Structural Analysis and Magnetic Properties of FeCo Alloys Obtained by Mechanical Alloying

Sánchez-De Jesús, F.; Bolarín-Miró, A. M.; Cortés Escobedo, C. A.; Torres-Villaseñor, G.; Vera-Serna, P.

doi:https://doi.org/10.1155/2016/8347063

Journal of Metallurgy

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Research Article | Open Access

Volume 2016 | Article ID 8347063 | https://doi.org/10.1155/2016/8347063

Structural Analysis and Magnetic Properties of FeCo Alloys Obtained by Mechanical Alloying

F. Sánchez-De Jesús,¹A. M. Bolarín-Miró,¹C. A. Cortés Escobedo,²G. Torres-Villaseñor,³and P. Vera-Serna⁴

Academic Editor: Gerhard Sauthoff

Received08 Mar 2016

Revised06 Jun 2016

Accepted12 Jun 2016

Published13 Jul 2016

Abstract

A systematic study on the structural and magnetic properties of alloys (, in wt. percent) obtained by mechanical alloying is presented. Elemental powders of Fe and Co mixed in an adequate weight ratio were milled at room temperature in a shaker mixer mill using vials and balls of hardened steel as milling media with a ball : powder weight ratio of 12 : 1. The mixtures were milled for 3 h. The results show that, after milling, for almost all the composition (up to ), solid solutions based on bcc structures were obtained. For Co-rich alloys (), different phases were found, revealing the formation of a metastable intermetallic phase (FeCo, wairauite) together with fcc-Co and hcp-Co phases. The specific saturation magnetization increases by increasing Co content, reaching a maximum value of 225 emu/g for hcp-Fe₇₀Co₃₀, and then it shows a diminution up to 154 emu/g for bcc-Fe₃₀Co₇₀. All studied alloys () present low coercivity, in the range from 0 to 65 Oe, which is lower than reported. The coercivity increases with the increment in Co, reaching a maximum of 64.1 Oe for Fe₄₀Co₆₀. After that, the coercivity falls up to 24.5 Oe for Co-rich alloys, which make them a very low coercive material.

1. Introduction

FeCo alloys are competitive candidates with other highly magnetic materials, because of their high specific saturation magnetization, low coercivity, high permeability, and high Curie temperature, properties which make them useful for applications at high temperature. The negative heat of mixing of Fe and Co ( kJ mol⁻¹) and the small mismatch between their atomic radii and electronegativity make the formation of FeCo alloys easy, interesting, and feasible [1, 2].

A great number of techniques have been used to synthesize the FeCo powders, like reduction reactions [3], plasma-gas-condensation [4], wet chemical technique [5], and polyol [6]. Among the various synthesis methods, mechanical alloying (MA) is a method that creates a large number of crystal defects and stacking faults due to the severe plastic deformation that results from the high energy supplied to the system [7, 8]. This enables structural changes such as allotropic transformations [9–11] which normally occur at high temperatures [12]. In addition, the magnetic properties of mechanically alloyed materials can be notably influenced by the MA process due to the stresses and defects that are generated during the milling process together with a consequent grain size reduction that results in enhanced magnetic behavior [13, 14].

Several studies have been published for the last years when FeCo alloys are synthesized by mechanical alloying. Moumeni et al. [15] and Akkouche et al. [16] reported that after 24 h of high-energy ball milling the formation of a Fe-bcc solid solution with 50% in wt. of Co was obtained. Laala-Bouali et al. [1] studied the relationship between the microstructure and the microhardness for the Fe₇₀Co₃₀ alloy (in wt.) obtained after 3 h of milling, finding interesting results about the formation of a Fe-bcc solid solution, while Bergheul et al. [17] focused their research on synthesis of Fe₆₀Co₄₀ alloy; they found that Fe-based alloys obtained by mechanosynthesis are promising materials for microwave absorbing devices.

Zeleňáková et al. [18] studied some compositions of the FeCo system; they synthesized nanocrystalline (, 50, and 60 in % wt.) solid solutions by MA after 30 h of milling. The obtained alloys presented a disordered bcc-Fe(Co) solid solution with coercivity showing an increment from 2450 to 4000 Oe for contents of 30 and 60% in wt. of Co, respectively. The specific saturation magnetization did not show a tendency with the content of Co, keeping its value between 225 and 203.5 emu/g. Besides, Delshad Chermahini et al. [19] investigated the microstructure and magnetic properties of ( = 10, 45, 50, 77, and 90) dedicated in the description of the mechanism of formation of the solid solution during the mechanical alloying process and the effect of the milling time in their structural and magnetic properties.

Due to the interesting effect of the mechanical alloying in their magnetic and mechanical properties, the interest in the FeCo alloy synthesized by this method has been increased during the last years, especially when this alloy is combined with other elements such as Mo [20, 21], V [22], Ni [23], Nb [24], and Cr [25] and even when these materials are used to obtain encapsulated carbon [26].

Even though there are a great number of interesting works in this subject, in all of them the milling times used to obtain the alloy are so high (higher than 20 h) and there is not a complete study of the alloy in all the range of composition. Therefore, the aim of this work is to systematically study the magnetic properties of the alloy system with and synthesized by high-energy milling after a very short time (of 3 h).

2. Materials and Methods

Elemental iron powder (Sigma-Aldrich, >99.9%) with a mean particle size (D₅₀) of 2 μm and cobalt powder (Sigma-Aldrich, >99.9%) with a mean particle size (D₅₀) of 200 μm were used as precursors. These differences in particle size were selected in order to promote homogeneous distribution of small particles of Co into Fe. The raw materials were mixed in the appropriate weight ratio to obtain alloys, where varies from 10 to 90 with in % wt. A total amount of 5 g of the powder mixtures and 6 hardened steel balls with a diameter of 12.7 mm were loaded into a steel vial with 64.6 cm³ of volume and milled for 3 h. According to previous results, a total solid solution is achieved after 3 h of milling [27]. This milling time is not sufficient to obtain only a solid solution without the presence of unmilled raw material (Fe and Co). The mechanical alloying process was conducted at room temperature in an argon atmosphere using a SPEX 8000D shaker mill. The ball-to-powder weight ratio was 12 : 1. To prevent excessive overheating of the vials, all experiments were performed using cycles of 90 minutes of milling followed by 20 minutes of rest. The milled powders were analyzed by X-ray diffraction (XRD) for examining the phase transformations as a function of the alloy composition by a Siemens D5000 diffractometer. The diffraction parameters were collected with 2θ ranging from 40° to 110° with a step size of 0.02 and Co-K_α ( Å) radiation. Rietveld refinement was performed on the X-ray diffraction patterns using the program MAUD [28]. It was used to calculate the phase amount, cell parameters, and microstrain. This method takes into account all the information collected in a pattern, and it uses a least squares approach to refine a theoretical line until it matches the measured profile. The magnetic properties of the obtained materials, specific saturation magnetization () and coercivity (), were measured using a MicroSense V7 vibrating sample magnetometer (VSM) with a maximum applied field of 18 kOe. Morphological characterization of the milled powders was performed using a JEOL JSM-6300 electron microscope operated at 15–30 kV.

3. Results and Discussion

3.1. Structural Analysis

Figures 1 and 2 show the XRD patterns of mixtures of elemental Fe and Co milled for 3 h to obtain with from 10 to 90: ( as percentage in weight). In these figures, the XRD patterns corresponding to the mixture of the elemental powders, Fe and Co, without milling have been included. These patterns confirm the presence of three phases: bcc-Fe (COD 4113931, Im-3m bcc) and two allotropic structures of Co: Co-α (COD 9010968, Fm-3m) and Co-ε (COD 9012950, P63/mmc) [29].

(a)

(b)

(a)

(b)

The XRD patterns shown in Figure 1 confirm the integration of Co atoms into the Fe-bcc structure for compositions with from 10 to 40, forming a complete bcc solid solution (Im-3m structure), since the Co-fcc and Co-hcp reflection peaks, corresponding to the starting materials, have vanished, and only peaks corresponding to bcc-Fe are detected. As can be observed, when the cobalt level is increased, slight peak displacement is observed towards right, which is associated with a distortion of the crystal structure and variation in the cell parameter as a consequence of the plastic deformation in the early stage of milling. The Fe and Co radii are nearly similar. This distortion cannot be attributed to the incorporation of Co atoms into the Fe cell, due to the fact that Co and Fe radii are nearly similar (1.25 and 1.26 Å, resp.).

Different result was found for compositions with content in cobalt higher than 50% in wt., as can be observed in Figure 2, where different crystal structures were found for each composition. In addition, Rietveld refinement results are shown in Figure 2. It was observed that for Fe₃₀Co₇₀ a mixture of Fe-bcc/Im-3m and Co P63/mmc was formed, in good agreement with some authors [17, 18], while for a Co-rich alloy (Fe₁₀Co₉₀) a mixture of phases was found: Fe-bcc/Im-3m, Fe P63/mmc, Co Fm-3m, and Fe P21 ma [3, 19]. Finally, for Fe₂₀Co₈₀ coexistence of two phases, one corresponding to Fe-bcc/Im-3m (COD 9006597) and another metastable one, bcc-Co(Fe) (COD 9004228, Pm-3m), a cubic phase reported for the intermetallic FeCo, also called wairauite [30], was found. In this case, an exceptional experiment was carried on, increasing the milling time until 12 h, confirming that, after this time, the two phases remain in the material (not shown in this paper). The formation of these metastable intermetallic phases is associated with synthesis method (mechanical alloying), which generates enough energy to produce unexpected and out of equilibria phases [13].

Broadening of reflection peaks for all the studied compositions can be observed in all the XRD patterns (Figures 1 and 2); it is related to the refinement of the microstructure and the increase in the lattice strain caused by the introduction of defects into the crystal structure during the mechanical alloying and also due to the formation of new solid solutions.

In order to quantify the obtained results by X-ray diffraction, Rietveld refinement for all the composition was done using these patterns. Figure 3 presents a typical pattern of the results of the Rietveld refinement of mixtures of Fe and Co which were milled for 3 h in order to obtain Fe₅₀Co₅₀; this figure suggests high quality fit of the data with the refinement. This refinement was used to calculate the rms microstrain, cell parameter, and crystallite size of the obtained alloys. The obtained results of the refinement are shown in Table 1, which corroborate the formation of different solid solutions and give information about crystal parameters. As it is noticeable, Table 1 shows modifications in crystalline structure only in Co-rich compositions. For composition with down to 60, Fe-bcc solid solution is confirmed. For Co-rich alloys, an increment in the cell parameter is accompanied by the apparition of hexagonal and wairauite phases, which suggest that these transitional phases are intermediates for all the mixture of phases up to Fe₁₀Co₉₀ composition. These transitional phases provide high contributions to uncertainty; for this reason grain size and microstrain values calculated are not reliable because of the disorder generated.

From Fe₉₀Co₁₀ to Fe₄₀Co₆₀ a diminution in a cell parameter for bcc structure is observed, confirming the alloy formation, due to the incorporation of a smaller atom, such as substituting atoms of Co (metallic radii, 1.25 Å) for Fe (metallic radii, 1.26 Å) into the Fe-bcc (Pm-3m structure). This is produced by the severe plastic deformations together with an accumulation of large amount of structural defects during the milling process, modifying their final magnetic properties [15].

The crystallite size, shown in Table 1, depicts a large variation due to the formation of new phases and recrystallization of others. The formation of big crystallites shown in Table 1 is characteristic of the MA process when malleable powders are present because the materials are subjected to compressive forces between the grinding media causing the plastic deformation of particles and promoting the growing of the crystallite size [31], whereas the observed increment in crystallite size at the start of the compositional series, where iron is majority compound, is attributed to a major dislocation generation caused by severe plastic deformation and related to the formation of the fcc-Co(Fe) solid solutions. As it was expected, the rms microstrain shows slight increment with the cobalt content, due to the incorporation of Co into the Fe-bcc and all the above mentioned defects. Meanwhile, Co-rich alloys show important increment in rms microstrain because of the disorder in their component phases.

3.2. Magnetic Characterization

Figure 4 shows the hysteresis (M-H) curves for the alloys (). All the compositions show a similar magnetic behavior, low coercivity, and high specific saturation magnetization. Also, a significant increase in specific saturation magnetization is observed in between the compositions, with reference to pure Co, confirming a solid solution formation between pure elements (Fe and Co) after the milling process. In order to analyze some of the most important magnetic properties of the milled powder, in Figures 5 and 6, the magnetic parameters, specific saturation magnetization, , and coercivity, (obtained from M-H curves) versus the composition (content of Co, in wt.%), are presented.

As it can be observed in Figure 5, increases as the cobalt content increases, up to 30% of cobalt, where the solution achieves a maximum value of 225 emu/g, as is expected from Slater-Pauling curve, when the method of synthesis is under equilibrium conditions. Excluding the values of pure metals, the minimum value of was obtained for Fe₃₀Co₇₀ (151.1 emu/g), showing a value similar to the pure cobalt, about 150 emu/g; it can be due to the stabilization of the hcp structure, as it was observed in the XRD patterns in Figure 2.

Unexpected values higher than 220 emu/g of specific saturation magnetization in Fe₈₀Co₂₀, Fe₇₀Co₃₀, and Fe₆₀Co₄₀ alloys were found; it may be due to the selfhood of the mechanical alloying process and the distortion produced during the process, changing the magnetic interactions. The specific saturation magnetization decreases drastically from 225 emu/g for Fe₇₀Co₃₀ to 151.1 emu/g for Fe₃₀Co₇₀. This noticeable decrease of can be attributed to the dilution effect of the magnetic moment of cobalt atoms promoted by the formation of the Fe(Co) and Co(Fe) solid solutions (structural change).

For Co-rich alloys, the incorporation of Fe atoms into the fcc-Co and Co-hcp, together with the formation of transitional phase, bcc-Co, produces a remarkable increase in the specific saturation magnetization from 150 to 180 emu/g for 0 and 30% Fe in wt., respectively.

The coercivity behavior as a function of the cobalt content is shown in Figure 6. Alloys of present a similar behavior, high magnetization and low coercivity, in the range from 22 to 65 Oe (0–4774 A/m) for all studied milled samples, which is lower than reported by other authors for the same compositions [3, 12, 18, 19], who found values of coercivity in the range of 25–100 Oe (2–8 KA/m) for nanocrystalline FeCo alloys obtained by different methods, including mechanical alloying.

In the studied milled mixtures, a tendency to increase from 22.4 to 64.1 Oe for Fe₉₀Co₁₀ to Fe₄₀Co₆₀, respectively, is observed. In these compositions, a bcc-Fe(Co) alloy is completely formed and the incorporation of Co-atoms into the bcc-Fe structure increases the residual stresses; therefore, increases, due to the coercivity being an extrinsic property of magnetic materials which strongly depends on the microstructure of the material including the effects of internal defects, residual stresses, grain sizes, and nonmagnetic inclusions [32]. After 60% of Co (Fe₄₀Co₆₀), starts to fall up to 24.5 Oe for compositions upwards of 90% of cobalt. As is expected, the maximum value of coercivity (205 Oe) is achieved by the material consisting of 100% Co, because it crystallizes in hexagonal crystal structure (hcp), which has uniaxial crystalline anisotropy higher than that of the materials with cubic structure. The slight decreasing of observed for contents in cobalt higher than 60% may be explained as a consequence of the change of crystalline structure with respect to other compositions, that is, the obtaining of hexagonal hcp phase for Fe₇₀Co₃₀, cubic fcc phase for Fe₁₀Co₉₀, and cubic bcc phase for Fe₂₀Co₈₀. Also, a very interesting behavior is observed when Fe atoms are incorporated into the Co structure, promoting a decrease of 200% in its coercive field, as is noticeable in Figure 6. The coercivity is very much influenced by the residual stress, as well as the grain size, especially when mechanical alloying is used to obtain it.

3.3. Morphology

Figure 7 shows SEM micrographs that illustrate the morphology of the powder milled for the selected compositions. As can be observed, due to the repeated fracturing, cold welding, and agglomeration of the powders during the mechanical alloying, a noticeable change in the shape and size of the samples is obtained. The starting powders are so different in morphology and size; Co powder has a spherical-like morphology with few nanometers in size, while iron powder has irregular morphology with a particle size higher than 100 micrometers.

For all range of compositions, the milled powders show lamellar type morphology; flattened particles with irregular contours are observed, due to the plastic deformation induced during the milling process. It seems that particles of Fe are constantly fractured and joined into the lamellar particles; therefore, the increase of Fe content promotes a decrease in the particle size. On the other hand, the deformed particles of cobalt cover the iron particles, and it is for this reason that high cobalt contents promote the formation of large agglomerates.

4. Conclusions

Solid solutions of Co inserted into Fe-bcc structure were obtained by mechanical milling for 3 h in compositions with between 10 and 60 () increasing its specific saturation magnetization with the increment in up to 225 emu/g for . On the other hand, for Fe₃₀Co₇₀ a mixture of bcc and hcp phases was obtained. This composition results in the lowest specific saturation magnetization. Besides, for Fe₂₀Co₈₀, a mixture of wairauite intermetallic phase with fcc phase was found; this mixture of phases has lower value of coercivity than values reported previously. All the studied alloys () present low coercivity, down to 65 Oe. For Co-rich alloys (), the coercivity falls up to 24.5 Oe.

Competing Interests

The authors declare that they have no competing interests.

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Copyright © 2016 F. Sánchez-De Jesús et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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