Journal of Non-Crystalline Solids
Journal of Non-Crystalline Solids
Journal of Non-Crystalline Solids
A R T I C L E I N F O A B S T R A C T
Keywords: In this work, the structural evolution of Al–16 at.%Fe–2 at.%TM (Transition Metals (TM): Ti, Ni, Cu) alloys
Al-based amorphous alloy during mechanical alloying and their magnetic properties were investigated. The evolution of the phase
Structure evolution composition and microstructure of the alloys with the milling time was studied using X-ray diffraction (XRD) and
Mechanical alloying Transmission Electron Microscopy (TEM). The phase composition of the alloys was determined using the
Magnetic properties
Rietveld refinement of the XRD profiles. It was shown that the interaction between the components of the
powder mixtures during milling started with dissolution of Fe in the Al crystalline lattice and Al in the Fe
crystalline lattice. Upon further milling, ferromagnetic AlFe3 (DO3) formed and further transformed into
paramagnetic bcc-AlFe and later into an amorphous phase. It was found that the TM alloying elements
significantly influence the kinetics of the transformations during milling: the Al82Fe16Ti2 alloy was fully
amorphous after 40 h of milling, the Al82Fe16Ni2 alloy required 50 h of milling to achieve complete
amorphization, and the Al82Fe16Cu2 alloy was only partially amorphous after 60 h of milling. The interpretation
of the observed alloying effect has been proposed. The magnetic properties of the alloys were correlated with the
results of the structural characterization.
⁎
Corresponding author.
E-mail address: viet.nguyenhoang@hust.edu.vn (N.H. Viet).
http://dx.doi.org/10.1016/j.jnoncrysol.2017.04.037
Received 16 February 2017; Received in revised form 29 March 2017; Accepted 23 April 2017
Available online 03 May 2017
0022-3093/ © 2017 Elsevier B.V. All rights reserved.
N.T.H. Oanh et al. Journal of Non-Crystalline Solids 468 (2017) 67–73
2. Experimental
3. Results
The XRD patterns of the Al–16 at.%Fe–2 at.%TM (TM: Ti, Ni, Cu)
powders milled for different milling times are shown in Fig. 1. In the
patterns, the intensities are plotted against the scattering vector
(Q = 4πsinθ/λ, where θ is the Bragg's scattering angle and λ is the
radiation wavelength). A general observation can be made that under
continuous milling, Al and Fe reflections become wider, which can be
caused by a decrease in the crystallite size and accumulation of defects
in the crystalline structure of the metals. The Al (111) reflection
(~ 27 nm− 1) shifts slightly towards higher scattering vectors (Q) as Fig. 1. XRD patterns of the powders milled for different milling times (intensity vs.
the milling time increases. At the same time, the Fe (011) reflection scattering vector Q): (a) Al–16 at.%Fe–2 at.%Ti. (b) Al–16 at.%Fe–2 at.%Ni. (c) Al–16 at.
(~ 31 nm− 1) shifts towards smaller Q. These effects indicate that the %Fe–2 at.%Cu.
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N.T.H. Oanh et al. Journal of Non-Crystalline Solids 468 (2017) 67–73
Fig. 2. Fractions of the phases present in the powders as functions of the milling time obtained using Rietveld refinement of the XRD patterns.
Fig. 3. TEM analysis of the Al–16 at.%Fe–2 at.%Ti powder after 30 h of milling. (a) high-magnification bright-field image. The inset is the corresponding SAED pattern. (b) indexation of
the SAED pattern showing the presence of AlFe3 (DO3)-ferro phase. (c) indexation of the same SAED pattern showing the presence of bcc-AlFe-para. (d) blow-up of the SAED pattern
confirming the presence of two rings, the strong is from bcc-AlFe-para and the weak is from AlFe3 (DO3)-ferro. The numbers roughly indicate the interplanar distances in the reciprocal
space.
XRD analysis even in the unmilled mixtures. Ti, Ni and Cu can form Cu-containing alloy is still nanocrystalline (partially amorphous) after
solid solutions during milling. The effect of these elements on the 60 h of milling. A better understanding of the phase composition of the
kinetics of the formation of the Fe-Al phases is striking. By analyzing alloys was obtained by comparing the XRD results with magnetization
the curves in Fig. 2, it can be concluded that the transformation curves of the alloys, which will be discussed below.
reactions during the early stages of milling are accelerated when Ni is
introduced instead of Ti and Cu introduced used instead of Ni. This is
seen from “AlFe3” line having a slope (Fig. 2). This line connects the 3.2. Microstructural evolution
contents of AlFe3 after 5 h of milling and indicates that these values
increase from the Ti- to Ni- to Cu-containing alloy (the contents of AlFe3 The TEM analysis of the alloys was performed to verify the presence
are ~45%, ~50%, and ~58% in the Al82Fe16Ti2, Al82Fe16Ni2 and of the phases determined by the XRD analysis and confirm the crystal-
Al82Fe16Cu2 alloys, respectively). Interestingly, this effect disappears line or amorphous nature of the alloys. Here, it is worth mentioning
after 10 h of milling and at this milling time all three alloys show the that, as the selected area apertures cannot select areas less than
same content of this phase (~ 20%). After 10 h, the reactions are ~1 μm2, the selected area diffraction patterns were taken from larger
delayed in the Ti-Ni-Cu sequence: the Ti-containing alloy reaches an regions at lower magnifications than those used in the bright-field TEM
amorphous state after 40 h, the Ni-containing alloy – after 50 h, and the images hereafter presented. In this way, the diffraction patterns do not
stem exactly from the presented images, which are within the selected
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N.T.H. Oanh et al. Journal of Non-Crystalline Solids 468 (2017) 67–73
Fig. 5. High-magnification bright-field TEM images and corresponding SAED patterns of the Al–16 at.% Fe–2 at.%Ni powder (a) after 40 h of milling (the inset presents the corresponding
SAED pattern, which was indexed as the bcc-AlFe-para phase) and (b) after 50 h of milling (the inset presents the corresponding SAED pattern confirming the amorphization of the alloy).
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N.T.H. Oanh et al. Journal of Non-Crystalline Solids 468 (2017) 67–73
Fig. 6. High-magnification bright-field TEM images and the corresponding SAED patterns in the insets for the Al–16 at.%Fe–2 at.%Cu powder. (a) after 40 h of milling. (b) indexation of
the SAED pattern in the inset of Fig. 6a. (c) after 50 h of milling. (d) indexation of the SAED pattern in the inset of Fig. 6c. (e) after 60 h of milling. (f) indexation of the SAED pattern in the
inset of Fig. 6e.
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N.T.H. Oanh et al. Journal of Non-Crystalline Solids 468 (2017) 67–73
Fig. 8. Summary of the main properties obtained from the M–H curves (Fig. 7): (a) maximum saturation magnetization (Ms) and (b) coercive force (Hc).
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