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Journal of Materials

Volume 2014 (2014), Article ID 451587, 13 pages

Research Article

Experimental Investigation of the Phase Equilibria in the Al-Mn-Zn System at 400°C

Department of Mechanical Engineering, Concordia University, 1455 de Maisonneuve Boulevard West, Montreal, QC, Canada H3G 1M8

Received 5 April 2014; Accepted 16 June 2014; Published 17 July 2014

Academic Editor: Alok Singh

Copyright © 2014 Tian Wang et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


Al-Mn-Zn ternary system is experimentally investigated at 400°C using diffusion couples and key alloys. Phase relationships and homogeneity ranges are determined for binary and ternary compounds using EPMA, SEM/EDS, and XRD. Reported ternary compound T3 (Al11Mn3Zn2) is confirmed in this study and is denoted as τ2 in this paper. Two new ternary compounds (τ1 and τ3) are observed in this system at 400°C. τ1 is determined as a stoichiometric compound with the composition of Al31Mn8Zn11. τ3 has been found to have homogeneity range of AlxMnyZnz (  at%;  at%;  at%). The binary compounds Al4Mn and Al11Mn4 exhibit limited solid solubility of around 6 at% and 4 at% Zn, respectively. Terminal solid solution Al8Mn5 is found to have maximum ternary solubility of about 10 at% Zn. In addition, ternary solubility of Al-rich β-Mn′ at 400°C is determined as 4 at% Zn. Zn-rich β-Mn′′ has a ternary solubility of 3 at% Al. The solubility of Al in Mn5Zn21 is measured as 5 at%. Based on the current experimental results, the isothermal section of Al-Mn-Zn ternary system at 400°C has been constructed.

1. Introduction

Automotive industry represents one of the most important markets for aluminum alloys. The use of aluminum and its alloys offers considerable potential to reduce the weight of an automobile body or engine without compromising performance and safety [1]. Many different elements including Mg, Cu, Zn, Mn, Si, and so forth are used to improve the properties of Al alloy for specific applications. Al-Zn based alloys have high strength and hardness, improved creep, wear resistance, and low density. It is well known that a small amount of Mn added to Al alloys plays a positive role in improving the fracture toughness, recrystallization, grain refinement, and resistance to stress corrosion fatigue of these alloys [13]. Because the Al-Mn-Zn system is an important ternary system for the development of Al alloys, it is essential to understand the phase relationships in the system. In addition, this system is an essential subsystem for AZ, AM-series magnesium alloys, high strength steels, and for galvanizing-related alloy systems [4, 5].

The three constituent binary systems were reasonably studied. Khan and Medraj [6] reevaluated the Al-Mn system which was in good agreement with most of the experimental results [710]. From their work [6], thermodynamic calculation almost reproduced the EPMA results of Minamino et al. [11]. Their calculation was consistent with the observation of Okamoto [12] who suggested a smooth continuous liquidus curve between the terminal δ-phase (BCC) throughout the ε-phase (HCP) as mentioned by Taylor [13]. Al-Zn system was critically reviewed by Wasiur-Rahman and Medraj [14] lately. Their description showed good agreement with most of the experimental results. Mn-Zn system was reviewed by Okamoto and Tanner [15]. They proposed that there could be three possible separated phase fields (ε, ε1, and ε2) in the epsilon phase region. They [15] suggested that ε1 and ε2 phases can possibly be metastable phases, based on the analysis of [1619]. However, the presence of these separated phase regions has not been validated in the published literature. Recently, Liang et al. [2022] analyzed ε-phase at 400°C, 500°C, and 600°C. Based on their observations, the subdivision of the ε-phase region could not be confirmed.

Up to date little effort has been made to describe the phase relationships in the Al-Mn-Zn ternary system. The partial Al-Mn-Zn liquidus projection near the Zn-rich corner was studied by Gebhardt [23]. Later, Raynor and Wakeman [24] synthesized three ternary compounds (T1: Al24Mn5Zn, T2: Al9Mn2Zn, and T3: Al11Mn3Zn2) using electrolytic deposition and not by alloying. They [24] pointed out that Al4Mn dissolves up to 5.2 wt% Zn; whereas Al6Mn dissolves only 0.78 wt% Zn. These two compounds were characterized based on the substitution of Mn by Zn atoms. Subsequently, several researchers [2528] focused on the crystal structural analysis of the ternary compounds reported by Raynor and Wakeman [24]. Robinson [25] found that T1 was C-centered orthorhombic phase with , , and  nm lattice parameters. The structure of T3 was found by Damjanovic [26], which also has C-centered orthorhombic unit cell with , , and  nm lattice parameters. Schaefer et al. [27] showed that addition of Zn to Al-Mn alloys promoted the formation of decagonal phase. Singh et al. [28] used TEM to examine the formation and the approximant structures of Al24Mn5Zn and Al12Mn2.9Zn (close to T3 phase) quasicrystals in melt-spun condition. They [28] observed that melt spinning could lead to the formation of icosahedral phase in Al24Mn5Zn and decagonal phase in Al12Mn2.9Zn. Up to now, the experimental phase equilibrium information and thermodynamic data are insufficient for the accurate description of this system. Therefore, experimental investigations of the phase equilibrium in the Al-Mn-Zn ternary system are specifically performed in the present work to provide the phase relationships in this system at 400°C.

2. Experimental Procedures

Diffusion couple technique is a powerful and efficient tool for phase diagram determination [2931]. The layer formation in diffusion couples represents the local equilibria at the interfaces. Ternary diffusion couples may contain two phases in one layer, because of the additional degree of freedom [31]. Thus, three-phase equilibria can be determined at the interfaces of such layers. However, ternary diffusion couples have unpredictable diffusion paths that can lead to omitting some phases. Moreover, slow kinetic formation of some phases may cause the formation of extremely thin layers that might be difficult to be successfully analyzed. Therefore, key alloys are used to verify the phase relationships obtained from diffusion couple experiments. In this work, the experimental procedure was based on the combination of diffusion couple and key alloys techniques. The starting materials for both diffusion couples and key alloys were Al ingots, with purity 99.7%; Zn rods, with purity 99.99%; and Mn pieces, with purity 99%. All of which were supplied by Alfa Aesar, A Johnson Matthey Company. Alloys were prepared in an induction-melting furnace with a Ta crucible under an argon protective atmosphere. All samples were remelted three times to assure homogeneity. The actual global composition of the prepared samples was determined by inductively coupled plasma/optical emission spectrometry (ICP/OES). The specimens for ICP analysis were taken from 3 different locations of the sample to assure the accuracy of the analysis.

Preliminary study was carried out using three diffusion couples DC 1 to 3. Diffusion couples were prepared by grinding down the contacting interfaces using 1200 grit SiC paper and then polished up to 1 μm using alcohol-based diamond suspension. 99% pure ethanol was used as lubricant. The selected end-members were carefully pressed and clamped together using a stainless steel ring, placed in a Ta container, and sealed in a quartz tube under vacuum atmosphere. The encapsulated samples were then annealed at 400°C for 4 weeks. After obtaining preliminary results from the first three diffusion couples, two more diffusion couples (DC 4 and 5) and seventeen key alloys (1 to 17) were prepared to obtain the main phase relationships. The composition of the end-members used in diffusion couples are listed in Table 1. The selection of these end-members was based on preliminary thermodynamic calculations using the models of the binary systems reported by [6, 14, 32]. The probable diffusion paths were expected to cross several phase regions, which could lead to formation of large number of the diffusion layers. The compositions of the selected key alloys and the terminal composition of the diffusion couples are plotted in Figure 1. In order to identify the minor inconsistencies, the final study was preceded by preparing another nine key samples (18 to 26). All the key alloys were annealed at 400°C for 4 weeks.

Table 1: Terminal compositions of diffusion couples along with annealing time.
Figure 1: Terminal compositions of diffusion couples and actual compositions of key alloys.

The selection of annealing temperature is based on the homogenization time of alloys and their melting temperature. The annealing temperature should be high enough for fast homogenization interdiffusion and kinetics in the alloys. Meanwhile, the annealing temperature should be lower than the melting temperature of the alloys. The lowest eutectic temperature in this system is around 390°C in Zn-rich corner. However, this work is focused on Al-alloys and all samples were prepared away from Zn-rich corner. Therefore, 400°C was selected in order to have faster interdiffusion and relatively shorter annealing time.

Key alloys and diffusion couples were investigated using electron probe microanalysis (EPMA) and scanning electron microscopy (SEM) equipped with energy dispersive X-ray spectroscopy (EDS). The microstructure and phase composition of the samples were analyzed either by EPMA (JOEL-JXA-8900) or SEM/EDS (HITACHI S-3400N). The difference between EPMA and SEM/EDS results was less than 2 at% for Mn. This value was obtained by comparing the composition of several samples using both techniques. X-ray diffraction (XRD) was used for phase analysis of the key alloys and for the determination of the solubility limits of the compounds. The XRD patterns were obtained using PANanalytical Xpert Pro powder X-ray diffractometer [33] with a CuKα radiation at 45 kV and 40 mA. X-ray diffraction analysis of the samples was carried out using X'Pert HighScore Plus Rietveld analysis software [33]. Pearson’s crystal database [34] was used to identify the known phases in the Al-Mn-Zn system.

3. Results and Discussion

3.1. Experimental Study of Diffusion Couples

Isothermal section of the Al-Mn-Zn ternary system was constructed based on the experimental results of 5 diffusion couples and 26 key samples shown in Figure 1. During the preliminary study, three ternary compounds: τ1 (Al31Mn8Zn11), τ2 (Al71Mn16Zn13), and τ3 (Al10Mn15Zn75) have been found through diffusion couples analysis.

Backscattered electron image of DC 1 (Al-Mn11Zn89) is presented in Figure 2(a). Half of the image is colored for better representation of diffusion layers in this diffusion couple. The interdiffusion took place which led to the formation of several diffusion layers. The compositions of the formed phases were determined using EPMA point analysis. EPMA line-scan was used to determine the solubility ranges and phase equilibria among intermetallics. Based on the composition profile obtained by EPMA, as shown in Figure 2(b), the diffusion path was depicted based on the sequence of the phases as Mn5Zn21 → Al8Mn5 → Al11Mn4τ1 → Al-fcc. New ternary intermetallic compound τ1 has been found in this diffusion couple. τ1 was determined as a compound with the composition of Al62Mn16Zn22. As can be seen from Figure 2(b), the three points of EPMA results show no solubility range of τ1. Additional key alloy analysis was consistent with the results of DC 1 (Al-Mn11Zn89). This is why this compound is considered as stoichiometric. Figure 2(c) shows the estimated diffusion path of DC 1 (Al-Mn11Zn89) plotted on the Al-Mn-Zn Gibbs triangle. Layer number 1 was determined as Mn5Zn21. The solubility of Al in Mn5Zn21 was measured as 5 at%, where Al atoms substitute Zn atoms and Mn content remains constant at 16 at%. Based on the local equilibrium at the Mn5Zn21/Al8Mn5 interface, Mn5Zn21 is in equilibrium with Al8Mn5. In layer number 2, Al8Mn5 solid solution dissolves up to 7 at% Zn as shown in Figure 2(b). This homogeneity range was also confirmed by DC 4 (Mn-Al65Mn30Zn5), DC 5 (Al-Mn32Zn68), and key alloys 13–17. The composition of Al8Mn5 did not vary in DC 1 (Al-Mn11Zn89) because the diffusion path changed direction to form Al11Mn4 layer. Layer number 3 was determined as Al11Mn4 with limited ternary solubility of around 2 at% Zn. This value can be considered negligible, because the estimated error of EPMA measurement is about 2 at%. Layer number 4 contains two phases; these are Al11Mn4 and τ1. The results of point analysis indicated that Al11Mn4 has negligible ternary solubility, and τ1 has the composition of Al62Mn16Zn22. Layer number 5 was identified as τ1. Results of line-scan across τ1 layer showed that the composition of τ1 is constant as Al62Mn16Zn22. In layer number 6, Al-fcc was in equilibrium with τ1. The solubility of Zn in Al-fcc was found to reach up to 20 at%, based on the EPMA line-scan results.

Figure 2: (a) Backscattered electron image of DC 1 (Al-Mn11Zn89) and its schematic; (b) composition profile of the line-scan in DC 1 (Al-Mn11Zn89); (c) approximation of diffusion path of DC 1 (Al-Mn11Zn89).

DC 2 (Mn-Al94Zn6) was annealed at 400°C for two different time periods (15 and 25 days) in order to understand the phase formation kinetics. The annealing time resulted in significant growth of some compounds at the expense of others. This can be clearly seen in Figures 3(a) and 3(b), where the layer thickness of Al11Mn4 is growing at the expense of Al4Mn and τ2. Six layers were observed in this diffusion couple for both annealing times. The sequence of the observed phases is represented as follows: Al-fcc → τ2 → Al4Mn → Al11Mn4 → Al8Mn5β- β- → Mn. The ternary compound T3 (Al11Mn3Zn2) reported by [24] was observed in this diffusion couple and is denoted as τ2 in this paper, as shown in Figures 3(a) and 3(b). τ2 was determined as Al71Mn16Zn13, which is close to the composition of T3 (Al69Mn19Zn12) as reported by Raynor and Wakeman [24]. In DC 2 (Mn-Al94Zn6), finger-like structure morphology can be observed after annealing for 15 days as shown in Figure 3(b). This type of morphology indicates anisotropic diffusion of the three elements in this system. Al11Mn4 showed higher growth rate compared to other phases in this diffusion couple. This was concluded by comparing the micrographs of DC 2 (Figures 3(a) and 3(b)). Both thicknesses of τ2 and Al4Mn decreased after annealing for additional 10 days as shown in Figure 3(b). The Mn content of Al4Mn was found to vary from 18 at% to 20 at% after annealing for 15 days, whereas it became constant at 20 at% Mn after annealing for 25 days. The solubility of Zn in Al4Mn was measured as 5 at%. SEM/EDS analysis of DC 2 (Mn-Al94Zn6) annealed for 25 days is presented in Figure 3(c). The solubility of Zn in Al8Mn5 was measured as 5 at%. The ternary solid solubility of β- was found to be 4 at% Zn. β- shows limited ternary solubility of 3 at% Al.

Figure 3: (a) Backscattered electron image of DC 2 (Mn-Al94Zn6) annealed at 400°C for 15 days along with its schematic; (b) backscattered electron image of DC 2 (Mn-Al94Zn6) annealed at 400°C for 25 days along with its schematic; (c) diffusion path of DC 2 (Mn-Al94Zn6) annealed for 25 days; (d) comparisons of DC 2 (Mn-Al94Zn6) annealed at 15 days and 25 days.

DC 3 (Al-Mn13Zn87) was studied using the same approach as for DC 1 (Al-Mn11Zn89) and DC 2 (Mn-Al94Zn6). Four phases have been identified through EPMA analysis: τ3, Al8Mn5, Al11Mn4, and Al-fcc. EPMA point analysis indicated that the τ3 ternary compound had the composition of Al10Mn15Zn75. Other than this, the results of this diffusion couple only confirmed the data obtained from DC 1 and 2. Therefore, the details of DC 3 (Al-Mn13Zn87) are not mentioned here to avoid repetition.

3.2. Experimental Study of Key Alloys

Ten key alloys were prepared to verify the formation of phases reported in the literature and confirm the presence of the ternary compounds τ1, τ2, and τ3 found in this experimental study. The actual composition of these key alloys and the composition of the detected phases are presented in Table 2.

Table 2: The actual compositions of the key samples and the detected phases.

The ternary compounds T1 (Al24Mn5Zn) and T2 (Al9Mn2Zn) [24] were not observed in this system at 400°C. As shown in Table 2, key alloy 7 was prepared close to the composition of T1 compound; key alloys 5 and 6 were made close to the composition of T2 compound. However, T1 and T2 were not detected. It should be mentioned that Raynor and Wakeman [24] used only as-cast samples in their study and reported compounds could be metastable or high temperature phases. Furthermore, they [24] have used the wet chemical analysis of small quantities of extracted crystals, which may cause errors in phase compositions determination compared to EPMA point analysis used in our work. The existence of τ1 phase was confirmed in sample 1 as a stoichiometric compound with Al64Mn15Zn21 composition. The microstructure of this alloy is shown in Figure 4. τ1 formed during a peritectic reaction, which is hard to be terminated during short annealing period. Therefore, the primary phase Al4Mn was not decomposed completely even after annealing for 30 days. Similar phenomenon was also observed in key sample 7. Figures 5(a) and 5(b) show the as-cast and annealed microstructures of sample 7. It is clear that Al4Mn (the white phase) formed as a primary phase. Al6Mn then formed according to the peritectic reaction: L + Al4Mn → Al6Mn. After annealing for 30 days, the amount of Al4Mn decreased and decomposed to Al6Mn. The microstructure of annealed sample 7 is shown in Figure 5(b). Using XRD analysis, the weight fraction of Al4Mn and Al6Mn in the as-cast sample was measured as 56.2% and 29%, respectively, as shown in Figure 6(a). The amount of Al4Mn and Al6Mn changed dramatically after annealing for 30 days to become 14% and 82.2% as demonstrated in Figure 6(b). This variation indicates peritectic decomposition upon annealing. Due to the natural sluggish kinetics of peritectic reaction, the transformation of Al4Mn to Al6Mn requires very long time.

Figure 4: Backscattered electron image of sample 1.
Figure 5: (a) Backscattered electron image of as-cast sample 7; (b) backscattered electron image of annealed sample 7.
Figure 6: (a) XRD spectrum of as-cast sample 7; (b) XRD spectrum of annealed sample 7.

The formation of τ2 was confirmed after analysis of key alloys 2 to 6. The microstructure of sample 3 is shown in Figure 7. EPMA results indicated that τ2 is a stoichiometric compound with Al71Mn16Zn13 composition. It has been observed that the Mn content of Al4Mn varies in the range of 18–21 at%, which could be owing to the Zn substitution. The dissolved Zn in Al4Mn was found to reach up to 6 at%. Substitution of third element could lead to the small variations of compositions. On the other hand, these Mn content deviations could be due to the fact that Al4Mn forms quasicrystals. The structure of quasicrystal may change under different solidification conditions [27]. Schaefer et al. [27] mentioned that Al4Mn formed icosahedral or decagonal quasicrystals and structural changes in solid solutions could affect the compositions. They [27] observed that composition of ternary quasicrystals most likely fall in the range of 18–22 at% Mn, which was close to the composition region of the stable μ-Al4Mn phase. The composition of reported T1 is close to the homogeneity range of Al4Mn, which indicated that T1 might be a quasicrystal of Al4Mn with extended Zn solubility.

Figure 7: Backscattered electron image of sample 3.

τ3 was observed in DC 3 (Al-Mn13Zn87) and the composition was primarily determined as Al10Mn15Zn75. Several key alloys were prepared to study this new compound. The actual compositions of these samples and the compositions of the detected phases are listed in Table 2. The τ3 phase has a complex homogeneity range: 9–13 at% Al, 11–15 at% Mn, and 75–77 at% Zn, as was determined by the analysis of DC 3 (Al-Mn13Zn87) and key samples 9 to 13. Sample 9 is an example of these findings as shown in Figures 8(a) and 8(b). The sample contains residuals of the primary Al8Mn5 phase that decomposes according to the peritectic reaction: L+ Al8Mn5 → Al11Mn4. The decomposition of Al8Mn5 was not complete due to the slow kinetics of the peritectic reaction. τ3 phase formed a matrix in this alloy.

Figure 8: (a) Backscattered electron image of annealed sample 9 at 400°C for 30 days; (b) magnified area of sample 9; (c) backscattered electron image of sample 10 annealed at 400°C for 25 days; (d) backscattered electron image of sample 10 annealed at 400°C for 40 days.

The homogeneity ranges of the binary compounds were determined using EPMA. From the EPMA results, Al11Mn4 exhibited ternary solubility reaching up to 4 at% Zn. Al4Mn had the maximum ternary solubility of 6 at% Zn. The dissolved Zn in Al-fcc was found to reach up to 45 at%. Ternary homogeneity range of Al8Mn5 has been determined by EPMA as 11 at% Zn. These observations also confirmed the results which were inferred from DC 4 (Mn-Al65Mn30Zn5).

Additionally, another ternary phase τ4 was found in this ternary system. The composition of this phase is in the region around Al23Mn16Zn61. However, τ4 is found to be metastable. As shown in Figure 8(c), three phases Al11Mn4, τ3, and τ4 were found in sample 12 to be annealed at 400°C for 25 days. After prolonged annealing for another 15 days, τ4 decomposed to provide more τ3 and Al11Mn4.

In order to verify the observations of the ternary compounds, key alloys were studied using XRD. The XRD patterns of sample 1 are illustrated in Figure 9. Al-fcc and Al4Mn are positively identified in the XRD pattern. Besides, there are several peaks which do not belong to any of the known binary phases in the system. Based on the results of phase identifications, those peaks could correspond to τ1. Because of the lack of the reported prototype of τ1, the peaks which belong to τ1 were hard to separate, due to the several overlapping peaks in the XRD pattern of this sample. Thus, the crystal structure of this compound could not be determined in the current study. However, the peaks which could belong to τ1 have been labeled as shown in Figure 9.

Figure 9: XRD spectrum of annealed sample 1.

T3 phase reported by [24], denoted as τ2 in the current study, was confirmed through XRD analysis. Three XRD spectra of sample 2, 3, and 5 were used for this purpose. As shown in Figure 10, the XRD patterns of the three samples are similar. From position 40° to 45°, hump-like patterns can be observed due to peaks overlapping. This is because Al4Mn has very complex crystal structure and has around 550 atoms in a giant unit cell [34]. During the X-ray scanning process, the diffracted spectra of Al4Mn were overlapping with other peaks at numerous positions and generate these overlapped patterns. Using the crystallographic entry of T3 from Pearson’s database [34], T3 was positively identified among XRD analysis. Along with Al-fcc and Al4Mn, the triangulation among those three phases was established.

Figure 10: (a) XRD spectrum of annealed sample 2; (b) XRD spectrum of annealed sample 3; (c) XRD spectrum of annealed sample 5.

XRD analysis of ternary compound τ3 has similar issues to τ1 as elucidated above. Unfortunately too many peaks were overlapping in a multiphase alloy and a single-phase sample representing τ3 was not possible to prepare. Therefore, the crystal structure of this compound has not been determined either.

3.3. Description of Ternary Solid Solutions
3.3.1. Homogeneity Range of Al8Mn5 and Al11Mn4

Al8Mn5 has wide homogeneity range in Al-Mn binary system. However, it is difficult to estimate how much of Zn dissolved in this compound from the results of DC 2 (Mn-Al94Zn6). Thus, DC 4 (Mn-Al65Mn30Zn5) was prepared in order to determine the homogeneity range of Al8Mn5 in this ternary system. Because Al11Mn4 has higher growth rate, one end member of DC 4 (Mn-Al65Mn30Zn5) has been selected near the Al8Mn5 region to increase the atomic exchange between Al and Mn. From the backscattered electron image of DC 4 (Mn-Al65Mn30Zn5) shown in Figure 11(a), Al8Mn5 formed a thick layer and the color changed along with decreasing Mn content which suggests the presence of a homogeneity range. Line-scan, shown in Figure 11(b), was carried out to determine the homogeneity range of Al8Mn5. In the Al11Mn4 + Al8Mn5 two-phase region, dotted lines denote the concentrations of elements in Al11Mn4 and solid lines represent the concentrations of elements in Al8Mn5. The SEM/EDS analysis showed that Al8Mn5 has ternary solubility of 9 at% Zn and Al11Mn4 has maximum ternary solubility of 4 at% Zn. Al concentration in Al8Mn5 layer varied from 49 at% to 58 at%.

Figure 11: (a) Backscattered electron image of diffusion couple DC 4 (Mn-Al65Mn30Zn5); (b) composition profile of line-scan in diffusion couple DC 4 (Mn-Al65Mn30Zn5).

Al11Mn4 and Al8Mn5 showed extended ternary solubility in this system at 400°C. In order to confirm the results obtained from previous diffusion couples, four key alloys (14 to 17) were prepared. The composition and phase identification of these key samples are summarized in Table 2. The phase relations obtained from EPMA showed great consistency with the XRD results. Backscattered electron image of sample 14 is shown in Figure 12(a). From EPMA point analysis, Al11Mn4 has a ternary solubility of about 4 at% Zn and Al8Mn5 has a maximum ternary solubility of 10 at% Zn. These results were consistent with the previous EPMA observation of samples 9 and 11. Figure 12(b) shows that sample 15 contains mainly Al8Mn5 whose ternary solubility was measured around 4 at% Zn. The XRD analysis also confirmed that Al8Mn5 is dominating in sample 15 as shown in Figure 12(c). There are a few unlabeled small peaks indicating the presence of Al11Mn4 traces which could not be identified in the current study, because of their low intensity.

Figure 12: (a) Backscattered electron image of sample 14; (b) backscattered electron image of sample 15; (c) XRD spectrum of sample 15.
3.3.2. Single Region of Phase

Controversy on whether ε has three-phase separations reported in the assessment of Okamoto and Tanner [15] is still not resolved. In the current study, one end-member of DC 5 (Al-Mn32Zn68) has a composition in the ε-phase region. EPMA line-scan indicated that ε-phase has continuous binary solubility ranges reaching from Mn32Zn68 to Mn40Zn60 at 400°C. This finding also corresponds to the Mn-Zn binary system which was reported by [32, 35]. The backscattered electron image of DC 5 (Al-Mn32Zn68) is presented in Figure 13. Five phases have been identified: ε, Al-rich β- , Al8Mn5, Al11Mn4, and Al-fcc. In the current experimental investigation, the maximum solubility of Zn in β- was measured as 4 at%. Single ε-phase region with the Mn content from 32 to 40 at% was observed at 400°C and nothing indicated the presence of phase separation in this composition range. From the results of sample 17 (Al30Mn35Zn35), ε-phase was found to have limited ternary solubility of 4 at% Al.

Figure 13: Backscattered electron image of DC 5 (Al-Mn32Zn68).
3.4. Isothermal Section of Al-Mn-Zn System at 400°C

Combining the results which were obtained from the diffusion couples with those obtained from the key alloys, the Al-Mn-Zn isothermal section at 400°C was constructed and presented in Figure 14. Solid lines represent the experimentally verified phase boundaries and ternary solubility of binary phases. Dotted lines are the estimated phase relationships which were not confirmed in the current study. They were constructed based on the Gibbs phase rule [36] and Schreinemaker’s rule [37]. Grey, blue, and green areas indicate the single, two-phase, and three-phase regions separately, as shown in Figure 14.

Figure 14: Isothermal section of Al-Mn-Zn ternary system at 400°C constructed by diffusion couples and key samples.

4. Conclusion

The Al-Mn-Zn isothermal section at 400°C was constructed based on the current experimental results of diffusion couple technique and selected key alloys. Phase relationships and solubility limits have been determined for the ternary and binary compounds. The previously reported ternary compound T3 was confirmed in the current study and is denoted as τ2 in this paper. Two new ternary compounds: τ1 and τ3 have been found in this system at 400°C. τ1 does not show significant solubility ranges and is considered stoichiometric. τ3 is a solid solution with a narrow homogeneity range. The formulae of the three Al-Mn-Zn ternary intermetallic compounds are τ1: Al31Mn8Zn11, τ2: Al72Mn16Zn12, and τ3: AlxMnyZnz ( = 9–13 at%; = 11–15 at%; = 75–77 at%). A single-phase region of Al8Mn5 with extended solubility was found in this system at 400°C. Based on the current findings, the ternary solubilities of the Al8Mn5, Al4Mn, and Al11Mn4 compounds have been determined as 10 at%, 6 at%, and 4 at% Zn, respectively. ε and Mn5Zn21 exhibit their maximum solubilities of 4 at% and 5 at% Al. The solubility of Zn in β- has been found to be 4 at% and β- has ternary solubility of 3 at% Al.

Conflict of Interests

The authors declare that there is no conflict of interests of any sort that might have influenced the discussions or conclusions of this paper.


Financial support from General Motors of Canada Ltd. and the Natural Sciences and Engineering Research Council of Canada (NSERC) through the CRD grant program is gratefully acknowledged. The authors would also like to acknowledge the help of Mohammad Mezbahul-Islam of Mechanical Engineering Department, Concordia University, for his valuable suggestions.


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