Research Article | Open Access
Microstructural Changes and Mechanical Response of Aluminum-Based Composites Prepared with Dispersed CeO2 Nanoparticles
The effect of CeO2 nanoparticles on the microstructure of two different metal matrixes, AA2024 aluminum alloy and pure aluminum, were studied. The aluminum-based composites were synthesized by mechanical milling and subsequently sintering at 550°C under an argon atmosphere. The microstructural evolution of consolidated composites was evaluated by scanning electron microscopy, transmission electron microscopy, and X-ray diffraction. The experimental results revealed that the addition of CeO2 nanoparticles in the AA2024 alloy produced a dispersed needle-like Ce-Cu-rich phase that reduces the hardness of samples after sintering. On the contrary, the dispersion of CeO2 in pure aluminum shows significant improvement of hardness in comparison with the reinforced and unreinforced AA2024 aluminum alloy. During the sintering, the CeO2 nanoparticles show higher chemical stability in the aluminum matrix in comparison with the AA2024 matrix.
Aluminum and its alloys are attractive alternatives to replace some ferrous materials in many industrial applications because of their intrinsic properties, such as good machinability, surface finish capabilities, damage tolerance, low density, high specific strength, and good thermal and electrical conductivity [1–6]; all the above is combined with good mechanical properties. Aluminum alloys are excellent candidates for the synthesis of metal matrix composites (MMCs). Here, the addition of nanoparticles for the synthesis of MMCs combines the high ductility and low density of the metallic matrix with the beneficial hardness and stiffness of reinforcement particles, resulting in the generation of advanced materials with an excellent mechanical response .
For aluminum reinforcement, several metal oxide particles are excellent options to take into account. Moreover, the addition of oxides at the nanometric scale can improve the mechanical properties of the MMCs by reducing the interparticle spacing. Unfortunately, fine particles present a higher tendency toward heavy agglomeration. The strengthening mechanisms, i.e., nanoparticles addition, have a strong relationship based on their type, size, morphology, volume fraction, and distribution, as well during the composite synthesis.
From the wide variety of synthesis routes to prepare MMCs, the solid routes based on powder metallurgy (PM) provide better results regarding their versatility and ability to produce homogeneous dispersions of secondary phases into the aluminum matrixes. The PM process involves the mixing of reinforcement particles with the metal matrix (in powder form), followed by cold consolidation and sintering steps. The mechanical response of aluminum and its alloys can be enhanced with the use of mechanical alloying (MA) and/or mechanical milling (MM) techniques.
There is an increased interest for the development of advanced materials using some aircraft grade aluminum alloys as the metal matrix of composites preparation. The AA2024 aluminum alloy is extensively used in the aerospace industry due to their high strength, excellent wear resistance, lightweight, and good casting characteristics . At present, some research is conducted looking for improving the physical characteristics, mechanical properties , and corrosion resistance [9–11] of aluminum alloys by Ce addition. Due to the above, the AA2024 alloy constitutes an excellent candidate as a metal matrix to be reinforced with CeO2 nanoparticles.
In the present study, two metallic matrixes were selected: pure aluminum and a commercial AA2024 aluminum alloy. The aim of the present work is to study the effect of CeO2 nanoparticles dispersion on the microstructure of pure aluminum and AA2024 aluminum alloy, investigate the stability of these nanoparticles, and observe their interaction with the alloying elements.
2. Materials and Methods
The CeO2 nanoparticles were dispersed in two different aluminum-based materials by the mechanical milling route. Pure Al powder and AA2024 burrs (Table 1) were used as metal matrixes. The commercial CeO2 nanoparticles and Al powder (purity 99.5%) were supplied from Alfa Aesar company. For composite preparation, CeO2 nanoparticles were used in a concentration of 5 wt. percent. The weighted mixtures were processed in a hardened steel vial filled with 3 balls of 13 mm and 3 balls of 11 mm (in diameter) with a ball-to-powder ratio of 5 : 1 (in wt.), and the vial was sealed under an argon atmosphere. The MM process was performed at room temperature in a high-energy ball mill SPEX 8000M. The milling time was set to 3 h. Methanol was used as a process control agent (to avoid agglomeration of the highly ductile Al particles). Some consolidated composites were fabricated by uniaxial cold pressing at 900 MPa during 60 s. The compacted samples in the cylindrical form of 5 mm in diameter were then sintered for different times (1 to 7.5 h) at 550°C under an argon atmosphere with a heating rate of 50°C/min. The characterization was done through scanning electron microscopy (SEM) in a JEOL JSM-7401F and a Hitachi SU3500 microscope, both coupled with an energy dispersive spectrometer, and the transmission electron microscopy (TEM) was carried out with a JEOL-JEM2200FS device. The microhardness testing was performed on the consolidated composite samples using a Leco Microhardness tester LM 300AT under 200 g load and 10 s of dwell time.
3. Results and Discussion
3.1. Powder Characterization
Figure 1(a) shows a representative TEM image from the as-received CeO2 particles. The size of the CeO2 nanoparticles is in the range of 10–50 nm. The elemental EDS analysis performed on the nanoparticles confirms the composition of the cerium oxide, and the C content came from the carbon film that supports the sample. Figure 1(b) shows the XRD patterns from the CeO2 nanoparticles. The nanoceria presents a single-phase with a fluorite-type crystallographic structure. All peaks were indexed as CeO2 (ICDD 034-0390 card) with a lattice constant of 5.411 Å and Fm-3 m space group.
Some dark-field TEM micrographs of the AA2024-CeO2 and the Al-CeO2 are presented in Figure 2. Figure 2(a) shows two dark-field TEM images of the AA2024-CeO2 powder composite after 3 h of milling. Many bright rounded-like phases uniformly dispersed into the aluminum matrix are observed. The EDS-TEM analyses and elemental mapping show that rounded bright phases have a high Ce and Cu concentration in comparison with the aluminum matrix. Pandey et al.  reported in their work the grain refiner effect of the nanoceria addition in a Cu-Al-Ni shape memory alloy. The authors observed a nearly uniform distribution of CeO2 on the Cu-based alloy; furthermore, Cu favours the dissolution of CeO2. Based on this evidence, it is suggested that Al and Cu of the AA2024 alloy could reduce the CeO2, forming a Cu-Ce phase. On the other hand, Figure 2(b) shows that Ce-rich phases found in the pure aluminum matrix present a faceted morphology, noticeably different to the first observed (Cu-Ce phases).
3.2. Microstructural Characterization of Bulk Composites
Figure 3 shows some SEM micrographs exhibiting the microstructural evolution of AA2024-CeO2 composites at different sintering times (1 to 7.5 h). A bright phase is present in the microstructure of all samples; however, the volume fraction and size of these bright phase increase and its morphology changes from irregular to a needle-like shape after 2 h of sintering. A noticeable variation on the porosity as a direct function of the sintering time was also observed.
The chemical composition of the bright phase observed in Figure 3 was analyzed by SEM elemental mapping (Figure 4). The formation of needle-shaped Ce-Cu-rich phases in the bulk AA2024-CeO2 composites was confirmed. Tian-Jiao et al.  investigated the influence of CeO2 addition on the microstructure and tensile properties of the AA2024 alloy, reporting that cerium (IV) oxide can be reduced partly to metallic cerium by aluminum, and new phases such as Al3Ce and CeCu2 are formed during cerium interactions with aluminum and copper. After a relative short sintering time, the affinity of Cu with Ce, which was enhanced during the milling process, remains after sintering (Figure 2(a)). According to the elemental mapping, the needles contain an important concentration of Ce, Cu, and Si. In addition, a graph with the hardness of AA2024-CeO2 composites is presented in Figure 4. A tendency for reduction of hardness as a function of sintering time is observed. The well-known solid solution strengthening mechanism provided by Cu and Si in the AA2024 alloy is reduced because of their affinity with Ce inducing a negative effect on the mechanical response of composites as will be explained below.
Copper plays an important role in strengthening aluminum aircraft alloys such as AA2024-T6 due to the precipitation strengthening phenomena occurred during solution and artificial aging. The amount, distribution, and size of the precipitated phase play an important role in the strengthening rate, depending largely on the composition and processing route of the alloys , affecting the mechanical properties of the alloy. Hence, it is expected a negative effect on the mechanical performance of the AA2024 alloy due to the chemical affinity between Cu and Ce, which form phases that alter the kinetics of precipitation of AlCuX solutes. In addition, the morphology of the phases creates a high density of stress concentrator zones with undesirable effects on ductility and hardness.
The images from Figure 5 show the microstructure of Al-CeO2 composite after sintering at 550°C during 3 h. In the SEM image of Figure 5(a), a homogeneously dispersed bright phase with irregular and rounded morphology in the form of agglomerates, lesser than 5 µm in size, is observed. The EDS analyses corroborate the composition as a Ce-rich phase (yellow square in Figure 5(a)). In comparison with the AA2024-CeO2 composite, the needle-like phase is not observed, even after 3 h of sintering. Perez-Bustamante et al.  reported the effect of Al-6Ce-3La (ACL) master alloy additions on the AA7075 powder alloy. They found the presence of large needle-like Ce-La phases in the ACL master alloy. The use of mechanical milling to incorporate the ACL master alloy into A7075 had a positive effect on the reduction of needle-like morphology; however, the microstructural evolution at sintering temperatures was not evaluated.
Some TEM observations were carried out on the above-mentioned agglomerated bright phase. The TEM micrograph displayed in Figure 5(b) gives evidence about the formation of nanoscaled faceted Ce-rich nanophases. Figure 5(c) presents a detailed view of the yellow square shown in Figure 5(b). It is observed a faceted morphology of bright nanophases found in Al-CeO2 nanocomposites and the formation of an interface located between the cerium oxide nanoparticle and the aluminum matrix. Figure 5(d) displays a high-resolution micrograph (HRTEM) where the interface between a CeO2 nanoparticle and the metallic aluminum matrix is appreciable. We can notice four main zones indicating their interplanar distances (Figure 5(e)); zones 1 and 4 show a crystalline structure corresponding to the pure aluminum and CeO2 nanoparticle, respectively. The interplanar distance of 0.202 nm for the pure Al corresponds to the plane (200) and that of 0.192 nm for the CeO2 corresponds to the plane (311). The zone 2 corresponds to the interface between CeO2/Al, where the calculated interplanar distance (2.58 nm) is different from that corresponding to the pure aluminum. In Figure 5(f) is displayed the selected area electron diffraction (SAED) pattern and the corresponding simulated diffraction pattern of the same place (interface) based on the Al2O3 crystalline structure. The experimental and simulated patterns agree well with each other. A small variation in the interplanar distance of the zone between CeO2 nanoparticle and interface was detected and labeled as zone 3. According to the crystallography information of the ICSD card number 00-078-0484, the interplanar distance of 0.194 nm corresponds to the plane of the Ce2O3. A partial reduction of CeO2 to Ce2O3 led to the formation of the Al2O3 interface.
In order to evaluate the chemical stability of the added nanoparticles and their reinforcement capacity, the sintered samples (AA2024-CeO2 and Al-CeO2) were added to a pure AA2024 melted alloy at 750°C using a concentration of 1% (in wt.). Figure 6 displays some SEM micrographs showing the microstructure of the pure AA2024 alloy in as-cast condition (Figure 6(a)), AA2024 alloy + AA2024-CeO2 composite (Figure 6(b)) and AA2024 with Al-CeO2 composite (Figure 6(c)). A dendritic microstructure for the pure AA2024 alloy is observed, as is expected for an alloy produced following a liquid route (casting). The addition of the AA2024-CeO2 composite led to the formation of coarse precipitates with needle-like microstructure, while the Al-CeO2 composite acts as a grain refiner agent inducing the formation of a refined dendritic microstructure. There is no evidence of unwanted chemical reactions between the added ceria and the aluminum matrix, even though the process was carried out at a higher temperature where the chemical reactions between components are increased by the heat effect. In a liquid process, in which the cooling rate is slow, the dispersed material in the metal has enough time to grow, resulting in the formation of a coarse microstructure, detrimental to the mechanical response. In order to act as a reinforcement in the metal matrix and improve the mechanical response, the dispersed material would maintain a fine microstructure uniformly distributed in the matrix.
3.3. Mechanical Testing
Some microhardness results of sintered composites in the Vickers scale are displayed in Figure 7(a). For comparison purposes, the microhardness of a reference AA2024 alloy processed following the same sintering condition is presented. In both cases, the Al and the AA2024 showed an increase of hardness compared to the reference alloy. It has been reported that rare earth addition also improves several intrinsic properties of Al alloys such as strength, heat resistance, and corrosion resistance [16, 17]. Even though the addition of 5.0 percent (in wt.) of CeO2 nanoparticles increases ∼5% the hardness of the unreinforced AA2024 alloy, a noticeable result is achieved with the Al-CeO2 composite which presents an increase of ∼32% compared to the blank. It should be mentioned that the hardness of the Al-CeO2 composite exceeds more than twice to that of the pure aluminum (49 HV).
In Figure 7(b) are presented the hardness of the casted AA2024 alloy with 1% additions of both prepared AA2024-CeO2 and Al-CeO2 composites; it is observed a remarkable difference between them: the AA2024-CeO2 composite increases ∼11% the hardness of the AA2024 alloy while the Al-CeO2 composite improves its hardness over 50%. The results indicate that additions of nanoceria have a positive effect on the mechanical properties of prepared composites; however, the presence of the alloying elements affects the response of the composites. It is observed that the addition of cerium oxide acts as a positive reinforcement for pure aluminum matrix, causing fall in mechanical behaviour of Al-Cu alloys as a result of the chemical affinity between Ce and Cu (as was above mentioned) and the general morphology of the formed phases, affecting negatively the mechanical properties of the synthesized composites exposed in this study and considering for future studies, the effect produced by nanoparticles of this nature in the Al-Cu alloys under corrosive and thermomechanical evaluation.
The present study showed the viability for production of two composites using as reinforcement material ceria nanoparticles and two different metal matrixes, pure aluminum and a commercial AA2024 alloy, used frequently in the aeronautical industry. Both composites were synthesized using a solid-state route complemented by mechanical milling. Used nanoceria has a particle size in the range of 10–50 nm, its purity was confirmed by EDS, and the material presents a single-phase with a lattice constant of 5.411 Å and Fm-3 m space group. The SEM and TEM studies revealed that the addition of CeO2 nanoparticles in the AA2024 alloy produced a dispersed needle-like Ce-Cu-rich phase, which changed their volume fraction, size, and morphology from irregular to a needle-like shape after sintering. A noticeable variation on the porosity as a direct function of the sintering time was also observed. The presence of this phase had a negative effect on the mechanical performance of the AA2024 alloy due to the chemical affinity between Cu and Ce, which alter the kinetics of precipitation of the AlCuX solutes. On the contrary, the dispersion of CeO2 in pure aluminum showed a significant improvement of hardness. During the melting, the CeO2 nanoparticles showed a similar chemical stability compared to low-temperature sintering processing. The remarkable microstructural variation of both metal matrixes is related with Ce-Cu affinity in the AA2024 alloy and the high chemical stability of the ceria nanoparticles in pure aluminum.
The data used to support the findings of this study are included within the article
Conflicts of Interest
The authors declare that there are no conflicts of interest regarding the publication of this paper.
The authors gratefully acknowledge K. Campos-Venegas, E. Guerrero-Lestarjette, and C.E. Ornelas-Gutiérrez for their technical assistance. This research was carried out with economical support from the National Council of Science and Technology (CONACYT) of Mexico (project no. 20450).
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