Experimental parameters of Ni0.3Zn0.7Fe2O4 thin-film sol-gel spin-coating deposition process.
\r\n\t
",isbn:"978-1-83968-921-5",printIsbn:"978-1-83968-920-8",pdfIsbn:"978-1-83968-922-2",doi:null,price:0,priceEur:0,priceUsd:0,slug:null,numberOfPages:0,isOpenForSubmission:!1,hash:"9528d3b1ff011d68022c4fa750b4bc24",bookSignature:"Dr. Kieran Richard Hickey",publishedDate:null,coverURL:"https://cdn.intechopen.com/books/images_new/8491.jpg",keywords:"Tornadoes Causes, Characteristics, Features, Impacts, Temporal Variability, Spatial Variability, Regional Change, Climate Change, Climatological Context, Trends, Patterns, Projections",numberOfDownloads:null,numberOfWosCitations:0,numberOfCrossrefCitations:0,numberOfDimensionsCitations:null,numberOfTotalCitations:null,isAvailableForWebshopOrdering:!0,dateEndFirstStepPublish:"September 28th 2020",dateEndSecondStepPublish:"October 26th 2020",dateEndThirdStepPublish:"December 25th 2020",dateEndFourthStepPublish:"March 15th 2021",dateEndFifthStepPublish:"May 14th 2021",remainingDaysToSecondStep:"3 months",secondStepPassed:!0,currentStepOfPublishingProcess:4,editedByType:null,kuFlag:!1,biosketch:"Dr. Kieran R. Hickey is currently Head of the Department of Geography and also Head of the School of the Human Environment at the University College Cork, in addition, he is a Fellow of the Royal Meteorology Society and the Royal Geographical Society.",coeditorOneBiosketch:null,coeditorTwoBiosketch:null,coeditorThreeBiosketch:null,coeditorFourBiosketch:null,coeditorFiveBiosketch:null,editors:[{id:"17924",title:"Dr.",name:"Kieran",middleName:"Richard",surname:"Hickey",slug:"kieran-hickey",fullName:"Kieran Hickey",profilePictureURL:"https://mts.intechopen.com/storage/users/17924/images/system/17924.jpg",biography:"Dr. Kieran R. Hickey is a Senior Lecturer in Physical Geography in the School of the Human Environment in University College Cork, Rep. of Ireland where he is currently Head of the Department of Geography and also Head of the School of the Human Environment. He earned his B.A. in Geography and Economics in 1986 and his M.A. in Geography in 1990 from University College Cork, Republic of Ireland and his D.Phil from Coventry University, England in 1997. His research is in storms and hurricanes, climate change, historical climatology and climate disasters. He is a Fellow of the Royal Meteorology Society and the Royal Geographical Society. 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From chapter submission and review, to approval and revision, copyediting and design, until final publication, I work closely with authors and editors to ensure a simple and easy publishing process. I maintain constant and effective communication with authors, editors and reviewers, which allows for a level of personal support that enables contributors to fully commit and concentrate on the chapters they are writing, editing, or reviewing. I assist authors in the preparation of their full chapter submissions and track important deadlines and ensure they are met. I help to coordinate internal processes such as linguistic review, and monitor the technical aspects of the process. As an ASM I am also involved in the acquisition of editors. 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Venkateswarlu",coverURL:"https://cdn.intechopen.com/books/images_new/371.jpg",editedByType:"Edited by",editors:[{id:"58592",title:"Dr.",name:"Arun",surname:"Shanker",slug:"arun-shanker",fullName:"Arun Shanker"}],productType:{id:"1",chapterContentType:"chapter",authoredCaption:"Edited by"}},{type:"book",id:"878",title:"Phytochemicals",subtitle:"A Global Perspective of Their Role in Nutrition and Health",isOpenForSubmission:!1,hash:"ec77671f63975ef2d16192897deb6835",slug:"phytochemicals-a-global-perspective-of-their-role-in-nutrition-and-health",bookSignature:"Venketeshwer Rao",coverURL:"https://cdn.intechopen.com/books/images_new/878.jpg",editedByType:"Edited by",editors:[{id:"82663",title:"Dr.",name:"Venketeshwer",surname:"Rao",slug:"venketeshwer-rao",fullName:"Venketeshwer Rao"}],productType:{id:"1",chapterContentType:"chapter",authoredCaption:"Edited by"}}]},chapter:{item:{type:"chapter",id:"63869",title:"Spin-Coating Technique for Fabricating Nickel Zinc Nanoferrite (Ni0.3Zn0.7Fe2O4) Thin Films",doi:"10.5772/intechopen.80461",slug:"spin-coating-technique-for-fabricating-nickel-zinc-nanoferrite-ni0-3zn0-7fe2o4-thin-films",body:'\nNiZn nanocrystalline ferrite thin films have a spinel crystal structure which have been a subject of extensive attempt because of their potential applications in high-density magneto-optic recording devices, magnetic refrigeration and microwave materials due to its high electrical resistivity, low magnetic coercivity and low eddy current losses. NiZn nanoferrite thin films are structure sensitive, and it is not easy to produce a stoichiometric and point-defect-free NiZn ferrite, for high-resistivity applications. In NiZn ferrite thin-film fabrication, the accurate composition control and the uniformity throughout the film deposition are important. It is well known that properties of ferrite materials strongly depend on the preparation conditions. This issue is important in NiZn ferrite thin films because the effect of temperatures will lead to the change in the chemical composition of the ferrite films. These also will result in non-uniformity of film composition and the magnetic hysteresis parameter of ferrites. High-temperature synthesis of NiZn thin-film ferrite results in the evaporation of some constituents that lead to the nonstoichiometry, and zinc volatilization at higher temperature can result in the formation of Fe2+ ions that lead to increase the electron hopping and reducing the electrical resistivity [1]. Therefore, a low-temperature synthesis is required for the synthesis of NiZn ferrite film. Properties of ferrite film depend on the preparation route, due to its strong influence on type of the film (polycrystalline and epitaxial), particle size, chemical homogeneity, microstructure and cationic distribution between tetrahedral and octahedral sublattice sites [2, 3]. Synthesis of ferrite thin film is of great interest among researchers in this field of study. Widely used techniques are utilized to produce desirable final product of nickel zinc ferrite. These techniques can be classified into two major techniques which are the conventional technique and the nonconventional technique. The starting materials are conventionally oxides or precursors of oxide of the cations. This process involves the interdiffusion of the various metal ions of preselected compositions to form a mixed crystal. The nonconventional powder processing in a liquid medium may produce intermediate, finely divided mixed hydroxides or mixed organic salts to assist the subsequent diffusion process [4]. Most of ferrite films have been prepared using sputtering and pulsed laser deposition. Somehow, sol-gel method is a kind of potential film preparation process, which possesses advantages of chemical homogeneity, easy component adjustment, low calcination temperature and low cost. Spin coating gives an advantage to liquid film that leads to uniformity in thickness during spin-off [5]. Once uniform, it tends to remain provided the viscosity is not shear-dependent and does not vary over the substrate. Other than that, sol-gel and hydrothermal routes of ferrite synthesis have shown increasing importance. Recent years are marked by growing interest in sol-gel processed films in new areas, particularly in microelectronics. This is mainly due to intensively developing applications of silicate or siloxane sol-gel films in the VLSI multilevel interconnection process, the preparation of ferroelectric films for nonvolatile memory [6].
\nSpin coating is widely used in modern optical and microelectronic industries [7]. The understanding of its underlying physics remains limited, a fact attributed to the lack of experimental data for the evolution of various parameters during the process [8, 9], leading to the need for new evolution tools. A relative study of nickel zinc ferrite by sol-gel route and conventional solid-state reaction was carried out [10]. It was claimed that the homogeneity and high purity in the sol-gel samples and small grains confirmed the finer particles. Ni0.36Zn0.64Fe2O4 (NZF) thick films have been synthesized using sol-gel dip-coating method [11]. Combination with dispersion of ceramic NZF particles in starting sols has been proved to be useful for producing thick nickel zinc ferrite films. The best NZF powders are formed from dispersing at 300°C by hydrothermal grow. Nickel zinc ferrite thin films are successfully prepared using spin-deposited citrate-precursor route [12]. The formation of crystalline film at low temperature even though films were found to be X-ray amorphous revealed the formation of uniform grains in nanometer size range. Besides that, NiZn ferrite film was successfully fabricated by using photosensitive sol-gel method. The photosensitive gel film can be the photoresist of itself during the preparation process. The fine pattern of Ni0.5Zn0.5Fe2O4 film is obtained through UV radiation, rising and heat treatment [13]. The great potential of combining the microwave technique with nonaqueous sol-gel chemistry was successful [14]. Many transition metal ferrite nanoparticles with high crystallinity are uniformly morphological besides homogenous metal ferrite thin films on flat and curved substrates. The thickness of film can easily be adjusted in the range of 20–80 nm using precursor concentration. Other synthesis techniques of nickel zinc ferrite thin films are chemical vapor deposition, spray pyrolysis, sputtering, pulsed laser deposition and spin spray. Of these methods the earliest used was vapor deposition of metals followed by oxidation [15]. The films were porous and polycrystalline and approximately 1000 Å thick. Many common ferrites produced by this method were single-phase spinel in crystal structure. Spray pyrolysis is complicated and expensive and required special equipment and sometimes high processing temperature above 500°C. By using spray pyrolysis technique [3, 16], very homogenous ferrite thin films were obtained with good reproducibility. Nevertheless, for spinel ferrite thin-film growth, this method is used rarely. Also only a few works can be found on NiZn ferrites, obtained by spray pyrolysis where a focus on the investigation of microstructural, optical and magnetic properties was held [17]. Apart from that, the effect of oxygen plasma treatment on magnetic and NiZn ferrite films using the spin-spray plating method has been employed [18]. The oxygen plasma treatment increased the number of nucleation sites of ferrite and enhanced adhesion of the films to the substrates. It has been reported that spinel Zn ferrite can be synthesized without substrate heating by pulsed laser deposition [19]. However, this technique needs post-deposition and requires sputtered film at a high temperature to grow the spinel ferrite structure. The results were optimized and obtained 4000 Å NiZn ferrite films with low in-plane coercivity of Hc = 15.2 Oe and relatively high saturation magnetization Ms = 318 emu/cm3. Some other research works was working on preparing NiZn ferrite films by magnetron sputtering method. Most of the sputtered ferrite films must be deposited at a high substrate temperature and need high heat treatment to obtain ordered spinel structure. Sputtering method is prepared at room temperature without any post-annealing treatment [20]. By controlling the relative oxygen flow, grain size in a range 10–20 nm was developed. It revealed a maximum saturation magnetization of about 151 emu/cm3. The static magnetic measurement results are affected by the crystallinity, grain dimension and cation distribution.
\nNiZn ferrite thin film is prepared by a sol-gel process and spin-coating technique. The starting materials nickel nitrate hexahydrate (Ni(NO3)2·6H2O) (Sigma Aldrich, 99.999%), iron nitrate nonahydrate (Fe(NO3)3·9H2O) (Alfa Aesar, 99.999%) and zinc nitrate hexahydrate (Zn(NO3)2·6H2O) (Alfa Aesar, 99.999%) with high purity were used as a precursor for the starting sol preparation. The materials are in metal nitrate hydrates which are soluble in alcohol solvents. Acetone and deionized water were used as a medium for sol-gel reaction. Acetic acid (C6H8O7H2O) (Alfa Aesar, 99.99%) acts as the chelating agent. The precursors were dissolved in deionized water and stirred for 15 min with a molar ratio of Ni:Zn:Fe = 1:1:2 using hot plate. The former salt solution was dissolved into acetic acid solution with a molar ratio of 1:1 and stirred for 3 h at 80°C. A sol-gel formed was left 24 h for age.
\nThe thin film was deposited on indium tin oxide (ITO) glass. ITO has higher melting point around 1926°C. There is no phase change of substrate during deposition of the film. The typical properties of ITO glass substrate are listed in Table 1. The film deposition consists of substrate wash and spin coating. The steps are to wash the substrates firstly with distilled water in ultrasonic bath for 15 min. The substrate was then washed in ultrasonic bath using acetone liquid for 15 min. Coating was carried out in a clean room by using a spin coater. The setting parameters were listed in Table 2. The aged sol of 1.0 ml (Section 3.1) was dropped on ITO glass substrate and spin coated for 25 s at 3500 rpm (revolutions per min). The deposition was repeated several times to obtain the required thickness (300 nm). The film thickness can be controlled by the number of coating. The film with desired thickness can be obtained by repeating the deposition cycle. Then drying films were performed in a room temperature for a few minutes and annealed in air at temperature 400, 500, 600 and 700°C, respectively, with an increment of 100°C for 1 h. Annealing process was performed in a box furnace with rate of 5°C/min.
\nGlass substrate | \nITO coating glass | \n
Size of substrate | \n25 × 12 × 1.1 mm | \n
Gel drop | \n1 ml | \n
Wash ultrasonic bath | \n15 min | \n
Spin rotations per min (rpm) | \n3500 | \n
Duration of cycle | \n25 s | \n
Number of cycle | \n5 | \n
Annealing temperature | \n400–700°C | \n
Cooling rate after annealing | \n5°C/min | \n
Experimental parameters of Ni0.3Zn0.7Fe2O4 thin-film sol-gel spin-coating deposition process.
Speed rate (rpm) | \n3500 rpm (constant speed) | \n
Spin time (s) | \n25 s | \n
Volume of solution | \n1.0 ml | \n
Acceleration and deceleration | \n140 rpm/s | \n
Temperature | \nRoom temperature | \n
The X-ray diffraction (XRD) pattern of Ni0.3Zn0.7Fe2O4 thin films was obtained by using a Philips X’pert diffractometer model 7602 EA Almelo operating at 40 kV/30 mA in the 2θ range (20–80°) with CuKα radiation, λ = 1.5418 Å. The microstructural properties were observed using a FEI Nova NanoSEM 230 field emission scanning electron microscope. The distributions of grain sizes were obtained by taking more than 200 different grain images for the sample using J-image software. Hysteresis parameters of the loop of the Ni0.3Zn0.7Fe2O4 thin films were measured by using vibrating sample magnetometer (VSM) model 7404 Lake Shore. UV-Vis SHIMADZU model UV-3600 spectrophotometer has been used to analyse the optical transmission of the NiZn ferrite thin film in the wavelength range 200–800 nm.
\nFigure 1 shows the XRD pattern of spin coating and air-annealed ferrite thin films on the ITO glass substrate. The XRD patterns show single-cubic spinel-phase structures of (220), (311), (400), (511) and (440) in Ni0.3Zn0.7Fe2O4 ferrite thin films according to JCPDS reference code 74-2081 and 82-1049, respectively. Plane (311) is most intense in each annealing temperature, whereas others are at relatively low intensity [22]. These plane formed nickel zinc ferrite phases. The small peak intensities in XRD pattern revealed the existence of fine grain nanocrystalline with the most part as amorphous. The height of the highest XRD intensity is more intense at high temperature and improves the crystallinity of the films. As the annealing temperature increases, the grain size also increases, as indicated in the narrowing of the XRD spectrum lines. Increasing annealing temperature will enhance the crystallinity besides releasing the internal strains within the samples which results in better optical and magnetic properties. The intensity of the (311) peak increases as a function of the substrate temperature showing an improvement of the film crystallinity. Moreover the peak intensity increases, while its full width at half maximum (FWHM) decreases. Further increasing of substrate temperature leads to a slight decrease of the peak intensity for films prepared at 700°C. It indicates a saturation of film crystallinity. The crystallite sizes of all ferrite thin films are found to be between 16 and 18 nm. The average crystallite size, D (Table 4), was determined using the Scherrer’s formula [23] as given by Eq. (1):
where D is the crystallite size, β is full width at half maximum of the diffraction peak, λ is the wavelength of 1.54 Å, and θ is scanning angle.
\nXRD pattern of air-annealed Ni0.3Zn0.7Fe2O4 ferrite thin films. Reproduced with permission from [21].
The lattice constants of these films were calculated using indexing method [24] given by Eq. (2):
where d is interplanar spacing, λ is X-ray wavelength, and θ is reflection angle. The λ/4a2 is a constant and d = h2 + k2 + l2, which is determined by sin2θ value.
\nThese lattice constants are tabulated in Table 3. The lattice parameters of all the ferrite films do not match precisely with the standard JCPDS bulk values which could be attributed to the strains present on the surface of the films during the synthesis [25, 26]. Annealing temperature has a pronounced effect on grain size. The lattice parameter calculated for nickel ferrite thin film is 8.338 Å [27]. This is in accordance with the variation in lattice parameter with Zn content reported for the bulk ferrites.
\nAnnealing temperature (°C) | \n400 | \n500 | \n600 | \n700 | \n
---|---|---|---|---|
Rel. intensity counts (%) | \n100 | \n100 | \n100 | \n100 | \n
Position (2θ) | \n35.3661 | \n35.3717 | \n35.3991 | \n35.3247 | \n
FWHM (2θ) | \n0.5215 | \n0.5371 | \n0.5116 | \n0.4723 | \n
d-spacing (nm) | \n2.53595 | \n2.53557 | \n2.53207 | \n2.53993 | \n
Crystallite size (nm) | \n16.71 | \n16.22 | \n17.03 | \n18.45 | \n
Lattice strain (%) | \n0.71 | \n0.73 | \n0.70 | \n0.65 | \n
Space group | \nF d 3 m | \nF d 3 m | \nF d 3 m | \nF d 3 m | \n
Lattice parameter a = b = c (Å) | \n8.4030 | \n8.4030 | \n8.4030 | \n8.4030 | \n
Volume/Å3 | \n593.34 | \n593.34 | \n593.34 | \n593.34 | \n
Structural parameters of Ni0.3Zn0.7Fe2O4 thin films from XRD spectra.
The FESEM images revealed that the Ni0.3Zn0.7Fe2O4 films have dense and homogenous grains with an average grain size. Film annealed at 400°C was homogenous with dense microstructure, and they have high adhesion to the substrate. Film annealed at 500°C shows a well-developed grain. The grains slowly appeared with increasing annealed temperature. This is because the grain tends to combine with closer grain to form larger grain size. The structure formed in the thin films is a normal characteristic of film derived from sol-gel. The average grain sizes of the Ni0.3Zn0.7Fe2O4 nanoferrite thin films are 18.61 nm (400°C), 26.25 nm (500°C), 28.12 nm (600°C) and 41.32 nm (700°C). The grains of the films are spherical and uniform, and cohesion of grains is due to the magnetic attraction. The average grain size of the films is presented in Figure 2. The histogram of grain size distribution shifted to the larger grain size as the annealing temperature increased. However, based on the coercivity, Hc results (Section 4.3), the transition from 600 to 700°C of annealing temperature exhibits a fall of the Hc value.
\nFESEM images of the Ni0.3Zn0.7Fe2O nanoferrite films annealed at (a) 400, (b) 500, (c) 600 and (d) 700°C. Reproduced with permission from [21].
Figure 3 illustrates the cross section of the samples annealed at 400, 500, 600 and 700°C, respectively. The deposited films were uniform with two cycles of number deposition cycle. It was found that the thin films have thickness in the range of 145.7–285.6 nm which was confirmed by cross-sectional FESEM images. The grain size over 26 nm was further increased with a higher annealing temperature. Accordingly, the number of grain sizes beyond the single domain to multidomain critical size also increased. Therefore, the number of domain wall increased as the movement of domain wall contribution to make ease of magnetization increased [28].
\nCross-sectional of Ni0.3Zn0.7Fe2O nanoferrite films annealed at different temperatures.
Figure 4 presented the thickness of the Ni0.7Zn0.3Fe2O ferrite thin films and shows its relationship with the grain size. Annealing is a process related to secondary grain growth in the film. Thompson discussed the secondary grain growth mechanism and came to the conclusion that the secondary grain growth is driven by the reduction of the total grain boundary energy. Since the grain boundary energy is film-thickness-dependent, the secondary grain growth rate increases when the film thickness is reduced [29].
\nThe average grain size and film thickness as a function of annealed temperatures. Reproduced with permission from [21].
The plots of magnetization, M, against magnetic field strength, H (M−H hysteresis loop), for Ni0.3Zn0.7Fe2O4 films annealed at 400, 500, 600 and 700°C were shown in Figure 5. The hysteresis shape is narrow and has linear loops which have a low saturation magnetization, Ms. The saturation magnetization, Ms, and coercivity, Hc, values have been directly extracted from these curves and have been listed for various annealing temperatures in Table 4. The Ms and Hc could be attributed to the varied grain size and crystallinity. The lower value of saturation magnetization, Ms, Ni0.3Zn0.7Fe2O4 films (Figure 6(a)) could be caused by several reasons. A large grain boundary volume presented in thin films would result in the increase of the Ms [30]. Other reasons for the increase Ms are due to complex spinel structure; it was difficult to gain Ni0.3Zn0.7Fe2O nanoferrite films with perfect crystallization. The metal cations can occupy either A sites (tetrahedral) or B sites (octahedral), which will result in a partially disordered cation distribution in the crystal lattice [31]. The saturation magnetization (Ms) increases with the grain size, and the observations on larger decrease are interpreted mostly by oxygen absorption, characteristic to the preparation technique. The coercivity, Hc, was decreased as the annealing temperature and average grain size increased (Figure 6(b)). The maximum value of Hc was 16.54 Oe for the grain size 26.25 nm. The Hc observed were closed to the reported value of Hc which is within the range of 20–210 Oe [20]. The decreases of Hc were contributed from the transition of the single domain to the multidomain [32]. The coercivity (Hc) has a maximum grain size of about 26 nm and a steep decrease at larger grain sizes (41.3 nm). The smaller grain sizes and the decrease of Hc are due to the randomizing effects of thermal energy. Thermal energy has an important role in magnetic instability of single-domain magnetic particles. Due to the smaller grain sizes, the thermal agitation becomes small and will not be able to cause fluctuations in the magnetic spin orientations of the nanoparticles where they freeze in random orientations. The latter is probably due to the decreased anisotropy constant, which leads to a sharp decrease in coercivity according to the random anisotropy model. The relation between the decrease Hc and increase grain size shows the linear inverse proportionality between coercivity, Hc, and grain size, D, by Hc α 1/D [22, 33].
\n(a) Hysteresis loop of Ni0.7Zn0.3Fe2O ferrite thin films and (b) first quadrant of the magnetic hysteresis loops of the samples. Magnetization at any given field increased with heat treatment temperature. Reproduced with permission from [21].
Temperature (°C) | \nMs (±0.01 emu/g) | \nHc (±0.001 Oe) | \nD (±0.1 nm) | \ndxrd (±0.01 nm) | \n
---|---|---|---|---|
400 | \n1.287 | \n16.184 | \n18.6 | \n16.71 | \n
500 | \n2.395 | \n16.536 | \n26.3 | \n16.22 | \n
600 | \n2.653 | \n12.288 | \n28.1 | \n17.03 | \n
700 | \n3.421 | \n8.297 | \n42.32 | \n18.45 | \n
Saturation magnetization, Ms, coercivity, Hc, grain size, D, and calculated crystallite size from XRD dxrd of Ni0.3Zn0.7Fe2O4 nanoferrite thin films.
Reproduced with permission from [21].
Comparison of the variation in (a) Ms and (b) Hc as a function of annealed temperatures of the Ni0.3Zn0.7Fe2O nanoferrite thin films. Reproduced with permission from [21].
Figure 7 demonstrates the curves of absorbance and transmittance, respectively. The absorption spectrum exhibits that NiZn ferrite thin films have low absorbance in visible region and it is close to infrared region (Figure 7(a)). However, absorbance in UV region is high. This result of the optical behaviour is analogous to those claimed by [34] or cobalt ferrite thin film using microwave-assisted nonaqueous sol-gel process. Optical transmittance is plotted in a wavelength range of 200–800 nm as shown in Figure 7(b). The films are highly transparent in the visible range below 90%. The average transmittance is calculated and tabulated in Table 5. The optical transmittance spectra of annealed thin films show a good transmission in the visible region and a sharp fall in the UV region which corresponds to the band gap. The decrease of the transmittance is due to the interaction of the incident long-wavelength radiation with the free electron in the films [35].
\n(a) Absorbance spectra of thin film at various annealed temperatures and (b) transmittance spectra of NiZn ferrite thin films.
Annealing temperature (°C) | \nThickness (nm) (±0.1 nm) | \nDirect band-gap energy (αhv)2 (±0.01 eV) | \nIndirect band-gap energy (αhv)−1/2 (±0.01 eV) | \nAverage transmittance (T%) (±0.1%) | \nGrain size (±0.01 nm) | \n
---|---|---|---|---|---|
400 | \n145.7 | \n3.76 | \n3.03 | \n85.0 | \n18.61 | \n
500 | \n180.7 | \n3.66 | \n3.08 | \n78.0 | \n26.25 | \n
600 | \n221.5 | \n3.58 | \n3.16 | \n70.0 | \n28.12 | \n
700 | \n285.6 | \n3.04 | \n3.30 | \n70.0 | \n41.32 | \n
Thickness, band gap, transmittance and grain size of sample at various annealing temperatures.
Figure 8(a) and (b) demonstrates the optical band-gap energy direct and indirect of the films annealed at various temperatures. The band-gap energy (Eg) of the thin films was calculated from UV–Vis absorbance spectra. Direct and indirect band-gap energies can be obtained from the dependencies (αhv)2 on hv, where α is the absorption coefficient, whereas hv is the photon energy in eV [36]. A linear line was obtained by plotting (αhv)1/n against hv. The intersection of this straight line on x-axis gives the value of optical band gap. The values of band gap as listed in Table 5 do change with thickness. A dependence of band-gap energy shift on the grain size is attributed to electron confinement effect related with the grain size in the films. As a result, the observed decrease in Eg with increasing grain size is due to the decrease of resistivity and the increase of film thickness. It has been studied that the band gap does not change significantly with the thickness after the film grows completely [37]. The band gap becomes saturated for a particular value of thickness [38]. The presented values of optical band-gap energy are larger than reported value for NiZn ferrite film 1.66 eV [39] and bulk NiZn ferrite, 1.55–1.66 eV [40]. The direct and indirect band energy increases could be the effect of strain present in the films during heat treatment [41].
\n(a) Plot of (αhv)2 as a function of photon energy (eV) and (b) Plot of (αhv)1/2 as a function of photon energy (hv).
NiZn ferrite thin film with composition Ni0.3Zn0.7Fe2O4 was successfully prepared using sol-gel spin-coating technique. The structure formed in the thin films is a normal characteristic of film derived from sol-gel. Sol-gel spin-coating method was able to produce the similar trend and behaviour, among others, of ferrite thin film. The results are summarized as follows:
The phase analysis of films produced the complete phase with the formation of spinel structures of Ni0.3Zn0.7Fe2O4 ferrite which were observable at annealed 400°C and upwards. Further annealing temperature demonstrated the improvement in the degree of crystallinity of the annealed films.
The saturation magnetization, Ms, of the synthesized Ni0.3Zn0.7Fe2O4 ferrite thin films has been obtained at room temperature from the hysteresis loops which increases with annealing temperatures. The hysteresis shape shown is narrow and has linear loops which have a low Ms. The coercivity, Hc, decreases as the average grain size increases since the alignment of the magnetic moments inside the domain is fully controlled by thermal energy.
The micrograph revealed the increasing average grain size with the annealing temperature. The grains of the films are spherical and uniform, and cohesion of grains is due to the magnetic attraction.
The absorption spectrum exhibits that NiZn ferrite thin films have low absorbance in visible region and close to infrared region. The films are highly transparent in the visible range below 90%. The optical transmittance spectra of annealed thin films show a good transmission in the visible region and a sharp fall in the UV region which corresponds to the band gap.
The authors are grateful to the Ministry of Higher Education Malaysia (MOHE) and Universiti Putra Malaysia for Research University Grant (vote number 5526200). Reprinted by permission from Springer Nature and Copyright Clearance Center, Springer, Journal of the Australian Ceramic Society, Microstructure and magnetic properties of Ni-Zn ferrite thin film synthesized using sol-gel and spin-coating technique, Yusnita, Y.; Azis, R. S.; Kanagesan, S.; and Bahmanrokh, G., licence number: 4393541427573 (2017).
\nThe authors declare that they have no competing interest.
NiZn nanocrystalline ferrite thin films have a spinel crystal structure which have been a subject of extensive attempt because of their potential applications in high-density magneto-optic recording devices, magnetic refrigeration and microwave materials due to its high electrical resistivity, low magnetic coercivity and low eddy current losses. NiZn nanoferrite thin films are structure sensitive, and it is not easy to produce a stoichiometric and point-defect-free NiZn ferrite, for high-resistivity applications. In NiZn ferrite thin-film fabrication, the accurate composition control and the uniformity throughout the film deposition are important. It is well known that properties of ferrite materials strongly depend on the preparation conditions. This issue is important in NiZn ferrite thin films because the effect of temperatures will lead to the change in the chemical composition of the ferrite films. These also will result in non-uniformity of film composition and the magnetic hysteresis parameter of ferrites. High-temperature synthesis of NiZn thin-film ferrite results in the evaporation of some constituents that lead to the nonstoichiometry, and zinc volatilization at higher temperature can result in the formation of Fe2+ ions that lead to increase the electron hopping and reducing the electrical resistivity [1]. Therefore, a low-temperature synthesis is required for the synthesis of NiZn ferrite film. Properties of ferrite film depend on the preparation route, due to its strong influence on type of the film (polycrystalline and epitaxial), particle size, chemical homogeneity, microstructure and cationic distribution between tetrahedral and octahedral sublattice sites [2, 3]. Synthesis of ferrite thin film is of great interest among researchers in this field of study. Widely used techniques are utilized to produce desirable final product of nickel zinc ferrite. These techniques can be classified into two major techniques which are the conventional technique and the nonconventional technique. The starting materials are conventionally oxides or precursors of oxide of the cations. This process involves the interdiffusion of the various metal ions of preselected compositions to form a mixed crystal. The nonconventional powder processing in a liquid medium may produce intermediate, finely divided mixed hydroxides or mixed organic salts to assist the subsequent diffusion process [4]. Most of ferrite films have been prepared using sputtering and pulsed laser deposition. Somehow, sol-gel method is a kind of potential film preparation process, which possesses advantages of chemical homogeneity, easy component adjustment, low calcination temperature and low cost. Spin coating gives an advantage to liquid film that leads to uniformity in thickness during spin-off [5]. Once uniform, it tends to remain provided the viscosity is not shear-dependent and does not vary over the substrate. Other than that, sol-gel and hydrothermal routes of ferrite synthesis have shown increasing importance. Recent years are marked by growing interest in sol-gel processed films in new areas, particularly in microelectronics. This is mainly due to intensively developing applications of silicate or siloxane sol-gel films in the VLSI multilevel interconnection process, the preparation of ferroelectric films for nonvolatile memory [6].
\nSpin coating is widely used in modern optical and microelectronic industries [7]. The understanding of its underlying physics remains limited, a fact attributed to the lack of experimental data for the evolution of various parameters during the process [8, 9], leading to the need for new evolution tools. A relative study of nickel zinc ferrite by sol-gel route and conventional solid-state reaction was carried out [10]. It was claimed that the homogeneity and high purity in the sol-gel samples and small grains confirmed the finer particles. Ni0.36Zn0.64Fe2O4 (NZF) thick films have been synthesized using sol-gel dip-coating method [11]. Combination with dispersion of ceramic NZF particles in starting sols has been proved to be useful for producing thick nickel zinc ferrite films. The best NZF powders are formed from dispersing at 300°C by hydrothermal grow. Nickel zinc ferrite thin films are successfully prepared using spin-deposited citrate-precursor route [12]. The formation of crystalline film at low temperature even though films were found to be X-ray amorphous revealed the formation of uniform grains in nanometer size range. Besides that, NiZn ferrite film was successfully fabricated by using photosensitive sol-gel method. The photosensitive gel film can be the photoresist of itself during the preparation process. The fine pattern of Ni0.5Zn0.5Fe2O4 film is obtained through UV radiation, rising and heat treatment [13]. The great potential of combining the microwave technique with nonaqueous sol-gel chemistry was successful [14]. Many transition metal ferrite nanoparticles with high crystallinity are uniformly morphological besides homogenous metal ferrite thin films on flat and curved substrates. The thickness of film can easily be adjusted in the range of 20–80 nm using precursor concentration. Other synthesis techniques of nickel zinc ferrite thin films are chemical vapor deposition, spray pyrolysis, sputtering, pulsed laser deposition and spin spray. Of these methods the earliest used was vapor deposition of metals followed by oxidation [15]. The films were porous and polycrystalline and approximately 1000 Å thick. Many common ferrites produced by this method were single-phase spinel in crystal structure. Spray pyrolysis is complicated and expensive and required special equipment and sometimes high processing temperature above 500°C. By using spray pyrolysis technique [3, 16], very homogenous ferrite thin films were obtained with good reproducibility. Nevertheless, for spinel ferrite thin-film growth, this method is used rarely. Also only a few works can be found on NiZn ferrites, obtained by spray pyrolysis where a focus on the investigation of microstructural, optical and magnetic properties was held [17]. Apart from that, the effect of oxygen plasma treatment on magnetic and NiZn ferrite films using the spin-spray plating method has been employed [18]. The oxygen plasma treatment increased the number of nucleation sites of ferrite and enhanced adhesion of the films to the substrates. It has been reported that spinel Zn ferrite can be synthesized without substrate heating by pulsed laser deposition [19]. However, this technique needs post-deposition and requires sputtered film at a high temperature to grow the spinel ferrite structure. The results were optimized and obtained 4000 Å NiZn ferrite films with low in-plane coercivity of Hc = 15.2 Oe and relatively high saturation magnetization Ms = 318 emu/cm3. Some other research works was working on preparing NiZn ferrite films by magnetron sputtering method. Most of the sputtered ferrite films must be deposited at a high substrate temperature and need high heat treatment to obtain ordered spinel structure. Sputtering method is prepared at room temperature without any post-annealing treatment [20]. By controlling the relative oxygen flow, grain size in a range 10–20 nm was developed. It revealed a maximum saturation magnetization of about 151 emu/cm3. The static magnetic measurement results are affected by the crystallinity, grain dimension and cation distribution.
\nNiZn ferrite thin film is prepared by a sol-gel process and spin-coating technique. The starting materials nickel nitrate hexahydrate (Ni(NO3)2·6H2O) (Sigma Aldrich, 99.999%), iron nitrate nonahydrate (Fe(NO3)3·9H2O) (Alfa Aesar, 99.999%) and zinc nitrate hexahydrate (Zn(NO3)2·6H2O) (Alfa Aesar, 99.999%) with high purity were used as a precursor for the starting sol preparation. The materials are in metal nitrate hydrates which are soluble in alcohol solvents. Acetone and deionized water were used as a medium for sol-gel reaction. Acetic acid (C6H8O7H2O) (Alfa Aesar, 99.99%) acts as the chelating agent. The precursors were dissolved in deionized water and stirred for 15 min with a molar ratio of Ni:Zn:Fe = 1:1:2 using hot plate. The former salt solution was dissolved into acetic acid solution with a molar ratio of 1:1 and stirred for 3 h at 80°C. A sol-gel formed was left 24 h for age.
\nThe thin film was deposited on indium tin oxide (ITO) glass. ITO has higher melting point around 1926°C. There is no phase change of substrate during deposition of the film. The typical properties of ITO glass substrate are listed in Table 1. The film deposition consists of substrate wash and spin coating. The steps are to wash the substrates firstly with distilled water in ultrasonic bath for 15 min. The substrate was then washed in ultrasonic bath using acetone liquid for 15 min. Coating was carried out in a clean room by using a spin coater. The setting parameters were listed in Table 2. The aged sol of 1.0 ml (Section 3.1) was dropped on ITO glass substrate and spin coated for 25 s at 3500 rpm (revolutions per min). The deposition was repeated several times to obtain the required thickness (300 nm). The film thickness can be controlled by the number of coating. The film with desired thickness can be obtained by repeating the deposition cycle. Then drying films were performed in a room temperature for a few minutes and annealed in air at temperature 400, 500, 600 and 700°C, respectively, with an increment of 100°C for 1 h. Annealing process was performed in a box furnace with rate of 5°C/min.
\nGlass substrate | \nITO coating glass | \n
Size of substrate | \n25 × 12 × 1.1 mm | \n
Gel drop | \n1 ml | \n
Wash ultrasonic bath | \n15 min | \n
Spin rotations per min (rpm) | \n3500 | \n
Duration of cycle | \n25 s | \n
Number of cycle | \n5 | \n
Annealing temperature | \n400–700°C | \n
Cooling rate after annealing | \n5°C/min | \n
Experimental parameters of Ni0.3Zn0.7Fe2O4 thin-film sol-gel spin-coating deposition process.
Speed rate (rpm) | \n3500 rpm (constant speed) | \n
Spin time (s) | \n25 s | \n
Volume of solution | \n1.0 ml | \n
Acceleration and deceleration | \n140 rpm/s | \n
Temperature | \nRoom temperature | \n
The X-ray diffraction (XRD) pattern of Ni0.3Zn0.7Fe2O4 thin films was obtained by using a Philips X’pert diffractometer model 7602 EA Almelo operating at 40 kV/30 mA in the 2θ range (20–80°) with CuKα radiation, λ = 1.5418 Å. The microstructural properties were observed using a FEI Nova NanoSEM 230 field emission scanning electron microscope. The distributions of grain sizes were obtained by taking more than 200 different grain images for the sample using J-image software. Hysteresis parameters of the loop of the Ni0.3Zn0.7Fe2O4 thin films were measured by using vibrating sample magnetometer (VSM) model 7404 Lake Shore. UV-Vis SHIMADZU model UV-3600 spectrophotometer has been used to analyse the optical transmission of the NiZn ferrite thin film in the wavelength range 200–800 nm.
\nFigure 1 shows the XRD pattern of spin coating and air-annealed ferrite thin films on the ITO glass substrate. The XRD patterns show single-cubic spinel-phase structures of (220), (311), (400), (511) and (440) in Ni0.3Zn0.7Fe2O4 ferrite thin films according to JCPDS reference code 74-2081 and 82-1049, respectively. Plane (311) is most intense in each annealing temperature, whereas others are at relatively low intensity [22]. These plane formed nickel zinc ferrite phases. The small peak intensities in XRD pattern revealed the existence of fine grain nanocrystalline with the most part as amorphous. The height of the highest XRD intensity is more intense at high temperature and improves the crystallinity of the films. As the annealing temperature increases, the grain size also increases, as indicated in the narrowing of the XRD spectrum lines. Increasing annealing temperature will enhance the crystallinity besides releasing the internal strains within the samples which results in better optical and magnetic properties. The intensity of the (311) peak increases as a function of the substrate temperature showing an improvement of the film crystallinity. Moreover the peak intensity increases, while its full width at half maximum (FWHM) decreases. Further increasing of substrate temperature leads to a slight decrease of the peak intensity for films prepared at 700°C. It indicates a saturation of film crystallinity. The crystallite sizes of all ferrite thin films are found to be between 16 and 18 nm. The average crystallite size, D (Table 4), was determined using the Scherrer’s formula [23] as given by Eq. (1):
where D is the crystallite size, β is full width at half maximum of the diffraction peak, λ is the wavelength of 1.54 Å, and θ is scanning angle.
\nXRD pattern of air-annealed Ni0.3Zn0.7Fe2O4 ferrite thin films. Reproduced with permission from [21].
The lattice constants of these films were calculated using indexing method [24] given by Eq. (2):
where d is interplanar spacing, λ is X-ray wavelength, and θ is reflection angle. The λ/4a2 is a constant and d = h2 + k2 + l2, which is determined by sin2θ value.
\nThese lattice constants are tabulated in Table 3. The lattice parameters of all the ferrite films do not match precisely with the standard JCPDS bulk values which could be attributed to the strains present on the surface of the films during the synthesis [25, 26]. Annealing temperature has a pronounced effect on grain size. The lattice parameter calculated for nickel ferrite thin film is 8.338 Å [27]. This is in accordance with the variation in lattice parameter with Zn content reported for the bulk ferrites.
\nAnnealing temperature (°C) | \n400 | \n500 | \n600 | \n700 | \n
---|---|---|---|---|
Rel. intensity counts (%) | \n100 | \n100 | \n100 | \n100 | \n
Position (2θ) | \n35.3661 | \n35.3717 | \n35.3991 | \n35.3247 | \n
FWHM (2θ) | \n0.5215 | \n0.5371 | \n0.5116 | \n0.4723 | \n
d-spacing (nm) | \n2.53595 | \n2.53557 | \n2.53207 | \n2.53993 | \n
Crystallite size (nm) | \n16.71 | \n16.22 | \n17.03 | \n18.45 | \n
Lattice strain (%) | \n0.71 | \n0.73 | \n0.70 | \n0.65 | \n
Space group | \nF d 3 m | \nF d 3 m | \nF d 3 m | \nF d 3 m | \n
Lattice parameter a = b = c (Å) | \n8.4030 | \n8.4030 | \n8.4030 | \n8.4030 | \n
Volume/Å3 | \n593.34 | \n593.34 | \n593.34 | \n593.34 | \n
Structural parameters of Ni0.3Zn0.7Fe2O4 thin films from XRD spectra.
The FESEM images revealed that the Ni0.3Zn0.7Fe2O4 films have dense and homogenous grains with an average grain size. Film annealed at 400°C was homogenous with dense microstructure, and they have high adhesion to the substrate. Film annealed at 500°C shows a well-developed grain. The grains slowly appeared with increasing annealed temperature. This is because the grain tends to combine with closer grain to form larger grain size. The structure formed in the thin films is a normal characteristic of film derived from sol-gel. The average grain sizes of the Ni0.3Zn0.7Fe2O4 nanoferrite thin films are 18.61 nm (400°C), 26.25 nm (500°C), 28.12 nm (600°C) and 41.32 nm (700°C). The grains of the films are spherical and uniform, and cohesion of grains is due to the magnetic attraction. The average grain size of the films is presented in Figure 2. The histogram of grain size distribution shifted to the larger grain size as the annealing temperature increased. However, based on the coercivity, Hc results (Section 4.3), the transition from 600 to 700°C of annealing temperature exhibits a fall of the Hc value.
\nFESEM images of the Ni0.3Zn0.7Fe2O nanoferrite films annealed at (a) 400, (b) 500, (c) 600 and (d) 700°C. Reproduced with permission from [21].
Figure 3 illustrates the cross section of the samples annealed at 400, 500, 600 and 700°C, respectively. The deposited films were uniform with two cycles of number deposition cycle. It was found that the thin films have thickness in the range of 145.7–285.6 nm which was confirmed by cross-sectional FESEM images. The grain size over 26 nm was further increased with a higher annealing temperature. Accordingly, the number of grain sizes beyond the single domain to multidomain critical size also increased. Therefore, the number of domain wall increased as the movement of domain wall contribution to make ease of magnetization increased [28].
\nCross-sectional of Ni0.3Zn0.7Fe2O nanoferrite films annealed at different temperatures.
Figure 4 presented the thickness of the Ni0.7Zn0.3Fe2O ferrite thin films and shows its relationship with the grain size. Annealing is a process related to secondary grain growth in the film. Thompson discussed the secondary grain growth mechanism and came to the conclusion that the secondary grain growth is driven by the reduction of the total grain boundary energy. Since the grain boundary energy is film-thickness-dependent, the secondary grain growth rate increases when the film thickness is reduced [29].
\nThe average grain size and film thickness as a function of annealed temperatures. Reproduced with permission from [21].
The plots of magnetization, M, against magnetic field strength, H (M−H hysteresis loop), for Ni0.3Zn0.7Fe2O4 films annealed at 400, 500, 600 and 700°C were shown in Figure 5. The hysteresis shape is narrow and has linear loops which have a low saturation magnetization, Ms. The saturation magnetization, Ms, and coercivity, Hc, values have been directly extracted from these curves and have been listed for various annealing temperatures in Table 4. The Ms and Hc could be attributed to the varied grain size and crystallinity. The lower value of saturation magnetization, Ms, Ni0.3Zn0.7Fe2O4 films (Figure 6(a)) could be caused by several reasons. A large grain boundary volume presented in thin films would result in the increase of the Ms [30]. Other reasons for the increase Ms are due to complex spinel structure; it was difficult to gain Ni0.3Zn0.7Fe2O nanoferrite films with perfect crystallization. The metal cations can occupy either A sites (tetrahedral) or B sites (octahedral), which will result in a partially disordered cation distribution in the crystal lattice [31]. The saturation magnetization (Ms) increases with the grain size, and the observations on larger decrease are interpreted mostly by oxygen absorption, characteristic to the preparation technique. The coercivity, Hc, was decreased as the annealing temperature and average grain size increased (Figure 6(b)). The maximum value of Hc was 16.54 Oe for the grain size 26.25 nm. The Hc observed were closed to the reported value of Hc which is within the range of 20–210 Oe [20]. The decreases of Hc were contributed from the transition of the single domain to the multidomain [32]. The coercivity (Hc) has a maximum grain size of about 26 nm and a steep decrease at larger grain sizes (41.3 nm). The smaller grain sizes and the decrease of Hc are due to the randomizing effects of thermal energy. Thermal energy has an important role in magnetic instability of single-domain magnetic particles. Due to the smaller grain sizes, the thermal agitation becomes small and will not be able to cause fluctuations in the magnetic spin orientations of the nanoparticles where they freeze in random orientations. The latter is probably due to the decreased anisotropy constant, which leads to a sharp decrease in coercivity according to the random anisotropy model. The relation between the decrease Hc and increase grain size shows the linear inverse proportionality between coercivity, Hc, and grain size, D, by Hc α 1/D [22, 33].
\n(a) Hysteresis loop of Ni0.7Zn0.3Fe2O ferrite thin films and (b) first quadrant of the magnetic hysteresis loops of the samples. Magnetization at any given field increased with heat treatment temperature. Reproduced with permission from [21].
Temperature (°C) | \nMs (±0.01 emu/g) | \nHc (±0.001 Oe) | \nD (±0.1 nm) | \ndxrd (±0.01 nm) | \n
---|---|---|---|---|
400 | \n1.287 | \n16.184 | \n18.6 | \n16.71 | \n
500 | \n2.395 | \n16.536 | \n26.3 | \n16.22 | \n
600 | \n2.653 | \n12.288 | \n28.1 | \n17.03 | \n
700 | \n3.421 | \n8.297 | \n42.32 | \n18.45 | \n
Saturation magnetization, Ms, coercivity, Hc, grain size, D, and calculated crystallite size from XRD dxrd of Ni0.3Zn0.7Fe2O4 nanoferrite thin films.
Reproduced with permission from [21].
Comparison of the variation in (a) Ms and (b) Hc as a function of annealed temperatures of the Ni0.3Zn0.7Fe2O nanoferrite thin films. Reproduced with permission from [21].
Figure 7 demonstrates the curves of absorbance and transmittance, respectively. The absorption spectrum exhibits that NiZn ferrite thin films have low absorbance in visible region and it is close to infrared region (Figure 7(a)). However, absorbance in UV region is high. This result of the optical behaviour is analogous to those claimed by [34] or cobalt ferrite thin film using microwave-assisted nonaqueous sol-gel process. Optical transmittance is plotted in a wavelength range of 200–800 nm as shown in Figure 7(b). The films are highly transparent in the visible range below 90%. The average transmittance is calculated and tabulated in Table 5. The optical transmittance spectra of annealed thin films show a good transmission in the visible region and a sharp fall in the UV region which corresponds to the band gap. The decrease of the transmittance is due to the interaction of the incident long-wavelength radiation with the free electron in the films [35].
\n(a) Absorbance spectra of thin film at various annealed temperatures and (b) transmittance spectra of NiZn ferrite thin films.
Annealing temperature (°C) | \nThickness (nm) (±0.1 nm) | \nDirect band-gap energy (αhv)2 (±0.01 eV) | \nIndirect band-gap energy (αhv)−1/2 (±0.01 eV) | \nAverage transmittance (T%) (±0.1%) | \nGrain size (±0.01 nm) | \n
---|---|---|---|---|---|
400 | \n145.7 | \n3.76 | \n3.03 | \n85.0 | \n18.61 | \n
500 | \n180.7 | \n3.66 | \n3.08 | \n78.0 | \n26.25 | \n
600 | \n221.5 | \n3.58 | \n3.16 | \n70.0 | \n28.12 | \n
700 | \n285.6 | \n3.04 | \n3.30 | \n70.0 | \n41.32 | \n
Thickness, band gap, transmittance and grain size of sample at various annealing temperatures.
Figure 8(a) and (b) demonstrates the optical band-gap energy direct and indirect of the films annealed at various temperatures. The band-gap energy (Eg) of the thin films was calculated from UV–Vis absorbance spectra. Direct and indirect band-gap energies can be obtained from the dependencies (αhv)2 on hv, where α is the absorption coefficient, whereas hv is the photon energy in eV [36]. A linear line was obtained by plotting (αhv)1/n against hv. The intersection of this straight line on x-axis gives the value of optical band gap. The values of band gap as listed in Table 5 do change with thickness. A dependence of band-gap energy shift on the grain size is attributed to electron confinement effect related with the grain size in the films. As a result, the observed decrease in Eg with increasing grain size is due to the decrease of resistivity and the increase of film thickness. It has been studied that the band gap does not change significantly with the thickness after the film grows completely [37]. The band gap becomes saturated for a particular value of thickness [38]. The presented values of optical band-gap energy are larger than reported value for NiZn ferrite film 1.66 eV [39] and bulk NiZn ferrite, 1.55–1.66 eV [40]. The direct and indirect band energy increases could be the effect of strain present in the films during heat treatment [41].
\n(a) Plot of (αhv)2 as a function of photon energy (eV) and (b) Plot of (αhv)1/2 as a function of photon energy (hv).
NiZn ferrite thin film with composition Ni0.3Zn0.7Fe2O4 was successfully prepared using sol-gel spin-coating technique. The structure formed in the thin films is a normal characteristic of film derived from sol-gel. Sol-gel spin-coating method was able to produce the similar trend and behaviour, among others, of ferrite thin film. The results are summarized as follows:
The phase analysis of films produced the complete phase with the formation of spinel structures of Ni0.3Zn0.7Fe2O4 ferrite which were observable at annealed 400°C and upwards. Further annealing temperature demonstrated the improvement in the degree of crystallinity of the annealed films.
The saturation magnetization, Ms, of the synthesized Ni0.3Zn0.7Fe2O4 ferrite thin films has been obtained at room temperature from the hysteresis loops which increases with annealing temperatures. The hysteresis shape shown is narrow and has linear loops which have a low Ms. The coercivity, Hc, decreases as the average grain size increases since the alignment of the magnetic moments inside the domain is fully controlled by thermal energy.
The micrograph revealed the increasing average grain size with the annealing temperature. The grains of the films are spherical and uniform, and cohesion of grains is due to the magnetic attraction.
The absorption spectrum exhibits that NiZn ferrite thin films have low absorbance in visible region and close to infrared region. The films are highly transparent in the visible range below 90%. The optical transmittance spectra of annealed thin films show a good transmission in the visible region and a sharp fall in the UV region which corresponds to the band gap.
The authors are grateful to the Ministry of Higher Education Malaysia (MOHE) and Universiti Putra Malaysia for Research University Grant (vote number 5526200). Reprinted by permission from Springer Nature and Copyright Clearance Center, Springer, Journal of the Australian Ceramic Society, Microstructure and magnetic properties of Ni-Zn ferrite thin film synthesized using sol-gel and spin-coating technique, Yusnita, Y.; Azis, R. S.; Kanagesan, S.; and Bahmanrokh, G., licence number: 4393541427573 (2017).
\nThe authors declare that they have no competing interest.
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\\n\\nOur expertise – We’ve published more than 4,500 books by more than 118,000 authors and editors.
\\n\\nOur reach – Our books have more than 130 million downloads and more than 108,170 Web of Science citations. We increase citations via indexing in all the major databases, including the Book Citation Index at Web of Science and Google Scholar.
\\n\\nOur services – The support we offer our authors and editors is second to none. Each book in our program receives the following:
\\n\\nOur end-to-end publishing service frees our authors and editors to focus on what matters: research. We empower them to shape their fields and connect with the global scientific community.
\\n\\n"In developing countries until now, advancement in science has been very limited, because insufficient economic resources are dedicated to science and education. These limitations are more marked when the scientists are women. In order to develop science in the poorest countries and decrease the gender gap that exists in scientific fields, Open Access networks like IntechOpen are essential. Free access to scientific research could contribute to ameliorating difficult life conditions and breaking down barriers." Marquidia Pacheco, National Institute for Nuclear Research (ININ), Mexico
\\n\\nInterested? Contact Ana Pantar (book.idea@intechopen.com) for more information.
\\n"}]'},components:[{type:"htmlEditorComponent",content:'We have more than a decade of experience in Open Access publishing. The advantages of publishing with IntechOpen include:
\n\nOur platform – IntechOpen is the world’s leading publisher of OA books, built by scientists, for scientists.
\n\nOur reputation – Everything we publish goes through a two-stage peer review process. We’re proud to count Nobel laureates among our esteemed authors. We meet European Commission standards for funding, and the research we’ve published has been funded by the Bill and Melinda Gates Foundation and the Wellcome Trust, among others. IntechOpen is a member of all relevant trade associations (including the STM Association and the Association of Learned and Professional Society Publishers) and has a selection of books indexed in Web of Science's Book Citation Index.
\n\nOur expertise – We’ve published more than 4,500 books by more than 118,000 authors and editors.
\n\nOur reach – Our books have more than 130 million downloads and more than 108,170 Web of Science citations. We increase citations via indexing in all the major databases, including the Book Citation Index at Web of Science and Google Scholar.
\n\nOur services – The support we offer our authors and editors is second to none. Each book in our program receives the following:
\n\nOur end-to-end publishing service frees our authors and editors to focus on what matters: research. We empower them to shape their fields and connect with the global scientific community.
\n\n"In developing countries until now, advancement in science has been very limited, because insufficient economic resources are dedicated to science and education. These limitations are more marked when the scientists are women. In order to develop science in the poorest countries and decrease the gender gap that exists in scientific fields, Open Access networks like IntechOpen are essential. Free access to scientific research could contribute to ameliorating difficult life conditions and breaking down barriers." Marquidia Pacheco, National Institute for Nuclear Research (ININ), Mexico
\n\nInterested? Contact Ana Pantar (book.idea@intechopen.com) for more information.
\n'}]},successStories:{items:[]},authorsAndEditors:{filterParams:{sort:"featured,name"},profiles:[{id:"105746",title:"Dr.",name:"A.W.M.M.",middleName:null,surname:"Koopman-van Gemert",slug:"a.w.m.m.-koopman-van-gemert",fullName:"A.W.M.M. Koopman-van Gemert",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/105746/images/5803_n.jpg",biography:"Dr. Anna Wilhelmina Margaretha Maria Koopman-van Gemert MD, PhD, became anaesthesiologist-intensivist from the Radboud University Nijmegen (the Netherlands) in 1987. She worked for a couple of years also as a blood bank director in Nijmegen and introduced in the Netherlands the Cell Saver and blood transfusion alternatives. She performed research in perioperative autotransfusion and obtained the degree of PhD in 1993 publishing Peri-operative autotransfusion by means of a blood cell separator.\nBlood transfusion had her special interest being the president of the Haemovigilance Chamber TRIP and performing several tasks in local and national blood bank and anticoagulant-blood transfusion guidelines committees. Currently, she is working as an associate professor and up till recently was the dean at the Albert Schweitzer Hospital Dordrecht. She performed (inter)national tasks as vice-president of the Concilium Anaesthesia and related committees. \nShe performed research in several fields, with over 100 publications in (inter)national journals and numerous papers on scientific conferences. \nShe received several awards and is a member of Honour of the Dutch Society of Anaesthesia.",institutionString:null,institution:{name:"Albert Schweitzer Hospital",country:{name:"Gabon"}}},{id:"83089",title:"Prof.",name:"Aaron",middleName:null,surname:"Ojule",slug:"aaron-ojule",fullName:"Aaron Ojule",position:null,profilePictureURL:"//cdnintech.com/web/frontend/www/assets/author.svg",biography:null,institutionString:null,institution:{name:"University of Port Harcourt",country:{name:"Nigeria"}}},{id:"295748",title:"Mr.",name:"Abayomi",middleName:null,surname:"Modupe",slug:"abayomi-modupe",fullName:"Abayomi Modupe",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/no_image.jpg",biography:null,institutionString:null,institution:{name:"Landmark University",country:{name:"Nigeria"}}},{id:"94191",title:"Prof.",name:"Abbas",middleName:null,surname:"Moustafa",slug:"abbas-moustafa",fullName:"Abbas Moustafa",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/94191/images/96_n.jpg",biography:"Prof. Moustafa got his doctoral degree in earthquake engineering and structural safety from Indian Institute of Science in 2002. He is currently an associate professor at Department of Civil Engineering, Minia University, Egypt and the chairman of Department of Civil Engineering, High Institute of Engineering and Technology, Giza, Egypt. He is also a consultant engineer and head of structural group at Hamza Associates, Giza, Egypt. Dr. Moustafa was a senior research associate at Vanderbilt University and a JSPS fellow at Kyoto and Nagasaki Universities. He has more than 40 research papers published in international journals and conferences. He acts as an editorial board member and a reviewer for several regional and international journals. His research interest includes earthquake engineering, seismic design, nonlinear dynamics, random vibration, structural reliability, structural health monitoring and uncertainty modeling.",institutionString:null,institution:{name:"Minia University",country:{name:"Egypt"}}},{id:"84562",title:"Dr.",name:"Abbyssinia",middleName:null,surname:"Mushunje",slug:"abbyssinia-mushunje",fullName:"Abbyssinia Mushunje",position:null,profilePictureURL:"//cdnintech.com/web/frontend/www/assets/author.svg",biography:null,institutionString:null,institution:{name:"University of Fort Hare",country:{name:"South Africa"}}},{id:"202206",title:"Associate Prof.",name:"Abd Elmoniem",middleName:"Ahmed",surname:"Elzain",slug:"abd-elmoniem-elzain",fullName:"Abd Elmoniem Elzain",position:null,profilePictureURL:"//cdnintech.com/web/frontend/www/assets/author.svg",biography:null,institutionString:null,institution:{name:"Kassala University",country:{name:"Sudan"}}},{id:"98127",title:"Dr.",name:"Abdallah",middleName:null,surname:"Handoura",slug:"abdallah-handoura",fullName:"Abdallah Handoura",position:null,profilePictureURL:"//cdnintech.com/web/frontend/www/assets/author.svg",biography:null,institutionString:null,institution:{name:"École Supérieure des Télécommunications",country:{name:"Morocco"}}},{id:"91404",title:"Prof.",name:"Abdecharif",middleName:null,surname:"Boumaza",slug:"abdecharif-boumaza",fullName:"Abdecharif Boumaza",position:null,profilePictureURL:"//cdnintech.com/web/frontend/www/assets/author.svg",biography:null,institutionString:null,institution:{name:"Abbès Laghrour University of Khenchela",country:{name:"Algeria"}}},{id:"105795",title:"Prof.",name:"Abdel Ghani",middleName:null,surname:"Aissaoui",slug:"abdel-ghani-aissaoui",fullName:"Abdel Ghani Aissaoui",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/105795/images/system/105795.jpeg",biography:"Abdel Ghani AISSAOUI is a Full Professor of electrical engineering at University of Bechar (ALGERIA). He was born in 1969 in Naama, Algeria. He received his BS degree in 1993, the MS degree in 1997, the PhD degree in 2007 from the Electrical Engineering Institute of Djilali Liabes University of Sidi Bel Abbes (ALGERIA). He is an active member of IRECOM (Interaction Réseaux Electriques - COnvertisseurs Machines) Laboratory and IEEE senior member. He is an editor member for many international journals (IJET, RSE, MER, IJECE, etc.), he serves as a reviewer in international journals (IJAC, ECPS, COMPEL, etc.). He serves as member in technical committee (TPC) and reviewer in international conferences (CHUSER 2011, SHUSER 2012, PECON 2012, SAI 2013, SCSE2013, SDM2014, SEB2014, PEMC2014, PEAM2014, SEB (2014, 2015), ICRERA (2015, 2016, 2017, 2018,-2019), etc.). His current research interest includes power electronics, control of electrical machines, artificial intelligence and Renewable energies.",institutionString:"University of Béchar",institution:{name:"University of Béchar",country:{name:"Algeria"}}},{id:"99749",title:"Dr.",name:"Abdel Hafid",middleName:null,surname:"Essadki",slug:"abdel-hafid-essadki",fullName:"Abdel Hafid Essadki",position:null,profilePictureURL:"//cdnintech.com/web/frontend/www/assets/author.svg",biography:null,institutionString:null,institution:{name:"École Nationale Supérieure de Technologie",country:{name:"Algeria"}}},{id:"101208",title:"Prof.",name:"Abdel Karim",middleName:"Mohamad",surname:"El Hemaly",slug:"abdel-karim-el-hemaly",fullName:"Abdel Karim El Hemaly",position:null,profilePictureURL:"https://mts.intechopen.com/storage/users/101208/images/733_n.jpg",biography:"OBGYN.net Editorial Advisor Urogynecology.\nAbdel Karim M. A. El-Hemaly, MRCOG, FRCS � Egypt.\n \nAbdel Karim M. A. El-Hemaly\nProfessor OB/GYN & Urogynecology\nFaculty of medicine, Al-Azhar University \nPersonal Information: \nMarried with two children\nWife: Professor Laila A. Moussa MD.\nSons: Mohamad A. M. El-Hemaly Jr. MD. Died March 25-2007\nMostafa A. M. El-Hemaly, Computer Scientist working at Microsoft Seatle, USA. \nQualifications: \n1.\tM.B.-Bch Cairo Univ. June 1963. \n2.\tDiploma Ob./Gyn. Cairo Univ. April 1966. \n3.\tDiploma Surgery Cairo Univ. Oct. 1966. \n4.\tMRCOG London Feb. 1975. \n5.\tF.R.C.S. Glasgow June 1976. \n6.\tPopulation Study Johns Hopkins 1981. \n7.\tGyn. Oncology Johns Hopkins 1983. \n8.\tAdvanced Laparoscopic Surgery, with Prof. Paulson, Alexandria, Virginia USA 1993. \nSocieties & Associations: \n1.\t Member of the Royal College of Ob./Gyn. London. \n2.\tFellow of the Royal College of Surgeons Glasgow UK. \n3.\tMember of the advisory board on urogyn. FIGO. \n4.\tMember of the New York Academy of Sciences. \n5.\tMember of the American Association for the Advancement of Science. \n6.\tFeatured in �Who is Who in the World� from the 16th edition to the 20th edition. \n7.\tFeatured in �Who is Who in Science and Engineering� in the 7th edition. \n8.\tMember of the Egyptian Fertility & Sterility Society. \n9.\tMember of the Egyptian Society of Ob./Gyn. \n10.\tMember of the Egyptian Society of Urogyn. \n\nScientific Publications & Communications:\n1- Abdel Karim M. El Hemaly*, Ibrahim M. Kandil, Asim Kurjak, Ahmad G. Serour, Laila A. S. Mousa, Amr M. Zaied, Khalid Z. El Sheikha. \nImaging the Internal Urethral Sphincter and the Vagina in Normal Women and Women Suffering from Stress Urinary Incontinence and Vaginal Prolapse. Gynaecologia Et Perinatologia, Vol18, No 4; 169-286 October-December 2009.\n2- Abdel Karim M. El Hemaly*, Laila A. S. Mousa Ibrahim M. Kandil, Fatma S. El Sokkary, Ahmad G. Serour, Hossam Hussein.\nFecal Incontinence, A Novel Concept: The Role of the internal Anal sphincter (IAS) in defecation and fecal incontinence. Gynaecologia Et Perinatologia, Vol19, No 2; 79-85 April -June 2010.\n3- Abdel Karim M. El Hemaly*, Laila A. S. Mousa Ibrahim M. Kandil, Fatma S. El Sokkary, Ahmad G. Serour, Hossam Hussein.\nSurgical Treatment of Stress Urinary Incontinence, Fecal Incontinence and Vaginal Prolapse By A Novel Operation \n"Urethro-Ano-Vaginoplasty"\n Gynaecologia Et Perinatologia, Vol19, No 3; 129-188 July-September 2010.\n4- Abdel Karim M. El Hemaly*, Ibrahim M. Kandil, Laila A. S. Mousa and Mohamad A.K.M.El Hemaly.\nUrethro-vaginoplasty, an innovated operation for the treatment of: Stress Urinary Incontinence (SUI), Detursor Overactivity (DO), Mixed Urinary Incontinence and Anterior Vaginal Wall Descent. \nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/ urethro-vaginoplasty_01\n\n5- Abdel Karim M. El Hemaly, Ibrahim M Kandil, Mohamed M. Radwan.\n Urethro-raphy a new technique for surgical management of Stress Urinary Incontinence.\nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/\nnew-tech-urethro\n\n6- Abdel Karim M. El Hemaly, Ibrahim M Kandil, Mohamad A. Rizk, Nabil Abdel Maksoud H., Mohamad M. Radwan, Khalid Z. El Shieka, Mohamad A. K. M. El Hemaly, and Ahmad T. El Saban.\nUrethro-raphy The New Operation for the treatment of stress urinary incontinence, SUI, detrusor instability, DI, and mixed-type of urinary incontinence; short and long term results. \nhttp://www.obgyn.net/urogyn/urogyn.asp?page=urogyn/articles/\nurethroraphy-09280\n\n7-Abdel Karim M. El Hemaly, Ibrahim M Kandil, and Bahaa E. El Mohamady. Menopause, and Voiding troubles. \nhttp://www.obgyn.net/displayppt.asp?page=/English/pubs/features/presentations/El-Hemaly03/el-hemaly03-ss\n\n8-El Hemaly AKMA, Mousa L.A. Micturition and Urinary\tContinence. Int J Gynecol Obstet 1996; 42: 291-2. \n\n9-Abdel Karim M. El Hemaly.\n Urinary incontinence in gynecology, a review article.\nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/abs-urinary_incotinence_gyn_ehemaly \n\n10-El Hemaly AKMA. Nocturnal Enuresis: Pathogenesis and Treatment. \nInt Urogynecol J Pelvic Floor Dysfunct 1998;9: 129-31.\n \n11-El Hemaly AKMA, Mousa L.A.E. Stress Urinary Incontinence, a New Concept. Eur J Obstet Gynecol Reprod Biol 1996; 68: 129-35. \n\n12- El Hemaly AKMA, Kandil I. M. Stress Urinary Incontinence SUI facts and fiction. Is SUI a puzzle?! http://www.obgyn.net/displayppt.asp?page=/English/pubs/features/presentations/El-Hemaly/el-hemaly-ss\n\n13-Abdel Karim El Hemaly, Nabil Abdel Maksoud, Laila A. Mousa, Ibrahim M. Kandil, Asem Anwar, M.A.K El Hemaly and Bahaa E. El Mohamady. \nEvidence based Facts on the Pathogenesis and Management of SUI. http://www.obgyn.net/displayppt.asp?page=/English/pubs/features/presentations/El-Hemaly02/el-hemaly02-ss\n\n14- Abdel Karim M. El Hemaly*, Ibrahim M. Kandil, Mohamad A. Rizk and Mohamad A.K.M.El Hemaly.\n Urethro-plasty, a Novel Operation based on a New Concept, for the Treatment of Stress Urinary Incontinence, S.U.I., Detrusor Instability, D.I., and Mixed-type of Urinary Incontinence.\nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/urethro-plasty_01\n\n15-Ibrahim M. Kandil, Abdel Karim M. El Hemaly, Mohamad M. Radwan: Ultrasonic Assessment of the Internal Urethral Sphincter in Stress Urinary Incontinence. The Internet Journal of Gynecology and Obstetrics. 2003. Volume 2 Number 1. \n\n\n16-Abdel Karim M. El Hemaly. Nocturnal Enureses: A Novel Concept on its pathogenesis and Treatment.\nhttp://www.obgyn.net/urogynecolgy/?page=articles/nocturnal_enuresis\n\n17- Abdel Karim M. El Hemaly. Nocturnal Enureses: An Update on the pathogenesis and Treatment.\nhttp://www.obgyn.net/urogynecology/?page=/ENHLIDH/PUBD/FEATURES/\nPresentations/ Nocturnal_Enuresis/nocturnal_enuresis\n\n18-Maternal Mortality in Egypt, a cry for help and attention. The Second International Conference of the African Society of Organization & Gestosis, 1998, 3rd Annual International Conference of Ob/Gyn Department � Sohag Faculty of Medicine University. Feb. 11-13. Luxor, Egypt. \n19-Postmenopausal Osteprosis. The 2nd annual conference of Health Insurance Organization on Family Planning and its role in primary health care. Zagaziz, Egypt, February 26-27, 1997, Center of Complementary Services for Maternity and childhood care. \n20-Laparoscopic Assisted vaginal hysterectomy. 10th International Annual Congress Modern Trends in Reproductive Techniques 23-24 March 1995. Alexandria, Egypt. \n21-Immunological Studies in Pre-eclamptic Toxaemia. Proceedings of 10th Annual Ain Shams Medical Congress. Cairo, Egypt, March 6-10, 1987. \n22-Socio-demographic factorse affecting acceptability of the long-acting contraceptive injections in a rural Egyptian community. Journal of Biosocial Science 29:305, 1987. \n23-Plasma fibronectin levels hypertension during pregnancy. The Journal of the Egypt. Soc. of Ob./Gyn. 13:1, 17-21, Jan. 1987. \n24-Effect of smoking on pregnancy. Journal of Egypt. Soc. of Ob./Gyn. 12:3, 111-121, Sept 1986. \n25-Socio-demographic aspects of nausea and vomiting in early pregnancy. Journal of the Egypt. Soc. of Ob./Gyn. 12:3, 35-42, Sept. 1986. \n26-Effect of intrapartum oxygen inhalation on maternofetal blood gases and pH. Journal of the Egypt. Soc. of Ob./Gyn. 12:3, 57-64, Sept. 1986. \n27-The effect of severe pre-eclampsia on serum transaminases. The Egypt. J. Med. Sci. 7(2): 479-485, 1986. \n28-A study of placental immunoreceptors in pre-eclampsia. The Egypt. J. Med. Sci. 7(2): 211-216, 1986. \n29-Serum human placental lactogen (hpl) in normal, toxaemic and diabetic pregnant women, during pregnancy and its relation to the outcome of pregnancy. Journal of the Egypt. Soc. of Ob./Gyn. 12:2, 11-23, May 1986. \n30-Pregnancy specific B1 Glycoprotein and free estriol in the serum of normal, toxaemic and diabetic pregnant women during pregnancy and after delivery. Journal of the Egypt. Soc. of Ob./Gyn. 12:1, 63-70, Jan. 1986. Also was accepted and presented at Xith World Congress of Gynecology and Obstetrics, Berlin (West), September 15-20, 1985. \n31-Pregnancy and labor in women over the age of forty years. Accepted and presented at Al-Azhar International Medical Conference, Cairo 28-31 Dec. 1985. \n32-Effect of Copper T intra-uterine device on cervico-vaginal flora. Int. J. Gynaecol. Obstet. 23:2, 153-156, April 1985. \n33-Factors affecting the occurrence of post-Caesarean section febrile morbidity. Population Sciences, 6, 139-149, 1985. \n34-Pre-eclamptic toxaemia and its relation to H.L.A. system. Population Sciences, 6, 131-139, 1985. \n35-The menstrual pattern and occurrence of pregnancy one year after discontinuation of Depo-medroxy progesterone acetate as a postpartum contraceptive. Population Sciences, 6, 105-111, 1985. \n36-The menstrual pattern and side effects of Depo-medroxy progesterone acetate as postpartum contraceptive. Population Sciences, 6, 97-105, 1985. \n37-Actinomyces in the vaginas of women with and without intrauterine contraceptive devices. Population Sciences, 6, 77-85, 1985. \n38-Comparative efficacy of ibuprofen and etamsylate in the treatment of I.U.D. menorrhagia. Population Sciences, 6, 63-77, 1985. \n39-Changes in cervical mucus copper and zinc in women using I.U.D.�s. Population Sciences, 6, 35-41, 1985. \n40-Histochemical study of the endometrium of infertile women. Egypt. J. Histol. 8(1) 63-66, 1985. \n41-Genital flora in pre- and post-menopausal women. Egypt. J. Med. Sci. 4(2), 165-172, 1983. \n42-Evaluation of the vaginal rugae and thickness in 8 different groups. Journal of the Egypt. Soc. of Ob./Gyn. 9:2, 101-114, May 1983. \n43-The effect of menopausal status and conjugated oestrogen therapy on serum cholesterol, triglycerides and electrophoretic lipoprotein patterns. Al-Azhar Medical Journal, 12:2, 113-119, April 1983. \n44-Laparoscopic ventrosuspension: A New Technique. Int. J. Gynaecol. Obstet., 20, 129-31, 1982. \n45-The laparoscope: A useful diagnostic tool in general surgery. Al-Azhar Medical Journal, 11:4, 397-401, Oct. 1982. \n46-The value of the laparoscope in the diagnosis of polycystic ovary. Al-Azhar Medical Journal, 11:2, 153-159, April 1982. \n47-An anaesthetic approach to the management of eclampsia. Ain Shams Medical Journal, accepted for publication 1981. \n48-Laparoscopy on patients with previous lower abdominal surgery. Fertility management edited by E. Osman and M. Wahba 1981. \n49-Heart diseases with pregnancy. Population Sciences, 11, 121-130, 1981. \n50-A study of the biosocial factors affecting perinatal mortality in an Egyptian maternity hospital. Population Sciences, 6, 71-90, 1981. \n51-Pregnancy Wastage. Journal of the Egypt. Soc. of Ob./Gyn. 11:3, 57-67, Sept. 1980. \n52-Analysis of maternal deaths in Egyptian maternity hospitals. Population Sciences, 1, 59-65, 1979. \nArticles published on OBGYN.net: \n1- Abdel Karim M. El Hemaly*, Ibrahim M. Kandil, Laila A. S. Mousa and Mohamad A.K.M.El Hemaly.\nUrethro-vaginoplasty, an innovated operation for the treatment of: Stress Urinary Incontinence (SUI), Detursor Overactivity (DO), Mixed Urinary Incontinence and Anterior Vaginal Wall Descent. \nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/ urethro-vaginoplasty_01\n\n2- Abdel Karim M. El Hemaly, Ibrahim M Kandil, Mohamed M. Radwan.\n Urethro-raphy a new technique for surgical management of Stress Urinary Incontinence.\nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/\nnew-tech-urethro\n\n3- Abdel Karim M. El Hemaly, Ibrahim M Kandil, Mohamad A. Rizk, Nabil Abdel Maksoud H., Mohamad M. Radwan, Khalid Z. El Shieka, Mohamad A. K. M. El Hemaly, and Ahmad T. El Saban.\nUrethro-raphy The New Operation for the treatment of stress urinary incontinence, SUI, detrusor instability, DI, and mixed-type of urinary incontinence; short and long term results. \nhttp://www.obgyn.net/urogyn/urogyn.asp?page=urogyn/articles/\nurethroraphy-09280\n\n4-Abdel Karim M. El Hemaly, Ibrahim M Kandil, and Bahaa E. El Mohamady. Menopause, and Voiding troubles. \nhttp://www.obgyn.net/displayppt.asp?page=/English/pubs/features/presentations/El-Hemaly03/el-hemaly03-ss\n\n5-El Hemaly AKMA, Mousa L.A. Micturition and Urinary\tContinence. Int J Gynecol Obstet 1996; 42: 291-2. \n\n6-Abdel Karim M. El Hemaly.\n Urinary incontinence in gynecology, a review article.\nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/abs-urinary_incotinence_gyn_ehemaly \n\n7-El Hemaly AKMA. Nocturnal Enuresis: Pathogenesis and Treatment. \nInt Urogynecol J Pelvic Floor Dysfunct 1998;9: 129-31.\n \n8-El Hemaly AKMA, Mousa L.A.E. Stress Urinary Incontinence, a New Concept. Eur J Obstet Gynecol Reprod Biol 1996; 68: 129-35. \n\n9- El Hemaly AKMA, Kandil I. M. Stress Urinary Incontinence SUI facts and fiction. Is SUI a puzzle?! http://www.obgyn.net/displayppt.asp?page=/English/pubs/features/presentations/El-Hemaly/el-hemaly-ss\n\n10-Abdel Karim El Hemaly, Nabil Abdel Maksoud, Laila A. Mousa, Ibrahim M. Kandil, Asem Anwar, M.A.K El Hemaly and Bahaa E. El Mohamady. \nEvidence based Facts on the Pathogenesis and Management of SUI. http://www.obgyn.net/displayppt.asp?page=/English/pubs/features/presentations/El-Hemaly02/el-hemaly02-ss\n\n11- Abdel Karim M. El Hemaly*, Ibrahim M. Kandil, Mohamad A. Rizk and Mohamad A.K.M.El Hemaly.\n Urethro-plasty, a Novel Operation based on a New Concept, for the Treatment of Stress Urinary Incontinence, S.U.I., Detrusor Instability, D.I., and Mixed-type of Urinary Incontinence.\nhttp://www.obgyn.net/urogyn/urogyn.asp?page=/urogyn/articles/urethro-plasty_01\n\n12-Ibrahim M. Kandil, Abdel Karim M. El Hemaly, Mohamad M. Radwan: Ultrasonic Assessment of the Internal Urethral Sphincter in Stress Urinary Incontinence. The Internet Journal of Gynecology and Obstetrics. 2003. Volume 2 Number 1. \n\n13-Abdel Karim M. El Hemaly. Nocturnal Enureses: A Novel Concept on its pathogenesis and Treatment.\nhttp://www.obgyn.net/urogynecolgy/?page=articles/nocturnal_enuresis\n\n14- Abdel Karim M. El Hemaly. 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