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

Authors: F. Sánchez-De Jesús; A. M. Bolarín-Miró; C. A. Cortés Escobedo; G. Torres-Villaseñor; P. Vera-Serna
Journal: Journal of Metallurgy
 (2016)

---

## Abstract

A systematic study on the structural and magnetic properties ofF
e
100
-
x
C
o
x alloys (10
<
x
<
90, Δ
x
=
10 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 x
=
60), solid solutions based on bcc structures were obtained. For Co-rich alloys (x
≥
70), 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 (F
e
100
-
x
C
o
x) 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.


---

## Body

## 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 (Δ
H
F
e
C
o
=
-
1 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 F
e
100
-
x
C
o
x (x
=
40, 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 F
e
100
-
x
C
o
x (x = 10, 45, 50, 77, and 90) dedicated in the description of the mechanism of formation of the solid solution F
e
100
-
x
C
o
x 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 theF
e
100
-
x
C
o
x alloy in all the range of composition. Therefore, the aim of this work is to systematically study the magnetic properties of the F
e
100
-
x
C
o
x alloy system with 10
≤
x
≤
90 and Δ
x
=
10 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 F
e
100
-
x
C
o
x alloys, where x varies from 10 to 90 with Δ
x
=
10 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-Kα (λ
=
1.7889 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 (M
s) and coercivity (H
c), 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

Figures1 and 2 show the XRD patterns of mixtures of elemental Fe and Co milled for 3 h to obtain F
e
100
-
x
C
o
x with x from 10 to 90: Δ
x
=
10 (x 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].Figure 1
(a) XRD patterns ofF
e
100
-
x
C
o
x samples with x from 10 to 60 (Δ
x
=
10) milled for 3 h. (b) Enlargement of the main peak.
(a)
(b)Figure 2
(a) XRD patterns ofF
e
100
-
x
C
o
x samples with x from 70 to 90 (Δ
x
=
10) milled for 3 h. (b) Refined patterns.
(a)
(b)The XRD patterns shown in Figure1 confirm the integration of Co atoms into the Fe-bcc structure for compositions F
e
100
-
x
C
o
x with x 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 Figure2, 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, FeP63/mmc, CoFm-3m, and FeP21 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 (Figures1 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. Figure3 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 F
e
100
-
x
C
o
x with x 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.Table 1
Crystal structure, cell parameters, microstrain, and grain size from Rietveld refinement.
Composition Fe100
-
xCox
Crystal structure/space group
% vol.
Cell parameter(s), (a, b, c) (Å)
rms, microstrain
Grain size (nm)
Fe90Co10
bcc/Im-3m
100
2.86
0.0035
294
Fe80Co20
bcc/Im-3m
100
2.87
0.0036
265
Fe70Co30
bcc/Im-3m
100
2.86
0.0039
286
Fe60Co40
bcc/Im-3m
100
2.87
0.0040
261
Fe50Co50
bcc/Im-3m
50.3
2.85
0.0076
168
bcc/Im-3m
49.7
2.86
0.0052
2520
Fe40Co60
bcc/Im-3m
100
2.84
0.0041
234
Fe30Co70
Fe-bcc/Im-3m
51.6
2.88
0.0001
165
Co P63/mmc
48.4
2.51, 2.51, 4.07
0.0176
967
Fe20Co80
Fe-bcc/Im-3m
49.8
2.89
0.0062
103
FeCo bcc/Pm-3m
50.2
2.84
0.0029
96
Fe10Co90
Fe-bcc/Im-3m
45.1
2.897
0.00005
102
Fe P63/mmc
46.1
2.35, 2.35, 3.81
0.01767
892
Co Fm-3m
7.6
3.54
0.00482
977
Co P21 ma
1.2
7.94, 7.9, 15.3
0.00029
1000
Co, Fe
Fe-bcc/Im-3m
6.7
2.86
0.00063
2000
Co P63/mmc
43.3
2.51, 2.51, 4.07
0.00012
240
Fe Fm-3m
7.2
3.54
0.00213
3209
Fe-bcc/Im-3m
42.7
2.86
0.00086
3117Figure 3
Rietveld refinement of X-ray powder diffraction pattern of a mixture of Fe and Co milled for 3 h in order to obtain Fe50Co50.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 Table1, 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

Figure4 shows the hysteresis (M-H)curves for the F
e
100
-
x
C
o
x alloys (0
≤
x
≤
100). 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, M
S, and coercivity, H
c (obtained fromM-H curves) versus the composition (content of Co, in wt.%), are presented.Figure 4
Hysteresis loops forF
e
100
-
x
C
o
x alloys for different values of x.Figure 5
Specific saturation magnetization as function of Co content forF
e
100
-
x
C
o
x alloys.Figure 6
Coercivity field versus Co content forF
e
100
-
x
C
o
x alloy.As it can be observed in Figure5, M
S 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 M
s 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 M
S 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 Figure6. Alloys of F
e
100
-
x
C
o
x 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, H
c 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), H
c 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 H
c 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

Figure7 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.Figure 7
SEM micrographs of mixtures of Fe and Co milled for 3 h to obtainF
e
100
-
x
C
o
x.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.


## 3.1. Structural Analysis

Figures1 and 2 show the XRD patterns of mixtures of elemental Fe and Co milled for 3 h to obtain F
e
100
-
x
C
o
x with x from 10 to 90: Δ
x
=
10 (x 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].Figure 1
(a) XRD patterns ofF
e
100
-
x
C
o
x samples with x from 10 to 60 (Δ
x
=
10) milled for 3 h. (b) Enlargement of the main peak.
(a)
(b)Figure 2
(a) XRD patterns ofF
e
100
-
x
C
o
x samples with x from 70 to 90 (Δ
x
=
10) milled for 3 h. (b) Refined patterns.
(a)
(b)The XRD patterns shown in Figure1 confirm the integration of Co atoms into the Fe-bcc structure for compositions F
e
100
-
x
C
o
x with x 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 Figure2, 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, FeP63/mmc, CoFm-3m, and FeP21 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 (Figures1 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. Figure3 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 F
e
100
-
x
C
o
x with x 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.Table 1
Crystal structure, cell parameters, microstrain, and grain size from Rietveld refinement.
Composition Fe100
-
xCox
Crystal structure/space group
% vol.
Cell parameter(s), (a, b, c) (Å)
rms, microstrain
Grain size (nm)
Fe90Co10
bcc/Im-3m
100
2.86
0.0035
294
Fe80Co20
bcc/Im-3m
100
2.87
0.0036
265
Fe70Co30
bcc/Im-3m
100
2.86
0.0039
286
Fe60Co40
bcc/Im-3m
100
2.87
0.0040
261
Fe50Co50
bcc/Im-3m
50.3
2.85
0.0076
168
bcc/Im-3m
49.7
2.86
0.0052
2520
Fe40Co60
bcc/Im-3m
100
2.84
0.0041
234
Fe30Co70
Fe-bcc/Im-3m
51.6
2.88
0.0001
165
Co P63/mmc
48.4
2.51, 2.51, 4.07
0.0176
967
Fe20Co80
Fe-bcc/Im-3m
49.8
2.89
0.0062
103
FeCo bcc/Pm-3m
50.2
2.84
0.0029
96
Fe10Co90
Fe-bcc/Im-3m
45.1
2.897
0.00005
102
Fe P63/mmc
46.1
2.35, 2.35, 3.81
0.01767
892
Co Fm-3m
7.6
3.54
0.00482
977
Co P21 ma
1.2
7.94, 7.9, 15.3
0.00029
1000
Co, Fe
Fe-bcc/Im-3m
6.7
2.86
0.00063
2000
Co P63/mmc
43.3
2.51, 2.51, 4.07
0.00012
240
Fe Fm-3m
7.2
3.54
0.00213
3209
Fe-bcc/Im-3m
42.7
2.86
0.00086
3117Figure 3
Rietveld refinement of X-ray powder diffraction pattern of a mixture of Fe and Co milled for 3 h in order to obtain Fe50Co50.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 Table1, 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

Figure4 shows the hysteresis (M-H)curves for the F
e
100
-
x
C
o
x alloys (0
≤
x
≤
100). 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, M
S, and coercivity, H
c (obtained fromM-H curves) versus the composition (content of Co, in wt.%), are presented.Figure 4
Hysteresis loops forF
e
100
-
x
C
o
x alloys for different values of x.Figure 5
Specific saturation magnetization as function of Co content forF
e
100
-
x
C
o
x alloys.Figure 6
Coercivity field versus Co content forF
e
100
-
x
C
o
x alloy.As it can be observed in Figure5, M
S 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 M
s 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 M
S 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 Figure6. Alloys of F
e
100
-
x
C
o
x 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, H
c 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), H
c 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 H
c 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

Figure7 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.Figure 7
SEM micrographs of mixtures of Fe and Co milled for 3 h to obtainF
e
100
-
x
C
o
x.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 compositionsF
e
100
-
x
C
o
x with x between 10 and 60 (Δ
x
=
10) increasing its specific saturation magnetization with the increment in x up to 225 emu/g for x
=
30. 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 (F
e
100
-
x
C
o
x) present low coercivity, down to 65 Oe. For Co-rich alloys (x
>
70), the coercivity falls up to 24.5 Oe.



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*Source: 8347063-2016-07-13.xml*