Crystallization Behavior of Al70Fe12.5V12.5Nb5 Amorphous Alloy Formed by Mechanical Alloying

In this study, the formation and crystallization of the Al70Fe12.5V12.5Nb5 amorphous alloys has been investigated. The addition of Nb enhances the supercooled liquid region and glass forming ability of the Al-Fe-V amorphous alloys. The Al70Fe12.5V12.5Nb5 amorphous alloy exhibits two distinct crystallization steps and a large supercooled liquid region at more than 100 K. Kissinger and Ozawa analyses showed that the two activation energies for crystallization (Ex) were estimated to be 366.3 ± 23.9 and 380.5 ± 23.9 kJ/mol. Large supercooled liquid regions are expected to gain an application field of Al-based amorphous alloys.


Introduction
Currently, the application of amorphous powder in bulk metallic glasses, composite, coating, and 3D printing has widened the application scope of amorphous alloys [1][2][3][4]. In particular, Aluminum-based amorphous alloys have attracted increasing attention due to their exceptional physical properties, low glass forming ability (GFA), and poor thermal stability [5][6][7]. However, Al-based amorphous alloys with low GFA are challenging to be synthesized via the traditional rapid quenching (RQ). The size factor restricts the practical application of Aluminum-based amorphous alloys. Indeed, up to now, the maximum diameter of an Al-based amorphous alloys sample is 2.5 mm by RQ [8]. Mechanical alloying (MA) is an effective process to produce amorphous alloy powders without a high cooling rate [9,10]. Therefore, it is noteworthy to prepare Al-based amorphous powders via MA to widen their application [11][12][13][14][15]. To use amorphous powder, a large supercooled liquid region (∆T x ) is necessary, and enhancement of the GFA and thermal stability is required.
The addition of Nb can improve the GFA, thermal stability, and the corrosion resistance of Zr-based Zr-Ni-Al-Nb bulk metallic glasses with high compressive yield strength [16]. A similar phenomenon has been observed in some Al-based amorphous alloys [17,18]. It has been reported that, in the case of the Nb-Al system, the sequence of phase formation varies widely depending upon Al content: for example, Al 80 Fe 10 Nb 10 created via an MA process lasted 100 h is a powder mixture [19,20]. However, according to the efficient cluster packing (ECP) model, Nb has the same atomic radius as Al, so they can be mixed with an arbitrary ratio to occupy the Ω position of the solvent atoms without changing the cluster packing structure in the amorphous alloys [21]. Thus, it is interesting to investigate the GFA and thermal stability of in Al-based amorphous alloys in which Nb has replaced Al. Al 75 V 12.5 Fe 12.5 amorphous alloys with high GFA and thermal stability were prepared via MA and based on the ECP model [22]. In general, a negative heating of the mixing enthalpy (∆H mix ) among elements in the amorphous alloy is beneficial for enhancing the GFA [23]. Nb contribution to the enthalpy leads to a negative ∆H mix with Al (−18 kJ/mol), Fe (−16 kJ/mol), and V (−1 kJ/mol) [24]. Therefore, the GFA and thermal stability expect to be enhanced with the Nb addition in the Al-Fe-V alloys. In this work, we synthesized alloys with 5% of Al replaced by Nb. The GFA and thermal stability were investigated according to the values obtained from differential scanning calorimetry (DSC). The aim of this study is to obtain Al-based amorphous powder with high ∆T x and thermal stability for industrial applications.

Experimental Details
The Al 70 Fe 12.5 V 12.5 Nb 5 (at %) amorphous alloy powders were prepared via MA of a mixture of elemental Al (99.9%), Fe (99.8%), V (99.9%), and Nb (99.7%) powders. Stearic acid powder (2 wt. %) was used as the process control agent. The MA was conducted in a high-energy planetary ball mill (QM-3SP4, Instrument Factory of Nanjing University, Nanjing, China) using a stainless steel vial and a steel ball bearing (GGr15 with diameters of 20 mm, 10 mm, and 5 mm are mixed) with the rotation speed of 350 rpm and ball-to-powder weight ratio of 20:1 in a highly pure Ar atmosphere. The vial is introduced into the vacuum glove box every 10 h to obtain the powder samples for analysis. The powder samples were characterized via X-ray diffraction (XRD, X' Pert Pro MPD, Philips) using Cu Ka radiation in the 2θ range of 20 • to 90 • . The X'Pert HighScore Plus software (Version: 3.0) is used to analyze the XRD curves of the mixed powder after ball milling. The microstructures of the amorphous powders were examined using transmission electron microscopy (TEM, JEOL 2010, JEOL) and selected area electron diffraction (SAED) operating at 200 kV. The thermal properties, such as T g (the glass transition temperature), T x (the onset crystallization temperature), T p1 (the first crystallization peak temperature), T p2 (the secondary crystallization peak temperature), T m (the melting temperature), T l (the liquidus temperature), were measured via the DSC (NETZSCH DSC 404F3) at heating rates of 10, 20, 30, 40 K/min from 303 K to 1473 K in an Ar atmosphere.

Results and Discussion
XRD results of Al 70 Fe 12.5 V 12.5 Nb 5 alloy powders milled for different periods (10 h, 20 h, 30 h, 40 h, 50 h and 60 h) are shown in Figure 1. It can be seen from Figure 1 that the crystalline phase is formed by ball milling 10 h, X'Pert HighScore Plus software results suggest that the crystalline phase is AlNb 2 . With the increase of milling time, no new diffraction peaks have been found in the XRD curve, indicating that no new crystalline phase is formed except for AlNb 2 . From the DSC curve of 10 h to 30 h, the intensity of the diffraction peak corresponding to the initial addition of powder elements is reduced with the strongest diffraction peak position moving towards higher 2θ angles of 0.2 • . According to the Scherrer formula, this means that the lattice of Al has infiltrated other atoms with a smaller atomic radius and formed a solid solution. The atomic radius of Fe (0.124 nm) and V (0.132 nm) is shorter than the radius of Al (0.143 nm); therefore, the product is the Al-Fe-V solid solution formed by Fe and V dissolved in Al. When milling to 40 h, the diffraction peak still exists and has broadened, indicating that the amorphous phase is formed and there are crystalline phases and solid solutions at this time. After milling 50 h, the diffraction peaks of all crystals disappear, while different diffuse peaks can be identified at a 2θ angle of 37 • . Until the 60 h milling treatment, only the typical broad halo peak showing the amorphous structure exists, indicating that the powders are amorphous.
To verify the amorphous structure, the TEM and selected area electron diffraction (SEAD) images of Al 70 Fe 12.5 V 12.5 Nb 5 alloys powder milled for 60 h are shown in Figure 2. There is no visible crystals in the TEM image, and the broad diffuse halo and the absence of rings or diffraction spots in the SEAD pattern further confirms the amorphous structure.
The GFA and thermal stability of the amorphous alloy are related to atomic radii mismatch and thermodynamics of the alloy systems: it can be displayed by the milling time of MA amorphous  To verify the amorphous structure, the TEM and selected area electron diffraction (SEAD) images of Al70Fe12.5V12.5Nb5 alloys powder milled for 60 h are shown in Figure 2. There is no visible crystals in the TEM image, and the broad diffuse halo and the absence of rings or diffraction spots in the SEAD pattern further confirms the amorphous structure. The GFA and thermal stability of the amorphous alloy are related to atomic radii mismatch and thermodynamics of the alloy systems: it can be displayed by the milling time of MA amorphous powders. Compared with the Al75V12.5Fe12.5−xCux amorphous alloys reported in the literature [22], the Al70Fe12.5V12.5Nb5 amorphous alloy milling time is reduced.
The parameter Delta is adopted to describe the effect of atomic radii mismatch of multi-component alloys as follows [25]: Here, the n is the number of components in the amorphous alloy system, is the atomic percentage of the i component, and is the atomic radius, ̅ ( ̅ = ∑ ) is the average atomic radius. Intensity (a.u.) To verify the amorphous structure, the TEM and selected area electron diffraction (SEAD) images of Al70Fe12.5V12.5Nb5 alloys powder milled for 60 h are shown in Figure 2. There is no visible crystals in the TEM image, and the broad diffuse halo and the absence of rings or diffraction spots in the SEAD pattern further confirms the amorphous structure. The GFA and thermal stability of the amorphous alloy are related to atomic radii mismatch and thermodynamics of the alloy systems: it can be displayed by the milling time of MA amorphous powders. Compared with the Al75V12.5Fe12.5−xCux amorphous alloys reported in the literature [22], the Al70Fe12.5V12.5Nb5 amorphous alloy milling time is reduced.
The parameter Delta is adopted to describe the effect of atomic radii mismatch of multi-component alloys as follows [25]: Here, the n is the number of components in the amorphous alloy system, is the atomic percentage of the i component, and is the atomic radius, ̅ ( ̅ = ∑ ) is the average atomic radius. The parameter Delta is adopted to describe the effect of atomic radii mismatch of multi-component alloys as follows [25]: Here, the n is the number of components in the amorphous alloy system, c i is the atomic percentage of the i component, and r i is the atomic radius, r (r = ∑ n i=1 c i r i ) is the average atomic radius. By calculating the Delta, the Al 70 Fe 12.5 V 12.5 Nb 5 and Al 75 V 12.5 Fe 12.5−x Cu x amorphous alloys have the same value. We can then infer that the influence of atomic radii mismatch of the two systems can be neglected.
Another parameter, the equation of the Gibbs free energy (∆G mix ), is used to characterize the thermodynamics of alloy systems. According to Equation (2), a low mixing enthalpy (∆H mix ) or a high entropy of mixing (∆S mix ) can decrease the ∆G mix , thus lowering the crystallization driving force, which consequently renders the formation of the amorphous phase easier. ∆H mix and ∆S mix can be calculated by Equations (3) and (4), respectively.
where Ω ij = 4∆H ij , the ∆H ij is the mixing enthalpy of the i and j elements, and R is the gas constant. It can be concluded that the ∆H mix increases in the order of the  Figure 3a shows the DSC curves of the Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy at the heating rates of 10, 20, 30, and 40 K/min. Two exothermic crystallization events can be observed and are associated with the transformations from an amorphous state to the equilibrium phases. The temperature of T g that indicates glass transition at the different heating rate (see Figure 3b). The thermal properties of T g , T x , T p1 , T p2 , T m , T l are marked with arrows in Figure 3a and listed in Table 1, which also contains the empirical criteria of GFA [23,26], ∆T x (∆T x = T x − T g ), the reduced glass transition temperature T rg (T rg = T g /T l ), the γ val (γ = T x /(T g + T l )). It is clear that, with the increase of heating rate, T g , T x , T p1 , T p2 , turn to a higher temperature, while the ∆T x fluctuates between 106.5 and 117.5 K. This shows that the thermal properties of Al 70 Fe 12.5 V 12.5 Nb 5 at different heating rates are influenced by kinetic factors. The values of T x and ∆T x of Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy are 854.1 K and 118.6 K at the heating rates of 20 K/min, respectively, whereas the T m is almost unchanged. It should be noted that the change of ∆T x for Al 70 Fe 12.5 V 12.5 Nb 5 is more than 100 K, which is higher than Al 75 V 12.5 Fe 12.5−x Cu x amorphous alloys and other Al-based amorphous alloys [27]. The higher ∆T x ,T rg , γ indicates that the Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy has a higher glass forming ability. Therefore, it is a promising candidate for thermoplastic forming BMGs and composite materials via the consolidation of amorphous powders.     The activation energies of E x , E p1 , E p2 corresponding to T x , T p1 , T p2 , respectively, can be estimated via the equations of Kissinger (Equation (5)) and Ozawa (Equation (6)) [28,29]:

β(K/min) T g (K) T x (K) T p1 (K) T p2 (K) T m (K) T l (K)
Here, the β is the heating rates, T represents the specific temperature (T x , T p1 , T p2 ), E is the corresponding activation energy (E x , E p1 , E p2 ), and R is the gas constant. Figure 4 reports the Kissinger and Ozawa plots by linear fitting of ln (β/T 2 ) versus 1/T or ln (β) versus 1/T. The estimated activation energies (E x , E p1 , E p2 ) corresponding to T x , T p1 , T p2 were evaluated by the Kissinger and Ozawa methods, and listed in Table 2. The fitted curves are close to the straight lines; the Adjusted R-square is higher than 96, and the results of the two equations have the same tendency, which proves the reliability of the data. It is clear that the effective activation energies evaluated by the Kissinger equation are smaller than Ozawa equation. The E x values resulting by the application of the Kissinger and Ozawa methods can be calculated: 366.3 ± 23.9 and 380.5 ± 23.9 kJ/mol, respectively. at the heating rates of 10, 20, 30, and 40 K/min. (b) Enlarged area of the DSC curves shown in (a) of the Tg. Table 1.The thermal properties and ΔTx, Trg, γ of Al70Fe12.5V12.5Nb5 measured at 10, 20, 30, and 40 K/min heating rates. The activation energies of Ex, Ep1, Ep2 corresponding to Tx, Tp1, Tp2, respectively, can be estimated via the equations of Kissinger (Equation (5)) and Ozawa (Equation (6)) [28,29]:

β(K/min) Tg(K) Tx (K) Tp1 (K) Tp2 (K) Tm(K) Tl (K) ΔTx(K) Trg
Here, the β is the heating rates, T represents the specific temperature (Tx, Tp1, Tp2), E is the corresponding activation energy (Ex, Ep1, Ep2), and R is the gas constant. Figure 4 reports the Kissinger and Ozawa plots by linear fitting of ln (β/T 2 ) versus 1/T or ln (β)versus1/T. The estimated activation energies (Ex, Ep1, Ep2) corresponding to Tx, Tp1, Tp2 were evaluated by the Kissinger and Ozawa methods, and listed in Table 2. The fitted curves are close to the straight lines; the Adjusted R-square is higher than 96, and the results of the two equations have the same tendency, which proves the reliability of the data. It is clear that the effective activation energies evaluated by the Kissinger equation are smaller than Ozawa equation. The Ex values resulting by the application of the Kissinger and Ozawa methods can be calculated: 366.3 ± 23.9 and 380.5 ± 23.9 kJ/mol, respectively.  The DSC curves in Figure 3 have two obvious endothermic peaks, which means that there are two crystallization processes. To further understand the crystallization of the new crystalline phases  The DSC curves in Figure 3 have two obvious endothermic peaks, which means that there are two crystallization processes. To further understand the crystallization of the new crystalline phases during the exothermic processes, five heat treatments of the Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy powders were studied. Figure 5 shows the XRD pattern of the Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy powders after five different heat treatments. Different heat treatment temperatures have been selected: 773 K (below T x and above T g ), 973 K (between T P1 and T P2 ), and 1173 K (above T P2 ).
Materials 2019, 12, x FOR PEER REVIEW 6 of 8 during the exothermic processes, five heat treatments of the Al70Fe12.5V12.5Nb5 amorphous alloy powders were studied. Figure 5 shows the XRD pattern of the Al70Fe12.5V12.5Nb5 amorphous alloy powders after five different heat treatments. Different heat treatment temperatures have been selected: 773K (below Tx and above Tg), 973K (between TP1 and TP2), and 1173K (above TP2). The crystal phase is not observed when the sample has been heated to 773K before rapid cooling (heat treatment a in Figure 5). When amorphous alloy samples are annealed at 773 K for 100 min (heat treatment b), a few Al3Nb phases of the amorphous sample can be observed. It is shown that the short-range atom structure retained in the amorphous alloy has been partly changed after low-temperature annealing, while a certain degree of relaxation has occurred. Although the crystallization temperature has not been reached, the atom diffusion ability of the amorphous alloy has increased after annealing for 100 min with the Nb addition. Al5Fe2 and Al3Nb phases have been mainly observed after initial crystallization and rapid cooling immediately after heating to 973 K (heat treatment c). The Al23V4 phase is also found at 973 K annealing for 100 min (heat treatment d) and heating to 1173 K (heat treatment e). New crystalline phases precipitate when the amorphous sample is annealed, which may be due to the relaxation of the amorphous structure. To reduce the internal free energy of the amorphous alloy, a certain crystallization phase has precipitated in the amorphous alloy.

Conclusions
Amorphous alloy Al70Fe12.5V12.5Nb5 (at %) powders were successfully prepared via MA. The replacement of Al with Nb in the Al75V12.5Fe12.5 amorphous alloy effectively enhances its glass forming ability and thermal stability. The Al70Fe12.5V12.5Nb5 amorphous alloy exhibits a larger supercooled liquid region than 100K, higher GFA with the Trg of 0.522, and γ of 0.398 (20 K/min). The crystallization of the Al70Fe12.5V12.5Nb5 amorphous alloy takes place in two distinct steps, as observed via DSC analyses. Our study provides deeper insights into the development of Al-base amorphous alloys to be used in powder metallurgy industry.  The crystal phase is not observed when the sample has been heated to 773 K before rapid cooling (heat treatment a in Figure 5). When amorphous alloy samples are annealed at 773 K for 100 min (heat treatment b), a few Al 3 Nb phases of the amorphous sample can be observed. It is shown that the short-range atom structure retained in the amorphous alloy has been partly changed after low-temperature annealing, while a certain degree of relaxation has occurred. Although the crystallization temperature has not been reached, the atom diffusion ability of the amorphous alloy has increased after annealing for 100 min with the Nb addition. Al 5 Fe 2 and Al 3 Nb phases have been mainly observed after initial crystallization and rapid cooling immediately after heating to 973 K (heat treatment c). The Al 23 V 4 phase is also found at 973 K annealing for 100 min (heat treatment d) and heating to 1173 K (heat treatment e). New crystalline phases precipitate when the amorphous sample is annealed, which may be due to the relaxation of the amorphous structure. To reduce the internal free energy of the amorphous alloy, a certain crystallization phase has precipitated in the amorphous alloy.

Conclusions
Amorphous alloy Al 70 Fe 12.5 V 12.5 Nb 5 (at %) powders were successfully prepared via MA. The replacement of Al with Nb in the Al 75 V 12.5 Fe 12.5 amorphous alloy effectively enhances its glass forming ability and thermal stability. The Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy exhibits a larger supercooled liquid region than 100 K, higher GFA with the T rg of 0.522, and γ of 0.398 (20 K/min). The crystallization of the Al 70 Fe 12.5 V 12.5 Nb 5 amorphous alloy takes place in two distinct steps, as observed via DSC analyses. Our study provides deeper insights into the development of Al-base amorphous alloys to be used in powder metallurgy industry.