ABSTRACT

Aluminum-based alloys play a key role in modern engineering and are widely used in construction components in aircraft, automobiles and other means of transportation due to their light weight and superior mechanical properties. Introduction of different nano-structure features can improve the service and the physical properties of such alloys. An improvement of an Al-based alloy has been performed based on the understanding of the relationships among compositions, processing, microstructural characteristics and properties. Knowledge of the decomposition process of the microstructure during the precipitation reaction is particularly important for future technical developments. The objective of this study is to investigate the nano-scale chemical composition in the Al-Cu, Al-Li and Al-Li-Cu alloys during the early stage of the precipitation sequence and to describe whether this compositional difference correlates with variations in the observed precipitation kinetics. Investigation of the fine scale segregation effects of dilute solutes in aluminum alloys which were experienced different heat treatments by using atom probe tomography has been achieved. The results show that an Al-1.7 at.% Cu alloy requires a long ageing time of approximately 8 h at 160˚C to allow the diffusion of Cu atoms into Al matrix. For the Al-8.2 at.% Li alloy, a combination of both the natural ageing condition (48 h at room temperature) and a short artificial ageing condition (5 min at 160˚C) induces increasing on the number density of the Li clusters and hence increase number of precipitated particles. Applying this combination of natural ageing and short artificial ageing conditions onto the ternary Al-4 at.% Li-1.7 at.% Cu alloy induces the formation of a Cu-rich phase. Increasing the Li content in the ternary alloy up to 8 at.% and increasing the ageing time to 30 min resulted in the precipitation processes ending with δ' particles. Thus the results contribute to the understanding of Al-alloy design.

Keywords:

Phase Decomposition, Atom Probe Tomography, Early Stage of Precipitation

1. Introduction

Aluminum of high purity in an annealed condition has a low strength near 10 MPa [1] . Generally, pure metals are strengthened by the introduction of obstacles (i.e., any inhomogeneity) in their microstructures to pin dislocations. Thus, the introduction of solute atoms into the Al matrix is considered to be an important method to improve conventional Al alloys. Adding solute atoms to a solid solution in the solvent atom’s lattice typically produces an alloy that is stronger than pure Al due to the differences in the radius, modulus and valance between the Al matrix and the solute atoms [2] . In general, the solute must have an appreciable solid solubility in the matrix at the annealing temperature, and has also to remain in the solid solution after slowly cooling and must not be removed by reacting with other elements in the alloy [1] . Additions of Li and/or Cu to Al have been identified as an efficient strategy to improve the strength in age-hardenable or heat-treatable Al alloys via the precipitation hardening phenomenon.

The formation of precipitates, nano-scale structure features which are formed during the fine-scale segregation of dilute solutes, in a metal’s microstructure during ageing occurs in many different ways. After quenching from a solid solution, the microstructure of Al alloys typically contains regions of solute segregation or solute-atom clusters. These clusters gradually transform into semi-coherent and non-coherent second-phase particles during artificial ageing [2] . The size, shape, volume fraction and coherency of the second phase precipitates determine the precipitation hardening of an alloy. These required parameters depend on the ageing temperature and ageing time. Thus, investigation of the precipitation kinetics in Al alloy is important.

The scale of the microstructures in modern metallic materials is becoming increasingly smaller [3] . A discussion of microstructures at such a small dimension is typically based on crystallographic structures and chemical characteristics relevant to the structure. However, this type of discussion was not possible until the development of more advanced tools, such as transmission electron microscopy (TEM) and electron energy loss spectroscopy (EELS). However, all of these advanced techniques have limitations when analyzing nano-scale particles embedded in a matrix phase. The atom probe tomography (APT) technique, particularly in its current form, has a truly quantitative analytical capability to characterize nanometer-scale particles in a metallic system. Thus, it has been used to investigate nano-scale microstructural evolution for binary Al-Cu, Al-Li alloys and ternary Al-Li-Cu alloys at the early stage of decomposition.

The binary Al-Cu alloy is a well-studied precipitation system and forms the basis for a wide range of age-hardenable alloys that are technologically important. The model for describing the fundamentals of the precipitation sequence in the binary Al-Cu alloy is [4] :

The presence of Cu-rich groups of atoms that were coherent with the {100} atomic planes of the Al matrix has been discovered by Guinier and Perston [5] . Based on this, GPI and GPII are the coherent zones, which were named by their discoveries, i.e. Guinier and Perston. Later, studies showed that the GPI zone could be described as consisting of a single layer of Cu atom on the {001} Al planes, while the structural model of the GPII zone consists of two Cu {002} layers separated by three Al planes with the stoichiometry of [6] [7] . The metastable θ' phase, is considered to be the primary strengthening phase, has a body-centered tetragonal crystal structure with the stoichiometry Al₂Cu [8] . The precipitation sequence ends with the transformation of θ' into the incoherent equilibrium θ phase (Al₂Cu), which exhibits a tetragonal C16 crystal structure.

The increasing use of Al-Cu alloys in commercial applications requires further studies of the properties of the system and in particular the primary strength phase (i.e., the θ' phase). Relatively speaking, little is known about the compositional evolution of θ' compared to its properties. There are few studies in the literature on the presence of small, disordered clusters of atoms prior to the formation of GP zones. Because commercial optimization tools rely upon accurate predictions of alloy microstructures as functions of heat-treatment conditions, it is important to investigate the influence of nano-scale chemical compositions on precipitation kinetics.

The early stages of phase decomposition of Al-Li binary alloys have been reported to be a subject of controversy [9] . Earlier studies by electron microscopy [10] [11] reported that the precipitation process of this system is quite simple:

where SSS is an abbreviation of “super saturated solid” solution, δ' is the Al₃Li metastable phase with an structure, and δ is a stable phase with a B32 structure. The TEM images of the as-quenched alloy show a high density of small δ' precipitate particles; thus, it was found that the δ' phase formed during quenching after the solution heat treatment [9] . Controversy on the phase decomposition of this system arose from the presence of disordered GP zones prior to the precipitation of the phase or not. On the other hand, a selected area diffraction pattern (SADP) from the as-quenched alloys showed strong L1₂ ordering spots, which suggest the presence of δ' particles from the beginning of the process [10] [11] . Khachaturyan et al. [12] suggested different transformation paths in this alloy system and investigated transformation from a solid solution to an L1₂ phase using the mean field approximation; they suggested that a solid solution decomposes into an ordered structure without any composition change (i.e., congruent ordering) and that this ordered structure is further separated into Li-rich, ordered δ' regions and Li-depleted, disordered regions via a spinodal decomposition. There are two models of congruent ordering: Nucleation and growth of the ordered domains, and spontaneous homogeneous ordering. In either case, the quenched SSS should order congruently before the spinodal decomposition proceeds. To prove this transformation path, it is important to show the presence of the congruent order before the compositional fluctuation appears. Different studies have investigated this phenomenon [12] - [14] . The primary conclusion that has been drawn from all of these studies is that the kinetics of decomposition are too rapid to be followed by high-resolution techniques such as high-resolution transmission electron microscopy HRTEM. Thus, our objective in this study is to examine the microstructure at the early stage of decomposition in an Al-Li alloy to determine the presence of atom clustering or fine segregation. Because a subtle variation in the heat-treatment condition can exert considerable influence over the volume fraction of already formed δ' particles during subsequent precipitation reactions, APT analyses were performed to investigate the precipitation behavior after applying the heat treatment conditions in Table 1.

Al-Li-Cu alloys typically exhibit high strengths and good mechanical properties compared to Al-Li alloys. Due to their superior mechanical properties, these alloys are typically used in applications where strength is the limiting factor in the design. The experimental data for Al-Li-Cu systems is primarily concentrated in the Al corner of the phase diagram [15] . The first systematic study of the phase equilibria in Al-Li-Cu systems was performed by Hardy and Silcock [16] , who reported on a total of six ternary solid phases. The solidus and solvus temperatures were determined for different ternary Al-Li-Cu alloys with different compositions [17] . The thermodynamic properties of the phases in this system were studied by different researchers [18] [19] . The T₁(Al₂LiCu) phase is the primary strengthening phase in Al-Li-Cu alloys and is formed congruently near 695˚C [20] . The hexagonal crystal structure of the T₁ phase was first proposed by Hardy and Silcock [16] . The T₁ phase formation was assumed to occur via direct nucleation and growth from a saturated Al solid solution following a stacking fault mechanism [21] . Refinement of the hexagonal structure of Al₂LiCu was achieved using single-crystal X-ray diffraction by Van Sammleen [22] . Semi-coherent and incoherent precipitation of the T₁ phase was detected and reported in reference [23] without any indication of the presence of quenched vacancies.

The determination of precipitation behavior is typically performed using an advanced technique such as APT for specimens that have experienced different conditions.

However, it is difficult to ensure an accurate following of the precipitation sequence due to the complexity caused by the nucleation stage. The competition between different phases in the binary and ternary system increases the challenge for any phase analysis. Co-precipitation is usually dominated by the phase that can minimize the interphase boundary energy and form at defects that can assist in the reduction of the nucleation energy barrier [24] . The simultaneous formation of different phases usually occurs when they are disparate, preferred sites; then, the competition would be for solutes that are necessary for growth; if a phase is metastable, it would dissolve during competitive growth and at the same time, the more stable phase would continue growing. Thus, it is necessary to follow precipitation sequence in the binary Al-Cu, Al-Li alloys and ternary Al-Li-Cu alloys at the early stages of the decomposition of the microstructure.

The objective of this study in the context introduced above is to investigate the nano-scale chemical composition in the Al-Cu, Al-Li and Al-Li-Cu alloys during the early stage of precipitation sequence and to describe whether this compositional difference correlates with variations in the observed precipitation kinetics. Knowledge of the decomposition process itself is particularly important for future technical developments.

2. Material and Methods

Three different alloys with different chemical compositions were prepared and heat-treated. The first alloy was an Al-1.7 at.% Cu alloy. The ingot of this alloy was prepared from high purity materials. Al and Cu shots were arc-melted under an Ar atmosphere. Melting was repeated using inert-gas induction melting in a carbon crucible to ensure good mixing of the elements. The second alloy was an Al-8.2 at.% Li alloy, which was bought as a master alloy due to the difficulty of its lab preparation; this difficulty was caused by the high diffusion coefficient of Li in the melt, which causes Li to typically fluidize on the top of the melt. The third alloy was an Al-4 at.% Li-1.7 at.% Cu alloy that was prepared by alloying Cu with an Al-4 at.% Li master alloy using induction melting. The inductive melting procedure melted the mixed Al, Cu and Li at the casting temperature (750˚C) for 2 min. All three alloys were cast into plates with dimensions of 30 × 30 × 30 mm³. After casting the samples, they were homogenized for 60 to 70 min at 513˚C in a salt melt (75 wt.% KNO₃, 20 wt.% NaN O₃, 5 wt.% NaNO₂). The samples were cut using a low-speed diamond saw into a rod that was 30 um thick and 30 um long. After cutting the samples, they were re-homogenized at 530˚C for 20 min in high-vacuum quartzite ampules and then quenched in cold water. After water quenching from the homogenization temperature, each alloy was then artificially aged under three different conditions. A summary of the ageing conditions that were used in this study is shown in Table 1 along with their indication names. The abbreviations of the names of the artificial ageing conditions are used in the remainder of this paper. A chart that summarizes the preparation procedure is shown in Figure 1.

To prepare APT specimens, the raw material was first ground to a 200 μm thickness and was then cut into blocks of 15 × 0.2 × 0.2 mm³ using a wire-saw machine.

Needle-shaped specimens were then fabricated using electro-polishing. This electro- polishing procedure was performed in a solution containing 25 vol.% of nitric acid in methanol with a 3 - 5 V DC electric potential. APT analyses were performed in a Cameca LEAP HR 4000 (Local Electrode Atom Probe 4000) in voltage-pulse mode with a pulse fraction of 18% for the Al-Li and Al-Li-Cu alloys, and 15% for Al-Cu alloy. The specimens were maintained at a cryogenic temperature near 22 K for the Al-Li and Al-Li-Cu alloys, and near 30 K for the Al-Cu alloy under ultrahigh vacuum conditions of about Pa. A detection rate of 0.001 ions per pulse was maintained throughout the experiments. Visualization and reconstruction of the data done by using IVAS, a software provided by Cameca. Different algorithms have been applied during the data treatment. These algorithms are: isoconcentration surface [25] , cluster search [26] and the binomial distribution frequency statistics [27] .

3. Results and Discussion

3.1. Al-Cu Alloy

Because APT is capable of resolving nano-scale microstructures including atomic clusters and other fine scale segregation effects, we used APT to analyze the microstructure of the three Al-1.7 at.% Cu alloys, which have been subjected to the three heat treatment conditions shown in Table 1 (i.e., 1 S, 2 S and 3 S). An atomic probe mass spectrum of Al-1.7 at.% Cu alloys that have been aged based on 1 S or 2 S or 3 S shows the presence of some Al ions which were detected as hydrides (i.e.), and some Cu ions which were also detected as hydrides (i.e.). The formation of these hydrides is most likely caused by the residual gas inside the analysis chamber. However, whatever the origin of the hydrogen, it apparently does not affect the analysis because the overall average composition obtained by APT analysis is close to the nominal alloy composition.

Figure 2(a) shows a typical view of Cu-atom distributions from different APT experiments on Al-1.7 at.% Cu alloys that have already been subjected to 1 S or 2 S or 3 S heat treatments. The figure shows that there is no spatial correlation in the distributions of the Cu atoms. Binomial frequency distribution analysis has been used to identify the presence of nano-scale solute-clustering processes and other segregations, which are sometimes difficult to visualize in APT datasets. Using this methodology, the identification of fine-scale solute clustering in the early stage of phase decomposition in the alloy investigated in this study is possible. A detailed explanation of the quantitative binomial distribution analysis of nano-scale atom clustering and segregation in the APT data can be found in reference [28] . The binomial distribution of the Cu atoms in Figure 2(a) is plotted together with the experimental frequency distribution in Figure 2(b), which shows a good agreement between the binomial distribution and the experimental frequency distribution. This suggests homogeneity of the microstructures and thus indicates that Cu has not clustered under these heat treatment conditions. An additional nearest neighbor analysis did also not give any reason to expect the existence of

clusters. To determine when precipitation starts, the ageing time was increased to 30 min, and the ageing temperature to 200˚C. Figure 3(a) shows the APT datasets that were experimentally acquired to evaluate the microstructure for the specimens that were heat-treated by increasing both the ageing time and the ageing temperature. The 3D reconstruction shows the position of Cu atoms. Again, the binomial frequency distribution analysis is used to study the evaluation of the clustering of Cu atoms (Figure 3(b)). The agreement between the binomial distribution and the experimental frequency distribution and analysis of the nearest neighbors suggests homogeneity of the microstructure in this case, too.

The second step in the context of the evaluation of the precipitation sequence in Al-Cu system is to increase the ageing time to 8 h while maintaining the temperature at 160˚C. Applying this ageing condition produced a thin platelet of θ', as shown in the 3D reconstruction in Figure 4(a), where only Cu atoms are shown. A comparison between the binomial distribution and experimental distribution in Figure 4(b) shows a clear shift between the two curves, which is an indication that the Cu atoms are arranging as second-phase particles. The chemical composition of the θ' phase in this case is determined to be (15.2 ± 4) at.% Cu. This is based on the composition profile forms from the isoconcentration surface of 8 at.% Cu (Figure 4(c)).

The absence of clusters of Cu atoms, GP zones and θ' precipitates from the microstructure of the specimens subjected to the three heat-treatment conditions in Table 1 (1 S, 2 S and 3 S) (Figure 2) and from the microstructure of the specimens heat treated with increasing ageing time and ageing temperature (Figure 3) can be explained as follows: The lack of nano-features in this case is based on the vacancy concentrations. It seems that under these heat-treatment conditions, the Cu atoms are not able to cluster

together and thus nucleate and grow; this phenomenon might be due to a diminished excess-vacancy concentration, which arises from vacancy sink sources. Increasing the ageing temperature to 200˚C causes a reduction of the driving force for particle nucleation [29] . Additionally, kinetic limitations during the precipitation sequence in this system are perhaps due to the low diffusivity of Cu into Al (diffusion coefficient D = 0.89 × 10⁻²⁰ m²s⁻¹ at 190˚C) [30] .

The ageing treatment at 160˚C for 8 h produces thin platelet precipitates that were identified as θ' platelets. The low density of the θ' platelets under this ageing condition might be related to the short ageing time (8 h). 20 vol.% θ' precipitates were reported for ageing an Al-4 wt.% Cu alloy for 3.5 days [31] . The transformation of GP zones into θ' precipitates occurred when the ageing time was >48 h [32] . The difficulty of detecting GP zones in the microstructure of the proposed alloy system is owing to the limited resolution of the obtained APT data. The off-stoichiometry of the θ' platelet in Figure 4 stills an open issue. It might be explained due to a limited Cu diffusion and a limited formation of point defects.

Based on the Al-Cu phase diagram [33] , the full sequence of the transition precipitate will be observed only if annealing or ageing is performed below the GP zone precipitate solvus (i.e., nearly 100˚C) with a long ageing time due to the low diffusivity of Cu into Al. The large diameter and small density of the different precipitates represent other challenges to analyze in the complex precipitation sequence in Al-Cu systems.

3.2. Al-Li Alloy

APT has been used to analyze Al-8.2 Li at.% alloys that have been subjected to the three stages of heat treatment (i.e., 1 S, 2 S and 3 S) shown in Table 1. Example of the APT datasets which were experimentally acquired for the specimens under the 1 S or 2 S ageing conditions to examine the evolution of the microstructure at the early stage of decomposition is shown in Figure 5(a). Comparing the binomial distribution and the experimental distribution in Figure 5(b) shows a marginal shift between the two curves.

It seems that individual applying of the natural annealing condition and individual applying of the artificial ageing condition at 160˚C for 5 min alone does induce the formation of small clusters of Li atoms. These are observed in the microstructure after applying the cluster-search algorithm on the dataset with and order number of 3 for Li atom. A statistical calculation based on findings from applying cluster search algorithms show that the microstructure under 1 S and 2 S heat treatment conditions contains Li clusters with size of (1.3 ± 0.3) nm, chemical composition of (20 ± 1.5) at.% Li and number density ranges between 3 - 4 × 10²³ m⁻³ (Figure 5(c)). It worth to mention, that the selection of cluster search parameters was performed based on nearest neighbor investigations [27] that examine the interatomic separation in the immediate vicinity around each Li atom. The distribution distances separating each Li atom and the nearest other Li atoms in Al-8.2 at.% Li dataset compare to the distances that would be expected if the atoms in solution were random is shown in Figure 6.

However, the shift between the binomial and experimental distributions becomes more pronounced when the specimen is heat-treated under the 3 S ageing condition (i.e., a combination of natural and artificial ageing), as shown in Figure 7. The experimental distribution calculated from the reconstructed volume in Figure 7(a) is shown to be shifted to the left compared to its corresponding binomial distribution (Figure 7(b)). Thus, the presence of second-phase particles can expect in this microstructure. Applying the cluster-search algorithm on the dataset in Figure 7(a) (with the same cluster search parameters as in Figure 5) shows the presence of Li atoms clusters with size of (2.1 ± 0.2) nm and chemical composition of (22.2 ± 1) at.% Li (Figure 7(c)). The number density of Li clusters under this aging condition is recorded as 6 × 10²³ m⁻³. It is worth notable that the number density of Li clusters in the microstructure under 3 S heat treated condition is higher than that in the microstructure under 1 S or 2 S heat treated conditions by around two orders of magnitude.

The presence of second-phase particles or clusters of Li atoms from the microstructure of the samples heat treated with 1 S and 2 S conditions (Figure 5) is expected because a number of studies reported the presence of δ' particles in quenched samples [9] [13] . For our case, observation of these particles has been recorded statistically based on applying the cluster-search algorithm to the datasets (Figure 5(c)). A possible explanation for the observation in Figure 5 can be a high concentration of vacancies in the microstructure. It has been reported that in Al-Li systems, quenched vacancies and thermal vacancies play important roles in the kinetics [34] . An import factor in controlling the kinetics when ageing after quenching is solute-vacancy binding, where the suggested path is that vacancies become coupled to Li atoms during quenching. Ceresaraa et al. [34] claims that vacancy-Li couples can be reduced during quenching at the recovery stage in case of Al-0.38 at.% Li alloy. However, this recovery procedure is unexpected in our respective alloy with high supersaturation of Li (8.2 at.%). The presence of a sufficient density of δ' particles (or Li clusters) in the microstructure of our naturally aged sample can be explained by the coupling of Li atoms with quenched vacancies, while thermal vacancies play an important role when the specimen is aged at 160˚C for 5 min, i.e. under 2 S condition. The microstructure of specimen under the combination of natural and artificial ageing conditions contains a higher number density of Li clusters. This could be explained by the higher density of quenched vacancies that start clustering during the natural aging. The thermal vacancies during the artificial aging contribute then to the formation of the δ' particles, as shown in Figure 7(c).

3.3. Al-Li-Cu Alloy

To understand the early stage of decomposition of the microstructure of ternary Al-4

at.% Li-1.7 at.% Cu alloy, APT experiments were performed for the specimens that were heat-treated based on the three stages (1 S, 2 S and 3 S) shown in Table 1. In figure 8, a typical Cu and Li atom maps are provided, which are from APT experiments on the ternary alloy that were subjected to 1 S and 2 S ageing conditions. Similar to the situation in Figure 2 and Figure 5 for Al-Cu and Al-Li alloys, which have experienced the 1 S and 2 S ageing conditions, the absence of inhomogeneity in the microstructure is shown in Figure 8(a); this is also confirmed by comparing the binomial distribution to the experimental frequency distribution in Figure 8(b). No shifting between the two curves of the Li and Cu atoms is found, which supports assuming the absence of any clustering or solute-atom segregation under these conditions. Nearest Neighbor analyses for Li and Cu also do not show any signs of clustering. The possible explanation of this observation is the low vacancy concentrations which might delay the clustering event.

Conversely, the reconstructed volume of the specimen that was heat-treated under the 3 S ageing condition in Figure 9(a) shows an inhomogeneous distribution, particularly for Cu atoms. The experimental distribution calculated from this reconstructed volume is shown in Figure 9(b). The experimental distribution for the Cu atoms is shifted to the left, while the difference is smaller for the Li atoms. Applying the isoconcentration procedure in the reconstructed volume in Figure 9(a) visualizes enriched

region of Cu atoms that is decorated sparsely with Li atoms. The chemical composition of this enriched region is shown in Figure 9(c). Based on the quantitative analysis in Figure 9(c), the chemical composition of the Cu-enriched region (from the isoconcentration surface of 22 at.% Cu) is (33 ± 1) at.% Cu, (5.3 ± 1) at.% Li. Thus, the Cu-enriched region can be identified as a θ' precipitate.

The equilibrium phases in Al-Li-Cu phase diagram [15] for the compositions of interest are T₁, T₂ and T₃. However, none of these phases have been detected in the APT analyses performed (Figure 8 and Figure 9); this result could be explained by the similarity of the precipitation processes in both Cu-rich alloys and binary Al-Cu alloys [35] . The presence of Li atoms might modify the orientation relation and structure of the homogenously nucleated zone [10] . The Li atoms are also known to enhance the precipitation of the θ' phase, as shown in Figure 9(c). Based on this analysis, it can be concluded that the early stage of the ternary Al-4 at.% Li-1.7 at.% Cu alloy starts by the precipitation of the θ' phase which is enriched with Li, and thus would be transfer to the phase at the later stage of ageing.

To investigate the influence of changing the composition on the precipitation behavior, a new ternary alloy with a nominal composition of Al-8 at.% Li-1.7 at.% Cu was prepared based on the preparation procedure shown in Figure 1. Only the 3 S ageing condition was applied. Different from the situation in Figure 9(a), the microstructure of this specimen is rather homogenous (Figure 10(a)). No difference between the binomial and experimental frequency distributions for both Cu and Li atoms was detected (Figure 10(b)). A nearest neighbor analysis also showed no clustering. The

homogeneity of the microstructure in Figure 10 is likely caused by Li atoms that, with their high vacancy binding energy (0.26 eV), block excess vacancies and postpone or prevent the precipitation reaction of Cu. However, increasing the ageing time to 30 min for this alloy drastically changes the outcome; in this case δ' are clearly present in Figure 10(c). The deviation from the binomial distribution is shown in Figure 10(d), indicating that Li atoms are not fully homogenously distributed in the matrix. Thus one can conclude that a marginal change in the ageing time induces the precipitation of δ' particles, and that the solubility of Li in Al does not seem to be affected by the presence of Cu atoms.

Finally, from this comparison of the three studied samples, it is clear that the θ' phase is the dominant phase in the binary Al-1.7 at.% Cu alloy, while the δ' is the dominant one in the binary Al-8.2 at.% Li alloy. On the other hand, in the ternary Al-4 at.% Li-1.7 at.% Cu alloy, the microstructure decomposition ends up with the formation of Cu-rich phase (the θ' phase), while increasing the Li content in this ternary alloy up to 8 at.% induces the formation of δ' particles.

4. Conclusions

In this study, an APT method with a comparing between binomial frequency distribution and experimental frequency distribution that quantifies the deviation from the random has been proposed to investigate the early stage of decomposition of the microstructure of a binary Al-1.7 at.% Cu alloy, a binary Al-8.2 at.% Li alloy and a ternary Al-4 at.% Li-1.7 at.% Cu alloy.

Atomic resolution microscopy experiments in conjunction with a statistical test demonstrate that the phase decomposition in Al-1.7 at.% Cu alloy requires a long ageing time of approximately 8 h at 160˚C to allow the diffusion of Cu atoms into Al matrix. For the Al-8.2 at.% Li alloy, a combination of both the natural ageing condition (48 h at room temperature) and a short artificial ageing condition (5 min at 160˚C) increases the size and the number density of the observed δ' particles. Applying this combination of natural ageing and short artificial ageing conditions onto a ternary Al-4 at.% Li-1.7 at.% Cu alloy induces the formation of a Cu-rich phase (i.e., the θ' phase). Increasing the Li content in the ternary alloy up to 8 at.% and increasing the ageing time to 30 min resulted in the precipitation processes ending with δ' particles.

A key strength of the demonstrated APT based approach is the ability to identify and quantify the fine-scale segregation effects of dilute solutes in Al alloys; this supports the understanding of precipitation behavior in this important technical material.

Acknowledgements

Prof. Talaat Al-Kassab (Associate Professor of material science and engineering, King Abdullah University of Science and Technology), Prof. Ferdinand Haider (professor at University Augsburg, Inst. f. Physics) and Pascal Niebecker (PhD student at Technische Universität München) are gratefully acknowledged. M. Khushaim gratefully acknowledges financial support provided through King Abdullah University of Science and Technology (KAUST) base-line funding program.

Cite this paper

Khushaim, M. and Boll, T. (2016) Experimental Investigation of the Early Stage of Precipitation on Binary Al-Li, Al-Cu Alloys and Ternary Al-Li-Cu Alloys by Means of Atom Probe Tomography. Open Journal of Metal, 6, 25-44. http://dx.doi.org/10.4236/ojmetal.2016.62003

References