Engineering Papers⌕ Search

SEARCH · Engineering Papers

Results for “Al-Cu-Mg”

Search indexed NASA NTRS and DOE OSTI research on propulsion, heat transfer, battery materials and energy systems. Follow report and document links to the original sources.

Quote a phrase for an exact phrase match. Source license links do not imply unrestricted reuse.

An evaluation of the benefits of utilizing rapid solidification for development of 2XXX (Al-Cu-Mg) alloys

The advantages of rapid solidification processing over ingot metallurgy processing in the development of 2XXX aluminum alloy compositions were evaluated using a similarly processed ingot metallurgy (IM) control alloy. The powder metallurgy (PM) alloy extrusions showed a reduced age-hardening response in comparison with similar IM compositions, with higher tensile properties for naturally aged extrusions but lower properties for artificially aged ones. However, the tensile properties of naturally and artificially aged PM alloy extrusions based on a version of IM 2034 alloy, but containing 0.6 weight percent zirconium, were comparable to those of the IM control extrusions and had significantly superior combinations of strength and toughness. The tensile properties of this PM alloy showed even greater advantage in 6.4-mm (0.25-in.) and 1.8-mm (0.070-in.) plate and sheet, the yield strength being about 68 MPa (10 ksi) greater than reported values for the IM 2034 alloy sheet. An artificially aged PM alloy based on 2219 alloy also showed a strength and strength-toughness combination comparable to those of the PM Al-Cu-Mg-Zr alloy, substantially outperforming the IM 2219 alloy. These results show that rapid solidification offers the flexibility needed to modify conventional IM compositions to produce new alloy compositions with superior mechanical properties.

Paris, H. G.↗

Dispersion strengthening of precipitation hardened Al-Cu-Mg alloys prepared by rapid solidification and mechanical alloying

Several Al-4Cu-1Mg-1.5Fe-0.75Ce alloys have been processed from either rapidly solidified or mechanically alloyed powder using various vacuum degassing parameters and consolidation techniques. Strengthening by the fine subgrains, grains, and the dispersoids individually or in combination is more effective when the alloys contain shearable precipitates; consequently, the strength of the alloys is higher in the naturally aged rather than the artificially aged condition. The strengths of the mechanically alloyed variants are greater than those produced from prealloyed powder. Properties and microstructural features of these dispersion strengthened alloys are discussed in regards to their processing histories.

Gilman, P. S.↗

Solution chemistry effects on the stress corrosion cracking behavior of alloy 2090 (Al-Li-Cu) and alloy 2024 (Al-Cu-Mg)

The SCC initiation behavior of alloys 2090 and 2024 is examined in various NaCl-based environments. The pre-exposure and bulk/local solution chemistry effects discovered by Holroyd et al. (1986) are investigated, with emphasis on the effect of bulk solution chemistries and atmospheric CO2 on the occluded cell environment and the role of the occluded environment in the crack initiation and early-stage propagation processes. It was found that constant immersion in NaCl does not promote SCC in alloy 2090 or alloy 2024. Upon removal from NaCl, SCC is quickly facilitated, but only in the presence of atmospheric CO2. The need for CO2 is attributed to an increase in carbonate concentrations, eventually allowing passivation of blunted fissures by precipitation of Li2CO3. It is inferred that any effects due to aging are small in magnitude, relative to the effects of subtle changes in the bulk/local solution chemistries.

Moran, James P.↗

Characterization of Al-Cu-Mg-Ag Alloy RX226-T8 Plate

Aluminum-copper-magnesium-silver (Al-Cu-Mg-Ag) alloys that were developed for thermal stability also offer attractive ambient temperature strength-toughness combinations, and therefore, can be considered for a broad range of airframe structural applications. The current study evaluated Al-Cu-Mg-Ag alloy RX226-T8 in plate gages and compared performance with sheet gage alloys of similar composition. Uniaxial tensile properties, plane strain initiation fracture toughness, and plane stress tearing resistance of RX226-T8 were examined at ambient temperature as a function of orientation and thickness location in the plate. Properties were measured near the surface and at the mid-plane of the plate. Tensile strengths were essentially isotropic, with variations in yield and ultimate tensile strengths of less than 2% as a function of orientation and through-thickness location. However, ductility varied by more than 15% with orientation. Fracture toughness was generally higher at the mid-plane and greater for the L-T orientation, although the differences were small near the surface of the plate. Metallurgical analysis indicated that the microstructure was primarily recrystallized with weak texture and was uniform through the plate with the exception of a fine-grained layer near the surface of the plate. Scanning electron microscope analysis revealed Al-Cu-Mg second phase particles which varied in composition and were primarily located on grain boundaries parallel to the rolling direction. Fractography of toughness specimens for both plate locations and orientations revealed that fracture occurred predominantly by transgranular microvoid coalescence. Introduction High-strength, low-density Al-Cu-Mg-Ag alloys were initially developed to replace conventional 2000 (Al-Cu-Mg) and 7000 (Al-Zn-Cu-Mg) series aluminum alloys for aircraft structural applications [1]. During the High Speed Civil Transport (HSCT) program, improvements in thermal stability were demonstrated for candidate aircraft wing and fuselage skin materials through the addition of silver to Al-Cu-Mg alloys based on Al 2519 chemistry [2]. Thermal stability of the resulting Al-Cu-Mg-Ag alloys, C415-T8 and C416-T8, was due to co-precipitation of the thermally stable . (AlCu) and ' (Al2Cu) strengthening phases [1-4]. The strength and toughness behavior was investigated for these alloys produced as 0.090-inch thick rolled sheet in the T8 condition and after various thermal exposures. The mechanical properties were shown to be competitive with conventional aircraft alloys, 2519-T8 and 2618-T8 [2]. During the Integral Airframe Structure (IAS) program, advanced aluminum alloys were examined for use in an integrally stiffened airframe structure where the skin and stiffeners would be machined from plate and extruded frames would be mechanically attached (see Figure 1) [5]. Advantages of integrally stiffened structure include reduced part count, and reduced assembly times compared to conventional built-up airframe structure. The near-surface properties of a thick plate are of significance for a machined integrally stiffened airframe structure since this represents the skin location. Properties measured at the mid-plane of the plate are more representative of the stiffener web. RX226 was developed to exploit strength-toughness improvements and thermal stability benefits of Al-Cu-Mg-Ag alloys in plate gages. This study evaluated the microstructure and properties of three gages of plate produced in the T8 condition.

Lach, Cynthia L.↗

Thermodynamic Modeling of the Al-Ce-Cu-Mg-Si System and Its Application to Aluminum-Cerium Alloy Design

Recently discovered AlCe alloys have shown promise in a number of applications, but the propensity of Ce to react with Al and other alloying elements can complicate the phase equilibria and design approach. To solve this, the CALPHAD method is used to explore an alloy within the quinary Al-Ce-Cu-Mg-Si system by developing a thermodynamic database with self-consistent parameters. The database includes a description of all 10 binary systems and 8 ternary systems consisting of: (i) 6 Al-containing ternaries (Al-Ce-Cu, Al-Ce-Mg, Al-Ce-Si, Al-Cu-Mg, Al-Cu-Si and Al-Mg-Si); and (ii) 2 additional ternaries that include Mg and Si (i.e., Ce-Mg-Si and Cu-Mg-Si). The thermodynamic description for the Al-Ce-Mg and Al-Mg-Si systems were reassessed to ensure consistency with the binary systems and the Ce-Mg-Si system is presented for the first time and compared to theoretical data from DFT (Density Functional Theory). In addition to the ternary interactions, the quaternary compound Al3Cu2Mg9Si7 and solid solution extending from the ternary Al2CuMg phase (Al,Si)2CuMg are incorporated. The CALPHAD method is employed and leveraged through the use of a Materials Design Simulator (MDS) to accelerate the design of novel aluminum-cerium-based alloys. The combination of a CALPHAD-based framework with experimental efforts and industrial insight permits the development of three new Al-Ce alloys: Al-3.5Ce-0.4Mg-7Si (Ce-modified A356), Al-5Ce-1Cu-0.5Mg-10Si and Al-19Ce-0.9Mg-1.1Si.

36 MATERIALS SCIENCE↗

The effect of water vapor on fatigue crack Growth in 7475-t651 aluminum alloy plate

The effects of water vapor on fatigue crack growth in 7475-T651 aluminum alloy plate at frequencies of 1 Hz and 10 Hz were investigated. Twenty-five mm thick compact specimens were subjected to constant amplitude fatigue testing at a load ratio of 0.2. Fatigue crack growth rates were calculated from effective crack lengths determined using a compliance method. Tests were conducted in hard vacuum and at water vapor partial pressures ranging from 94 Pa to 3.8 kPa. Fatigue crack growth rates were frequency insensitive under all environment conditions tested. For constant stress intensity factor ranges crack growth rate transitions occurred at low and high water vapor pressures. Crack growth rates at intermediate pressures were relatively constant and showed reasonable agreement with published data for two Al-Cu-Mg alloys. The existence of two crack growth rate transitions suggests either a change in rate controlling kinetics or a change in corrosion fatigue mechanism as a function of water vapor pressure. Reduced residual deformation and transverse cracking specimens tested in water vapor versus vacuum may be evidence of embrittlement within the plastic zone due to environmental interaction.

Dicus, D. L.↗

Effect of water vapor on fatigue crack growth in 7475-T651 aluminum alloy plate

The effects of water vapor on fatigue crack growth in 7475-T651 aluminum alloy plate at frequencies of 1 Hz and 10 Hz were investigated. Twenty-five mm thick compact specimens were subjected to constant amplitude fatigue testing at a load ratio of 0.2. Fatigue crack growth rates were calculated from effective crack lengths determined using a compliance method. Tests were conducted in hard vacuum and at water vapor partial pressures ranging from 94 Pa to 3.8 kPa. Fatigue crack growth rates were frequency insensitive under all environment conditions tested. For constant stress intensity factor ranges crack growth rate transitions occurred at low and high water vapor pressures. Crack growth rates at intermediate pressures were relatively constant and showed reasonable agreement with published data for two Al-Cu-Mg alloys. The existence of two crack growth rate transitions suggests either a change in rate controlling kinetics or a change in corrosion fatigue mechanism as a function of water vapor pressure. Reduced residual deformation and transverse cracking specimens tested in water vapor versus vacuum may be evidence of embrittlement within the plastic zone due to environmental interaction.

Dicus, D. L.↗

Development and characterization of Powder Metallurgy (PM) 2XXX series Al alloy products and Metal Matrix Composite (MMC) 2XXX Al/SiC materials for high temperature aircraft structural applications

The results of a series of material studies performed by the Lockheed Aeronautical Systems Company over the time period from 1980 to 1991 are discussed. The technical objective of these evaluations was to develop and characterize advanced aluminum alloy materials with temperature capabilities extending to 350 F. An overview is given of the first five alloy development efforts under this contract. Prior work conducted during the first five modifications of the alloy development program are listed. Recent developments based on the addition of high Zr levels to an optimum Al-Cu-Mg alloy composition by powder metallurgy processing are discussed. Both reinforced and SiC or B4C ceramic reinforced alloys were explored to achieve specific target goals for high temperature aluminum alloy applications.

Chellman, D. J.↗

Metals Technology for Aerospace Applications in 2020: Development of High Temperature Aluminum Alloys For Aerospace Applications

The role of trace additions on the nucleation and stability of the primary strengthening phase, omega, is of paramount importance for the enhancement of mechanical properties for moderate temperature application of Al-Cu-Mg-(Ag) alloys. In order to better understand the competition for solute, which governs the microstructural evolution of these alloys, a series of Al-Cu-Mg-Si quaternary alloys were prepared to investigate the role of trace Si additions on the nucleation of the omega phase. Si additions were found to quell omega nucleation in conjunction with the enhanced matrix precipitation of competing phases. These initial results indicate that it is necessary to overcome a critical Mg/Si ratio for omega precipitation, rather than a particular Si content.

Dicus, Dennis↗

Effect of Thermal Exposure on the Tensile Properties of Aluminum Alloys for Elevated Temperature Service

Tensile properties were evaluated for four aluminum alloys that are candidates for airframe applications on high speed transport aircraft. These alloys included the Al-Cu-Mg-Ag alloys C415 and C416 and the Al-Cu-Li-Mg-Ag alloys RX818 and ML377. The Al-Cu-Mg alloys CM001, which was used on the Concorde SST, and 1143, which was modified from the alloy used on the TU144 Russian supersonic aircraft, were tested for comparison. The alloys were subjected to thermal exposure at 200 F, 225 F and 275 F for times up to 30,000 hours. Tensile tests were performed on thermally-exposed and as-received material at -65 F, room temperature, 200 F, 225 F and 275 F. All four candidate alloys showed significant tensile property improvements over CM001 and 1143. Room temperature yield strengths of the candidate alloys were at least 20% greater than for CM001 and 1143, for both the as-received and thermally-exposed conditions. The strength levels of alloy RX818 were the highest of all materials investigated, and were 5-10% higher than for ML377, C415 and C416 for the as-received condition and after 5,000 hours thermal exposure. RX818 was removed from this study after 5,000 hours exposure due to poor fracture toughness performance observed in a parallel study. After 30,000 hours exposure at 200 F and 225 F, the alloys C415, C416 and ML377 showed minor decreases in yield strength, tensile strength and elongation when compared to the as-received properties. Reductions in tensile strength from the as-received values were up to 25% for alloys C415, C416 and ML377 after 15,000 hours exposure at 275 F.

Edahl, Robert A., Jr.↗

Al-Li Alloy 1441 for Fuselage Applications

A cooperative investigation was conducted to evaluate Al-Cu-Mg-Li alloy 1441 for long service life fuselage applications. Alloy 1441 is currently being used for fuselage applications on the Russian Be-103 amphibious aircraft, and is expected to be used for fuselage skin on a new Tupolev business class aircraft. Alloy 1441 is cold-rollable and has several attributes that make it attractive for fuselage skin applications. These attributes include lower density and higher specific modulus with similar strength as compared to conventional Al-Cu-Mg alloys. Cold-rolled 1441 Al-Li sheet specimens were tested at NASA Langley Research Center (LaRC) and at the All-Russia Institute of Aviation Materials (VIAM) in Russia to evaluate tensile properties, fracture toughness, impact resistance, fatigue life and fatigue crack growth rate. In addition, fuselage panels were fabricated by Tupolev Design Bureau (TDB) using 1441 skins and Al-Zn-Mg-Cu alloy stiffeners. The panels were subjected to cyclic pressurization fatigue tests at TDB and at LaRC to simulate fuselage pressurization/depressurization during aircraft service. This paper discusses the results from this investigation.

Bird, R. K.↗

Materials Data on Mg2Al5Cu6 by Materials Project

Al5Cu6Mg2 crystallizes in the cubic Pm-3 space group. The structure is three-dimensional. Mg is bonded in a 12-coordinate geometry to one Mg, six equivalent Cu, and eight Al atoms. The Mg–Mg bond length is 2.96 Å. There are two shorter (2.84 Å) and four longer (2.85 Å) Mg–Cu bond lengths. There are a spread of Mg–Al bond distances ranging from 2.99–3.13 Å. There are two inequivalent Cu sites. In the first Cu site, Cu is bonded in a 6-coordinate geometry to six Al atoms. There are four shorter (2.55 Å) and two longer (2.63 Å) Cu–Al bond lengths. In the second Cu site, Cu is bonded in a 12-coordinate geometry to three equivalent Mg, five equivalent Cu, and four Al atoms. There are four shorter (2.63 Å) and one longer (2.73 Å) Cu–Cu bond lengths. There are a spread of Cu–Al bond distances ranging from 2.45–2.53 Å. There are three inequivalent Al sites. In the first Al site, Al is bonded in a 4-coordinate geometry to four equivalent Mg and four Cu atoms. In the second Al site, Al is bonded in a 12-coordinate geometry to three equivalent Mg and six Cu atoms. In the third Al site, Al is bonded in a cuboctahedral geometry to twelve equivalent Cu atoms.

36 MATERIALS SCIENCE↗

Materials Data on MgAl2Cu by Materials Project

Al2CuMg crystallizes in the orthorhombic Cmcm space group. The structure is three-dimensional. Mg is bonded in a 1-coordinate geometry to three equivalent Cu and ten equivalent Al atoms. There are one shorter (2.65 Å) and two longer (2.82 Å) Mg–Cu bond lengths. There are six shorter (3.04 Å) and four longer (3.12 Å) Mg–Al bond lengths. Cu is bonded in a 9-coordinate geometry to three equivalent Mg and six equivalent Al atoms. There are two shorter (2.51 Å) and four longer (2.54 Å) Cu–Al bond lengths. Al is bonded in a 3-coordinate geometry to five equivalent Mg and three equivalent Cu atoms.

36 MATERIALS SCIENCE↗

Materials Data on Mg3(AlCu2)2 by Materials Project

Mg3(Cu2Al)2 crystallizes in the triclinic P-1 space group. The structure is three-dimensional. there are three inequivalent Mg sites. In the first Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, eight Cu, and four Al atoms. There are a spread of Mg–Mg bond distances ranging from 3.05–3.13 Å. There are a spread of Mg–Cu bond distances ranging from 2.92–2.99 Å. There are a spread of Mg–Al bond distances ranging from 2.98–3.02 Å. In the second Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, seven Cu, and five Al atoms. The Mg–Mg bond length is 3.17 Å. There are a spread of Mg–Cu bond distances ranging from 2.94–2.99 Å. There are a spread of Mg–Al bond distances ranging from 2.95–3.01 Å. In the third Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. There are one shorter (3.05 Å) and two longer (3.12 Å) Mg–Mg bond lengths. There are a spread of Mg–Cu bond distances ranging from 2.93–2.99 Å. There are one shorter (2.98 Å) and two longer (3.00 Å) Mg–Al bond lengths. There are five inequivalent Cu sites. In the first Cu site, Cu is bonded to six Mg, four Cu, and two equivalent Al atoms to form CuMg6Al2Cu4 cuboctahedra that share corners with five AlMg6Al2Cu4 cuboctahedra, corners with thirteen CuMg6Al2Cu4 cuboctahedra, edges with two equivalent AlMg6Al2Cu4 cuboctahedra, edges with four equivalent CuMg6Al2Cu4 cuboctahedra, faces with six AlMg6Al2Cu4 cuboctahedra, and faces with twelve CuMg6Al3Cu3 cuboctahedra. All Cu–Cu bond lengths are 2.55 Å. Both Cu–Al bond lengths are 2.53 Å. In the second Cu site, Cu is bonded to six Mg, three Cu, and three Al atoms to form distorted CuMg6Al3Cu3 cuboctahedra that share corners with six AlMg6Al2Cu4 cuboctahedra, corners with twelve CuMg6Al2Cu4 cuboctahedra, edges with six equivalent CuMg6Al3Cu3 cuboctahedra, faces with nine CuMg6Al2Cu4 cuboctahedra, and faces with nine AlMg6Al2Cu4 cuboctahedra. There are one shorter (2.56 Å) and one longer (2.57 Å) Cu–Cu bond lengths. There are a spread of Cu–Al bond distances ranging from 2.51–2.55 Å. In the third Cu site, Cu is bonded to six equivalent Mg, four Cu, and two equivalent Al atoms to form distorted CuMg6Al2Cu4 cuboctahedra that share corners with four equivalent AlMg6Cu6 cuboctahedra, corners with fourteen CuMg6Al2Cu4 cuboctahedra, edges with six equivalent CuMg6Al2Cu4 cuboctahedra, faces with six equivalent AlMg6Cu6 cuboctahedra, and faces with twelve CuMg6Al2Cu4 cuboctahedra. Both Cu–Cu bond lengths are 2.57 Å. Both Cu–Al bond lengths are 2.51 Å. In the fourth Cu site, Cu is bonded to six Mg, two equivalent Cu, and four Al atoms to form distorted CuMg6Al4Cu2 cuboctahedra that share corners with four equivalent AlMg6Cu6 cuboctahedra, corners with fourteen CuMg6Al2Cu4 cuboctahedra, edges with six CuMg6Al2Cu4 cuboctahedra, faces with eight CuMg6Al2Cu4 cuboctahedra, and faces with ten AlMg6Al2Cu4 cuboctahedra. There are two shorter (2.51 Å) and two longer (2.55 Å) Cu–Al bond lengths. In the fifth Cu site, Cu is bonded to six Mg, four Cu, and two equivalent Al atoms to form distorted CuMg6Al2Cu4 cuboctahedra that share corners with six AlMg6Al2Cu4 cuboctahedra, corners with twelve CuMg6Al2Cu4 cuboctahedra, edges with six CuMg6Al2Cu4 cuboctahedra, faces with seven AlMg6Al2Cu4 cuboctahedra, and faces with eleven CuMg6Al2Cu4 cuboctahedra. Both Cu–Al bond lengths are 2.51 Å. There are three inequivalent Al sites. In the first Al site, Al is bonded to six Mg, four Cu, and two equivalent Al atoms to form distorted AlMg6Al2Cu4 cuboctahedra that share corners with six AlMg6Al2Cu4 cuboctahedra, corners with twelve CuMg6Al2Cu4 cuboctahedra, edges with six AlMg6Al2Cu4 cuboctahedra, faces with four equivalent AlMg6Al2Cu4 cuboctahedra, and faces with fourteen CuMg6Al2Cu4 cuboctahedra. Both Al–Al bond lengths are 2.53 Å. In the second Al site, Al is bonded to six Mg and six Cu atoms to form distorted AlMg6Cu6 cuboctahedra that share corners with eight AlMg6Al2Cu4 cuboctahedra, corners with ten CuMg6Al2Cu4 cuboctahedra, edges with six AlMg6Al2Cu4 cuboctahedra, a faceface with one AlMg6Al2Cu4 cuboctahedra, and faces with seventeen CuMg6Al2Cu4 cuboctahedra. In the third Al site, Al is bonded to six Mg, four Cu, and two equivalent Al atoms to form AlMg6Al2Cu4 cuboctahedra that share corners with eight AlMg6Cu6 cuboctahedra, corners with ten CuMg6Al2Cu4 cuboctahedra, edges with two equivalent AlMg6Al2Cu4 cuboctahedra, edges with four equivalent CuMg6Al2Cu4 cuboctahedra, faces with six AlMg6Al2Cu4 cuboctahedra, and faces with twelve CuMg6Al3Cu3 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on MgAlCu by Materials Project

MgCuAl crystallizes in the trigonal R-3m space group. The structure is three-dimensional. there are seven inequivalent Mg sites. In the first Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, six Cu, and six equivalent Al atoms. There are three shorter (3.19 Å) and one longer (3.26 Å) Mg–Mg bond lengths. There are three shorter (2.84 Å) and three longer (3.05 Å) Mg–Cu bond lengths. All Mg–Al bond lengths are 3.13 Å. In the second Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. The Mg–Mg bond length is 2.86 Å. There are six shorter (2.99 Å) and three longer (3.10 Å) Mg–Cu bond lengths. All Mg–Al bond lengths are 3.07 Å. In the third Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. There are one shorter (2.86 Å) and three longer (3.19 Å) Mg–Mg bond lengths. There are six shorter (2.99 Å) and three longer (3.10 Å) Mg–Cu bond lengths. All Mg–Al bond lengths are 3.07 Å. In the fourth Mg site, Mg is bonded in a 12-coordinate geometry to one Mg, three equivalent Cu, and nine equivalent Al atoms. All Mg–Cu bond lengths are 3.08 Å. There are three shorter (3.04 Å) and six longer (3.06 Å) Mg–Al bond lengths. In the fifth Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. There are one shorter (2.86 Å) and three longer (3.19 Å) Mg–Mg bond lengths. There are six shorter (2.99 Å) and three longer (3.10 Å) Mg–Cu bond lengths. All Mg–Al bond lengths are 3.07 Å. In the sixth Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. All Mg–Mg bond lengths are 3.19 Å. There are six shorter (2.99 Å) and three longer (3.10 Å) Mg–Cu bond lengths. All Mg–Al bond lengths are 3.07 Å. In the seventh Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. All Mg–Mg bond lengths are 3.19 Å. There are six shorter (2.99 Å) and three longer (3.10 Å) Mg–Cu bond lengths. All Mg–Al bond lengths are 3.07 Å. There are three inequivalent Cu sites. In the first Cu site, Cu is bonded to six Mg, three equivalent Cu, and three equivalent Al atoms to form CuMg6Al3Cu3 cuboctahedra that share corners with six equivalent AlMg6Al4Cu2 cuboctahedra, corners with nine CuMg6Al3Cu3 cuboctahedra, edges with six equivalent CuMg6Al3Cu3 cuboctahedra, faces with nine equivalent AlMg6Al4Cu2 cuboctahedra, and faces with ten CuMg6Cu6 cuboctahedra. All Cu–Cu bond lengths are 2.55 Å. All Cu–Al bond lengths are 2.55 Å. In the second Cu site, Cu is bonded to six Mg and six Cu atoms to form CuMg6Cu6 cuboctahedra that share corners with eight CuMg6Al3Cu3 cuboctahedra, corners with ten equivalent AlMg6Al4Cu2 cuboctahedra, edges with two equivalent CuMg6Cu6 cuboctahedra, edges with four equivalent AlMg6Al4Cu2 cuboctahedra, faces with four equivalent AlMg6Al4Cu2 cuboctahedra, and faces with fourteen CuMg6Al3Cu3 cuboctahedra. All Cu–Cu bond lengths are 2.63 Å. In the third Cu site, Cu is bonded to six equivalent Mg and six equivalent Al atoms to form CuMg6Al6 cuboctahedra that share corners with twelve equivalent AlMg6Al4Cu2 cuboctahedra, edges with six equivalent CuMg6Al6 cuboctahedra, faces with two equivalent CuMg6Al3Cu3 cuboctahedra, and faces with eighteen equivalent AlMg6Al4Cu2 cuboctahedra. All Cu–Al bond lengths are 2.60 Å. Al is bonded to six Mg, two Cu, and four equivalent Al atoms to form distorted AlMg6Al4Cu2 cuboctahedra that share corners with nine CuMg6Al3Cu3 cuboctahedra, corners with nine equivalent AlMg6Al4Cu2 cuboctahedra, edges with two equivalent CuMg6Cu6 cuboctahedra, edges with four equivalent AlMg6Al4Cu2 cuboctahedra, faces with eight CuMg6Al3Cu3 cuboctahedra, and faces with ten equivalent AlMg6Al4Cu2 cuboctahedra. There are two shorter (2.61 Å) and two longer (2.64 Å) Al–Al bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on Mg3(AlCu2)2 by Materials Project

Mg3(Cu2Al)2 crystallizes in the monoclinic C2/m space group. The structure is three-dimensional. there are three inequivalent Mg sites. In the first Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, nine Cu, and three equivalent Al atoms. There are a spread of Mg–Mg bond distances ranging from 3.02–3.12 Å. There are a spread of Mg–Cu bond distances ranging from 2.93–2.97 Å. There are one shorter (2.98 Å) and two longer (2.99 Å) Mg–Al bond lengths. In the second Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, eight Cu, and four Al atoms. There are one shorter (3.11 Å) and two longer (3.12 Å) Mg–Mg bond lengths. There are a spread of Mg–Cu bond distances ranging from 2.94–2.99 Å. There are a spread of Mg–Al bond distances ranging from 2.95–3.04 Å. In the third Mg site, Mg is bonded in a 12-coordinate geometry to four Mg, seven Cu, and five Al atoms. The Mg–Mg bond length is 3.12 Å. There are a spread of Mg–Cu bond distances ranging from 2.94–3.00 Å. There are a spread of Mg–Al bond distances ranging from 2.93–3.02 Å. There are three inequivalent Cu sites. In the first Cu site, Cu is bonded to six Mg, four equivalent Cu, and two Al atoms to form distorted CuMg6Al2Cu4 cuboctahedra that share corners with five AlMg6AlCu5 cuboctahedra, corners with thirteen CuMg6Al2Cu4 cuboctahedra, edges with two equivalent AlMg6Al2Cu4 cuboctahedra, edges with four equivalent CuMg6Al2Cu4 cuboctahedra, faces with six AlMg6AlCu5 cuboctahedra, and faces with twelve CuMg6Al4Cu2 cuboctahedra. There are two shorter (2.53 Å) and two longer (2.56 Å) Cu–Cu bond lengths. There are one shorter (2.46 Å) and one longer (2.50 Å) Cu–Al bond lengths. In the second Cu site, Cu is bonded to six Mg, two equivalent Cu, and four Al atoms to form CuMg6Al4Cu2 cuboctahedra that share corners with four equivalent AlMg6AlCu5 cuboctahedra, corners with fourteen CuMg6Al2Cu4 cuboctahedra, edges with six CuMg6Al4Cu2 cuboctahedra, faces with eight CuMg6Al2Cu4 cuboctahedra, and faces with ten AlMg6AlCu5 cuboctahedra. Both Cu–Cu bond lengths are 2.55 Å. There are two shorter (2.54 Å) and two longer (2.55 Å) Cu–Al bond lengths. In the third Cu site, Cu is bonded to six Mg, four Cu, and two Al atoms to form distorted CuMg6Al2Cu4 cuboctahedra that share corners with six AlMg6AlCu5 cuboctahedra, corners with twelve CuMg6Al2Cu4 cuboctahedra, edges with six CuMg6Al4Cu2 cuboctahedra, faces with seven AlMg6AlCu5 cuboctahedra, and faces with eleven CuMg6Al2Cu4 cuboctahedra. Both Cu–Cu bond lengths are 2.55 Å. Both Cu–Al bond lengths are 2.50 Å. There are three inequivalent Al sites. In the first Al site, Al is bonded to six Mg, five Cu, and one Al atom to form distorted AlMg6AlCu5 cuboctahedra that share corners with eight AlMg6AlCu5 cuboctahedra, corners with ten CuMg6Al2Cu4 cuboctahedra, edges with six equivalent AlMg6AlCu5 cuboctahedra, faces with three equivalent AlMg6Al2Cu4 cuboctahedra, and faces with fifteen CuMg6Al2Cu4 cuboctahedra. The Al–Al bond length is 2.61 Å. In the second Al site, Al is bonded to six equivalent Mg and six Cu atoms to form distorted AlMg6Cu6 cuboctahedra that share corners with six equivalent AlMg6AlCu5 cuboctahedra, corners with twelve CuMg6Al2Cu4 cuboctahedra, edges with six equivalent AlMg6Cu6 cuboctahedra, and faces with eighteen CuMg6Al2Cu4 cuboctahedra. In the third Al site, Al is bonded to six Mg, four equivalent Cu, and two equivalent Al atoms to form distorted AlMg6Al2Cu4 cuboctahedra that share corners with eight AlMg6AlCu5 cuboctahedra, corners with ten CuMg6Al2Cu4 cuboctahedra, edges with two equivalent AlMg6Al2Cu4 cuboctahedra, edges with four equivalent CuMg6Al2Cu4 cuboctahedra, faces with six equivalent AlMg6AlCu5 cuboctahedra, and faces with twelve CuMg6Al4Cu2 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on Mg11(Al2Cu)6 by Materials Project

Mg11(CuAl2)6 crystallizes in the cubic Fd-3m space group. The structure is three-dimensional. there are five inequivalent Mg sites. In the first Mg site, Mg is bonded in a 12-coordinate geometry to four equivalent Mg and twelve equivalent Al atoms. All Mg–Mg bond lengths are 2.93 Å. All Mg–Al bond lengths are 3.19 Å. In the second Mg site, Mg is bonded in a 10-coordinate geometry to four equivalent Cu and six Al atoms. There are two shorter (2.91 Å) and two longer (2.98 Å) Mg–Cu bond lengths. There are two shorter (2.99 Å) and four longer (3.13 Å) Mg–Al bond lengths. In the third Mg site, Mg is bonded in a 3-coordinate geometry to one Mg, three equivalent Cu, and six equivalent Al atoms. The Mg–Mg bond length is 3.26 Å. All Mg–Cu bond lengths are 2.76 Å. All Mg–Al bond lengths are 3.12 Å. In the fourth Mg site, Mg is bonded in a 12-coordinate geometry to four equivalent Mg and twelve equivalent Al atoms. All Mg–Al bond lengths are 3.12 Å. In the fifth Mg site, Mg is bonded in a 8-coordinate geometry to two Mg and six equivalent Al atoms. The Mg–Mg bond length is 2.84 Å. All Mg–Al bond lengths are 3.00 Å. Cu is bonded in a 9-coordinate geometry to five Mg and four Al atoms. There are a spread of Cu–Al bond distances ranging from 2.43–2.56 Å. There are two inequivalent Al sites. In the first Al site, Al is bonded in a 11-coordinate geometry to five Mg, three equivalent Cu, and three equivalent Al atoms. There are one shorter (2.65 Å) and two longer (2.66 Å) Al–Al bond lengths. In the second Al site, Al is bonded in a distorted single-bond geometry to seven Mg and one Cu atom.

36 MATERIALS SCIENCE↗