decreases with the increasing of

*and*H

*. The energy barrier increases quadratic with the increasing of*θ

*and*H

*. The energy of electron spin*θ

*has bigger values for Mn*x

^{3+}ions in the case when

*= 10 K. The values of energy of interaction between two electrons are bigger when*T

*= 35 K.*T

## Acknowledgments

The author would like to express here gratefulness to Pr. Dr. Ing. Karem Boubaker, Unité de physique des dispositifs à semi-conducteurs, Tunis EL MANAR University, Tunisia, for providing hausmannite thin films for investigation. The author would like to thank for the financial support of the project RD-08-109/08.02.2016 from Shumen University “Konstantin Preslavsky.”

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