# Characterization of Precipitation in Al-Li Alloy AA2195 by means of Atom Probe Tomography and Transmission Electron Microscopy

Authors: Muna Khushaim; Torben Boll; Judith Seibert; Ferdinand Haider; Talaat Al-Kassab
Journal: Advances in Condensed Matter Physics
 (2015)

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## Abstract

The microstructure of the commercial alloy AA2195 was investigated on the nanoscale after conducting T8 tempering. This particular thermomechanical treatment of the specimen resulted in the formation of platelet-shapedT1Al2CuLi/θ′Al2Cu precipitates within the Al matrix. The electrochemically prepared samples were analyzed by scanning transmission electron microscopy and atom probe tomography for chemical mapping. The θ′ platelets, which are less than 2 nm thick, have the stoichiometric composition consistent with the expected Al2Cu equilibrium composition. Additionally, the Li distribution inside the θ′ platelets was found to equal the same value as in the matrix. The equally thin T1  platelet deviates from the formula (Al2CuLi) in its stoichiometry and shows Mg enrichment inside the platelet without any indication of a higher segregation level at the precipitate/matrix interface. The deviation from the (Al2CuLi) stoichiometry cannot be simply interpreted as a consequence of artifacts when measuring the Cu and Li concentrations inside the T1 platelet. The results show rather a strong hint for a true lower Li and Cu contents, hence supporting reasonably the hypothesis  that the real chemical composition for the thin T1  platelet in the T8 tempering condition differs from the equilibrium composition of the thermodynamic  stable bulk phase.


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## Body

## 1. Introduction

One of the upcoming materials used for the structural components of aircrafts is aluminum-lithium alloys. This class of alloys is commonly selected because it exhibits an enhanced strength/weight ratio that makes it an attractive material for weight critical applications. A series of Al-Li-Cu alloys with minor amount of Mg, Ag, and Zr known as Weldalite that exhibit desirable combinations of strength and toughness have been developed in recent years [1].The current study focuses on one member of the Weldalite family, namely, the commercial AA2195 alloy, which is considered as a promising candidate for aerospace applications due to its high strength, high modulus, low density, good corrosion resistance, excellent fatigue properties, and fracture toughness at cryogenic temperatures [2]. The alloy exhibits superior mechanical properties after processing a thermomechanical treatment termed “T8.” This treatment begins with a solution treatment in a single phase region, followed by quenching to obtain a supersaturated solid solution. Plastic deformation (cold working) is then applied to the samples. The final stage is an artificial aging far below the temperature of the strengthening phase solvus line [3]. It has been shown that alloy conducting T8 tempering has a combination of excellent fracture toughness (~60 MPam) and an improved strength (~550 MPa) [4]. The presence of various microalloying elements at a variable volume fraction and adequate subsequent treatment causes the precipitation of different possible phases within the Weldalite family such as T1Al2CuLi, θ′Al2Cu, β′Al3Zr, and δ′Al3Li. The T1 phase has a plate-shaped morphology lying on {111} planes and is the primary phase responsible for the strengthening effect in AA2195 at temperatures below 533 K [5]. The nucleation of this phase is difficult without the presence of secondary alloying elements such as Mg and Ag, which can offer nucleation sites within the matrix for this phase [6]. The nucleation of the T1 phase also depends on the application of plastic deformation prior to artificial aging [7]. Applying this plastic deformation prior to artificial ageing will increase the number of the nucleation sites for the T1 phase and hence promote a uniform distribution of heterogeneously nucleated T1 precipitates. These precipitates will act as nonshearable obstacles to dislocation motion and promote slip homogenization [4].TheT1 phase coexists with the θ′Al2Cu phase which lies as plates on the {100} matrix planes [8]. This phase is dominant in the early stage of the heat treatment at elevated temperatures 588–644 K [5]. In addition to the T1 and θ′ phases, Zr forms coherent spherical β′Al3Zr precipitates with L12-structure that can already form during the alloying process within the melt. They are designed to control the grain structure and degree of recrystallization after the solidification of the ingot [9]. Finally, the δ′Al3Li is usually reported to precipitate upon quenching from the melt for alloy compositions higher than 5 at.% Li in the matrix [10–12].Atom probe studies have provided a range of information on the different types of precipitates present in Al-Li-Cu alloys. Murayama and Hono [13] reported their observation of Mg clusters at the early stage of aging and the possibility of the segregation of Mg and Ag atoms to the broad interface of the T1 plates. Moreover, Gault et al. [14] studied the early stages of clustering, precipitate interactions, solute segregation at the matrix/precipitate interfaces, and the chemical composition of the different phases.The aim of this study is to characterize the different precipitates that dominate the microstructure of the AA2195 alloy. Since the composition evaluation of subnanometer scale platelet precipitates is extremely difficult, atom probe tomography has been employed to characterize the local chemical composition of the precipitates and to determine the location of the various alloying atoms.


## 2. Material and Methods

The chemical composition of AA2195 is shown in Table1. The table shows the nominal composition for the alloy and the measured composition by inductively coupled plasma optical emission spectrometry (Varian ICP-OES 720-ES). Samples in the form of ingots were obtained in a T8 temper state. Samples on the T8 condition were solution treated for 1 h to 783 K, quenched, stretched to 3%, and subsequently aged to 423 K for 30 h.Table 1
Chemical composition of alloying elements in AA2195.
Alloying element
Cu
Li
Mg
Ag
Zr
Al
Nominal (wt.%)
4
1
0.36
0.28
0.14
94.22
Nominal (at.%)
1.69
3.87
0.39
0.06
0.04
93.95
ICP (at.%)
1.74 ± 0.19
3.67 ± 0.05
0.36 ± 0.01
0.08 ± 0.02
0.04 ± 0.0004
94.11 ± 0.27Vickers microhardness measurements were performed using a load of 0.2 kg applied on the sheet sample. The Vickers hardness number (VHN), which was obtained by averaging ten measurements, was found to be (160±7) HV/1.96 and thus confirms the success of the heat treatment.Small rods (0.3 mm × 0.3 mm × 10 mm) were spark machined from the bulk and then electropolished to a sharp needle-shaped specimen for atom probe tomography (APT) analyses and scanning transmission electron microscopy (STEM). Electropolishing was carried out using a solution of 30 vol.% nitric acid in methanol at temperatures between 253 and 298 K in the range of 5–7 V. The specimens were prepared for transmission electron microscopy (TEM) by standard twin-jet electropolishing using a solution of 30 vol.% nitric acid in methanol at 243 K.STEM images were recorded using a Titan CT with a dedicated APT holder (E.A. Fischione 2025 Tomoholder). TEM analysis was carried out using a Jeol2100F, operated at 200 kV. The APT experiments were performed on both the Cameca laser assisted wide angle tomographic atom probe (LAWATAP) in the voltage mode at temperatures between 25 and 30 K with a pulse fraction between 20% and 22.5% at a vacuum level of10-8 Pa and the Cameca local electrode atom probe (LEAP- 4000HR) in the voltage mode at 22 K and 18% of pulse fraction at 10-8 Pa.The obtained data was visualized using the TAP3D and IVAS software programs provided by Cameca. The compositions of the precipitates were measured quantitatively using the proximity histogram (proxigram) technique [15]. In this methodology, an isoconcentration surface is first defined in the reconstructed volume to delineate the precipitates. Then, starting at the isoconcentration surface, which is the origin of the proxigram, and moving toward the center of precipitates (positive distance), the composition of the precipitate is measured in discrete shells with the shape of isoconcentration surface at fixed intervals. The matrix composition is obtained by starting at the isoconcentration surface and moving into the matrix (negative distance). All proxigrams, in this study, were computed with a 0.1 nm bin size. To increase the statistical accuracy of the composition, bins containing fewer than 50 atoms were eliminated.An isoconcentration surface is the surface that envelops a volume with concentrations higher than the selected concentration of one or more elements. This surface was obtained by sampling the atom probe tomography reconstruction with0.8×0.8×0.8nm3 voxels after applying a delocalization procedure developed by Hellman et al. [16] with smoothing parameters of 1.5 nm for the x and y coordinates and 0.75 nm for the z coordinate.


## 3. Results and Discussion

Several different precipitates were identified in AA2195 and are discussed below.


### 3.1. Electron Microscopy

Conventional TEM bright field images revealed a complex microstructure encompassing different precipitates with platelet and spherical morphologies as shown in Figure1. Precipitates were characterized using an exact [110] zone to detect T1 platelets, θ′ platelets, and spherical precipitates with L12-structure. A schematic of the indexed selected area diffraction pattern (SADP) in the [101] direction is integrated with the bright field-TEM image (Figure 1(a)). This indicates the presence of two variants of T1 precipitate as streaks along the 111 direction in the pattern. The other two variants of this phase produce spots adjacent to 200 positions. The streaks along the 200 direction reveal the presence of one variant of θ′. The superlattice reflections in the diffraction pattern may originate from an L12-ordered structure representing δ′Al3Li and/or β′Al3Zr precipitates. The L12 unit cell is based on the face centered cubic (fcc) unit cell of aluminum. However, the corner atoms are replaced by either Li or Zr, respectively. This means that all 100 directions are superstructure directions. The spherical precipitates are most probably of the β′-type, since the Li composition in the investigated alloy is less than 5 at.%. It is worth noting that, from the diffraction pattern alone, no decision can be achieved whether the precipitates are δ′ or β′ because of the similarity of the lattice constant. Figure 1(b) presents a simulated diffraction pattern matching all spots and streaks in the [101] selected area diffraction pattern.Figure 1
Evolution of the microstructure as observed by TEM. (a) Typical bright field image showing a complex microstructure with theT1, θ′, and β′ precipitates and the corresponding [101] selected area diffraction pattern (SADP). (b) Schematic of a simulated diffraction pattern that assigns the reflections and streaks in the SADP to the corresponding precipitates.
(a)
(b)High angle annular bright field scanning transmission electron microscopy (HAABF) STEM-contrast also revealed the existence of both spherical and platelet precipitates (Figure2). As illustrated in Figure 2, the heterogeneous formation of platelet precipitate can be clearly observed at grain boundaries by imaging the sample from different angles (±75° in steps of 1°). A low angle grain boundary in Figure 2 was identified while rotating the specimen and monitoring the diffraction pattern at various locations within the sample. Moreover, the distribution of platelet precipitates and spherical precipitates within the matrix could be observed. The heterogonous nucleation site of the T1 phase on the grain boundary agrees well with the previous observation reported by Cassada et al. [7], who proposed that the precipitation of the T1 phase at subgrain boundaries results from the easy migration of Cu and Li atoms and the sufficient concentration of mobile vacancies at these locations. Moreover, Lee et al. [17] observed that an increase in aging time caused a rapid precipitation of the T1 phase both within the matrix and at subgrain boundaries, consistent with the (HAABF) STEM image presented in Figure 2.Figure 2
High angle annular bright field scanning transmission electron microscopy image showing the heterogeneous formation of a bright imaging platelet precipitate at the grain boundary and the distribution of platelets and spherical precipitates within the matrix.


### 3.2. Atom Probe Tomography Analyses

The presence of several alloying elements such as Li, Cu, Mg, Zr, and Ag in AA2195 leads to complex interactions between the different types of precipitates, which has led to many studies on the evolution of such precipitates in alloys. The use of atom probe tomography allows for the determination of the chemical composition within small-thickness platelets (less than 2 nm) embedded in an Al matrix as discussed in this section.


#### 3.2.1. LAWATAP Analyses at 30 K and 20% of Pulse Fraction

Figure3 shows the reconstructed volume of the sample analyzed by a LAWATAP at 30 K and 20% of pulse fraction (ratio of pulse voltage, Vpulse, to DC standing voltage, VDC).Figure 3
LAWATAP analysis of the microstructure at 30 K and 20% of pulse fraction. (a) Reconstructed volume showing the distribution of theT1 and θ′ phases. (b) Corresponding proxigram composition profile for the T1 platelet indicating chemical composition of (11±1) at.% Cu, (13±1) at.% Li, (3±1) at.% Mg, and (1.5±0.4) at.% Ag. (c) Corresponding combined proxigram composition profile for the θ′ platelet with a chemical composition of (27±3) at.% Cu, (3.8±0.2) at.% Li, and (0.7±0.2) at.% Mg.
(a)
(b)
(c)This figure demonstrates that platelet precipitates are distributed within the matrix. Based on the knowledge of the angles between different crystallographic directions, it can be confirmed that the two plates in the upper part of the reconstructed volume areT1 precipitates. The direction of the analysis has been identified as 200. This identification is based on measuring the distance between the atomic planes in the atom probe tomography dataset that are perpendicular to this zone axis, that is, the 200 direction. As shown in Figure 3(a), the angle between the normal of the T1 platelet plane, the 111 direction, and the 200 zone axis was found to be (55° ± 1), which is within the margin of error for the expected crystallographic angle between these two directions (the calculated value of this angle from the unit cell is 54.76°). Due to their orientations perpendicular to the 200 zone axis, the remaining platelets in the reconstructed volume can be identified as θ′ precipitates.A combined corresponding proxigram profile for theT1 platelets is shown in Figure 3(b). The T1 precipitates are delineated by 6 at.% Li isoconcentration surface. The chemical composition for the T1 platelets was found to be (11±1) at.% Cu, (13±1) at.% Li, (3±1) at.% Mg, and (1.5±0.4) at.% Ag, indicating a clear deviation from the Al2CuLi stoichiometry. A combined proxigram profile from 4 at.% Cu isoconcentration surfaces of θ′ platelets is shown in Figure 3(c). According to this profile, the chemical composition for the θ′ precipitates was found to be (27±3) at.% Cu, (3.8±0.2) at.% Li, and (0.7±0.2) at.% Mg. This quantitative analysis reveals a clear evidence for a significant concentration level of Li atoms inside the θ′ platelets, without any indication for the presence of Ag or Zr. The chemical compositions for these platelets are very close to the Al2Cu stoichiometry. The partitioning of Li atoms to the θ′ precipitates might indicate the possible occurrence of the phase transformation of the θ′ precipitates at the later stages of the ageing.To obtain a high spatial resolution perpendicular to the platelets, it is desirable to align this direction with the tip axis of the prepared samples. Since the material possesses a strong rolling texture (sheet normal to{110} planes, rolling direction is 112), it is possible to prepare samples with a defined orientation; for example, samples were prepared with their axis parallel to the 111 direction. Figure 4 shows APT results for such preferentially oriented samples. The (111) Al atomic planes can be identified. Thus, three out of four orientations of one T1 precipitate on the {111} matrix planes can be observed (Figure 4(a)). The magnified view of one T1 platelet with resolved {111} planes is shown in Figure 4(b). Figure 4(c) is a proxigram profile from 4 at.% Cu isoconcentration surface of the T1 platelet. Even though that the measured chemical composition for this platelet was improved by preforming an APT analysis in this direction, the deviation from the stoichiometric value can be clearly seen in the chemical composition of (14±2) at.% Cu, (14±3) at.% Li, (4±1) at.% Mg, and (1.4±0.4) at.% Ag. This quantitative analysis demonstrates the enrichment of Mg atoms inside the platelet without any indication for enrichment at the interface. Furthermore, there is no statistical significant enrichment of Ag or Zr. This corresponds with previous observation reported by Gault et al. [14].Figure 4
LAWATAP analysis for the specimen with rolling texture with the same experimental parameters as in Figure3. (a) Reconstructed volume showing three out of four orientations of the T1 precipitate on the {111} matrix planes. (b) Magnified view of the T1 platelet with resolved {111} planes reveals the distribution of Mg within the T1 platelet. (c) Corresponding proxigram composition profile for the T1 platelet on the {111} plane gives the chemical composition as (14±2) at.% Cu, (14±3) at.% Li, (4±1) at.% Mg, and (1.4±0.4) at.% Ag.
(a)
(b)
(c)The deviation of the experimentally measured chemical composition of theT1 platelet to the Al2CuLi stoichiometry has been observed by Murayama and Hono [13] as well. They interpreted this deviation as a result of the unstable ionization behavior of atoms near or within the T1 precipitates resulting from the very low evaporation field of Li. Moreover, Gault et al. [14] interpret this deviation as a result of a convolution of the matrix concentration with that of the precipitates due to the presence of trajectory aberrations in the APT analyses. This artifact leads to an overestimation of the Al content inside the platelet. However, significant notes could be observed on the correction method suggested by Gault et al. [14]. Most notably, the assumption of having correct aluminum contents in all precipitates and calculating their chemical composition as a function of apparent aluminum concentration enhances the uncertainties of their measured chemical composition.As far as the trajectory aberrations are concerned, the thickness of the platelets will be overestimated in the 3D reconstructed volume (Figures3(a) and 4(a)). However, an accurate platelet thickness can be determined by counting the atomic planes of the Al-rich matrix in the 111 direction. By multiplying the number of Al atomic planes by the interplanar spacing of a/h2+k2+l2 (where a is the lattice parameter for fcc Al, a=0.405 nm, and h=k=l=1) the T1 platelet thickness was found to be (1.4±0.2) nm. As the presence of different alloying elements with low chemical concentrations [18] does not affect largely the value of the lattice parameter of the Al-rich matrix (Table 1), it can be justified to set the value of the lattice parameter for the Al-rich matrix to be equal to that of pure Al. Furthermore, local magnification effects that cause variations in atomic density between matrix and precipitates [19] can lead to an underestimation of the Li and Cu content of the thin T1 platelets. These APT artifacts might affect the estimation of the chemical composition for the T1 platelets precipitates, and hence great care is required for the analyses of this phase. Menand et al. have reported optimized experimental conditions for the analysis of Al-Li alloys which allow minimizing such APT artifacts [10]. These conditions consist of a low tip temperature of 20 to 30 K and a pulse fraction of greater than 15%. On this basis, atom probe tomography experiments were slightly changed.


#### 3.2.2. LAWATAP Analyses at 25 K and 22.5% of Pulse Fraction

The series of images in Figure5 reveals the effect of changing the experimental parameters on the detected chemical composition within the precipitates. Figure 5(a) shows various T1 and θ′ platelets. The proxigram profiles were computed by following the same procedure as mentioned above. Proxigram profiles corresponding to θ′ and T1 platelets where θ′ precipitates are delineated by 10 at.% Cu isoconcentration surfaces and T1 precipitates are delineated by 10 at.% Li isoconcentration surfaces are presented in Figures 5(b) and 5(c), respectively. As illustrated in Figure 5(b), the chemical composition for θ′ was found to be (30±2) at.% Cu, (3±1) at.% Li, and (1±0.7) at.% Mg. It is worth noting that analyses of the θ′ precipitates under these experimental conditions resulted in θ′ stoichiometries consistent with the expected Al2Cu equilibrium composition. Given its importance for strengthening Al, a large number of studies of the Al-Cu precipitation sequence have focused on the properties of metastable θ′ [20, 21]. Relatively, little is known concerning the compositional evolution of θ′ precipitates, since its nanometer-scale platelet-like morphology makes quantitative analytical electron microscopy analyses extremely difficult. Recent study by Biswas et al. [22] shows that θ′ precipitates are observed upon ageing between 190°C and 260°C in a binary Al-1.7 at.% Cu alloy. They observed that, after ageing the alloy for 8 h at 190°C, θ′ precipitates exhibit a range of Cu-deficient core concentration which differ from the equilibrium composition of Al2Cu. In contrast, alloy aged at 260°C for 4 h exhibited precipitates with Cu core concentrations close to the equilibrium value. According to the authors, the cause of Cu deficiency in the θ′ precipitates at the lower ageing temperature remains an open issue. In our study, the applied T8 heat treatment implies artificial ageing of the alloy for 30 h at 150°C. It is worth noting that our ageing temperature is located below the metastable solvus boundary for the θ′ precipitates in Al-Cu phase diagram [23]. Our compositional analysis of the θ′ platelet showed the stoichiometric composition consistent with the expected Al2Cu equilibrium composition. This can be explained in terms of increasing the ageing time that will induce the Cu diffusion to the existing defects in the microstructure resulting in a core concentration close to the equilibrium one.Figure 5
LAWATAP analysis with new experimental parameters 25 K and 22.5% of pulse fraction. (a) Reconstructed volume, obtained with laser assisted wide angle tomographic atom probe, showsT1 and θ′ platelets. (b) Corresponding proxigram composition profile for θ′ gives an optimistic chemical composition as (30±2) at.% Cu, (3±1) at.% Li, and (1±0.7) at.% Mg. (c) Corresponding combined proxigram composition profile for T1 with the chemical composition of (14±1) at.% Cu, (14±2) at.% Li, (3.8±1) at.% Mg, and (0.8±0.4) at.% Ag.
(a)
(b)
(c)A combined proxigram profile for severalT1 platelets is shown in Figure 5(c). The chemical compositions for the T1 platelets was found to be (14±1) at.% Cu, (14±2) at.% Li, (3.8±1) at.% Mg, and (0.8±0.4) at.% Ag. This confirms both the deviation from Al2CuLi stoichiometry and potential enrichment of the T1 phase with Mg. By considering the current model proposed by Cassada et al. [7], the precipitation of the T1 phase on the {111} Al planes requires the presence of one or more partial dislocation bounded by a stacking fault. Because the stacking fault energy (SFE) of Al is very high, the dissociation of dislocations into partials is believed to be necessary for nucleating the T1 phase. This can be facilitated by elements known to decrease the SFE of Al and among these elements Mg and Ag have been found to be highly effective [24]. Regarding the effect of Mg enrichment inside the T1 platelet on the mechanical properties of the alloy, it has been shown that single addition of Ag in Al-Cu-Li-Zr alloy had no effect on the age hardenable curve, while Mg addition significantly raises the peak hardness and shortens the time to the peak [6]. The peak hardness further increases when Ag is added together with Mg. This effect is explained as follows. In a case of single addition of Ag, the T1 platelet nucleated only on dislocation loop around a Zr dispersoids. In contrast, Mg addition has been revealed to cause the formation of octahedral microvoids and new GP zones on {111} Al planes; and these act as nucleation sites for the T1 phase providing a fine dispersion and hence increase the hardness of the system. Thus, it can be concluded that Mg and Ag are known to aid the precipitation of T1 phase and hence improve the hardness of the alloy. The distribution of these elements in the structure of the T1 platelets as well as their portioning between precipitates and matrix is the subject of conflict report [25].


#### 3.2.3. LEAP Analyses at 22 K and 18% of Pulse Fraction

The use of the wider field of view of the detector in the LEAP permits the collection of larger datasets. Furthermore, using a different machine allows determining any device specific artifacts.A top view of the reconstructed volume of a sample analyzed by a LEAP in voltage mode at 22 K and 18% pulse fraction is shown in Figure6(a). The intersections of three T1 platelets with the (111) pole are visible. According to the proxigram (Figure 6(b)) from 8 at.% Li isoconcentration surface of these platelets, this analysis yielded the close values for the chemical compositions of the T1 platelets, with (14.3±2) at.% Cu, (15.5±3) at.% Li, (2.5±1) at.% Mg, and (0.8±0.5) at.% Ag, as LAWATAP analyses.Figure 6
LEAP analysis at 22 K and 18% of pulse fraction. (a) Top view of the reconstructed volume of a sample shows the intersections of theT1 platelets with the (111) pole. (b) Corresponding combined proxigram composition profile for T1 with the chemical composition of (14.3±2) at.% Cu, (15.5±3) at.% Li, (2.5±1) at.% Mg, and (0.8±0.5) at.% Ag.
(a)
(b)One should note that the observation of theβ′Al3Zr precipitates has not been recorded in APT analysis. This is simply due to the fact of the large diameter and small number density of this phase in the microstructure, which make the APT analyses challenging.The combination of results from different atom probes at different experimental conditions, even including laser based results from Gault et al. [14], suggests that the actual chemical composition for the thin T1 platelets could differ from the Al2CuLi of the stable bulk phase, since changing the parameters should induce a change in the significance of the artifacts. Furthermore, it seems unlikely that the artifacts would only influence the Cu detection for the T1 platelets but not the θ′ platelets. Even if one assumes that Li changes the evaporation behavior of Cu, it is difficult to understand why it should not also affect Al and thus negate this effect. Such an effect should also result in an extremely decreased atomic density, since about half of all otherwise detected atoms would be missing. But this is not observed at the platelet positions according to the density profiles of the cylinders perpendicular to these thin platelets. In fact, the average difference between the detected atoms in the matrix and the precipitates dose not exceed 32 atoms.In conclusion, it seems reasonable to propose that the concentration in theT1 phase is indeed nonstoichiometric after treatment of the samples in the T8 condition. This finding is also supported by high angle annular dark field scanning transmission electron microscopy (HAADF) STEM and small angle X-ray scattering (SAXS) results from Donnadieu et al. [26]. In this study the authors investigated a similar alloy, conducting a similar thermomechanical treatment. The observed microstructure also consists of a homogenous distribution of thin platelets precipitates with 1 nm thickness and parallel to (111) Al planes. They noted that the composition of the layers of the thin T1 precipitates may deviate from the Al2CuLi stoichiometry of the stable bulk phase and proposed that this may be either due to the presence of higher Al content than would be expected for the T1Al2CuLi or due to the nature of the interface planes. Their results reported Al content higher than expected for T1Al2CuLi phase and the occurrence of matrix/T1 interface on Al-Cu mixed layer instead of Al-Li layer. The authors also suggested that the actual atomic structure of the thin T1 platelet could present stoichiometry different from that for the bulk T1 phase. With regard to the atomic structure of the bulk T1 phase, several models have been proposed. The first model is proposed by Huang and Ardell [27]. According to this model, the T1 phase structure consists of a stack of hexagonal layers similar to {111} Al planes. The basal plane and the medium one (z=0 and 1/2) are formed by a mix of Al-Li layer, while the inner planes (z=1/4 and 3/4) are hexagonal layers of Cu and Al atoms. The second proposed model of the structure of the T1 phase has been made by Howe et al. [28]. In this model, the authors suggested that the basal plane (z=0) is formed by Al layer, while the medium one (z=1/2) is made of Li atoms. The inner planes (z=1/4 and 3/4) are somewhat similar to that in Huang and Ardell model. The third structure of the T1 phase has been proposed by Van Smaalen et al. [29]. Their proposed structure displays mix of Al-Li layers for z=0 and z=1/2, which are corrugated, while the inner layers are corrugated Al-Cu layers. The Huang and Ardell study [27] was, until very recently, the generally accepted structure for the T1 phase. However, the two recent and independent studies, by Donnadieu et al. [26] and Dwyer et al. [30], determined that the structure of the thin T1 platelets embedded in Al matrix was actually very close to that of the bulk T1 phase proposed by Van Smaalen et al. [29]. But the case might be different for the T1 precipitates with the thickness less than one unit cell. Thus, it can be concluded that although Van Smaalen et al. [29] structure provides the basis for the structure of the T1 precipitates, for the earliest stage of precipitation, modifications may occur.On the other hand, more recent APT study proposed by Araullo-Peters et al. [25] reported the presence of the T1 precursor at the early stage of ageing. However, the observed T1 platelets in this study are between 5 and 10 nm in thickness with the chemical compositions different from that for the bulk T1 phase.In particular, our results demonstrated the presence of lower Li and Cu contents with 1 : 1 ratio in the thinT1 platelets. These results confirm the fact of the Al content higher than what would be expected for this phase. As far as the matrix/T1 interface is considered, APT is more appropriate tool to investigate the local chemistry at the interface. Figure 7 displays a higher magnification image for the T1 platelet. It can be seen that the density of Cu atoms at the matrix/T1 interface is higher than that for Li atoms. Moreover, the correlation between Mg and Li atoms is clearly visible. This observation confirms the assumption of the occurrence of the matrix/T1 interface on Al-Cu layer instead of Al-Li layer and the consumption of the first compact Al-Li layer in the nucleation of the T1 phase. It comes out then that the composition of the T1 precipitates deviates from that of the stable bulk phase. The deviation of the T1 phase from thermodynamic equilibrium composition for the stable bulk phase suggests that the T8 condition is corresponding to the thermodynamical nonequilibrium condition. The obtained microstructure in this condition has appreciable supersaturation of defects, which means that the nucleation and growth of different phases are still at their intermediate stages.Figure 7
The magnified view of theT1 platelet showing the density of Cu, Li, and Mg atoms at the matrix/precipitates interface.


## 3.1. Electron Microscopy

Conventional TEM bright field images revealed a complex microstructure encompassing different precipitates with platelet and spherical morphologies as shown in Figure1. Precipitates were characterized using an exact [110] zone to detect T1 platelets, θ′ platelets, and spherical precipitates with L12-structure. A schematic of the indexed selected area diffraction pattern (SADP) in the [101] direction is integrated with the bright field-TEM image (Figure 1(a)). This indicates the presence of two variants of T1 precipitate as streaks along the 111 direction in the pattern. The other two variants of this phase produce spots adjacent to 200 positions. The streaks along the 200 direction reveal the presence of one variant of θ′. The superlattice reflections in the diffraction pattern may originate from an L12-ordered structure representing δ′Al3Li and/or β′Al3Zr precipitates. The L12 unit cell is based on the face centered cubic (fcc) unit cell of aluminum. However, the corner atoms are replaced by either Li or Zr, respectively. This means that all 100 directions are superstructure directions. The spherical precipitates are most probably of the β′-type, since the Li composition in the investigated alloy is less than 5 at.%. It is worth noting that, from the diffraction pattern alone, no decision can be achieved whether the precipitates are δ′ or β′ because of the similarity of the lattice constant. Figure 1(b) presents a simulated diffraction pattern matching all spots and streaks in the [101] selected area diffraction pattern.Figure 1
Evolution of the microstructure as observed by TEM. (a) Typical bright field image showing a complex microstructure with theT1, θ′, and β′ precipitates and the corresponding [101] selected area diffraction pattern (SADP). (b) Schematic of a simulated diffraction pattern that assigns the reflections and streaks in the SADP to the corresponding precipitates.
(a)
(b)High angle annular bright field scanning transmission electron microscopy (HAABF) STEM-contrast also revealed the existence of both spherical and platelet precipitates (Figure2). As illustrated in Figure 2, the heterogeneous formation of platelet precipitate can be clearly observed at grain boundaries by imaging the sample from different angles (±75° in steps of 1°). A low angle grain boundary in Figure 2 was identified while rotating the specimen and monitoring the diffraction pattern at various locations within the sample. Moreover, the distribution of platelet precipitates and spherical precipitates within the matrix could be observed. The heterogonous nucleation site of the T1 phase on the grain boundary agrees well with the previous observation reported by Cassada et al. [7], who proposed that the precipitation of the T1 phase at subgrain boundaries results from the easy migration of Cu and Li atoms and the sufficient concentration of mobile vacancies at these locations. Moreover, Lee et al. [17] observed that an increase in aging time caused a rapid precipitation of the T1 phase both within the matrix and at subgrain boundaries, consistent with the (HAABF) STEM image presented in Figure 2.Figure 2
High angle annular bright field scanning transmission electron microscopy image showing the heterogeneous formation of a bright imaging platelet precipitate at the grain boundary and the distribution of platelets and spherical precipitates within the matrix.


## 3.2. Atom Probe Tomography Analyses

The presence of several alloying elements such as Li, Cu, Mg, Zr, and Ag in AA2195 leads to complex interactions between the different types of precipitates, which has led to many studies on the evolution of such precipitates in alloys. The use of atom probe tomography allows for the determination of the chemical composition within small-thickness platelets (less than 2 nm) embedded in an Al matrix as discussed in this section.


### 3.2.1. LAWATAP Analyses at 30 K and 20% of Pulse Fraction

Figure3 shows the reconstructed volume of the sample analyzed by a LAWATAP at 30 K and 20% of pulse fraction (ratio of pulse voltage, Vpulse, to DC standing voltage, VDC).Figure 3
LAWATAP analysis of the microstructure at 30 K and 20% of pulse fraction. (a) Reconstructed volume showing the distribution of theT1 and θ′ phases. (b) Corresponding proxigram composition profile for the T1 platelet indicating chemical composition of (11±1) at.% Cu, (13±1) at.% Li, (3±1) at.% Mg, and (1.5±0.4) at.% Ag. (c) Corresponding combined proxigram composition profile for the θ′ platelet with a chemical composition of (27±3) at.% Cu, (3.8±0.2) at.% Li, and (0.7±0.2) at.% Mg.
(a)
(b)
(c)This figure demonstrates that platelet precipitates are distributed within the matrix. Based on the knowledge of the angles between different crystallographic directions, it can be confirmed that the two plates in the upper part of the reconstructed volume areT1 precipitates. The direction of the analysis has been identified as 200. This identification is based on measuring the distance between the atomic planes in the atom probe tomography dataset that are perpendicular to this zone axis, that is, the 200 direction. As shown in Figure 3(a), the angle between the normal of the T1 platelet plane, the 111 direction, and the 200 zone axis was found to be (55° ± 1), which is within the margin of error for the expected crystallographic angle between these two directions (the calculated value of this angle from the unit cell is 54.76°). Due to their orientations perpendicular to the 200 zone axis, the remaining platelets in the reconstructed volume can be identified as θ′ precipitates.A combined corresponding proxigram profile for theT1 platelets is shown in Figure 3(b). The T1 precipitates are delineated by 6 at.% Li isoconcentration surface. The chemical composition for the T1 platelets was found to be (11±1) at.% Cu, (13±1) at.% Li, (3±1) at.% Mg, and (1.5±0.4) at.% Ag, indicating a clear deviation from the Al2CuLi stoichiometry. A combined proxigram profile from 4 at.% Cu isoconcentration surfaces of θ′ platelets is shown in Figure 3(c). According to this profile, the chemical composition for the θ′ precipitates was found to be (27±3) at.% Cu, (3.8±0.2) at.% Li, and (0.7±0.2) at.% Mg. This quantitative analysis reveals a clear evidence for a significant concentration level of Li atoms inside the θ′ platelets, without any indication for the presence of Ag or Zr. The chemical compositions for these platelets are very close to the Al2Cu stoichiometry. The partitioning of Li atoms to the θ′ precipitates might indicate the possible occurrence of the phase transformation of the θ′ precipitates at the later stages of the ageing.To obtain a high spatial resolution perpendicular to the platelets, it is desirable to align this direction with the tip axis of the prepared samples. Since the material possesses a strong rolling texture (sheet normal to{110} planes, rolling direction is 112), it is possible to prepare samples with a defined orientation; for example, samples were prepared with their axis parallel to the 111 direction. Figure 4 shows APT results for such preferentially oriented samples. The (111) Al atomic planes can be identified. Thus, three out of four orientations of one T1 precipitate on the {111} matrix planes can be observed (Figure 4(a)). The magnified view of one T1 platelet with resolved {111} planes is shown in Figure 4(b). Figure 4(c) is a proxigram profile from 4 at.% Cu isoconcentration surface of the T1 platelet. Even though that the measured chemical composition for this platelet was improved by preforming an APT analysis in this direction, the deviation from the stoichiometric value can be clearly seen in the chemical composition of (14±2) at.% Cu, (14±3) at.% Li, (4±1) at.% Mg, and (1.4±0.4) at.% Ag. This quantitative analysis demonstrates the enrichment of Mg atoms inside the platelet without any indication for enrichment at the interface. Furthermore, there is no statistical significant enrichment of Ag or Zr. This corresponds with previous observation reported by Gault et al. [14].Figure 4
LAWATAP analysis for the specimen with rolling texture with the same experimental parameters as in Figure3. (a) Reconstructed volume showing three out of four orientations of the T1 precipitate on the {111} matrix planes. (b) Magnified view of the T1 platelet with resolved {111} planes reveals the distribution of Mg within the T1 platelet. (c) Corresponding proxigram composition profile for the T1 platelet on the {111} plane gives the chemical composition as (14±2) at.% Cu, (14±3) at.% Li, (4±1) at.% Mg, and (1.4±0.4) at.% Ag.
(a)
(b)
(c)The deviation of the experimentally measured chemical composition of theT1 platelet to the Al2CuLi stoichiometry has been observed by Murayama and Hono [13] as well. They interpreted this deviation as a result of the unstable ionization behavior of atoms near or within the T1 precipitates resulting from the very low evaporation field of Li. Moreover, Gault et al. [14] interpret this deviation as a result of a convolution of the matrix concentration with that of the precipitates due to the presence of trajectory aberrations in the APT analyses. This artifact leads to an overestimation of the Al content inside the platelet. However, significant notes could be observed on the correction method suggested by Gault et al. [14]. Most notably, the assumption of having correct aluminum contents in all precipitates and calculating their chemical composition as a function of apparent aluminum concentration enhances the uncertainties of their measured chemical composition.As far as the trajectory aberrations are concerned, the thickness of the platelets will be overestimated in the 3D reconstructed volume (Figures3(a) and 4(a)). However, an accurate platelet thickness can be determined by counting the atomic planes of the Al-rich matrix in the 111 direction. By multiplying the number of Al atomic planes by the interplanar spacing of a/h2+k2+l2 (where a is the lattice parameter for fcc Al, a=0.405 nm, and h=k=l=1) the T1 platelet thickness was found to be (1.4±0.2) nm. As the presence of different alloying elements with low chemical concentrations [18] does not affect largely the value of the lattice parameter of the Al-rich matrix (Table 1), it can be justified to set the value of the lattice parameter for the Al-rich matrix to be equal to that of pure Al. Furthermore, local magnification effects that cause variations in atomic density between matrix and precipitates [19] can lead to an underestimation of the Li and Cu content of the thin T1 platelets. These APT artifacts might affect the estimation of the chemical composition for the T1 platelets precipitates, and hence great care is required for the analyses of this phase. Menand et al. have reported optimized experimental conditions for the analysis of Al-Li alloys which allow minimizing such APT artifacts [10]. These conditions consist of a low tip temperature of 20 to 30 K and a pulse fraction of greater than 15%. On this basis, atom probe tomography experiments were slightly changed.


### 3.2.2. LAWATAP Analyses at 25 K and 22.5% of Pulse Fraction

The series of images in Figure5 reveals the effect of changing the experimental parameters on the detected chemical composition within the precipitates. Figure 5(a) shows various T1 and θ′ platelets. The proxigram profiles were computed by following the same procedure as mentioned above. Proxigram profiles corresponding to θ′ and T1 platelets where θ′ precipitates are delineated by 10 at.% Cu isoconcentration surfaces and T1 precipitates are delineated by 10 at.% Li isoconcentration surfaces are presented in Figures 5(b) and 5(c), respectively. As illustrated in Figure 5(b), the chemical composition for θ′ was found to be (30±2) at.% Cu, (3±1) at.% Li, and (1±0.7) at.% Mg. It is worth noting that analyses of the θ′ precipitates under these experimental conditions resulted in θ′ stoichiometries consistent with the expected Al2Cu equilibrium composition. Given its importance for strengthening Al, a large number of studies of the Al-Cu precipitation sequence have focused on the properties of metastable θ′ [20, 21]. Relatively, little is known concerning the compositional evolution of θ′ precipitates, since its nanometer-scale platelet-like morphology makes quantitative analytical electron microscopy analyses extremely difficult. Recent study by Biswas et al. [22] shows that θ′ precipitates are observed upon ageing between 190°C and 260°C in a binary Al-1.7 at.% Cu alloy. They observed that, after ageing the alloy for 8 h at 190°C, θ′ precipitates exhibit a range of Cu-deficient core concentration which differ from the equilibrium composition of Al2Cu. In contrast, alloy aged at 260°C for 4 h exhibited precipitates with Cu core concentrations close to the equilibrium value. According to the authors, the cause of Cu deficiency in the θ′ precipitates at the lower ageing temperature remains an open issue. In our study, the applied T8 heat treatment implies artificial ageing of the alloy for 30 h at 150°C. It is worth noting that our ageing temperature is located below the metastable solvus boundary for the θ′ precipitates in Al-Cu phase diagram [23]. Our compositional analysis of the θ′ platelet showed the stoichiometric composition consistent with the expected Al2Cu equilibrium composition. This can be explained in terms of increasing the ageing time that will induce the Cu diffusion to the existing defects in the microstructure resulting in a core concentration close to the equilibrium one.Figure 5
LAWATAP analysis with new experimental parameters 25 K and 22.5% of pulse fraction. (a) Reconstructed volume, obtained with laser assisted wide angle tomographic atom probe, showsT1 and θ′ platelets. (b) Corresponding proxigram composition profile for θ′ gives an optimistic chemical composition as (30±2) at.% Cu, (3±1) at.% Li, and (1±0.7) at.% Mg. (c) Corresponding combined proxigram composition profile for T1 with the chemical composition of (14±1) at.% Cu, (14±2) at.% Li, (3.8±1) at.% Mg, and (0.8±0.4) at.% Ag.
(a)
(b)
(c)A combined proxigram profile for severalT1 platelets is shown in Figure 5(c). The chemical compositions for the T1 platelets was found to be (14±1) at.% Cu, (14±2) at.% Li, (3.8±1) at.% Mg, and (0.8±0.4) at.% Ag. This confirms both the deviation from Al2CuLi stoichiometry and potential enrichment of the T1 phase with Mg. By considering the current model proposed by Cassada et al. [7], the precipitation of the T1 phase on the {111} Al planes requires the presence of one or more partial dislocation bounded by a stacking fault. Because the stacking fault energy (SFE) of Al is very high, the dissociation of dislocations into partials is believed to be necessary for nucleating the T1 phase. This can be facilitated by elements known to decrease the SFE of Al and among these elements Mg and Ag have been found to be highly effective [24]. Regarding the effect of Mg enrichment inside the T1 platelet on the mechanical properties of the alloy, it has been shown that single addition of Ag in Al-Cu-Li-Zr alloy had no effect on the age hardenable curve, while Mg addition significantly raises the peak hardness and shortens the time to the peak [6]. The peak hardness further increases when Ag is added together with Mg. This effect is explained as follows. In a case of single addition of Ag, the T1 platelet nucleated only on dislocation loop around a Zr dispersoids. In contrast, Mg addition has been revealed to cause the formation of octahedral microvoids and new GP zones on {111} Al planes; and these act as nucleation sites for the T1 phase providing a fine dispersion and hence increase the hardness of the system. Thus, it can be concluded that Mg and Ag are known to aid the precipitation of T1 phase and hence improve the hardness of the alloy. The distribution of these elements in the structure of the T1 platelets as well as their portioning between precipitates and matrix is the subject of conflict report [25].


### 3.2.3. LEAP Analyses at 22 K and 18% of Pulse Fraction

The use of the wider field of view of the detector in the LEAP permits the collection of larger datasets. Furthermore, using a different machine allows determining any device specific artifacts.A top view of the reconstructed volume of a sample analyzed by a LEAP in voltage mode at 22 K and 18% pulse fraction is shown in Figure6(a). The intersections of three T1 platelets with the (111) pole are visible. According to the proxigram (Figure 6(b)) from 8 at.% Li isoconcentration surface of these platelets, this analysis yielded the close values for the chemical compositions of the T1 platelets, with (14.3±2) at.% Cu, (15.5±3) at.% Li, (2.5±1) at.% Mg, and (0.8±0.5) at.% Ag, as LAWATAP analyses.Figure 6
LEAP analysis at 22 K and 18% of pulse fraction. (a) Top view of the reconstructed volume of a sample shows the intersections of theT1 platelets with the (111) pole. (b) Corresponding combined proxigram composition profile for T1 with the chemical composition of (14.3±2) at.% Cu, (15.5±3) at.% Li, (2.5±1) at.% Mg, and (0.8±0.5) at.% Ag.
(a)
(b)One should note that the observation of theβ′Al3Zr precipitates has not been recorded in APT analysis. This is simply due to the fact of the large diameter and small number density of this phase in the microstructure, which make the APT analyses challenging.The combination of results from different atom probes at different experimental conditions, even including laser based results from Gault et al. [14], suggests that the actual chemical composition for the thin T1 platelets could differ from the Al2CuLi of the stable bulk phase, since changing the parameters should induce a change in the significance of the artifacts. Furthermore, it seems unlikely that the artifacts would only influence the Cu detection for the T1 platelets but not the θ′ platelets. Even if one assumes that Li changes the evaporation behavior of Cu, it is difficult to understand why it should not also affect Al and thus negate this effect. Such an effect should also result in an extremely decreased atomic density, since about half of all otherwise detected atoms would be missing. But this is not observed at the platelet positions according to the density profiles of the cylinders perpendicular to these thin platelets. In fact, the average difference between the detected atoms in the matrix and the precipitates dose not exceed 32 atoms.In conclusion, it seems reasonable to propose that the concentration in theT1 phase is indeed nonstoichiometric after treatment of the samples in the T8 condition. This finding is also supported by high angle annular dark field scanning transmission electron microscopy (HAADF) STEM and small angle X-ray scattering (SAXS) results from Donnadieu et al. [26]. In this study the authors investigated a similar alloy, conducting a similar thermomechanical treatment. The observed microstructure also consists of a homogenous distribution of thin platelets precipitates with 1 nm thickness and parallel to (111) Al planes. They noted that the composition of the layers of the thin T1 precipitates may deviate from the Al2CuLi stoichiometry of the stable bulk phase and proposed that this may be either due to the presence of higher Al content than would be expected for the T1Al2CuLi or due to the nature of the interface planes. Their results reported Al content higher than expected for T1Al2CuLi phase and the occurrence of matrix/T1 interface on Al-Cu mixed layer instead of Al-Li layer. The authors also suggested that the actual atomic structure of the thin T1 platelet could present stoichiometry different from that for the bulk T1 phase. With regard to the atomic structure of the bulk T1 phase, several models have been proposed. The first model is proposed by Huang and Ardell [27]. According to this model, the T1 phase structure consists of a stack of hexagonal layers similar to {111} Al planes. The basal plane and the medium one (z=0 and 1/2) are formed by a mix of Al-Li layer, while the inner planes (z=1/4 and 3/4) are hexagonal layers of Cu and Al atoms. The second proposed model of the structure of the T1 phase has been made by Howe et al. [28]. In this model, the authors suggested that the basal plane (z=0) is formed by Al layer, while the medium one (z=1/2) is made of Li atoms. The inner planes (z=1/4 and 3/4) are somewhat similar to that in Huang and Ardell model. The third structure of the T1 phase has been proposed by Van Smaalen et al. [29]. Their proposed structure displays mix of Al-Li layers for z=0 and z=1/2, which are corrugated, while the inner layers are corrugated Al-Cu layers. The Huang and Ardell study [27] was, until very recently, the generally accepted structure for the T1 phase. However, the two recent and independent studies, by Donnadieu et al. [26] and Dwyer et al. [30], determined that the structure of the thin T1 platelets embedded in Al matrix was actually very close to that of the bulk T1 phase proposed by Van Smaalen et al. [29]. But the case might be different for the T1 precipitates with the thickness less than one unit cell. Thus, it can be concluded that although Van Smaalen et al. [29] structure provides the basis for the structure of the T1 precipitates, for the earliest stage of precipitation, modifications may occur.On the other hand, more recent APT study proposed by Araullo-Peters et al. [25] reported the presence of the T1 precursor at the early stage of ageing. However, the observed T1 platelets in this study are between 5 and 10 nm in thickness with the chemical compositions different from that for the bulk T1 phase.In particular, our results demonstrated the presence of lower Li and Cu contents with 1 : 1 ratio in the thinT1 platelets. These results confirm the fact of the Al content higher than what would be expected for this phase. As far as the matrix/T1 interface is considered, APT is more appropriate tool to investigate the local chemistry at the interface. Figure 7 displays a higher magnification image for the T1 platelet. It can be seen that the density of Cu atoms at the matrix/T1 interface is higher than that for Li atoms. Moreover, the correlation between Mg and Li atoms is clearly visible. This observation confirms the assumption of the occurrence of the matrix/T1 interface on Al-Cu layer instead of Al-Li layer and the consumption of the first compact Al-Li layer in the nucleation of the T1 phase. It comes out then that the composition of the T1 precipitates deviates from that of the stable bulk phase. The deviation of the T1 phase from thermodynamic equilibrium composition for the stable bulk phase suggests that the T8 condition is corresponding to the thermodynamical nonequilibrium condition. The obtained microstructure in this condition has appreciable supersaturation of defects, which means that the nucleation and growth of different phases are still at their intermediate stages.Figure 7
The magnified view of theT1 platelet showing the density of Cu, Li, and Mg atoms at the matrix/precipitates interface.


## 3.2.1. LAWATAP Analyses at 30 K and 20% of Pulse Fraction

Figure3 shows the reconstructed volume of the sample analyzed by a LAWATAP at 30 K and 20% of pulse fraction (ratio of pulse voltage, Vpulse, to DC standing voltage, VDC).Figure 3
LAWATAP analysis of the microstructure at 30 K and 20% of pulse fraction. (a) Reconstructed volume showing the distribution of theT1 and θ′ phases. (b) Corresponding proxigram composition profile for the T1 platelet indicating chemical composition of (11±1) at.% Cu, (13±1) at.% Li, (3±1) at.% Mg, and (1.5±0.4) at.% Ag. (c) Corresponding combined proxigram composition profile for the θ′ platelet with a chemical composition of (27±3) at.% Cu, (3.8±0.2) at.% Li, and (0.7±0.2) at.% Mg.
(a)
(b)
(c)This figure demonstrates that platelet precipitates are distributed within the matrix. Based on the knowledge of the angles between different crystallographic directions, it can be confirmed that the two plates in the upper part of the reconstructed volume areT1 precipitates. The direction of the analysis has been identified as 200. This identification is based on measuring the distance between the atomic planes in the atom probe tomography dataset that are perpendicular to this zone axis, that is, the 200 direction. As shown in Figure 3(a), the angle between the normal of the T1 platelet plane, the 111 direction, and the 200 zone axis was found to be (55° ± 1), which is within the margin of error for the expected crystallographic angle between these two directions (the calculated value of this angle from the unit cell is 54.76°). Due to their orientations perpendicular to the 200 zone axis, the remaining platelets in the reconstructed volume can be identified as θ′ precipitates.A combined corresponding proxigram profile for theT1 platelets is shown in Figure 3(b). The T1 precipitates are delineated by 6 at.% Li isoconcentration surface. The chemical composition for the T1 platelets was found to be (11±1) at.% Cu, (13±1) at.% Li, (3±1) at.% Mg, and (1.5±0.4) at.% Ag, indicating a clear deviation from the Al2CuLi stoichiometry. A combined proxigram profile from 4 at.% Cu isoconcentration surfaces of θ′ platelets is shown in Figure 3(c). According to this profile, the chemical composition for the θ′ precipitates was found to be (27±3) at.% Cu, (3.8±0.2) at.% Li, and (0.7±0.2) at.% Mg. This quantitative analysis reveals a clear evidence for a significant concentration level of Li atoms inside the θ′ platelets, without any indication for the presence of Ag or Zr. The chemical compositions for these platelets are very close to the Al2Cu stoichiometry. The partitioning of Li atoms to the θ′ precipitates might indicate the possible occurrence of the phase transformation of the θ′ precipitates at the later stages of the ageing.To obtain a high spatial resolution perpendicular to the platelets, it is desirable to align this direction with the tip axis of the prepared samples. Since the material possesses a strong rolling texture (sheet normal to{110} planes, rolling direction is 112), it is possible to prepare samples with a defined orientation; for example, samples were prepared with their axis parallel to the 111 direction. Figure 4 shows APT results for such preferentially oriented samples. The (111) Al atomic planes can be identified. Thus, three out of four orientations of one T1 precipitate on the {111} matrix planes can be observed (Figure 4(a)). The magnified view of one T1 platelet with resolved {111} planes is shown in Figure 4(b). Figure 4(c) is a proxigram profile from 4 at.% Cu isoconcentration surface of the T1 platelet. Even though that the measured chemical composition for this platelet was improved by preforming an APT analysis in this direction, the deviation from the stoichiometric value can be clearly seen in the chemical composition of (14±2) at.% Cu, (14±3) at.% Li, (4±1) at.% Mg, and (1.4±0.4) at.% Ag. This quantitative analysis demonstrates the enrichment of Mg atoms inside the platelet without any indication for enrichment at the interface. Furthermore, there is no statistical significant enrichment of Ag or Zr. This corresponds with previous observation reported by Gault et al. [14].Figure 4
LAWATAP analysis for the specimen with rolling texture with the same experimental parameters as in Figure3. (a) Reconstructed volume showing three out of four orientations of the T1 precipitate on the {111} matrix planes. (b) Magnified view of the T1 platelet with resolved {111} planes reveals the distribution of Mg within the T1 platelet. (c) Corresponding proxigram composition profile for the T1 platelet on the {111} plane gives the chemical composition as (14±2) at.% Cu, (14±3) at.% Li, (4±1) at.% Mg, and (1.4±0.4) at.% Ag.
(a)
(b)
(c)The deviation of the experimentally measured chemical composition of theT1 platelet to the Al2CuLi stoichiometry has been observed by Murayama and Hono [13] as well. They interpreted this deviation as a result of the unstable ionization behavior of atoms near or within the T1 precipitates resulting from the very low evaporation field of Li. Moreover, Gault et al. [14] interpret this deviation as a result of a convolution of the matrix concentration with that of the precipitates due to the presence of trajectory aberrations in the APT analyses. This artifact leads to an overestimation of the Al content inside the platelet. However, significant notes could be observed on the correction method suggested by Gault et al. [14]. Most notably, the assumption of having correct aluminum contents in all precipitates and calculating their chemical composition as a function of apparent aluminum concentration enhances the uncertainties of their measured chemical composition.As far as the trajectory aberrations are concerned, the thickness of the platelets will be overestimated in the 3D reconstructed volume (Figures3(a) and 4(a)). However, an accurate platelet thickness can be determined by counting the atomic planes of the Al-rich matrix in the 111 direction. By multiplying the number of Al atomic planes by the interplanar spacing of a/h2+k2+l2 (where a is the lattice parameter for fcc Al, a=0.405 nm, and h=k=l=1) the T1 platelet thickness was found to be (1.4±0.2) nm. As the presence of different alloying elements with low chemical concentrations [18] does not affect largely the value of the lattice parameter of the Al-rich matrix (Table 1), it can be justified to set the value of the lattice parameter for the Al-rich matrix to be equal to that of pure Al. Furthermore, local magnification effects that cause variations in atomic density between matrix and precipitates [19] can lead to an underestimation of the Li and Cu content of the thin T1 platelets. These APT artifacts might affect the estimation of the chemical composition for the T1 platelets precipitates, and hence great care is required for the analyses of this phase. Menand et al. have reported optimized experimental conditions for the analysis of Al-Li alloys which allow minimizing such APT artifacts [10]. These conditions consist of a low tip temperature of 20 to 30 K and a pulse fraction of greater than 15%. On this basis, atom probe tomography experiments were slightly changed.


## 3.2.2. LAWATAP Analyses at 25 K and 22.5% of Pulse Fraction

The series of images in Figure5 reveals the effect of changing the experimental parameters on the detected chemical composition within the precipitates. Figure 5(a) shows various T1 and θ′ platelets. The proxigram profiles were computed by following the same procedure as mentioned above. Proxigram profiles corresponding to θ′ and T1 platelets where θ′ precipitates are delineated by 10 at.% Cu isoconcentration surfaces and T1 precipitates are delineated by 10 at.% Li isoconcentration surfaces are presented in Figures 5(b) and 5(c), respectively. As illustrated in Figure 5(b), the chemical composition for θ′ was found to be (30±2) at.% Cu, (3±1) at.% Li, and (1±0.7) at.% Mg. It is worth noting that analyses of the θ′ precipitates under these experimental conditions resulted in θ′ stoichiometries consistent with the expected Al2Cu equilibrium composition. Given its importance for strengthening Al, a large number of studies of the Al-Cu precipitation sequence have focused on the properties of metastable θ′ [20, 21]. Relatively, little is known concerning the compositional evolution of θ′ precipitates, since its nanometer-scale platelet-like morphology makes quantitative analytical electron microscopy analyses extremely difficult. Recent study by Biswas et al. [22] shows that θ′ precipitates are observed upon ageing between 190°C and 260°C in a binary Al-1.7 at.% Cu alloy. They observed that, after ageing the alloy for 8 h at 190°C, θ′ precipitates exhibit a range of Cu-deficient core concentration which differ from the equilibrium composition of Al2Cu. In contrast, alloy aged at 260°C for 4 h exhibited precipitates with Cu core concentrations close to the equilibrium value. According to the authors, the cause of Cu deficiency in the θ′ precipitates at the lower ageing temperature remains an open issue. In our study, the applied T8 heat treatment implies artificial ageing of the alloy for 30 h at 150°C. It is worth noting that our ageing temperature is located below the metastable solvus boundary for the θ′ precipitates in Al-Cu phase diagram [23]. Our compositional analysis of the θ′ platelet showed the stoichiometric composition consistent with the expected Al2Cu equilibrium composition. This can be explained in terms of increasing the ageing time that will induce the Cu diffusion to the existing defects in the microstructure resulting in a core concentration close to the equilibrium one.Figure 5
LAWATAP analysis with new experimental parameters 25 K and 22.5% of pulse fraction. (a) Reconstructed volume, obtained with laser assisted wide angle tomographic atom probe, showsT1 and θ′ platelets. (b) Corresponding proxigram composition profile for θ′ gives an optimistic chemical composition as (30±2) at.% Cu, (3±1) at.% Li, and (1±0.7) at.% Mg. (c) Corresponding combined proxigram composition profile for T1 with the chemical composition of (14±1) at.% Cu, (14±2) at.% Li, (3.8±1) at.% Mg, and (0.8±0.4) at.% Ag.
(a)
(b)
(c)A combined proxigram profile for severalT1 platelets is shown in Figure 5(c). The chemical compositions for the T1 platelets was found to be (14±1) at.% Cu, (14±2) at.% Li, (3.8±1) at.% Mg, and (0.8±0.4) at.% Ag. This confirms both the deviation from Al2CuLi stoichiometry and potential enrichment of the T1 phase with Mg. By considering the current model proposed by Cassada et al. [7], the precipitation of the T1 phase on the {111} Al planes requires the presence of one or more partial dislocation bounded by a stacking fault. Because the stacking fault energy (SFE) of Al is very high, the dissociation of dislocations into partials is believed to be necessary for nucleating the T1 phase. This can be facilitated by elements known to decrease the SFE of Al and among these elements Mg and Ag have been found to be highly effective [24]. Regarding the effect of Mg enrichment inside the T1 platelet on the mechanical properties of the alloy, it has been shown that single addition of Ag in Al-Cu-Li-Zr alloy had no effect on the age hardenable curve, while Mg addition significantly raises the peak hardness and shortens the time to the peak [6]. The peak hardness further increases when Ag is added together with Mg. This effect is explained as follows. In a case of single addition of Ag, the T1 platelet nucleated only on dislocation loop around a Zr dispersoids. In contrast, Mg addition has been revealed to cause the formation of octahedral microvoids and new GP zones on {111} Al planes; and these act as nucleation sites for the T1 phase providing a fine dispersion and hence increase the hardness of the system. Thus, it can be concluded that Mg and Ag are known to aid the precipitation of T1 phase and hence improve the hardness of the alloy. The distribution of these elements in the structure of the T1 platelets as well as their portioning between precipitates and matrix is the subject of conflict report [25].


## 3.2.3. LEAP Analyses at 22 K and 18% of Pulse Fraction

The use of the wider field of view of the detector in the LEAP permits the collection of larger datasets. Furthermore, using a different machine allows determining any device specific artifacts.A top view of the reconstructed volume of a sample analyzed by a LEAP in voltage mode at 22 K and 18% pulse fraction is shown in Figure6(a). The intersections of three T1 platelets with the (111) pole are visible. According to the proxigram (Figure 6(b)) from 8 at.% Li isoconcentration surface of these platelets, this analysis yielded the close values for the chemical compositions of the T1 platelets, with (14.3±2) at.% Cu, (15.5±3) at.% Li, (2.5±1) at.% Mg, and (0.8±0.5) at.% Ag, as LAWATAP analyses.Figure 6
LEAP analysis at 22 K and 18% of pulse fraction. (a) Top view of the reconstructed volume of a sample shows the intersections of theT1 platelets with the (111) pole. (b) Corresponding combined proxigram composition profile for T1 with the chemical composition of (14.3±2) at.% Cu, (15.5±3) at.% Li, (2.5±1) at.% Mg, and (0.8±0.5) at.% Ag.
(a)
(b)One should note that the observation of theβ′Al3Zr precipitates has not been recorded in APT analysis. This is simply due to the fact of the large diameter and small number density of this phase in the microstructure, which make the APT analyses challenging.The combination of results from different atom probes at different experimental conditions, even including laser based results from Gault et al. [14], suggests that the actual chemical composition for the thin T1 platelets could differ from the Al2CuLi of the stable bulk phase, since changing the parameters should induce a change in the significance of the artifacts. Furthermore, it seems unlikely that the artifacts would only influence the Cu detection for the T1 platelets but not the θ′ platelets. Even if one assumes that Li changes the evaporation behavior of Cu, it is difficult to understand why it should not also affect Al and thus negate this effect. Such an effect should also result in an extremely decreased atomic density, since about half of all otherwise detected atoms would be missing. But this is not observed at the platelet positions according to the density profiles of the cylinders perpendicular to these thin platelets. In fact, the average difference between the detected atoms in the matrix and the precipitates dose not exceed 32 atoms.In conclusion, it seems reasonable to propose that the concentration in theT1 phase is indeed nonstoichiometric after treatment of the samples in the T8 condition. This finding is also supported by high angle annular dark field scanning transmission electron microscopy (HAADF) STEM and small angle X-ray scattering (SAXS) results from Donnadieu et al. [26]. In this study the authors investigated a similar alloy, conducting a similar thermomechanical treatment. The observed microstructure also consists of a homogenous distribution of thin platelets precipitates with 1 nm thickness and parallel to (111) Al planes. They noted that the composition of the layers of the thin T1 precipitates may deviate from the Al2CuLi stoichiometry of the stable bulk phase and proposed that this may be either due to the presence of higher Al content than would be expected for the T1Al2CuLi or due to the nature of the interface planes. Their results reported Al content higher than expected for T1Al2CuLi phase and the occurrence of matrix/T1 interface on Al-Cu mixed layer instead of Al-Li layer. The authors also suggested that the actual atomic structure of the thin T1 platelet could present stoichiometry different from that for the bulk T1 phase. With regard to the atomic structure of the bulk T1 phase, several models have been proposed. The first model is proposed by Huang and Ardell [27]. According to this model, the T1 phase structure consists of a stack of hexagonal layers similar to {111} Al planes. The basal plane and the medium one (z=0 and 1/2) are formed by a mix of Al-Li layer, while the inner planes (z=1/4 and 3/4) are hexagonal layers of Cu and Al atoms. The second proposed model of the structure of the T1 phase has been made by Howe et al. [28]. In this model, the authors suggested that the basal plane (z=0) is formed by Al layer, while the medium one (z=1/2) is made of Li atoms. The inner planes (z=1/4 and 3/4) are somewhat similar to that in Huang and Ardell model. The third structure of the T1 phase has been proposed by Van Smaalen et al. [29]. Their proposed structure displays mix of Al-Li layers for z=0 and z=1/2, which are corrugated, while the inner layers are corrugated Al-Cu layers. The Huang and Ardell study [27] was, until very recently, the generally accepted structure for the T1 phase. However, the two recent and independent studies, by Donnadieu et al. [26] and Dwyer et al. [30], determined that the structure of the thin T1 platelets embedded in Al matrix was actually very close to that of the bulk T1 phase proposed by Van Smaalen et al. [29]. But the case might be different for the T1 precipitates with the thickness less than one unit cell. Thus, it can be concluded that although Van Smaalen et al. [29] structure provides the basis for the structure of the T1 precipitates, for the earliest stage of precipitation, modifications may occur.On the other hand, more recent APT study proposed by Araullo-Peters et al. [25] reported the presence of the T1 precursor at the early stage of ageing. However, the observed T1 platelets in this study are between 5 and 10 nm in thickness with the chemical compositions different from that for the bulk T1 phase.In particular, our results demonstrated the presence of lower Li and Cu contents with 1 : 1 ratio in the thinT1 platelets. These results confirm the fact of the Al content higher than what would be expected for this phase. As far as the matrix/T1 interface is considered, APT is more appropriate tool to investigate the local chemistry at the interface. Figure 7 displays a higher magnification image for the T1 platelet. It can be seen that the density of Cu atoms at the matrix/T1 interface is higher than that for Li atoms. Moreover, the correlation between Mg and Li atoms is clearly visible. This observation confirms the assumption of the occurrence of the matrix/T1 interface on Al-Cu layer instead of Al-Li layer and the consumption of the first compact Al-Li layer in the nucleation of the T1 phase. It comes out then that the composition of the T1 precipitates deviates from that of the stable bulk phase. The deviation of the T1 phase from thermodynamic equilibrium composition for the stable bulk phase suggests that the T8 condition is corresponding to the thermodynamical nonequilibrium condition. The obtained microstructure in this condition has appreciable supersaturation of defects, which means that the nucleation and growth of different phases are still at their intermediate stages.Figure 7
The magnified view of theT1 platelet showing the density of Cu, Li, and Mg atoms at the matrix/precipitates interface.


## 4. Conclusion

This paper reports a characterization of the commercial aluminum-lithium-copper alloy AA2195 in the T8 condition using electron microscopy and atom probe tomography. The results confirm that the microstructure of the alloy in this temper state consists of platelet-shapedT1Al2CuLi,θ′Al2Cu, and spherical β′Al3Zr precipitates.Owing to the ability of atom probe tomography to resolve the chemical position on a subnanometer scale, compositional analyses of thin platelet precipitates (less than 2 nm) have been performed. The measuredθ′ stoichiometry is consistent with the expected Al2Cu equilibrium composition with a significant partitioning of Li atoms within this precipitate. For the T1 platelets, a deviation from the stoichiometric Al2CuLi of the bulk phase was observed. This phase is enriched with Mg atoms without any indication of the presence of Mg and Ag atoms at the phase/matrix interface. The off-stoichiometry of the thin T1 platelet cannot be simply attributed to artifacts in the APT measurements and might be considered as a true deviation from the thermodynamic equilibrium composition of the thin T1 platelets for the stable bulk phase.



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*Source: 647468-2015-06-22.xml*