Natural Aging Effect of Al-20Zn-3Cu Alloy on Mechanical Properties and Its Relation to Microstructural Change

: We investigate the effect of the natural age-hardening response of the Al-20Zn-3Cu alloy with natural aging times up to 12 months. The ultimate tensile strength of the Al-20Zn-3Cu alloy is drastically enhanced from 308 to 320 MPa after 2 months and from 320 to 346 MPa after 9 months. Then, natural age hardening becomes saturated after 9 months. A microstructural investigation reveals that the natural age-hardening mechanism is mainly induced by the diffusion of the Zn element. First, a rapid decrease in the volume fraction of the eutectoid lamellae ( α -Al+ η -Zn) is observed at the early stage of natural aging, leading to an increase in the tensile strength. This originates from the relatively high diffusivity of Zn due to its low melting temperature. Then, the diffusion of Zn into the Al matrix induces clusters of solute atoms that enhance the growth rate of the nanoprecipitates formed in the Al matrix. As a consequence, the tensile strength of the natural-aged Al-20Zn-3Cu alloy increases drastically after 9 months, whereas the ductility is signiﬁcantly degraded.


Introduction
Automotive components have been developed to reduce the total weight of vehicles to improve energy efficiency. For achieving the requirement, the number of Al alloys-based components is widely used in vehicles up to approximately 30% [1][2][3][4]. With regard to Al alloys, these are mainly applied to the transmission case, wheel, engine block, converter housing, and various structural components in a chassis of vehicles [5,6]. Among several Al alloys, ADC12 (Al-Si-Cu) alloy is a conventional cast alloy applied to power train and transmission cases due to its high castability with a low shrinkage rate [7][8][9]. Nevertheless, ADC12 has a brittle nature because of the formation of intermetallic phase containing Si element [7,[10][11][12][13]. Recently, high-Zn Al-based-alloys have attracted much research interest as a promising Al-cast alloy for automotive applications. High-Zn Al-based alloys show high strength, good wear resistance, and damping properties in comparison with such conventional cast Al-Si alloys [14][15][16][17]. In addition, the melting point of Al is gradually reduced as the amount of Zn increases, leading to a low production cost of the casting process [18].
In an earlier study, Shin et al. reported non-heat treatable Al-xZn-3Cu (x = 20, 30, 40, 45 in wt%) alloy fabricated using the high-pressure die casting (HPDC) method [19]. Interestingly, the reported die-cast alloys exhibit a significant high tensile strength of 490 MPa with an elongation of ≈4% even though any post treatments such as homogenization and artificial aging are not applied onto the alloys. These superior mechanical properties mainly stem from the unique microstructure induced by the Zn element while the small amount of Cu is also added in order to increase mechanical strength [19][20][21]. According to the reported binary phase diagram of Al-Zn, Zn elements can be dissolved in Al up to 70 at % for a wide range of temperatures [18]. No intermetallic compounds are formed in the Al-Zn binary system due to the very weak chemical interaction between Al and Zn [22]. Instead, Zn forms very fine nanoprecipitates in the Al matrix and complex microstructures consisting of eutectoid lamellae (α-Al and η-Zn) and the Zn phase in the vicinity of the grain boundaries [19,23,24]. This complex microstructure is more developed as the amount of Zn increases such that the mechanical strength of high-Zn Al-based alloys is correspondingly enhanced according to the amount of Zn.
On the other hand, it has been reported that the Zn element in Al alloy strongly affects mechanical properties during natural aging [25]. In earlier work, a 3DAP (threedimensional atom probe) analysis demonstrated that the Zn element enhances the growth rate of clusters in the Al matrix during natural aging, leading to the segregation of solute atoms from the Al matrix into clusters [26]. Then, by natural aging over time, the number density and volume fraction of clusters are the major factors to increase mechanical strength [27].
Therefore, based on the above considerations, it is evident that the natural aging response of high-Zn Al-based alloys should be carefully considered when developing Al-cast alloys for the applications in automotive components. In this study, we investigated the effect of natural aging on the microstructural evolution and its resultant mechanical properties of high-Zn Al-based alloys. For the purpose, the Al-20Zn-3Cu alloy was selected as the representative alloy to demonstrate the natural aging response in high-Zn Al-based alloy. The Al-20Zn-3Cu alloy was prepared using a conventional gravity casting method. Then, the as-cast specimen was naturally aged up to 9 months, and the variations of the mechanical properties were investigated based on structural investigations. Table 1 shows the nominal compositions of the synthesized Al-20Zn-3Cu alloys. Highpurity metals (Al, Cu, Zn) and master alloys (Al-5 wt% Ti, Al-5 wt% Fe, and Al-12 wt% Zr) were used to fabricate the developed alloys. Additionally, minor elements of Cu, Si, Fe, Ti, and Zr were added to enhance the castability and mechanical properties. The alloy components were melted in an electric resistance furnace at 730 • C. Then, the molten alloy was degassed using N 2 gas and stabilized in the furnace at 700 • C for 30 min. Alloy ingots were finally fabricated using a gravity casting method at room temperature. Then, the as-cast specimens were naturally aged for 2 months, 9 months, and 12 months at room temperature. Tensile tests were performed using a universal testing machine (UTM, DEAKYUNG TECH. & TESTER Mfg. Co., Ltd., DTU-900MHN, Incheon, Republic of Korea) with a constant strain rate of 1 mm/min at room temperature. All test specimens were prepared based on the ASTM E8 standard (Standard Test Method for the Tensile Testing of Metal Materials) [28]. Tensile tests were performed at least ten times for each alloy in order to obtain average values. On the macroscopic scale, the microstructures of synthesized alloys were investigated using an optical microscope (OM, KEYENCE Co., Ltd., VHX-1000E, Osaka, Japan). Then, phase identification was done using X-ray diffraction (XRD, BRUKER Co., D8 ADVANCE, Billerica, MA, USA) having a resolution of 0.01 • in 2θ. The microscopic structures were studied in detail using a field-emission scanning electron microscopy (FE-SEM, JEOL Ltd., JSM-7100F, Akishima, Japan) with an energy-dispersive X-ray spectroscopy (EDXS) detector. The local nanoscopic microstructure was further investigated using a transmission electron microscope (FE-TEM, FEI Company, TECNAI ST-F20, Hillsboro, WA, USA). The TEM specimens were mechanically polished down to 10-15 µm and then Ar-ion milled at an acceleration voltage of 4 kV with an incident angle of 6 • for electron transparency. Figure 1 shows the tensile properties of Al-20Zn-3Cu at different natural aging times from as-cast to 12 months. As reported earlier, the Al-20Zn-3Cu alloy shows fracture strength (σ f ) of 308 MPa with elongation of ε f = ≈6%. For the natural aging response, the tensile strength of Al-20Zn-3Cu alloy is naturally aged from σ f = 304 (±3.83) MPa to σ f = 320 (±4.28) MPa after 2 months with a slight decrease in the elongation from 6.5 (±1.30)% to 5.4 (±0.87)%. After 9 months, the tensile strength improves drastically to ≈346 (±6.72) MPa with a significant reduction in the degree of elongation at ≈1.2 (±0.64)%. Then, it mostly plateaus around σ f = 346 MPa with a similar elongation rate of ≈1.2%. (EDXS) detector. The local nanoscopic microstructure was further investigated using a transmission electron microscope (FE-TEM, FEI Company, TECNAI ST-F20, Hillsboro, USA). The TEM specimens were mechanically polished down to 10-15 μm and then Ar-ion milled at an acceleration voltage of 4 kV with an incident angle of 6° for electron transparency. Figure 1 shows the tensile properties of Al-20Zn-3Cu at different natural aging times from as-cast to 12 months. As reported earlier, the Al-20Zn-3Cu alloy shows fracture strength (σf) of 308 MPa with elongation of εf = ≈6%. For the natural aging response, the tensile strength of Al-20Zn-3Cu alloy is naturally aged from σf = 304 (±3.83) MPa to σf = 320 (±4.28) MPa after 2 months with a slight decrease in the elongation from 6.5 (±1.30)% to 5.4 (±0.87)%. After 9 months, the tensile strength improves drastically to ≈346 (±6.72) MPa with a significant reduction in the degree of elongation at ≈1.2 (±0.64)%. Then, it mostly plateaus around σf = 346 MPa with a similar elongation rate of ≈1.2%.    Considering the experimental 2θ values of Al, the peaks are slightly shifted to a higher 2θ angle, indicating the existence of compressive strain in the Al matrix. This may stem from the residual stress induced during the solidification process due to the high content of Zn element, which is often observed in a gravity-cast processing of high-Zn-based Al alloys. The major peaks of Al are constant regardless of the natural aging time. This indicates that the residual stress existing in the Al matrix is not affected by the level of natural aging. For the weak XRD peaks, the as-cast Al-20Zn-3Cu alloy consists of the secondary phases of Zn (hcp, P63/mmc, 194), Cu (fcc, Fm3m, 225), Al 3 Zr (tetragonal, I4/mmm, 139), and Al 2 Cu (tetragonal, I4/mcm, 140), which are determined using the reported crystallographic information. On the other hand, the peak intensities of the secondary phases gradually change with longer natural aging times. In the XRD profiles of the Al-20Zn-3Cu alloy, the peak related to the Zn phase abruptly decreases after 2 months, while other secondary peaks remain nearly identical. The configuration of the XRD scan profile shows no distinct changes after 9 months. As shown in Figure 1, the Metals 2021, 11, 1485 4 of 9 natural age-hardening response is observed after 2 months of natural aging. Therefore, considering the XRD profiles, the microstructural changes observed in the XRD profiles are closely related to the mechanical properties. er hand, the peak intensities of the secondary phases gradually change with longer natural aging times. In the XRD profiles of the Al-20Zn-3Cu alloy, the peak related to the Zn phase abruptly decreases after 2 months, while other secondary peaks remain nearly identical. The configuration of the XRD scan profile shows no distinct changes after 9 months. As shown in Figure 1, the natural age-hardening response is observed after 2 months of natural aging. Therefore, considering the XRD profiles, the microstructural changes observed in the XRD profiles are closely related to the mechanical properties.   (Figure 3a), as reported in a previous study [19], the grain boundary regions of the Al-20Zn-3Cu alloy mainly consists of pure Cu and a complex lamellae structure, respectively indicated as I and II in Figure  3a. The inset of Figure 3a is a magnified image of the complex lamellae structure consisting of α-Al and η (Zn, HCP). This microstructure is still observed after 2 months, as shown in the inset of Figure 3b. However, the volume fraction of the complex lamellae structure decreases drastically after 9 months, as shown in Figure 3c,d. As demonstrated earlier, the eutectoid lamellae in the grain boundaries impedes the crack propagation, resulting in the increase in elongation of Al-20Zn-3Cu alloy [19]. Therefore, the significant decrease in elongation shown in Figure 1 is considered to be a result from the significant reduction eutectoid lamellae in the grain boundaries of Al-20Zn-3Cu alloy.   (Figure 3a), as reported in a previous study [19], the grain boundary regions of the Al-20Zn-3Cu alloy mainly consists of pure Cu and a complex lamellae structure, respectively indicated as I and II in Figure 3a. The inset of Figure 3a is a magnified image of the complex lamellae structure consisting of α-Al and η (Zn, HCP). This microstructure is still observed after 2 months, as shown in the inset of Figure 3b. However, the volume fraction of the complex lamellae structure decreases drastically after 9 months, as shown in Figure 3c,d. As demonstrated earlier, the eutectoid lamellae in the grain boundaries impedes the crack propagation, resulting in the increase in elongation of Al-20Zn-3Cu alloy [19]. Therefore, the significant decrease in elongation shown in Figure 1 is considered to be a result from the significant reduction eutectoid lamellae in the grain boundaries of Al-20Zn-3Cu alloy.

Results and Discussion
R PEER REVIEW 5 of 9  Figure 4 shows the elemental mapping results of Al-20Zn-3Cu for the different natural aging times. In the as-cast Al-20Zn-3Cu alloy, the Cu and Zn elements are mostly found in the vicinity of the grain boundaries, correspondingly indicated here by I and II, as shown in Figure 4a. As demonstrated in the BSE images (Figure 3), the Cu and Zn elements found in the grain boundaries form large particles of pure Cu and eutectoid lamellae consisting of Al and Zn phases. The elemental mapping outcome of the Al-20Zn-3Cu alloy indicates that the Zn constituents gradually migrate into the Al matrix with longer natural aging times. Thus, a decrease in the Zn element leads to a decrease in the volume fraction of the η phase in the grain boundaries, resulting in a decrease in the eutectoid lamellae structures, as demonstrated in Figure 3a-d. It was reported that Zn-contained alloy is naturally aged even at room temperature due to the relatively high diffusivity of Zn. This originates from the low melting point of Zn. Resultantly, the Zn-added Al alloys show enhanced natural age-hardening responses compared to a Zn-free alloy [26,29]. In contrast to the Zn element, the large Cu particles show no obvious changes in the naturally aged Al-20Zn-3Cu alloy. Hence, the increase in the tensile strength of the Al-20Zn-3Cu alloy after 2 months is considered to originate from the decrease in the eutectoid lamella structures in the vicinity of the grain boundaries. However, after 2 months of natural aging time, the volume fraction of the eutectoid lamellae slowly decreases such that the enhancement of the tensile strength after 2 months of natural aging time should be considered at microscopic scale. This will be discussed further in conjunction with the results of the TEM investigation.  Figure 4 shows the elemental mapping results of Al-20Zn-3Cu for the different natural aging times. In the as-cast Al-20Zn-3Cu alloy, the Cu and Zn elements are mostly found in the vicinity of the grain boundaries, correspondingly indicated here by I and II, as shown in Figure 4a. As demonstrated in the BSE images (Figure 3), the Cu and Zn elements found in the grain boundaries form large particles of pure Cu and eutectoid lamellae consisting of Al and Zn phases. The elemental mapping outcome of the Al-20Zn-3Cu alloy indicates that the Zn constituents gradually migrate into the Al matrix with longer natural aging times. Thus, a decrease in the Zn element leads to a decrease in the volume fraction of the η phase in the grain boundaries, resulting in a decrease in the eutectoid lamellae structures, as demonstrated in Figure 3a-d. It was reported that Zn-contained alloy is naturally aged even at room temperature due to the relatively high diffusivity of Zn. This originates from the low melting point of Zn. Resultantly, the Zn-added Al alloys show enhanced natural age-hardening responses compared to a Zn-free alloy [26,29]. In contrast to the Zn element, the large Cu particles show no obvious changes in the naturally aged Al-20Zn-3Cu alloy. Hence, the increase in the tensile strength of the Al-20Zn-3Cu alloy after 2 months is considered to originate from the decrease in the eutectoid lamella structures in the vicinity of the grain boundaries. However, after 2 months of natural aging time, the volume fraction of the eutectoid lamellae slowly decreases such that the enhancement of the tensile strength after 2 months of natural aging time should be considered at microscopic scale. This will be discussed further in conjunction with the results of the TEM investigation.   Figure 5 shows Z-contrast images of the Al-20Zn-3Cu alloys according to the natural aging times, in this case as-cast and 9 months. As shown in Figure 5a,b, the Al-20Zn-3Cu alloy consists of very fine nanoprecipitates. Two types of nanoprecipitates can be observed in the α-Al matrix of the Al-20Zn-3Cu alloy, as indicated by the I and II arrows in Figure 5a. A chemical investigation showed that the nanoprecipitates I and II are respectively composed of a Zn-Cu-rich and a Zn-rich phase. More details of phase identification can be found elsewhere [30]. Nanoprecipitate I (Zn-Cu-rich phase) has average dimensions of ≈5 × 15 nm 2 in terms of the length and width, while nanoprecipitate II (Zn-rich phase) has an average diameter of ≈3 nm. Due to the very fine sizes of these nanoprecipitates, the corresponding [110] electron diffraction (ED) pattern has no distinct patterns of the nanoprecipitates that formed in the α-Al matrix. Similarly, as shown in Figure 5b, the morphology of nanoprecipitates in the α-Al matrix shows no significant change after 2 months of natural aging time. In contrast, severe microstructural evolution is observed after 9 months of natural aging time. As shown in Figure 5c, fine nanoprecipitates of Zn-Cu-rich and Zn-rich phases drastically grow compared to the as-cast Al-20Zn-3Cu alloy. Accordingly, the satellite electron spots around the election spots in the α-Al matrix are evidence of the coarsened nanoprecipitates.  Figure 5 shows Z-contrast images of the Al-20Zn-3Cu alloys according to the natural aging times, in this case as-cast and 9 months. As shown in Figure 5a,b, the Al-20Zn-3Cu alloy consists of very fine nanoprecipitates. Two types of nanoprecipitates can be observed in the α-Al matrix of the Al-20Zn-3Cu alloy, as indicated by the I and II arrows in Figure 5a. A chemical investigation showed that the nanoprecipitates I and II are respectively composed of a Zn-Cu-rich and a Zn-rich phase. More details of phase identification can be found elsewhere [30]. Nanoprecipitate I (Zn-Cu-rich phase) has average dimensions of ≈5 × 15 nm 2 in terms of the length and width, while nanoprecipitate II (Zn-rich phase) has an average diameter of ≈3 nm. Due to the very fine sizes of these nanoprecipitates, the corresponding [110] electron diffraction (ED) pattern has no distinct patterns of the nanoprecipitates that formed in the α-Al matrix. Similarly, as shown in Figure 5b, the morphology of nanoprecipitates in the α-Al matrix shows no significant change after 2 months of natural aging time. In contrast, severe microstructural evolution is observed after 9 months of natural aging time. As shown in Figure 5c, fine nanoprecipitates of Zn-Cu-rich and Zn-rich phases drastically grow compared to the as-cast Al-20Zn-3Cu alloy. Accordingly, the satellite electron spots around the election spots in the α-Al matrix are evidence of the coarsened nanoprecipitates. Considering the above, in consequence, the change in the mechanical properties of the Al-20Zn-3Cu alloy ( Figure 1) is strongly affected by the diffusion of Zn into the Al matrix. The diffusivity of Zn element is known to be relatively high at room temperature due to the low melting point of Zn [29], meaning that natural aging proceeds spontaneously. In addition, it has been reported that the Zn element accelerates the aggregation of clusters in the Al matrix [26], which enhances the strength and lowers the ductility. The decrease in the Zn phase can also be confirmed from the XRD profiles shown in Figure 2. The amount of the Zn phase obviously decreases after 2 months of natural aging in the Al-20Zn-3Cu alloys. As demonstrated in Figure 5, the clusters are induced by the Zn element in the growth of nanoprecipitates with an increase in the natural aging time.

Conclusions
In this study, we investigated the effects of natural aging on the tensile properties of the Al-20Zn-3Cu alloy. It was demonstrated that the change of tensile properties according to natural aging times resulted from the microstructural evolution of Al-20Zn-3Cu alloy. The microstructural change is caused by the relatively high diffusivity of the Zn element at room temperature. First, the diffusion of the Zn element from the grain boundaries into the α-Al matrix induces a decrease in the volume fraction of large eutectoid structures consisting of the α-Al and η (Zn) phases in the Al-20Zn-3Cu alloy with 2 months of natural aging. As a result, the tensile strength of the Al-20Zn-3Cu alloy increases from 308 to 320 MPa. As the natural aging grows longer, gradual Zn diffusion facilitates the formation of clusters in the α-Al matrix, causing the size of the nanoprecipitates in the Al-20Zn-3Cu alloy to increase drastically, which is very similar to the effect of the peak-aging process. Then, the significant growth of nanoprecipitates enables the highest tensile strength of ≈346 MPa in the Al-20Zn-3Cu alloy with significantly reduced ductility by approximately 1%.   Considering the above, in consequence, the change in the mechanical properties of the Al-20Zn-3Cu alloy ( Figure 1) is strongly affected by the diffusion of Zn into the Al matrix. The diffusivity of Zn element is known to be relatively high at room temperature due to the low melting point of Zn [29], meaning that natural aging proceeds spontaneously. In addition, it has been reported that the Zn element accelerates the aggregation of clusters in the Al matrix [26], which enhances the strength and lowers the ductility. The decrease in the Zn phase can also be confirmed from the XRD profiles shown in Figure 2. The amount of the Zn phase obviously decreases after 2 months of natural aging in the Al-20Zn-3Cu alloys. As demonstrated in Figure 5, the clusters are induced by the Zn element in the growth of nanoprecipitates with an increase in the natural aging time.

Conclusions
In this study, we investigated the effects of natural aging on the tensile properties of the Al-20Zn-3Cu alloy. It was demonstrated that the change of tensile properties according to natural aging times resulted from the microstructural evolution of Al-20Zn-3Cu alloy. The microstructural change is caused by the relatively high diffusivity of the Zn element at room temperature. First, the diffusion of the Zn element from the grain boundaries into the α-Al matrix induces a decrease in the volume fraction of large eutectoid structures consisting of the α-Al and η (Zn) phases in the Al-20Zn-3Cu alloy with 2 months of natural aging. As a result, the tensile strength of the Al-20Zn-3Cu alloy increases from 308 to 320 MPa. As the natural aging grows longer, gradual Zn diffusion facilitates the formation of clusters in the α-Al matrix, causing the size of the nanoprecipitates in the Al-20Zn-3Cu alloy to increase drastically, which is very similar to the effect of the peak-aging process. Then, the significant growth of nanoprecipitates enables the highest tensile strength of ≈346 MPa in the Al-20Zn-3Cu alloy with significantly reduced ductility by approximately 1%.