Open access peer-reviewed chapter

Spinel‐Structured Nanoparticles for Magnetic and Mechanical Applications

By Malik Anjelh Baqiya, Ahmad Taufiq, Sunaryono, Khuroti Ayun, Mochamad Zainuri, Suminar Pratapa, Triwikantoro and Darminto

Submitted: May 19th 2016Reviewed: October 12th 2016Published: March 8th 2017

DOI: 10.5772/66293

Downloaded: 1845


Nanoparticles of Fe3O4 have been successfully synthesized using a simple coprecipitation technique from natural iron sands, employing HNO3 and NH4OH as dispersing and precipitating agents, respectively. The substitution of Fe with Mn to result in Fe3-xMnxO4 (0 ≤ x ≤ 3) was conducted to control the magnetic strength of this nano‐sized spinel powder. It is shown that magnetic properties depend not only on the particle size and Mn doping but also on the particles clustering. The applications for magnetic fluids, gels, and coating are extensively described. Meanwhile, the spinel MgAl2O4 nanoparticles have also been prepared by the same simple method from commercial starting materials. This powder was used as a nano‐reinforcer of Al‐matrix composites. In addition, MgAl2O4 micro‐sized powder forming a thick layer was successfully grown by electroless plating on the interface of matrix‐filler in Al/SiC composites. The strengthening of mechanical properties with respect to the varying uses of these MgAl2O4 powders is discussed.


  • Fe3O4
  • MgAl2O4
  • Powders
  • Coprecipitation
  • Magnetic
  • mechanical properties

1. Introduction

Spinel structures have the general formula of AB2X4, where X can be oxygen (oxides) or a chalcogen element, such as sulfur (thio‐spinels) and selenium (seleno‐spinels). A and B in the spinel structures can be divalent, trivalent, or tetravalent cations, such as iron, magnesium, aluminum (Al), zinc, manganese, chromium, and titanium. The various compounds of spinel family including their chemical and physical properties depend not only on the arrangement of cations and anions in the structures but also on how the spinels are produced. The spinels can be magnetic or non‐magnetic compounds depending on the nature of the cations among the A and B sub‐lattices. Fe3O4 (FeO.Fe2O3) is one of the so‐called spinel ferrite having magnetic properties, whereas MgAl2O4 is also spinel (should not be confused with the spinel structure described earlier) which is non‐magnetic one. This chapter covers some of the physical properties of the spinel compounds in more detail.


2. Magnetite (Fe3O4) nanoparticles

Fe3O4 (magnetite) or the black iron oxide in the form of nanoparticles has huge potential for applications in many fields. However, preparing Fe3O4 particles in small size with high quality is enormously challenging for several reasons. Therefore, the preparation of Fe3O4 nanoparticles in several forms and various sizes with high purity and homogeneity becomes an essential task before applications. The following section provides more details on the preparation and applications of Fe3O4 nanoparticles.

Several synthesis methods to prepare high‐purity Fe3O4 nanoparticles in various forms and sizes have been reported in the literature. In general, Fe3O4 nanoparticles have been successfully prepared through sonochemical [1], thermal decomposition [2], ionothermal [3], hydrothermal [4], micro‐emulsion [5], sol‐gel [6], modified hydrolysis [7], solvothermal [8], electrospinning [9], coprecipitation [10] methods, and so forth. However, high quality of the particles, such as good particle size distribution with high crystalline, structural and compositional homogeneity, still has become one of the main challenges in preparing Fe3O4 nanoparticles [11].

The improvement of synthesis methods has also been carried out for producing Fe3O4 nanoparticles in order to reduce cost and time of preparation. A simple method to produce Fe3O4 nanoparticles via coprecipitation method has been introduced using a local natural iron sand from Indonesia as a starting material. This coprecipitation method is considered to be the easiest method for preparing Fe3O4 nanoparticles [12] because of its simplicity, efficiency, and inexpensiveness [13]. The use of starting material from commercial product can be substituted by natural iron sand.

As for the preparation of Fe3O4 nanoparticles using coprecipitation method, the ratio of ferrous and ferric ions is very crucial affecting the synthesis result. The effects include the particle diameter and magnetic properties. Iida et al. [14] have reported that the valence of the metal salt is an important factor for determining the particle size of the magnetic particles. In their experiments, they have succeeded in obtaining Fe3O4 nanoparticles in the size range of 9–40 nm with various molar contents of ferrous ions in the total amount of the iron ions. Furthermore, Gnanaprakash et al. [15] have also reported that initial pH and temperature of the iron salt solution during coprecipitation process have strong influences for the formation of magnetite nanoparticles. They reported that the average of particle size having initial pH value of 0.7, 1.5, 3, and 4.7 are 6.7, 7.6, 9.9, and 9.9 nm, respectively. Determination of particle size is very important according to how they will be used for certain applications, namely for magnetic fluids and gels.

In the magnetic nanoparticles’ syntheses, the so‐called templating method has been employed to form certain particle shapes and sizes, such as one dimensional (1‐D) particles or nanorods. Lian et al. [16] have successfully synthesized nanorods of Fe3O4 through the addition of polyethylene glycol (PEG) 1000 as a template with the average particle diameter and length of 80 nm and 2 µm, respectively. Therefore, templating technique has important role on the particle growth of magnetic nanomaterials. The greater value of the PEG’s molecular weight will lead to the higher possibility to obtain nanorods resulted from the synthesis [17]. Furthermore, based on the research of He et al. [18], Fe3O4 nanowire has successfully been prepared depending on the volume ratio of PEG and H2O. They have found that the best formation is achieved with the ratio of 1:3; a higher ratio gives higher viscosity and inhibits the particle formation.


3. Fe3O4 spinels for magnetic fluids and gels

Generally, the study of Fe3O4 nanoparticles has attracted attention for several disciplines. Physicists investigate the physical properties and propose the theories of the Fe3O4 nanoparticles. Chemists focus on the synthesis methods of the Fe3O4 nanoparticles. Biologists concentrate on developing Fe3O4 nanoparticles in bioapplications. Meanwhile, engineers study Fe3O4 nanoparticles with a focus on technological applications. Therefore, there is a great deal of interest in Fe3O4 nanoparticles by scientists and engineers, starting from synthesis and characterizations and followed by their many application potentials.

Fe3O4 ferrofluids or magnetic fluids are colloidal suspension containing magnetite nanoparticles in single domain, which are dispersed in a liquid carrier. Ferrofluids have unique characteristics because they have both the liquid and magnetic properties. In the ferrofluids, the liquid carriers can be polar or nonpolar medium. In order to prevent agglomerations, the Fe3O4 nanoparticles should be layered or covered by an appropriate material as a shell [19]. In the last decades, it has been reported that the Fe3O4 ferrofluids can be applied in various fields, that is, optical grating, optical switching [20], thermoelectric conversion [21], quenching media [22], sensor [23], controlling lubricant migration [24], biomedical applications [25], and so forth.

Another application for the magnetite spinel is in ferrogels, namely a hydrogel containing magnetic ferrous particles. The Fe3O4‐ferrogel can be defined as a polymer (nano)composites with polyvinyl alcohol (PVA) and Fe3O4 as the matrix and filler, respectively, cross‐linked together with a certain amount of liquid (water). Ferrogels can be physically or chemically cross‐linked without any chemical reaction between them. The physical properties of ferrogels depend on the preparation conditions, such as polymer and solvent ratio, particle size, distribution and concentration of the magnetic material. By combining the elastic medium and the magnetic properties from the particles, the elastic behavior of ferrogel can be manipulated by external magnetic field. This leads to a great opportunity for various advanced applications, namely soft actuators and artificial muscles [26].

In the development of magneto‐elastic materials, Li et al. [27] have prepared a polymeric gel in variety of shapes depending on the temperature. Furthermore, Zrínyi et al. [28] have developed a magneto‐sensitive gel with Fe3O4 as the magnetic filler. Ramanujan and Lao [26] have successfully produced magnetic gel consisting of PVA and micro‐sized Fe3O4 particles for artificial tissues. They have demonstrated an elastic behavior of the gel controlled by an external magnetic field.


4. Spinel MgAl2O4 grown as a thick coating and fillerreinforcer in composites

Compared to the conventional aluminum alloys, aluminum metal matrix composites (Al‐MMC) have been used in many kinds of applications (e.g. automobiles) due to their high specific strength and Young's modulus, improved yield and creep strengths, light weight, and excellent properties of wear resistance. The important parameter for improving their performances lies in the structure and bonding properties between the matrix and fillers. Some materials in any form of particles have been widely used as the particle‐matrix interfaces in order to improve the wettability [29], namely MgO, SiC, and Al2O3 in the micro‐ or nanostructures. It has been noted that the interface, particles size, and its distribution as well as the concentration (volume fraction) play a basic role in the modification of Al‐MMC.

A typical way to improve the mechanical properties of Al‐MMC is by additional reinforcement or interfacial modification. Recently, the spinel MgAl2O4 has been applied for this purpose. In the last decade, MgAl2O4 has been produced by several methods such as solid‐state reaction [30], high‐energy ball milling [31], polymerization method [32], pyrolysis [33], sol‐gel processes [34, 35], and coprecipitation techniques [3638]. The shape and size of the spinel particles vary depending on the preparation techniques [39, 40]. This spinel can be prepared in the form of ceramic foams [41, 42], whiskers [4345], thin films [46, 47], nanoparticles [37, 48, 49], and also layer of particle bonding in composite materials [50]. For the Al/SiC composites, in which Al acts as the matrix and SiC acts as the filler reinforcement, Al4C3 phase can be formed at the interface between matrix and fillers. This phase weakens the mechanical strength of the composite. Up to now, several experimental techniques have been proposed to prevent this problem including adding excessive Si into the matrix and introducing a thin coating layer on the SiC particle surface. The formation of interlayer phase is believed to be a stable interfacial bonding that improves the mechanical properties of the composite. However, the detail of this mechanism remains unclear.

Particulate‐reinforced composites with micron‐sized filler of various materials are the most commonly used composites in daily life. Particles are typically introduced to enhance the matrix elastic modulus and yield strength. It has been shown that the novel properties of composites are improved by adding nano‐scaled particles as the fillers [51]. The key role of mechanical strength in composites is the interface‐bonding quality between matrix and filler materials. The nano‐sized particles have much greater total area compared to particles with larger size at the same volume. The interface interaction can therefore be extended by reducing particle size of fillers down to nanometer scale.

Meanwhile, synthesis of particles in nanometer size of various materials is still an active area of research. Because of their very small size, nanoparticles tend to be aggregate to each other to form larger size particles [52]. As nanometer‐scaled filler, the particles have to be kept separate in the matrix. In this context, an effort to maintain nanoparticles as fillers from agglomeration was achieved by the introduction of a surfactant. Tetra‐methyl‐ammonium‐hydroxide (TMAH) could be used as surfactant in the process of filler‐matrix‐mixing media. Aluminum was chosen as matrix, while MgO and MgAl2O4 were used as nano‐fillers. In the case of Al/SiC composites, a thin‐layer MgAl2O4 is coated onto the SiC filler to enhance matrix‐filler interfacial bonding leading to increased mechanical strength. The SiC fillers were coated by spinel MgAl2O4 by electroless plating, soaking SiC particulate powder in solutions containing Mg and Al ions before heating process to grow spinel phase on the surface.


5. Preparation of Fe3O4 nanoparticles from iron sands

The detail of synthesis method for the preparation of Fe3O4 nanoparticles was described in our previous works [5357]. The iron sand was extracted by a magnetic separator to obtain dominantly Fe3O4 powders. Using a magnetic stirrer, the hydrochloric acid (HCl) was used to dissolve the Fe3O4 powder to produce FeCl3 and FeCl2 solutions at room temperature as written in Eq. (1).

Fe3O4 + 8HCl 2FeCl3 + FeCl2 +  4H2OE1

The solution of FeCl3 and FeCl2 was then reacted by dropping slowly ammonium hydroxide (NH4OH) to produce black precipitate at room temperature. The reaction mechanism for producing Fe3O4 particles is described as Eq. (2) [54]

2FeCl3 + FeCl2 + 8NH4OH Fe3O4 + 8NH4Cl + 4H2OE2

In order to synthesize MnxFe3‐xO4 nanoparticles discussed later and investigate its magnetic properties, the variation of Mn concentration from MnCl2 solution was also prepared to form MnxFe3-xO4 (0 <x≤ 1). The dissolved MnCl2 solution was mixed using a magnetic stirrer followed by a drop‐wise addition of NH4OH to obtain the precipitate of Fe3O4 and MnxFe3-xO4. The magnetic moment of Mn2+ ion is 25% higher than that of Fe2+ ion. Therefore, introducing Mn2+ into Fe3O4 to form MnxFe3‐xO4 structure will theoretically enhance the magnetization of Fe3O4 [58]. A washing process of the precipitate was then carried out for several times using distilled water until achieving normal pH condition. Finally, the Fe3O4 powders were prepared by drying process at 100°C for 1 h. For the preparation of Fe3O4 magnetic fluid, tetra‐methyl‐ammonium‐hydroxide (TMAH), as the stabilizing layers of the particles, was added in the precipitate. In the present investigation, Fe3O4 ferrogels were also synthesized using freezing‐thawing method as described in Refs. [57, 59].

To study the crystal structure, the particle size and its distribution as well as form and structural factor, and the magnetic properties of the sample, the Fe3O4 powders were then characterized by means of X‐ray diffractometry (XRD), small‐angle neutron scattering (SANS) spectrometer and superconducting quantum interference device (SQUID) magnetometer, respectively. The XRD measurements were carried out in the 2θrange from 20° to 70° using Cu‐Kα radiation. A 36‐m SANS spectrometer was used to investigate the primary and secondary particles as well as the fractal structure of Fe3O4 nanoparticles. The detailed SANS measurements have been given elsewhere [54, 60]. The two‐lognormal analysis was also performed to investigate the clustering effect of the magnetic fluid and hydrogel [55, 57].


6. Preparation of spinel MgAl2O4 as filler reinforcers

Magnesium oxide (MgO) and magnesium‐aluminum oxide (MgAl2O4) as fillers were synthesized by employing coprecipitation process. Mg (Aldrich, 99.9%) and Al (Aldrich, 99.9%) were dissolved in HCl (12.63 molar) with stoichiometric molar fraction. The NH4OH (6.5 molar) was used as precipitating agent to produce Mg(OH)2 and MgAl2O4 after filtering, washing process with distilled water for several times, and finally drying at 100°C. The resulting powders were then heated at 500°C for 1 h to convert them into MgO and MgAl2O4 phases. The powders were checked with XRD and transmission electron microscope (TEM) to explore the phase purity, crystallite size, particle shape, and size.

The MgO and MgAl2O4 powders were mixed with TMAH as surfactant to form a colloid system, consisting of individual MgO or MgAl2O4 particles which were homogeneously dispersed. To fabricate composites, Al powders as matrix were added into the colloid system and followed by thorough stirring and grinding to achieve homogeneity. The mixed powders were dried at 100°C for 3 h and then pressed into pellets having a diameter of 1 cm. During pelletization, the powders were compacted using a force of 1.5 kN applied for 15 min in an isostatic die with zinc stearate on the inner disc. Before sintering process at 500°C for 1 h, pellets were pre‐sintered at, respectively, 200 and 400°C for 20 min each. All heat treatments were conducted in a furnace with a controlled atmosphere of low vacuum (∼10-3 atm).

The samples produced consist of Al/MgO and Al/MgAl2O4 composites with various volume fractions (% vol) of fillers covering 10, 20, and 30%. We have also prepared the corresponding samples fabricated without TMAH for comparison. To study the effects of surfactant addition during the process on the fabricated composites, measurements of densities, porosity, elastic modulus by compressive test, and microhardness (Vicker's hardness number, VHN) of the samples were carried out.

Furthermore, to prepare the Al/SiC composites, the aluminum (PA) powders and particles of SiC ceramics (220 mesh) were employed as starting materials. The SiC reinforcement particles were cleaned by ultrasonic cleaner in alcohol (90%), and then dried in oven at 100°C. The SiC particles were then soaked in an electrolyte media of 40 ml HNO3 containing Al and Mg ions as the part of the electroless‐plating mechanism. The process of metal oxide coating was done using a magnetic stirrer at 125°C. The oxidation of SiC particles to grow the MgAl2O4 layer was performed in a furnace at 200°C for 1 h, and continued at 400°C for another 1 h. The electrolyte media for electroless plating can be controllably adjusted to grow various metal oxides on the SiC surface, such as MgO, CuO, Al2O3, and so forth, besides MgAl2O4. The metal oxide‐coated SiC particles were mixed with Al powders in n‐butanol (wet mixing) using magnetic stirrer at 100°C, having SiC volume fraction (%vol) of 10, 20, and 30%. The heating process of the green pellets was carried out in a vacuum (10-3 Torr, rotary pump) by applying a pre‐sintering at 200°C for 20 min and followed by sintering at 600°C for 1 h.


7. Results and discussion

7.1. Fe3O4 nanoparticles: magnetic properties and applications

The XRD pattern of Fe3O4 nano‐powders is shown in Figure 1. All peaks in the pattern show a single phase of spinel structure corresponding to the crystal structure of Fe3O4 with PDF No. 19‐0629 without any impurity. Based on the Rietveld analysis, the sample has lattice parameter a= b= cof approximately 8.377 Å.

Figure 1.

The XRD pattern of Fe3O4 nano‐powders (using Cu‐Kα radiation).

The SANS pattern of the Fe3O4 nano‐powders is presented in Figure 2. The SANS data were analyzed using a lognormal spherical model as a form factor P(R) and mass fractal model as a structure factor S(q), following Eqs. (3) and (4), respectively,


Figure 2.

SANS data of Fe3O4 nano‐powders.

with R0 and σ representing the radius of the distribution and standard deviation, respectively [61],


where q, Γ, D, and ξrepresent the scattering vector, gamma function, fractal dimension, and cut‐off distance, respectively [62]. The SANS curve was fitted globally using two lognormal spherical model as form factor combining with mass fractal model as structure factor regarding Eq. (5) [54]


Here, Iis the density, Nis the number density of particles, R1 is the primary particles, R2 is the secondary particles or clusters, and Fis the scattering amplitude.

Based on the analysis using lognormal and mass fractal models, the Fe3O4 nano‐powders have hierarchical nanostructure with the primary particles of 3.8 nm as a building block constructing secondary particles as clusters of 9.3 nm. The clusters of Fe3O4 nanoparticles have a fractal structure in three‐dimension with fractal dimension of 2.9. The SANS data analysis of magnetic nanoparticles coincides with the image produced by high‐resolution transmission electron microscopy (HRTEM) as shown in the previous work [54]. The details of the analysis of SANS data of the Fe3O4 nanoparticles were presented in the previous work [54].

The magnetic properties of the Fe3O4 nanoparticles as well as M versus H variations and zero‐field‐cooling (ZFC) curves are presented in Figures 3 and 4. The M versus H curve of the Fe3O4 nanoparticles was collected at room temperature by sweeping the magnetic field from -5 to 5 T. The Fe3O4 nanoparticles have saturated magnetization of 37.1 emu/g. Regarding Figure 3, it is clear that the M‐H curve of sample has S‐shape with nearly zero coercivity field, indicating the superparamagnetic behavior at room temperature. This result is consistent with the recent paper by Abboud et al. [63] where the magnetization was almost zero in the absence of external magnetic field. The superparamagnetic phenomenon in the magnetic nanoparticles has also been observed in the Fe3O4@SiO2 core‐shell composites [64], the dispersed Fe3O4 in the polymer matrix [65], and Fe3O4‐LiMo3Se3 [66]. Moreover, the zero‐field‐cooling (ZFC) measurement was also carried out to investigate the superparamagnetic phenomenon of the sample as shown in Figure 4. Based on the results in Figure 4, it is evident that the sample has a maximum peak of magnetic blocking temperature, TB, at 243 K. Theoretically, TB depends on the particle size and shape so the increase of nanoparticle's volume will increase the TB value [67].

Figure 3.

M‐H curve of Fe3O4 nanoparticles at room temperature.

Figure 4.

Zero‐field‐cooling (ZFC) curve of Fe3O4 nanoparticles (TB = 243 K).

Dutta et al. [68] have reported that Fe3O4 nanoparticles with the particles size ranging from 4 to 12 nm have blocking temperature lower than 100 K, which is not similar to the result of this work. The difference of these results can be explained in a sense of the presence of clusters or aggregations phenomena in the present work. In Ref. [68], the samples were constructed with primary particles in relatively homogeneous samples without any clusters or aggregations. On the other hand, the sample in this work consists of hierarchical nanostructures of primary particles forming secondary particles or clusters with fractal dimension in three‐dimensions. Despite the particles size and anisotropy constant, the clusters of magnetic nanoparticles give an effect on the blocking temperature. Theoretically, at magnetic‐blocking temperature, the thermal energy of particles is comparable with the anisotropy energy barrier. In bulk, the Fe3O4 is ferrimagnetic generated by net magnetic moments at tetrahedral and octahedral sites. The effect of clusters on magnetic properties was also documented by other researchers [69, 70].

In the magnetic nanoparticles, there is the so‐called blocking temperature or the energy barrier that can be obtained from ZFC and field‐cooling (FC) magnetization curves. With increasing temperature, a curve peak should appear in the ZFC measurement. This peak temperature can be considered as the average TB in the magnetic material. On the other hand, the increase of magnetic field should decrease the barrier energy, and results in a shift of the blocking temperature to lower temperatures. A typical of nanocrystalline Fe3O4 has shown superparamagnetic behavior (Figure 3). The superparamagnetism is related to the random fluctuation of the magnetization of a single domain when the thermal energy overcomes the anisotropy energy barrier. Below the TB, the magnetization of each domain of nanoparticles is oriented parallel to a certain crystallographic direction or the easy axis with minimum energy. Consequently, the magnetization is blocked in the nanoparticles. Above TB, the thermal energy can overcome the anisotropy energy (barrier energy) and the magnetization starts fluctuating and the magnetic susceptibility follows modified Curie‐law behavior at higher temperatures [71].

The effect of Mn2+ substitution on the magnetic properties of MnxFe3-xO4 nanoparticles has been intensively studied recently [54, 72]. It has been found that the lattice parameters and crystal volume of the MnxFe3-xO4 increase with the increase of Mn content. This is due to the fact that the ionic radius of Fe2+ is smaller than that of Mn2+ substituted in the spinel structure. Fe3O4 without any substitution has a cubic spinel structure, where the Fe2+ and Fe3+ ions occupy the tetrahedral (A) and octahedral (B) sites represented by (Fe3+)A(Fe3+Fe2+)BO2-4. The Fe3O4 is one example of the cubic inverse spinels, in which there is a mixed valence of Fe ions on the octahedral sublattice. In the MnxFe3‐xO4, the cationic distribution can be written as follows [54]:


The Mn2+ ions occupy the A sites of the spinel structure. A further analysis of the SANS data of the MnxFe3‐xO4 nanoparticles from x= 0 to 1 using the lognormal function has found that the particle size of the MnxFe3-xO4 depends on the Mn content. In this study, the increase of Mn content results in the smaller size of the nanoparticles. Moreover, the nanoparticles of MnxFe3-xO4 tend to become larger aggregates or clusters. The Mn content, particle size, and particle clustering are important factors influencing the magnetic properties of nanomaterials.

Taufiq et al. [55] have successfully synthesized Fe3O4 magnetic fluid with a chain‐like spinel structure using coprecipitation method. These results show that the Fe3O4 ferrofluid has a primary particle size of about 7.6 nm and the size of fractal aggregates of about 45 nm constructing the chain‐like structure. Even though there were chain aggregates, a homogeneous particle distribution with low polydispersity value of about 0.4 was found, which is lower than that in the former paper [55]. It is reported that both nanoparticles of Fe3O4 and MnxFe3-xO4 (xup to 1) exhibit superparamagnetic behavior and their saturation magnetization decreases with increasing Mn content [54, 72].

In the research of magnetic hydrogels, Fe3O4 ferrogels have been investigated by Sunaryono et al. [57]. It has been reported that the magneto‐elastic properties of the ferrogels were strongly affected by the preparation technique, the ratio of the magnetic particle and the polymer, and magnetic particle content as well as the particle clustering and distribution. It has also been shown that the magneto‐elasticity of the ferrogel tends to decrease with the increasing Fe3O4 content from 2.5 to 15% [56, 57]. Further analysis of the SAXS data using the two‐lognormal distribution function showed that Fe3O4 in the hydrogel has primary particles of about 3 nm with an average particle distance of about 18 nm. Higher Fe3O4 concentration in the hydrogel leads to the increase of Fe3O4 cluster size. Due to the surface effect, it influences the magnetization value of the ferrogel. Consequently, the saturation magnetization drops with decreasing particle size and the cluster of Fe3O4 nanoparticles in the hydrogel. It has been confirmed that Fe3O4 ferrogel exhibits a superparamagnetic behavior at room temperature which is a crucial parameter for biomedical applications.

7.2. Improved mechanical properties of aluminum matrix composites with surfactant‐coated MgAl2O4 nanofillers and MgAl2O4‐coated SiC particulates

Figure 5 presents the XRD spectra (using Cu‐Kα radiation, λ= 1.54 angstrom) of MgO and MgAl2O4 particles as results of coprecipitation process. The powders seem to be single phase as can be seen from the spectra, where no other additional diffraction peak is observed, except those associated with Miller indexes belonging to the MgO (periclase phase) and MgAl2O4 (spinel phase) as specified in Figure 5. Besides, the diffraction peaks are much broadened, featuring that the crystal is in nanometer size. If we take the full‐width at half maximum (FWHM) of diffraction peaks, by using Scherrer formula [73] and taking the apparatus‐broadening correction into account, we arrive at crystallite sizes of 17.5 ± 2.3 and 6.3 ± 0.7 nm for MgO and MgAl2O4 powders, respectively.

Figure 5.

XRD spectra of MgO and MgAl2O4.

Figure 6.

TEM images of (a) MgO and (b) MgAl2O4.

It is interesting to correlate the above crystallite size to the particle size of powders from TEM images depicted in Figure 6. The particle size for both powders, MgO in Figure 6a and MgAl2O4 in Figure 6b, is seen to be between 50 and less than 100 nm, confirming that the powders can be classified as nanoparticles. The shape of particles is observed to be varied from spherical, square, square with rounded edge, to semi‐rod. Comparing the crystal and the particle sizes, one can consider that both MgO and MgAl2O4 powders contain secondary particles, where each particle is constituted by several crystals or grains.

Figure 7.

Porosity of sintered Al/MgO and Al/MgAl2O4 composites with fillers specified.

Figure 8.

Elastic moduli of sintered Al/MgO and Al/MgAl2O4 composites with fillers specified.

To discuss further, the physical properties of composites, the density of pellets in the green state (after compaction) and after sintering significantly increases with increasing volume fraction of fillers and the use of surfactant (coated fillers by surfactant). The enhanced density has led to the lowering porosity in the pellets. By applying the formula to define porosity [52]: ρ= 1 –ρs/ρt, where ρs and ρt stand for, respectively, sintered and theoretical densities, the porosity of samples is exhibited in Figure 7. The increase of pellet densification has directly affected the mechanical properties, as reflected by the results of compressive tests (yielding elastic modulus) and hardness (VHN) measurements (see Figures 8 and 9).

Figure 9.

Micro‐hardness of sintered Al/MgO and Al/MgAl2O4 composites with fillers specified.

It is worth noting that the role of surfactant is to enhance the physical and therefore mechanical properties of these Al/MgO and Al/MgAl2O4 nanocomposites. The TMAH as a mixing media of matrix and filler is an ionic molecule which will attach on the surface of nanoparticles. A metal‐oxide nanoparticle is usually deficient of oxygen ion [74], hence its surface is positively charged. The negatively charged end of TMAH molecule is therefore attracted by metal‐oxide surface, while the opposite end is dangled. It may further create the situation where one may consider that MgO or MgAl2O4 nanoparticle is “coated” by TMAH. This in turn avoids nanoparticles from aggregation to each other in the matrix. So, the filler is still in nanometer scale to maintain its larger surface area, especially compared to the agglomerated fillers having the same volume fraction in the composites fabricated without TMAH. The larger filler surface will lead to stronger interface bonding between matrix and filler.

The next attractive point to address is that the surfactant‐coated MgO filler has led to considerably enhanced elastic modulus (∼60%) and microhardness (∼40%) of the Al‐matrix nanocomposites (Figures 8 and 9). The periclase phase of MgO has simpler crystal structure than the spinel MgAl2O4 one [75, 76]. The former phase is transformed from Mg(OH)2 at 500°C, whereas the latter one is already stable from 100°C as a result of coprecipitation process. Besides particles consolidation during the sintering at 500°C, the MgO filler will be possibly able to react further in a limited amount with Al matrix to form spinel phase on the matrix‐filler interface, creating a strong bonding. Such kind of process, except consolidation, may not occur in the Al/MgAl2O4 composite, because of stable MgAl2O4.

Figure 10.

Elastic modulus of Al/SiC composites depending on filler content, using SiC coated by metal oxides as specified.

Going to further study on Al/SiC composites, it can be seen in Figure 10 that a very clear distinction exists between SiC particles without coating and with coated metal oxides on the surface based on the modulus elasticity. The entire filler volume fraction (%vol) of SiC in Al‐SiC composites using coatings has higher value than that without coating. The experimental results show that the modulus of elasticity of the composites using metal‐oxide coating approaches the theoretical prediction [77], estimating a limit of lower and upper bounds. Based on the stress analysis, the composite having filler without metal oxide coating, for all low‐volume fraction of reinforcement, the modulus value lies in the outside of the upper and lower bounds, which indicates weak interaction between matrix and filler. This is much different from composites with filler using metal oxides, where for the entire volume fraction of reinforcement, the elastic modulus lies inside the region of the upper and lower bounds, implying that the compactibility between matrix and filler, and reinforcements are therefore going well. One can see in Figure 10 that coating with MgAl2O4 onto the SiC surface has produced the superior Al/SiC composites among the prepared samples, followed by Al2O3 and MgO. The three metal oxides coating materials mentioned seem to be compatible in facilitating and therefore enhancing interfacial bonding between Al matrix and SiC filler in the composites.


8. Conclusions

  1. Fe3O4 and the MnxFe3-xO4 (0 < x≤ 1) nanoparticles have been successfully prepared by coprecipitation method utilizing a local natural source (viz. natural iron sand) as the main raw material.

  2. The structures of Fe3O4 and MnxFe3-xO4 (0 < x≤ 1) nanoparticles, magnetic fluid, and magnetic hydrogel have intensively been studied by XRD, TEM, SANS, and SAXS data. These studies show that the magnetic materials have inverse spinel structure with a primary particle size of around 3–4 nm.

  3. The magnetic properties have also been investigated by observing the hysteresis (M‐H) behavior. It is found that Fe3O4 and MnxFe3-xO4 (0 < x< 1) nanoparticles exhibit superparamagnetic behavior at room temperature which depends on the particle size, doping content, and particle clustering.

  4. The physical and mechanical properties of Al/MgO and Al/MgAl2O4 nanocomposites have been enhanced by the introduction of TMAH as surfactant during the mixing process of matrix and filler. The surfactant‐coated MgO seems to be a more efficient filler compared to the surfactant‐coated MgAl2O4 for the lower content (<30%). The experiment results show that the elastic modulus of the samples with volume fraction of fillers up to 30% was enhanced by more than 60% and 40%, respectively, for Al/MgO and Al/MgAl2O4. The use of other kind of surfactant needs to be explored to further enhance the mechanical properties.

  5. A layer of the spinel MgAl2O4 micro‐sized grown on the surface of SiC filler has induced the enhancement of mechanical properties of the Al/SiC composites.



This chapter is based on research partially supported by LPPM ITS, Ministry of Research and Technology, and Ministry of Education and Culture, Republic of Indonesia, 2006–2015.

© 2017 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution 3.0 License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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Malik Anjelh Baqiya, Ahmad Taufiq, Sunaryono, Khuroti Ayun, Mochamad Zainuri, Suminar Pratapa, Triwikantoro and Darminto (March 8th 2017). Spinel‐Structured Nanoparticles for Magnetic and Mechanical Applications, Magnetic Spinels - Synthesis, Properties and Applications, Mohindar Singh Seehra, IntechOpen, DOI: 10.5772/66293. Available from:

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