New Zr-based Glass-Forming Alloys Containing Gd and Sm

The effect of minor additions of Gd and Sm on the glass-forming ability (GFA) of Cu-Zr-Al alloys is investigated here. The rationale for these additions is the fact that the atomic size distribution can increase GFA by changing the topology of the alloy as a function of cluster stability, which is tied to the electronegativity and ionic and covalent nature of alloys. Ingots with nominal compositions of Cu 40 Zr 49 Al 10.5 Gd 0.5 , Cu 40 Zr 49 Al 10.5 Sm 0.5 and Cu 39 Zr 50 Al 9 Gd 2 were prepared by arc-melting and rapidly quenched ribbons were produced by the melt-spinning technique. Bulk samples with a thickness of up to 10 mm were also produced by casting, using a wedge-shaped copper mold. The samples were characterized by differential scanning calorimetry, X-ray diffractometry and scanning electron microscopy. The three compositions showed a fully amorphous structure in the ribbons and a predominantly homogeneous amorphous structure with a thickness of up to 10 mm, although some gadolinium oxide crystals as well as samarium compounds were found to be scattered in the amorphous matrix in 5-mm-thick samples. The amorphous phases in the alloys showed high thermal stability with a supercooled liquid region (∆T x ) of about 70 K.


Introduction
Bulk metallic glasses (BMGs) have been studied extensively due to their exceptional properties.Among BMGs, Cu-based alloys stand out for their high strength, high thermal stability, high glass-forming ability (GFA), high corrosion resistance, and low costs 1 .The alloys of the Cu-Zr-Al system have a notably large supercooled liquid region, which may reach 70 K, and good mechanical properties evidenced by their high fracture strength above 1880 MPa [2] .Alloys with Cu-Zr-Al-Ag composition have been reported to exhibit a remarkable increase in GFA due to the effect of Ag in the system 3 .The addition of Y to Cu-Zr-Al alloys reportedly improves their GFA 4 .Moreover, the addition of rare earth elements such as La, Ce, Nd and Gd (Cu 45 Zr 48-x A l7 RE x (RE = La, Ce, Nd, and Gd, 0 ≤ x ≤ 5 at.(%))) has also been shown to increase the GFA 5 .Interesting results have been reported to the effect that the addition of Gd eliminates the harmful effect of oxygen by absorbing it and forming Gd-oxides, triggering heterogeneous nucleation of crystalline phases 3 , which leads to high GFA.
In this study, we added minor amounts of Gd and Sm to alloys of the Cu-Zr-Al system (Cu 40 Zr 49 Al 10.5 Gd 0.5 , Cu 40 Zr 49 Al 10.5 Sm 0.5 and Cu 39 Zr 50 Al 9 Gd 2 ) and examined their influence on the GFA of these alloys in response to improved atomic distribution, which is reflected in topological instability.Samarium was introduced due to its physical properties of lower melting temperature and electronegativity than gadolinium, and because of its crystalline structure, which is rhombohedral as opposed to the hexagonal structure of Gd.The metallic glass compositions were designed based on the synergic effect of topological instability, the λ-criterion, and the difference in the electronegativity of the elements 6,7 , combined with the average distribution of the chemical elements in the alloy.This criterion is strongly related with the efficient packing of atoms to form an icosahedral structure 8,9 .Close packing is a general criterion of packing efficiency.Traditionally, the highest package in crystalline structures is about 74% in face-centered cubic cells, which indicates densification.Amorphous materials have no basic cell; instead, they appear as clusters in a short-range order arrangement due to the differences in the electronegativities of their constituent alloys.
The λ-criterion was used to create minimum topological instability maps indicating the compositions in which topological instability reaches its maximum in the surrounding crystalline phases, and which are therefore expected to show better glass-forming ability.Topological instability indicates an atomic mismatch that induces stresses around an atom, which may be released by changing the occupancy of its nearest-neighbor shell.Thus, the GFA of metallic systems increases with increasing differences in size and is absent from elements with quasi-equal atomic radii.The difference in electronegativity among the elements (∆e) in each particular composition is assumed to be related to the formation enthalpy (∆H) and glass stability of the corresponding alloy [5][6][7] .Electronegativity describes the relativity ability of an atom to attract atoms in a chemical bond and can indicate the percentage of covalent bonding in the alloy 10 .

Experimental Procedure
High purity elements (above 99.9%) were used to produce ingots with nominal compositions of Cu 40 Zr 49 Al 10.5 Gd 0.5 , Cu 40 Zr 49 Al 10.5 Sm 0.5 and Cu 39 Zr 50 Al 9 Gd 2 , using arc-melting processes in Ti-gettered ultrapure argon atmosphere.Ribbons were then produced by rapid quenching on a copper wheel rotating at 30 m/s, using the melt-spinning technique.In addition, wedge-shaped bulk samples with a thickness of up to 10 mm were produced by casting, using a wedge-shaped copper mold and the suction technique.The resulting samples were characterized by X-ray diffraction (XRD), scanning electron microscopy (SEM) and differential scanning calorimetry (DSC).XRD measurements were taken with a Rigaku diffractometer using Cu-Kα radiation (λ = 1.5418Å) and 1 °C/min scan step from 10° to 90° (2θ).A Netzsch F203 calorimeter was used for thermal characterization in an ultrapure argon atmosphere, in a temperature range of 300 to 870 K, at a heating rate of 40 °C/min.The SEM analysis was performed with a field emission gun (FEG) coupled to an energy dispersive spectroscopy (EDS) system to determine the real composition of the samples.

Results and Discussion
After producing the alloys, the ingots were subjected to thermal analysis in a temperature range of 25 to 1200 K, applying a heating rate of 10 K/min, to determine their liquidus temperature (Tl, see Table 1).The 30 to 40 µm thick and 3 mm wide ribbons containing Gd exhibited brittleness, while the ribbons containing Sm exhibited ductility, as evidenced by their bending strength at 180 degrees without breaking.The XRD and DSC analyses (not shown here) indicated that the structure of both samples was fully amorphous, and the intensity of their diffraction patterns were used to determine the percentage of crystalline phases in the bulk wedge-shaped samples.
Figure 1 depicts XRD patterns of the Cu 40 Zr 49 Al 10.5 Gd 0.5 and Cu 40 Zr 49 Al 10.5 Sm 0.5 samples.These curves show the evolution of the structure in the core of the wedge bulk samples, corresponding to small intervals of the thickness (∆X).As can be seen, the amorphous structure prevails up to a thickness of 10 mm, although small peaks corresponding to an unidentified crystalline phase appear on the thicker part of the Cu 40 Zr 49 Al 10.5 Gd 0.5 sample.It is important to note that the Cu 39 Zr 50 Al 9 Gd 2 shows low GFA in the amorphous structure up to 3 mm of thickness, at which point the structure of the sample becomes fully crystalline (results not shown).
Figure 2a shows the DSC thermograms corresponding to different thicknesses along the axis of the wedge bulk samples.The presence of Gd clearly leads to the formation of a glassy structure up to 10 mm of thickness, although this amorphous phase undergoes only minor changes throughout the wedge.This modification is attributed to changes in composition or atomic arrangement (i.e., the metastability of the amorphous structure is influenced by the greater amount of crystalline phases), or possibly by differences in the free volume due to non-uniform cooling rates.Furthermore, while the crystallization of the 5-mm-thick amorphous phase occurs in one stage, the same transformation occurs in two stages in the 10-mm-thick phase, indicating that the  compositional change in the amorphous phase takes place in this range of the sample.With regard to the alloy containing Sm, the composition of the amorphous phase shows no evidence of changes.The crystallization peaks remain similar, and the only visible changes are in the energy of transformation due to the difference in crystalline phase fractions, as indicated in the XRD patterns.
Table 1 summarizes the thermal parameters determined from the DSC analysis of the compositions in 5-mm-thick samples.
The three relative thermal parameters in Table 1, ∆T x , T rg, and g, correspond to the theoretical glass-forming ability of these alloys.Τhe temperature interval of the supercooled liquid region represents the thermal stability of the glassy phase of these alloys.The reduced glass transition temperature, T rg = T g /T l , considers the nucleation frequency and crystal growth of a melt, which is the inverse of the viscosity of the liquid.Lastly, the g parameter considers both the stability and the resistance to crystallization of the liquid.Although these parameters were measured after the amorphous phase was obtained, they allow for a good estimation of the GFA of the alloys.
For the formation of the BMGs, the value of g is between 0.350 and 0.500, while ∆T x varies from 16.3 to 117 K and T rg ranges from 0.503 to 0.609 [11] .As can be seen, the parameters of the alloys of this study are in good agreement with these values, thus showing a good GFA.
Figures 3 and 4 show SEM micrographs of the Cu 40 Zr 49 Al 10.5 Gd 0.5 and Cu 40 Zr 49 Al 10.5 Sm 0.5 samples.The images were recorded on the central axis of the bulk samples, starting from the thinnest section and moving up to the thickest section of the bulk samples.From the tip of the bulk sample up to a thickness of 5 mm, both compositions show a fully amorphous structure.However, as the thickness increases, the two samples show clearly visible differences.

Table 1 .
Thermal parameters of the alloys obtained at 5 mm thickness sample.