# Influence of Annealing Temperature on the Magnetic Properties of Rapidly Quenched (Nd,Pr)2-(Fe,Co,Ga,Ti,C)14B/α-Fe Nanocomposite Ribbons

Authors: Rahim Sabbaghizadeh; Mansor Hashim; Reza Gholamipour; Ghazaleh Bahmanrokh; Mohd Shamsul Ezzad Shafie
Journal: Advances in Materials Science and Engineering
 (2013)

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## Abstract

The effects of different heat treatment temperatures on the structure and magnetic properties of Nd-Fe-B nanocomposite permanent magnetic alloys with nominal composition of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 have been investigated. The most practical method to produce nanostructured metallic materials is rapid solidification. Melt spinning with constant wheel speed of V=40 m/s was employed to produce ribbons. As-spun ribbons were examined by using differential scanning calorimetry (DSC) and X-ray diffractometer (XRD) with Cu-kα radiation. The ribbons were annealed at different temperatures in order to extract the best magnetic properties. The XRD and electron microscopy technique results confirm that grains are in the size of less than 50 nm. In addition, optimum magnetic properties were obtained at 700°C annealed temperature.


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## Body

## 1. Introduction

Recently, considerable attention has been focused on the magnetic properties of nanostructured Nd-Fe-B magnet alloy, which has been prepared by the recrystallization of either melt-spun or mechanically alloyed materials, because of their technological properties and unusual scientific behavior [1–6]. Neodymium-iron-boron nanocomposite magnets consist of a soft magnetic phase (α-Fe or Fe3b) and a hard magnetic phase (Nd2Fe14B). In these materials the soft magnetic phase has higher inherent magnetization, and the hard magnetic phase has a higher anisotropy constant and higher remanence; therefore, higher energy product will be achieved in comparison with single phase material because of exchange coupling between the magnetically soft and hard phases. In addition, a smaller amount of rare earth elements are required [7, 8]. The nanocomposite produced by crystallization of amorphous phase into a mixture of hard and soft phases mainly Nd2Fe14B/α-Fe. Usually α-Fe tends to grow during annealing and precipitates sooner than Nd2Fe14B. It is plainly visible that a uniform distribution of fine grains is essential for obtaining effective exchange coupling [9]. Fischer et al. proposed that an optimum microstructure consists of small soft magnetic grains with sizes of about 10 nm and hard magnetic grains with a mean grain diameter of about 20 nm [3]. In order to achieve a significant enhancement of remanence polarisation (Jr) and to preserve a high intrinsic coercivity in isotropic nanocrystalline Nd2Fe14B-based magnets, a mean grain size of less than 20 nm is required [10]. Furthermore, it was found that the size and volume fraction of α-Fe and Nd2Fe14B can be manipulated by thermal processing and by elemental substitution, leading to the increase of the magnetic properties, for example, Br and (BH)max of the fully processed materials [6]. In recent years various investigations have been carried out in order to increase magnetic properties by changing the heat treatment parameters. In this research effect of heat treatment on the structure and magnetic properties of melt-spun Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 has been investigated.


## 2. Experimental Procedure

An alloy with the nominal composition of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 was prepared by the vacuum arc melting (VAR) method under purified Ar atmosphere. The ingot was produced by this method remelted for four times in order to get the homogeneity. The melt spinning method was used to produce amorphous ribbons in the nanometer scale by a constant wheel speed of v=40 m/s. The chamber Ar pressure was 930 mbar and the ejection pressure was 0.3 bar, and the orifice diameter of quartz tube was 0.5 mm. The as-spun ribbon was sealed in a quartz tube under 4.5 × 10−4 mbar vacuum, after that annealed at four different temperatures (600°C, 650°C, 700°C, and 750°C) for 10 minutes, and then cooled in water. The structure of the ribbons was preliminarily examined using X-ray diffraction (XRD) with monochromatic Cu-Kα radiation before and after annealing. Crystallization evolution and determination of crystallization temperature of the as-cast sample were monitored using differential scanning calorimetry (DSC) on SDT 2960 TA instruments in an Ar atmosphere. Demagnetization curves were measured by using a vibrating sample magnetometer (VSM) after magnetizing the ribbons with a pulsed magnetic field of at least 1.5 T.


## 3. Results and Discussion

Figure1 shows the DSC traces for crystallization of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 alloy. It is noticeable that there is only one exothermic peak which means that the prior precipitation of α-Fe was inhibited and crystallization of both α-Fe and Nd2Fe14B occurs simultaneously. Powder X-ray diffraction patterns of as-quenched Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 ribbons are shown in Figure 2. The XRD scans of the as-spun ribbons can be used to qualitatively estimate the amount of glass formation [6]. As it was mentioned before the wheel speed is constant and because of the straight relation between cooling rate and wheel speed it can be concluded that the cooling rate in our experiment is constant so the formation of amorphous structures is due to change of critical cooling rate necessary to form an amorphous structure from the melt. The XRD pattern of ribbons after a thermal treatment from 600°C to 750°C is shown in Figure 3. It can be seen that the annealed samples consist of a hard magnetic Nd2Fe14B phase and soft magnetic α-Fe phase and TiC phase have precipitated as well as the hard and soft magnetic phases. It was found that the amounts of soft and hard phases are increased with increasing temperature, suggesting that the enhancement of crystallinity was due to the heat treatment. Figure 4 shows the surface microstructure of annealed samples. As can be seen, the darker parts of the micrographs are Nd2Fe14B and the lighter parts are related to α-Fe phase. Obviously, the micrographs indicate that grain growth is occurring. The average grain size of a sintered body was measured over 200 grains by the linear intercept method. The results are shown in Figure 5; the α-Fe grains have not been changed significantly during annealing, except the slight increase and decrease, which are related to the experimental errors with size of ±2 nanometer. Thus, heat treatment has not any effect on grain growth of the soft magnetic phase; on the other hand the Nd-Fe-B grain size increases with the increase of the heat treatment temperature. Magnetic properties of annealed ribbons were measured by alternate gradient force magnetometer (AGFM) with maximum applied field of 1.5 Tesla. The hysteresis loop results are illustrated in Figure 6, the calculated data are summarized in Table 1, and Figure 5 demonstrates the dependence of magnetic properties on the temperature of annealing. As can be seen magnetic properties of the composition differ by changing the annealing temperature; for Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 annealed ribbons the best magnetic properties achieve at 700°C. Generally, the grain growth which occurs at the higher temperatures leads to deterioration in the magnetic properties [11]; hence, heat treatment at 750°C leads to inferior properties than those for 700°C annealing temperature. Furthermore, the Jr/Js values are close to one another due to soft phase’s grain size similarity [12]. The maximum energy product (BHmax), which is sensitive to exchange coupling and grain size, was enhanced with anneals temperature increases until 700°C due to more suitable exchange coupling at higher temperatures [13]. But after 700°C decreases because of hard phase extra grain growth, the maximum energy product (BHmax) of the nanocomposite magnets depends sensitively on the form of nanostructure, for example, phases present, crystallite size, and defects present [14]. However, this is not the whole story since, in comparing the ribbons with the same composition, the 700°C annealed ribbon has improved maximum energy product (BHmax), due to more uniform grain size distribution and higher quality crystalline Nd2Fe14B grains. The coercivity of the ribbons increased to 700°C, and then it decreased due to optimum exchange coupling at 700°C, leading the best coercivity at this temperature.Table 1
Magnetic properties of annealed ribbon at different annealing temperature for 10 minutes.
Composition
Annealing temperature (K)
J
r
/
J
s
Hc (KA m−1)
(BHmax) (KJ/m3)
Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5
600
0.58
202
36.70
650
0.61
233
48.15
700
0.64
245
60.48
750
0.57
177
28.50Figure 1
DSC scans of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5.Figure 2
X-ray diffraction patterns of as-spun ribbon.XRD patterns of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 ribbon after thermal treatment at different temperature for 10 minutes.
(a)
(b)
(c)
(d)FESEM morphologies of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 at (a) 600°C, (b) 650°C,  (c) 700°C, and (d) 750°C annealed ribbons for 10 minutes.
(a)
(b)
(c)
(d)Figure 5
Grain sizes of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 annealed ribbon at different annealing temperature for 10 minutes.Hysteresis loops of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 annealed ribbon at different annealing temperature for 10 minutes.
(a)
(b)
(c)
(d)


## 4. Conclusion

The relationship between annealing temperature, microstructure and magnetic properties of Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 nanocomposite alloys was interpreted by XRD, DSC, and FESEM analysis. It has been generally found that the crystallization behaviour of amorphous Nd9.4Pr0.6Fe74.5Co6B6Ga0.5Ti1.5C1.5 alloy strongly depends on the heat treatment temperature. Additionally, it has been found that increase of annealing temperature leads to grow of Nd-Fe-B grains but does not have any effect on α-Fe grain size. It is plainly visible that magnetic properties increase significantly with heating rate up to 700°C and then will decrease. The best magnetic properties were obtained at 700°C annealing temperature.



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*Source: 620761-2013-12-09.xml*