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Magnetic Properties of Hausmannite Thin Films

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Petya Petkova

Submitted: May 19th, 2016 Reviewed: October 25th, 2016 Published: March 8th, 2017

DOI: 10.5772/66533

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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 Mn3O4 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—Mn2+ and Mn3+. Thus, spinel Mn3O4 occurs in nature as the mineral hausmannite [Mn2+Mn23+O4]. The Mn2+ cations occupy the tetrahedral sites and Mn3+cations occupy the octahedral sites [2]. The nanoparticles of Mn3O4 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.

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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 [811] 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 [1215].

Thin films of Mn3O4 were grown at 350°C on 1 × 2 cm2 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 (MnCl2.6H2O) 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).

Figure 1.

The experimental set up for the spray pyrolysis technique.

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 Mn3O4 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.

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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 ϕcan be expressed by the formula [17]:

Figure 2.

The Verdet constant for Mn3O4 in the spectral region 500–2500 nm.

ϕ(λ) =A/(λ2λ02),E1

where Ais a constant determined from the matrix elements of the interband transitions, λis the wavelength and λ0 is the wavelength related to the interband transitions and corresponding to the natural frequency ω0 = 2π/λ0 of an effective harmonic oscillator. The relationship between the rotation angle and the Verdet constant is ϕ= VBl, where B is the magnetic induction of the field and l is the sample thickness (Figure 3). The magneto-optic anomaly factor γ(Figure 4) can be taken as a measure of the degree of covalency that exists in the bonds connecting the ions and atoms [18]:

Figure 3.

The Faraday rotation angle as a function of the wave length (500–2500 nm) for Mn3O4 thin film.

Figure 4.

The magneto-optic anomaly factorγfor hausmannite in the spectral region 500–2500 nm.

γ = ϕe2mc2λDE2

In the paramagnetic materials, the anomaly factors γcan 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:

D= γcd2ndλ2 .E3
 γ=  VBleλ22mc2d2ndλ2 .E4

The spectral dependence of the spin-spin exchange interaction constant Kin the case of Mn3O4 thin film is presented in Figure 5. It can be calculated by the following formula [19]:

Figure 5.

The constant of spin-spin exchange interactionK(λ) for Mn2+ (a) and Mn3+ (b) in Mn3O4 thin film (500–2500 nm).

K(λ)= V[((λλg)21)]3/2χλ,E5

where Vis the Verdet constant, χis the magnetic susceptibility of the sample (Figure 6) and λgrepresents the band gap of the material. For the investigated vanadium doped crystal λg= 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].

Figure 6.

The dependenceχ(H) = dM/dHfor Mn3O4 in the magnetic field from −20,000 to 20,000 Oe.

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 rcof 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  |μp|= MSV, where Vis the particle volume and MSis saturation magnetization. The ferromagnetism and super paramagnetism are observed, respectively, below and above the blocking temperature TB. 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 EAof 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  Keff=KVn^, where Kis the effective uniaxial anisotropy constant (per unit volume) and n^is the unitary vector describing the easy-magnetization anisotropy. The energy term for the iparticle can be written as:

EA(i)= KiVi(μin^i|μi|)2= KiVicos2θ,E6

where θiis 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 EBof height KiVi.

Figure 7.

Schematic drawing of the ideal simplest model of noninteracting and parallel aligned easy axes along the applied field.

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:

Ei= EA(i)+ EZ(i)= KiVi(μin^i|μi|)2 μi.H,E7

where EAand EZare 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 θ0 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 TB. 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):

Figure 8.

The dependence of anisotropic energy barrier from the external magnetic field (a) and the angle between the applied field and easy anisotropy axis (b).

E= KVcos2θ MSVHcos θE8

when H <2K/MS, Eq. (8) gives two local minima (the directions of easy magnetization) at θ= 0, πwith values Emin= KV ± MSVH(Figure 9) and one maximum (the direction of hard magnetization) at θ=arccos(HMS/2K), with value Emax=KV(HMS/2K)2. The direction of hard magnetization is perpendicular of the anisotropy axis in the case, when H= 0. The value θ= 0 is valid, when the moment of particles is oriented parallel to the magnetic field (). The equation θ= πis fulfilled when the orientation of the moment of the particles is antiparallel to the magnetic field (). The difference between the shapes of the energy wells is connected with the different energy barriers. These barriers depend on the orientation of the moments of particles to the applied field which can be written as EBand EBfor the cases of antiparallelism and parallelism, respectively. The anisotropy field of the particles is introduced as HA= 2K/MS. The energy barriers can be calculated as the difference between the minimal and maximal energies: EB= KVHA2(H HA)2and EB= KVHA2(H+ HA)2(Figure 10). The difference between the heights of energy barriers also shows a change in the characteristic time for relaxation of the particles, since it depends on the relative orientation of the magnetic dipoles to the field: antiparallel oriented particles have smaller energy barrier in comparison with the particles which are oriented along the easy anisotropy axis. They have also small heat energy sufficient to overcome the barrier. The parallel oriented particles are limited by deeper anisotropy well and the jump of their magnetic moments requires higher heat energy. When the particle has to rotate its magnetic moment, the energy of jump beyond the energy barrier is EBKV. The characteristic time of heat fluctuations of the magnetic moments can be presented by the formula [23]:

Figure 9.

The local minimal energy ±Emin(H) in the directions of easy magnetization for the hausmannite Mn3O4.

Figure 10.

The dependence of the energy barriers EB of: applied magnetic field and angle ? in the case of antiparallelism.

τ=τ0exp(EB/kBT),E9

where  EB/kBT 1.

The multiplier τ0 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: EB/kBT 1. Therefore, the time of transition of the system in the state with minimal energy is small in comparison with the characteristic time of measurement τm. In this case, the system should not appear magnetic hysteresis. When EB/kBT 1, the time of transition of a system in the equilibrium state depends on the size of the particles. If τm> 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 τmand its magnetization does not change. The case when τm= τis connected with the blocking temperature:

TB= KV25kB.E10

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

TB(H)= TB(0)(1 HHc)k, E11

where k= 2 for small fields and k= 2/3 for big fields and Hc= 2kMS.

The magnetization curve increasing to reaching saturation magnetization is measured in the study of the magnetic properties of the hausmannite Mn3O4 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 (MZFC) 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 MZFC(T) and MFC(T) for the magnetic nano-objects coincide at sufficiently high temperatures, but they begin to vary below a temperature TH(irreversibility temperature). The curve MZFC(T) has a maximum at a certain temperature Tmax 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 MZFC(T) and MFC(T) 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 (θ= 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 His 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 (θ> 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 (T< TB), the system is in a metastable state with a small total magnetic moment MS2H3kV, which does not depend on the temperature.

Figure 11.

FC and ZFC induced magnetization as a function of temperature measured in a 2500 Oe field.

Figure 12.

The magnetizationM(H) of hausmannite thin film for two temperaturesT= 10 K (a) andT= 35 K (b).

At T= TB, the system jumps into a stable superparamagnetic state with magnetic moment

MZFC  MS2VH3kBTE12

When MSVHkBT and random orientation of the easy magnetization axes of particles, formula (12) is also valid for T> TB. The sample is cooled in a nonzero magnetic field during FC measurement and the magnetization at temperatures above TBis determined by formula (12). At T< TB, the system cannot change its magnetization during the measurement. Therefore, the magnetic moment which is determined by the FS method for T< TBis

MZFC  MS2VH3kBT=const.E13

The curves MZFC(T) and MFC(T) are not separated at T= TBfor a system consisting of a single-domain nanoparticles with dispersion of the size, the shape, etc. Their separation realizes at a higher temperature TH> TB, where THis called the irreversibility point. Another characteristic point on the curve MZFC(T) is the temperature Tmax which is often equated with the average blocking temperature of the system <TB>. At temperatures below <TB> we can observe the increase of MFC(T) that replaced section “saturation” and sometimes we can observe a maximum [25]. The value of THcan be identified with the blocking temperature for the particles with a maximum size and the temperature Tmax 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 MFC(T) at T< <TB> [26].

Note that the difference between the curves MZFC(T) and MFC(T) 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.

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):

Figure 13.

The energy of electron spinxas a function of the intensity of magnetic fieldHfor Mn3+ ions at temperaturesT= 10 K andT= 35 K.

x= |μ|(H+ λMε0c2),E14

where μ= 2.8363*10−4 eVT−1, λ= 5700 m−1, ε0 = 8.8542*10−12 Fm−1 and c= 8*108 m/s (Figure 13).

On the other hand, we can write that

x= |m|(H+dM/ε0c2)/kT,E15

where d= 2.2971 × 10−10 m.

The magnetic moment of the electron is

|m|= |μ|(H+ λMε0c2)(H+dM/ε0c2)/kT=2.4441 × 107,E16

where k= 8.6173 × 10−5 eVK−1:

thx=th[|m|(H+ dM/ε0c2)/kT]E17

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

Figure 14.

The average value of the energy of interaction between two electrons in Mn3+ ions as a function of the intensity of magnetic fieldH: (a)T= 10 K and (b)T= 35 K.

U= N|μ|(H+ M2ε0c2)thxE18
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4. Conclusions

The magneto-optic anomaly factor γfor the hausmannite thin films decreases with the increasing of the wave length. The spin-spin exchange interaction constant Kdecreases to λ1 = 2172 nm (for Mn2+ ions) and λ2 = 2180 nm (for Mn3+ ions) and after that it begins to increase. The magnetic susceptibility of Mn3O4 has maximal value, when the intensity of applied magnetic field is 5868 Oe. The anisotropic energy barrier decreases with the increasing of Hand θ. The energy barrier increases quadratic with the increasing of Hand θ. The energy of electron spin xhas bigger values for Mn3+ ions in the case when T= 10 K. The values of energy of interaction between two electrons are bigger when T= 35 K.

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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.”

References

  1. 1. Xiao J, Yang S, Wan I, Xiao F, Wang S, J. Power Sources 245 (2014) 1027
  2. 2. Chen W Z, Jiao Z, Wu H M, Shek H C, Wu L M C, Lai L K J, Progr. Mater. Sci. 56 (2011) 901
  3. 3. Sanga B, Nagoyab Y, Kushiyab K, Yamase O, Sol. Energ. Mat. Sol. Cells 75 (2003) 179
  4. 4. Fu Q, Hu L, Yu D, Sun J, Zhang H, Huo B, Zhao Z, Mater. Lett. 63 (2009) 316
  5. 5. Shimomura T, Kim D, Nakayama M, J. Lumin. 112 (2005) 191
  6. 6. Henley J S, Ashfold R N M, Cherns D, Surf. Coat. Technol. 177–178 (2004) 271
  7. 7. Sasi B, Gopchandran G K, Sol. Energ. Mat. Sol. Cells 91 (2007) 1505
  8. 8. Boukhachem A, Boughalmi R, Karyaoui M, Mhamdi A, Chtourou R, Boubaker K, Amlouk M, Mater. Sci. Eng. B 188 (2014) 72
  9. 9. Krunks M, Soon J, Unt T, Mere A, Mikli V, Vacuum 107 (2014) 242
  10. 10. Sharmaa R, Acharya D A, Shrivastava B S, Shripathi T, Ganesan V, Optik 125 (2014) 6751
  11. 11. Kerli S, Alver U, Yaykaşlı H, Appl. Surf. Sci. 318 (2014) 164
  12. 12. Boukhachem A, Kamoun O, Mrabet C, Mannai C, Zouaghi N, Yumakc A, Boubaker K, Amlouk M, Mater. Res. Bull. 72 (2015) 252
  13. 13. Boukhachem A, Bouzidi C, Boughalmi R, Ouerteni R, Kahlaoui M, Ouni B, Elhouichet H, Amlouk M, Ceram. Int. 40 (2014) 13427
  14. 14. Boukhachem A, Ziouche A, Ben Amor M, Kamoun O, Zergoug M, Maghraoui-Meherzi H, Yumak A, Boubaker K, Amlouk M, Mater. Res. Bull. 74 (2016) 202
  15. 15. Arifa H, Boukhachem A, Askri B, Boubaker K, Yumak A, Raouadi K, Ceram. Int. 42 (2016) 2147
  16. 16. Larbi T, Ouni B, Boukhachem A, Boubaker K, Amlouk M, Mater. Res. Bull. 60 (2014) 457–466
  17. 17. Kizel A V, Krassilov I J, Burkov I V, Uspehi fizicheskih nauk 114 (1974) 295
  18. 18. Sivaramakrishnan V, Magneto-optic study of some inorganic acids and their salts, Journal of the Indian Institute of Science. 1954
  19. 19. Syed M, Siahmakoun A, Optical Mat. 27 (2005) 1629–1636
  20. 20. Alwyn Scott, Encyclopedia of Nonlinear Science, Edited by Scott A, Taylor & Francis Group, New York, 2005
  21. 21. Jönsson E P, Super paramagnetism and spin glass dynamics of interacting magnetic nanoparticle systems, Edited by Rice SA, Advances in chemical physics, Hoboken, JN: John Wiley & Sons, Inc, 2004, vol. 128, pp. 191–248
  22. 22. Stoner C E, Wohlfarth P E, Proc. R Soc. Lond. A. 240 (1948) 599–642
  23. 23. Speliotis E D, J. Magn. Magn. Mater. 193 (1999) 29
  24. 24. Suzdalev P I, Suzdalev I P, Russian Chem. Rev. 70(3) (2001) 177–210
  25. 25. Chantrell W R, Grady O K, Magnetism, Boston: Dordrecht, 1992
  26. 26. Veynger I A, Zabrodskii G A, Tisnek V T, Phys. Technol. Semiconduct. 34 (2000) 1

Written By

Petya Petkova

Submitted: May 19th, 2016 Reviewed: October 25th, 2016 Published: March 8th, 2017