Crystal Structures of Al 2 Cu Revisited: Understanding Existing Phases and Exploring Other Potential Phases

: When processing single crystal X-ray di ﬀ raction datasets for twins of Al 2 Cu sample synthesized by the high-pressure sintering (HPS) method, we have clariﬁed why the crystal structure of Al 2 Cu was incorrectly solved about a century ago. The structural relationships between all existing Al 2 Cu phases, including the Owen-, θ -, θ ’-, and Ω -Al 2 Cu phases, were investigated and established based on a proposed pseudo Al 2 Cu phase. Two potential phases have been built up by adjusting the packing sequences of A / B layers of Al atoms that were inherent in all existing Al 2 Cu phases. The mechanical, thermal, and dynamical stability of two such novel phases and their electronic properties were investigated by ﬁrst-principles calculations.


Introduction
Al-Cu binary alloys are widely used in aerospace, automobile, and other fields, due to their high strength-to-weight ratio [1]. Among all compounds in the Al-Cu system, the Al 2 Cu phase has been extensively investigated due its significant effect on the properties of Al-Cu alloys. It was reported that Al 2 Cu adopts a tetragonal structure with a = b = 4.28 Å. and c = 2.40 Å, as determined by Owen et al. through powder X-ray diffraction patterns [2] (hereafter named the Owen phase). Then, Jette et al. [3] suggested a larger tetragonal unit cell (a = b = 6.052 Å and c = 4.878 Å) should be used to describe the θ-Al 2 Cu phase. Finally, Friauf [4] confirmed Jette's results and provided the exact atomic positions of θ-Al 2 Cu. During the next ninety years, it was again confirmed to have a tetragonal space group (a = b = 6.067(1) Å and c = 4.877(1) Å, S.G. I4/mcm) [5], which was generally accepted by the community [6,7]. The θ'-Al 2 Cu phase is another very important strengthening phase in aluminum alloys [8], which is generally accepted to have a body centered tetragonal structure (a = b = 4.04 Å and c = 5.80 Å, S.G. I4/mmm) [9]. In addition, the structural information of the Ω-Al 2 Cu phase has been hotly debated since its discovery and different structural models have been proposed [10][11][12]. The Ω phase is generally believed to have an orthorhombic structure (a = 4.96 Å, b = 8.56 Å, c = 8.48 Å), which is a distorted form of the tetragonal θ-Al 2 Cu [10,13]. Although extensive experimental and simulation works have been carried out on the structural, electronic, physical properties of the above-mentioned (θ, θ', Ω)-Al 2 Cu precipitated as well as interface phases [6,7,14,15], knowledge on their structural relations are still quite limited.
Here, we report the data processing of diffraction data sets collected with a four-circle single crystal X-ray diffractometer (Bruker D8 venture, Bruker AXS GmbH, Karlsruhe, Germany) for a piece of Al-Cu sample. During indexing, solving, and refining of the synthesized Al-Cu phase, a pseudo Al 2 Cu phase similar to that reported by Owen et al. [2] was proposed. The pseudo Al 2 Cu phase changes to the θ-Al 2 Cu phase if certain small number of reflections are carefully included during data processing. As will be illustrated, the pseudo Al 2 Cu phase can be considered to be the average structure of all other existing Al 2 Cu phases (θ-, θ'and Ω-Al 2 Cu phase). Based on such a rule, two other potential Al 2 Cu phases were built by rearranging the packing sequences of two atomic net planes encoded in all existing Al 2 Cu phases. Meanwhile, the mechanical, dynamical stability, as well as the formation enthalpy and electronic properties of the proposed phases were investigated by first-principles calculations.

Materials and Methods
The Al 2 Cu sample was discovered during efforts to prepare Al rich Al-Cu phase by mixing pure aluminum powder (indicated purity 99.8%) and copper powder (indicated purity 99.9%), in an atomic ratio if 6:1. Blended powders were then placed in a grinding tool of diameter 9.6 mm and were pressed into a tablet at about 4 MPa slowly and continuously for about five minutes. A cylindrical block 9.6 mm in diameter and 10 mm in height was obtained without cracks or deformations. The cylindrical block was encapsulated into an h-BN crucible covered by an h-BN gasket and wrapped in a graphite stove. Both ends of the graphite stove were filled with a pyrophyllite and dolomite composite medium and sealed by conducting steel rings. Finally, all of these components were put into a pyrophyllite rock that served as a pressure transition medium and were then inserted into a six-anvil high-pressure apparatus for high-pressure sintering (HPS) experiments (See Figure 1). Ultrahigh pressure 5 GPa was applied to the sample and heated to 1023 K for 30 min, cooled to 753 K for 2 h, and then rapidly cooled down to room temperature. Suitable pieces of crystals were selected for the single crystal X-ray diffraction measurements. structure of all other existing Al2Cu phases (θ-, θ'-and Ω-Al2Cu phase). Based on such a rule, two other potential Al2Cu phases were built by rearranging the packing sequences of two atomic net planes encoded in all existing Al2Cu phases. Meanwhile, the mechanical, dynamical stability, as well as the formation enthalpy and electronic properties of the proposed phases were investigated by firstprinciples calculations.

Materials and Methods
The Al2Cu sample was discovered during efforts to prepare Al rich Al-Cu phase by mixing pure aluminum powder (indicated purity 99.8%) and copper powder (indicated purity 99.9%), in an atomic ratio if 6:1. Blended powders were then placed in a grinding tool of diameter 9.6 mm and were pressed into a tablet at about 4 MPa slowly and continuously for about five minutes. A cylindrical block 9.6 mm in diameter and 10 mm in height was obtained without cracks or deformations. The cylindrical block was encapsulated into an h-BN crucible covered by an h-BN gasket and wrapped in a graphite stove. Both ends of the graphite stove were filled with a pyrophyllite and dolomite composite medium and sealed by conducting steel rings. Finally, all of these components were put into a pyrophyllite rock that served as a pressure transition medium and were then inserted into a six-anvil high-pressure apparatus for high-pressure sintering (HPS) experiments (See Figure 1). Ultrahigh pressure 5 GPa was applied to the sample and heated to 1,023 K for 30 min, cooled to 753 K for 2 h, and then rapidly cooled down to room temperature. Suitable pieces of crystals were selected for the single crystal X-ray diffraction measurements. All density functional theory (DFT) based first-principles calculations in this work including geometry optimization, total energy, and electronic structure calculations, were performed by the Vienna Ab initio Simulation Package (VASP) [16,17]. The generalized gradient approximations (GGA) of the Perdew-Burke-Ernzerhof (PBE) type were adopted for the exchange correlation potential [18]. The projection-augmented wave (PAW) method [19] was applied to simulate the potentials between electrons and ions. A plane wave basis was used to expand the wave functions All density functional theory (DFT) based first-principles calculations in this work including geometry optimization, total energy, and electronic structure calculations, were performed by the Vienna Ab initio Simulation Package (VASP) [16,17]. The generalized gradient approximations (GGA) of the Perdew-Burke-Ernzerhof (PBE) type were adopted for the exchange correlation potential [18]. The projection-augmented wave (PAW) method [19] was applied to simulate the potentials between electrons and ions. A plane wave basis was used to expand the wave functions with a cut-off energy of 500 eV. The Monkhorst-Pack scheme [20] was selected for the k-point sampling in the Brillouin zone (7 × 7 × 9 for both new phases). The static self-consistent convergence criteria were set at 1 × 10 −6 eV/atom. The phonon spectrums were simulated using the supercell approach, by utilizing the Phonopy package [21].

Structural Relations of the Existing Phases
A piece of sample of size 0.050 mm × 0.055 mm × 0.090 mm was selected for the single crystal X-ray diffraction measurements. The measured sample had a twin structure and it was found to quite easily neglect a small number of reflections (about 25%), while discriminating them from the two domains. Such reflections, as indicated by the red arrow in Figure 2a, resulted in a slightly different arrangement of reciprocal lattice points, as shown in Figure 2b. Surprisingly, with the incomplete reflections shown in Figure 2b, a pseudo Al 2 Cu phase could be indexed and refined to a tetragonal structure with a P4/mmm space group (a = b = 4.279(2) Å and c = 2.4337(13) Å, see the supplementary materials), similar to those of the Owen-phase. Considering the Owen-phase was corrected to be the θ-Al 2 Cu phase, it is of vital importance to clarify the relationship between the pseudo Al 2 Cu phase, the Owen-phase, and other existing (θ, θ', Ω)-Al 2 Cu phases. with a cut-off energy of 500 eV. The Monkhorst-Pack scheme [20] was selected for the k-point sampling in the Brillouin zone (7 × 7 × 9 for both new phases). The static self-consistent convergence criteria were set at 1 × 10 −6 eV/atom. The phonon spectrums were simulated using the supercell approach, by utilizing the Phonopy package [21].

Structural Relations of the Existing Phases
A piece of sample of size 0.050 mm × 0.055 mm × 0.090 mm was selected for the single crystal Xray diffraction measurements. The measured sample had a twin structure and it was found to quite easily neglect a small number of reflections (about 25%), while discriminating them from the two domains. Such reflections, as indicated by the red arrow in Figure 2a, resulted in a slightly different arrangement of reciprocal lattice points, as shown in Figure 2b. Surprisingly, with the incomplete reflections shown in Figure 2b, a pseudo Al2Cu phase could be indexed and refined to a tetragonal structure with a P4/mmm space group (a = b = 4.279(2) Å and c = 2.4337(13) Å, see the supplementary material), similar to those of the Owen-phase. Considering the Owen-phase was corrected to be the θ-Al2Cu phase, it is of vital importance to clarify the relationship between the pseudo Al2Cu phase, the Owen-phase, and other existing (θ, θ', Ω)-Al2Cu phases. First, let us study the relationship between the Owen-Al2Cu and the θ-Al2Cu phase. Figure 3a shows the established 2 × 2 × 2 supercell of the Owen-Al2Cu structure. It can be clearly observed that the established supercell can also be described by a θ-Al2Cu-type unit cell (indicated by black dotted lines with a = b = 4.28 × √2 = 6.053 Å and c = 2.40 × 2 = 4.80 Å, see Figure 3b). The main difference between the Owen-Al2Cu phase and that of the θ-Al2Cu phase (shown in Figure 3c) lie in that the two adjacent layers, each formed by the four Al atoms in the θ-Al2Cu phase, rotates around each other at δ = 45°, with clockwise and anti-clockwise rotation at δ/2 = 22.5°, compared to that of the Owen phase, as shown in Figure 3a-d. In the following, we name the layer represented by the four sky-blue and gray Al atoms in the θ-Al2Cu phase as the A and B layer, respectively (in all cases, the Brown ball denotes the copper atom). Therefore, the Owen phase could be represented by larger tetragonal cells as suggested by Jette et al. [3], but it has a different arrangement of layers formed by Al atoms from that of the θ-Al2Cu phase. In other words, Al atoms are packed by same kind of layers along the c-axis in the Owen phase, but has repeating A-B layer sequences in the θ-Al2Cu phase.
Second, let us consider the Ω-Al2Cu phase which is a slightly distorted θ-Al2Cu phase. To illustrate it clearly, the crystal structure of the Ω-Al2Cu phase was established on the basis of previous First, let us study the relationship between the Owen-Al 2 Cu and the θ-Al 2 Cu phase. Figure 3a shows the established 2 × 2 × 2 supercell of the Owen-Al 2 Cu structure. It can be clearly observed that the established supercell can also be described by a θ-Al 2 Cu-type unit cell (indicated by black dotted lines with a = b = 4.28 × √ 2 = 6.053 Å and c = 2.40 × 2 = 4.80 Å, see Figure 3b). The main difference between the Owen-Al 2 Cu phase and that of the θ-Al 2 Cu phase (shown in Figure 3c) lie in that the two adjacent layers, each formed by the four Al atoms in the θ-Al 2 Cu phase, rotates around each other at δ = 45 • , with clockwise and anti-clockwise rotation at δ/2 = 22.5 • , compared to that of the Owen phase, as shown in Figure 3a-d. In the following, we name the layer represented by the four sky-blue and gray Al atoms in the θ-Al 2 Cu phase as the A and B layer, respectively (in all cases, the Brown ball denotes the copper atom). Therefore, the Owen phase could be represented by larger tetragonal cells as suggested by Jette et al. [3], but it has a different arrangement of layers formed by Al atoms from that of the θ-Al 2 Cu phase. In other words, Al atoms are packed by same kind of layers along the c-axis in the Owen phase, but has repeating A-B layer sequences in the θ-Al 2 Cu phase.  Second, let us consider the Ω-Al 2 Cu phase which is a slightly distorted θ-Al 2 Cu phase. To illustrate it clearly, the crystal structure of the Ω-Al 2 Cu phase was established on the basis of previous reported results [10,13] (Figure 3e). It can be seen that the Al atoms are packed in A-B layer sequences in the Ω-Al 2 Cu phase, similar to that of the θ-Al 2 Cu phase. However, the Ω-Al 2 Cu phase adopts a larger unit cell than that of the θ-Al 2 Cu phase (b ≈ c ≈ 6.067 √ 2 ≈ 4.28 × 2 = 8.56 Å; a ≈ 2.40 × 2 = 4.80 Å) and it contains four θ-Al 2 Cu-type unit cell (two parallel and orthogonal to the rest two).
Third, let us turn to the simple but unique θ'-Al 2 Cu phase. One can observe that the Al atoms are packed in B-B layer sequences in the θ'-Al 2 Cu phase, similar to those in the Owen-Al 2 Cu phase (see Figure 3f). However, the copper atoms occupy the body center and the vertex positions of the lattice in the θ'-Al 2 Cu phase, resulting in a much larger c value and slightly smaller a or b values of lattice parameters (a = b = 4.04 Å and c = 5.80 Å), as compared to that of the Owen-phase and the θ-Al 2 Cu phase.
Last but not least, according to the refined crystal structure of the pseudo Al 2 Cu phase, there are 4 equivalent Al atom positions in the unit cell and each have a site occupancy factor of 0.493 (see Figure 3i and see Figure S1 in the supplementary materials). As the distance between two Al atoms along each edge is too short (1.575 Å), the Al atoms cannot simultaneously occupy two such positions. It can be easily acknowledged that the aforementioned A-B and B-B layer packing sequences are the two simplest packing arrangements of Al atoms, to avoid the meaningless short bond length of Al-Al atoms and to fit with a reasonable site occupancy factor less than 0.5. In other words, the pseudo Al 2 Cu phase can be considered as the average structure of the θand Ω-Al 2 Cu phase, while the Owen can be considered as the average structure of the pseudo Al 2 Cu phase. Detailed crystallographic information of all existing Al 2 Cu phases (Owen-, θ-, θ'and Ω-Al 2 Cu phase) are listed in Table 1.

Potential Phases and Diffraction Patterns
Encouraged by discovering that the pseudo Al 2 Cu phase has the average structure of all other existing Al 2 Cu phases, we decided to further explore other potential Al 2 Cu phases. According to the different packing sequences of A/B layers, two new structural models based on the pseudo Al 2 Cu phase were built. In the M1 model, the Al atoms were arranged in the A-A-B-B layer sequences and the copper atoms occupied the same positions as those in the θ-Al 2 Cu phase (see Figure 3g). Consequently, the M2 model was built-up by packing Al atoms in the A-A-A-B-B-B layer sequences and arranging copper atoms as those in the θ-Al 2 Cu phase (see Figure 3h). Although infinite number of new phases could be built-up in the same way, two such models are informative enough to investigate the stability and electronic properties of the Al 2 Cu phases, which will be discussed in the following section. It was verified that the M1 and M2 models still adopted the tetragonal symmetry (S. G. I4/mcm), containing 16 Al atoms and 8 Cu atoms, and 24 Al atoms and 12 Cu atoms, respectively.
To observe the close relationship of these Al 2 Cu phases, the power diffraction patterns (2θ = 0-25 • ) of all existing and potential Al 2 Cu phases were simulated. The powder diffraction patterns are shown in Figure 4. It can be seen that the two characterizing peaks of all phases between 2θ = 9 • and 14 • were indistinguishable, except those of the θ' phase. In the angle region beyond 14 • , the diffraction peaks of the Owen phase, the pseudo phase, the θ phase, and the Ω-Al 2 Cu phase were more comparable than those of other phases. There were only slight differences between the diffraction peaks of the Owen phase and the θ phase as indicated by the arrows inserted in Figure 4. Such observations might explain why the θ-Al 2 Cu phase was initially incorrectly refined to be the Owen phase [2] and was easily mis-indexed to be the pseudo Al 2 Cu phase during data processing of the present measured data sets. It also confirmed that the pseudo Al 2 Cu phase could be considered as the average structure of the θand Ω-Al 2 Cu phase, while the Owen might be considered to be the average structure of the pseudo Al 2 Cu phase discussed before. For the potential M1 and M2 phases, it could be observed that there were some additional peaks in the 2θ = 14 • and 16 • region, implying that they are quite different phases from that of the θ phase and the Ω-Al 2 Cu phase. Additional different reciprocal space information might be found in the projected simulated single crystal diffraction patterns (see the Supplementary Materials).

First-Principles Calculations
In this part, the mechanical, thermal and dynamic stability, as well as the electronic properties of the two proposed Al 2 Cu phases have been investigated by first-principles calculations method. Table 2 Metals 2019, 9, 1037 7 of 10 shows the calculated cell parameters, elastic constants, and the enthalpy of formation of the Owen-, M1-, M2-Al 2 Cu phases in the present work and for comparison, the θ-, θ'-, Ωphases reported by previous studies are also mentioned. It can be seen that the a and b lattice values of the M1 and M2 phase agree well with those of the θ-Al 2 Cu phase, implying that the packing of the A/B layers along the c direction has no effect on the in-plane arrangement of atoms. As mentioned earlier, the M1, M2, and the θ-Al 2 Cu phase has the same average structure as the pseudo Al 2 Cu phase, their lattice value of c is about double and triple of that of the θ-Al 2 Cu phase.
As the enthalpy of formation (∆H) indicates the forming ability of compounds, it was calculated according to the following formula [22]: where E tot represent the total energy of the studied system, x and y represents the number of Al and Cu atoms, respectively. E Al solid and E Cu solid are the energy of each Al and Cu atom in their normal FCC unit cell. Negative enthalpy of formation indicates an exothermic process, and the lower the value of enthalpy of formation, the stronger the alloying ability [23]. From Table 2, one can find that all structures including the existing (θ, θ', Ω)-Al 2 Cu and the proposed M1 and M2 have negative enthalpy of formation, implying that they might show up under some favorable conditions, such as stable or metastable phases. It is necessary to note that the enthalpy of formation of both M1 and M2 are greater than those of the (θ, θ', Ω)-Al 2 Cu phases, suggesting that they are metastable phases. The enthalpy of formation of the Owen phase has a much higher value of ∆H = −0.025 eV/atom than those of the M1/M2 phases, confirming that it is not the correct phase observed in previous experiments. From Table 2, one can also observe that the enthalpy of formation of the θ'-phase is slightly lower than that of the θ-phase and that of the Ω-phase is nearly equal to that of the θ-phase. However, precipitation experiments imply that the θ-phase should be the stable phase. It was found that the vibrational entropy reverses the energetic preference of the θ-phase and the θ'-phase at T = 150-200 K, which resolve the apparent discrepancy between theory and experiments [24]. The elastic constants can be used to estimate the resistance of crystals to external stress and to deduce the basic mechanical properties and structural mechanical stability. There are six independent elastic constants (C 11 , C 12 , C 13 , C 33 , C 44 , and C 66 ) for the tetragonal system, and its mechanical stability is determined according to the following formula (applied to Laue class 4/mmm) [25]: From Table 2, it can be concluded that both the M1 and M2 phase is mechanically stable as the independent elastic constants of M1 and M2 are all positive and satisfy the above criteria. It can also be found that the C 11 values of the M1 and M2 phase are much smaller than those of the (θ, θ', Ω)-Al 2 Cu phases, indicating that M1 and M2 are much easier to compress along the [100] directions.
In order to investigate the dynamical stability of the proposed M1 and M2 phases, their phonon dispersions were calculated by the finite displacement method, as shown in the Figure 5b. We can clearly see that there are no imaginary frequencies in the phonon spectrum, suggesting both M1 and M2 phases are dynamically stable. As all Al 2 Cu phases studied in the present work could be considered to be a special solution of the pseudo Al 2 Cu phase and the (θ, θ', Ω)-Al 2 Cu phases have been observed, it is reasonable to expect that the proposed M1 and M2 phases might also be synthesized and observed under certain conditions like high-temperature or low-temperature, high-pressure, films, nanometer sized precipitates in aluminum alloys, etc. From Table 2, it can be concluded that both the M1 and M2 phase is mechanically stable as the independent elastic constants of M1 and M2 are all positive and satisfy the above criteria. It can also be found that the C11 values of the M1 and M2 phase are much smaller than those of the (θ, θ', Ω)-Al2Cu phases, indicating that M1 and M2 are much easier to compress along the [100] directions.
In order to investigate the dynamical stability of the proposed M1 and M2 phases, their phonon dispersions were calculated by the finite displacement method, as shown in the Figure 5b. We can clearly see that there are no imaginary frequencies in the phonon spectrum, suggesting both M1 and M2 phases are dynamically stable. As all Al2Cu phases studied in the present work could be considered to be a special solution of the pseudo Al2Cu phase and the (θ, θ', Ω)-Al2Cu phases have been observed, it is reasonable to expect that the proposed M1 and M2 phases might also be synthesized and observed under certain conditions like high-temperature or low-temperature, highpressure, films, nanometer sized precipitates in aluminum alloys, etc. Considering the present assumptions might stimulate further experimental work, the electronic properties of the newly proposed M1 and M2 phases were also calculated including the band structure and density of states. As seen in Figure 6a,b, one can see that the energy band of both phases crossed the Fermi surface, indicating that they are still metallic. The density of states of both the M1 and M2 phases were quite similar, except that the density of states (DOS) at the Fermi level of the M2 was much higher than that of the M1 phase, as it contained more atoms. Their DOS could be divided into two regions-the one shown from −6 to −2 eV is mainly contributed by the Cu d states while the remaining region is mainly contributed by the Al s and p states. Considering the present assumptions might stimulate further experimental work, the electronic properties of the newly proposed M1 and M2 phases were also calculated including the band structure and density of states. As seen in Figure 6a,b, one can see that the energy band of both phases crossed the Fermi surface, indicating that they are still metallic. The density of states of both the M1 and M2 phases were quite similar, except that the density of states (DOS) at the Fermi level of the M2 was much higher than that of the M1 phase, as it contained more atoms. Their DOS could be divided into two regions-the one shown from −6 to −2 eV is mainly contributed by the Cu d states while the remaining region is mainly contributed by the Al s and p states. Metals 2019, 9, x FOR PEER REVIEW 9 of 10

Conclusions
In summary, we have clarified why the θ-Al2Cu phase was incorrectly indexed and was refined to be the Owen phase during processing the single crystal X-ray diffraction datasets for twins of Al2Cu sample. A pseudo Al2Cu phase has been proposed while discriminating the diffraction information of two Al2Cu phase single crystal domains, which could be considered as the average structure of the θ-and Ω-Al2Cu phase, while the Owen phase could be considered to be the average structure of the pseudo Al2Cu phase. It was confirmed that all existing Al2Cu phases could be reconstructed by adjusting the packing sequences of two Al atomic net planes, encoded in the pseudo Al2Cu phase. Furthermore, two potential Al2Cu phases have been built-up by rearranging the packing sequences of the A/B layers of Al atoms. First-principles calculations showed that both phases are mechanically and dynamically stable. However, both phases are metastable according to the calculated enthalpy of formation values, implying that they can be observed only under certain favorable conditions like high-temperature or low-temperature, high-pressure, films, nanometer sized precipitates in aluminum alloys, etc. Band structures and density of states showed that both proposed phases are also metallic.

Supplementary Materials:
The following are available online at www.mdpi.com/xxx/s1, Figure S1: The structural model of the pseudo Al2Cu phase, Figure S2: Projected simulated single crystal diffraction patterns of all existing and potential phases along [100], [010] and [001] directions, Table S1: Crystal data, data collection and structure refinement details of the pseudo Al2Cu phase, Table S2: Crystallographic information of all existing Al2Cu phases (the Owen-, θ-, θ'-and Ω phase) and two proposed potential Al2Cu phases (M1 and M2 phase) corresponding to the available cif files.

Conclusions
In summary, we have clarified why the θ-Al 2 Cu phase was incorrectly indexed and was refined to be the Owen phase during processing the single crystal X-ray diffraction datasets for twins of Al 2 Cu sample. A pseudo Al 2 Cu phase has been proposed while discriminating the diffraction information of two Al 2 Cu phase single crystal domains, which could be considered as the average structure of the θand Ω-Al 2 Cu phase, while the Owen phase could be considered to be the average structure of the pseudo Al 2 Cu phase. It was confirmed that all existing Al 2 Cu phases could be reconstructed by adjusting the packing sequences of two Al atomic net planes, encoded in the pseudo Al 2 Cu phase. Furthermore, two potential Al 2 Cu phases have been built-up by rearranging the packing sequences of the A/B layers of Al atoms. First-principles calculations showed that both phases are mechanically and dynamically stable. However, both phases are metastable according to the calculated enthalpy of formation values, implying that they can be observed only under certain favorable conditions like high-temperature or low-temperature, high-pressure, films, nanometer sized precipitates in aluminum alloys, etc. Band structures and density of states showed that both proposed phases are also metallic.

Supplementary Materials:
The following are available online at http://www.mdpi.com/2075-4701/9/10/1037/s1, Figure S1: The structural model of the pseudo Al2Cu phase, Figure S2: Projected simulated single crystal diffraction patterns of all existing and potential phases along [100], [010] and [001] directions, Table S1: Crystal data, data collection and structure refinement details of the pseudo Al2Cu phase, Table S2: Crystallographic information of all existing Al2Cu phases (the Owen-, θ-, θ'and Ω phase) and two proposed potential Al2Cu phases (M1 and M2 phase) corresponding to the available cif files.