Wear Dry Behavior of the Al-6061-Al 2 O 3 Composite Synthesized by Mechanical Alloying

: The present research deals with the comparative wear behavior of a mechanically milled Al-6061 alloy and the same alloy reinforced with 5 wt.% of Al 2 O 3 nanoparticles (Al-6061-Al 2 O 3 ) under different dry sliding conditions. For this purpose, an aluminum-silicon-based material was synthesized by high-energy mechanical alloying, cold consolidated, and sintered under pressureless and vacuum conditions. The mechanical behavior was evaluated by sliding wear and microhardness tests. The structural characterization was carried out by X-ray diffraction and scanning electron microscopy. Results showed a clear wear resistance improvement in the aluminum matrix composite (Al-6061-Al 2 O 3 ) in comparison with the Al-6061 alloy since nanoparticles act as a third hard body against wear. This behavior is attributed to the signiﬁcant increment in hardness on the reinforced material, whose strengthening mechanisms mainly lie in a nanometric size and homogeneous dispersion of particles offering an effective load transfer from the matrix to the reinforcement. Discussion of the wear performance was in terms of a protective thin ﬁlm oxide formation, where protective behavior decreases as a function of the sliding speed.


Introduction
The versatility of aluminum for different applications makes it an ideal structural material with high demand for aerospace, automotive, and other industries. Its mechanical properties are altered by adding alloying elements for the production or by incorporating reinforcing elements of different nature [1]. Being aluminum, one of the materials with the highest consumption globally by different industries, it represents an ideal material in manufacturing various components considered for structural applications. Secondary aluminum, obtained as waste material during the machining processes of such components [2], can be recycled by techniques requiring high energy consumption and, therefore, high cost. The reprocessing of metal shavings by mechanical means represents a low-cost alternative carried out at room temperature. Combined with techniques based on powder metallurgy and mechanical alloying, it represents a low energy consumption route in producing alloys and metal matrix composites. Table 1 summarizes the chemical composition of the aluminum powders obtained through the machining process of the Al-6061 commercial alloy into metal chips. Here, the reinforcing agent, Al 2 O 3 nanoparticles (see Figure 1) had an average size of 20 nm. Composites were produced in a high-energy ball mill Emax. The milling device and milling media used in the experiments were made from hardened steel. The powder mass was 50 g, and 4:1 ball-to-powder weight ratio was prepared. All millings runs were performed with methanol as a process control agent, and Argon as inert milling atmosphere at room temperature. Accordingly, the Al 2 O 3 particles concentration was set up to 5 wt.% and the milling time was 5 h. Thus, the compaction of the products was for 2 min under a pressure of 1862.65 MPa. Cold consolidated samples were pressure-less sintered for 3 h at 823 K under vacuum with a 50 K/min heating rate. Sintered products were held at 773 K and hot extruded into a rod of 10 mm in diameter by using indirect extrusion and an extrusion ratio of 16. For comparison purposes, an unreinforced milled, sintered, and hot extruded sample was employed as reference.  Table 1 summarizes the chemical composition of the aluminum powders obtained through the machining process of the Al-6061 commercial alloy into metal chips. Here, the reinforcing agent, Al2O3 nanoparticles (see Figure 1) had an average size of 20 nm. Composites were produced in a high-energy ball mill Emax. The milling device and milling media used in the experiments were made from hardened steel. The powder mass was 50 g, and 4:1 ball-to-powder weight ratio was prepared. All millings runs were performed with methanol as a process control agent, and Argon as inert milling atmosphere at room temperature. Accordingly, the Al2O3 particles concentration was set up to 5 wt.% and the milling time was 5 h. Thus, the compaction of the products was for 2 min under a pressure of 1862.65 MPa. Cold consolidated samples were pressure-less sintered for 3 h at 823 K under vacuum with a 50 K/min heating rate. Sintered products were held at 773 K and hot extruded into a rod of 10 mm in diameter by using indirect extrusion and an extrusion ratio of 16. For comparison purposes, an unreinforced milled, sintered, and hot extruded sample was employed as reference.

Experimental Characterization
The tribometer (ball-on-disc configuration) used in this research work was Anton Paar TRB ® (Anton Paar Mexico S. A. de C. V., Hidalgo, Mexico). The aluminum alloy (Al-6061) and the composite (Al-6061-Al2O3) were worn for 188.5 m against a 6 mm diameter counterface made of Sapphire (9 on the Mohs scale). Wear tests were carried out at room temperature (~25 °C) at three different levels of load (1, 2, 3 N) and sliding speed (4, 7, 10 cm/s). In previous wear tests, all specimens were polished until a 1-micron diamond paste was produced. At least two samples for each condition were tested, according to ASTM G99-17 [23].
Microhardness Vickers tests were carried out with a load of 100 g (HV/100) applied during 10 s according to ASTM E 384-17 [24], with a hardness tester Tukon 2500 TM (Illinois Tool Works Inc., Glenview, IL, USA). The average wear rate was calculated with the wear

Experimental Characterization
The tribometer (ball-on-disc configuration) used in this research work was Anton Paar TRB ® (Anton Paar Mexico S. A. de C. V., Hidalgo, Mexico). The aluminum alloy (Al-6061) and the composite (Al-6061-Al 2 O 3 ) were worn for 188.5 m against a 6 mm diameter counterface made of Sapphire (9 on the Mohs scale). Wear tests were carried out at room temperature (~25 • C) at three different levels of load (1, 2, 3 N) and sliding speed (4, 7, 10 cm/s). In previous wear tests, all specimens were polished until a 1-micron diamond paste was produced. At least two samples for each condition were tested, according to ASTM G99-17 [23].
Microhardness Vickers tests were carried out with a load of 100 g (HV/100) applied during 10 s according to ASTM E 384-17 [24], with a hardness tester Tukon 2500 TM (Illinois  The average wear rate was calculated with the wear  track profile, which was measured with a profilometer Taylor Hobson ® (Taylor Hobson  Inc., Queretaro, Mexico), and the friction coefficient was measured during each test by the relation between the load sensed by the tribometer and the applied load. Scanning electron microscopy (SEM) and energy dispersive spectroscopy (EDS) were employed to analyze worn surfaces on the samples and collected debris. Wear debris was characterized by X-ray diffraction (XRD) using Kα-Cu radiation (45 kV-40 mA) in an interval of 2theta from 20 • to 85 • with a scanning step size of 0.013 • and counting time of 13.77 s.

Distribution of Al 2 O 3 Nanoparticles
As can be seen from Figure 2a, a homogeneous distribution of Al 2 O 3 nanoparticles is shown, with their agglomeration in colonies homogenously dispersed along with the aluminum matrix, with an average size of approximately 0.5 to 1 µm in spherical-shape particles bunches. Additionally, Figure 2b presents the SEM-EDS as of one of the agglomerated nanoparticles, wherein it is possible to detect high oxygen content that is one of the main elements that constitute the Al 2 O 3 reinforcement. On the other hand, Figure 2c shows some agglomerated nanoparticles, where an oxygen content reduction can be seen due to the majority concentration of the matrix. In this context, Zaiemyekeh et al. [25] suggested that the homogeneous distribution of Al 2 O 3 nanoparticles in an aluminum matrix composite reveals the correct use of the process to fabricate the specimens. , and the friction coefficient was measured during each test by the relation between the load sensed by the tribometer and the applied load. Scanning electron microscopy (SEM) and energy dispersive spectroscopy (EDS) were employed to analyze worn surfaces on the samples and collected debris. Wear debris was characterized by X-ray diffraction (XRD) using Kα-Cu radiation (45 kV-40 mA) in an interval of 2theta from 20° to 85° with a scanning step size of 0.013° and counting time of 13.77 s.

Distribution of Al2O3 Nanoparticles
As can be seen from Figure 2a, a homogeneous distribution of Al2O3 nanoparticles is shown, with their agglomeration in colonies homogenously dispersed along with the aluminum matrix, with an average size of approximately 0.5 to 1 µm in spherical-shape particles bunches. Additionally, Figure 2b presents the SEM-EDS as of one of the agglomerated nanoparticles, wherein it is possible to detect high oxygen content that is one of the main elements that constitute the Al2O3 reinforcement. On the other hand, Figure 2c shows some agglomerated nanoparticles, where an oxygen content reduction can be seen due to the majority concentration of the matrix. In this context, Zaiemyekeh et al. [25] suggested that the homogeneous distribution of Al2O3 nanoparticles in an aluminum matrix composite reveals the correct use of the process to fabricate the specimens.  Figure 3 shows microhardness results for both materials (Al-6061 and Al-6061-Al 2 O 3 with 5 wt.% nanoparticles) and their respective Vickers indent footprints (see Figure 4), in the last figures, it is possible to observe a reduction in the indent footprint of the Al-6061-Al 2 O 3 in comparison with the Al-6061, due to the high mechanical resistance obtained by nanoparticles, as will be seen later.  Figure 3 shows microhardness results for both materials (Al-6061 and Al-6061-Al2O3 with 5 wt.% nanoparticles) and their respective Vickers indent footprints (see Figure 4), in the last figures, it is possible to observe a reduction in the indent footprint of the Al-6061-Al2O3 in comparison with the Al-6061, due to the high mechanical resistance obtained by nanoparticles, as will be seen later.  Results presented in Figure 3 show that microhardness was significantly higher in the Al-6061-Al2O3 than in the Al-6061 alloy. In this part, several strengthening mechanisms are considered, such as thermal mismatch during the sintering stage. However, due to the nature of the synthesis process, an important strengthening mechanism considers the excellent dispersion of the nanoparticles during the milling process [26,27], producing an efficient transfer load from the matrix to the reinforcement. Furthermore, due to the size of the reinforcement, the dispersion of these fine nanometric ceramic particles in the alloy  Figure 3 shows microhardness results for both materials (Al-6061 and Al-6061-Al2O3 with 5 wt.% nanoparticles) and their respective Vickers indent footprints (see Figure 4), in the last figures, it is possible to observe a reduction in the indent footprint of the Al-6061-Al2O3 in comparison with the Al-6061, due to the high mechanical resistance obtained by nanoparticles, as will be seen later.  Results presented in Figure 3 show that microhardness was significantly higher in the Al-6061-Al2O3 than in the Al-6061 alloy. In this part, several strengthening mechanisms are considered, such as thermal mismatch during the sintering stage. However, due to the nature of the synthesis process, an important strengthening mechanism considers the excellent dispersion of the nanoparticles during the milling process [26,27], producing an efficient transfer load from the matrix to the reinforcement. Furthermore, due to the size of the reinforcement, the dispersion of these fine nanometric ceramic particles in the alloy Results presented in Figure 3 show that microhardness was significantly higher in the Al-6061-Al 2 O 3 than in the Al-6061 alloy. In this part, several strengthening mechanisms are considered, such as thermal mismatch during the sintering stage. However, due to the nature of the synthesis process, an important strengthening mechanism considers the excellent dispersion of the nanoparticles during the milling process [26,27], producing an efficient transfer load from the matrix to the reinforcement. Furthermore, due to the size of the reinforcement, the dispersion of these fine nanometric ceramic particles in the alloy produces free path obstacles in the movement of dislocations in the subgrain structure, enhancing their hardness [28]. Additionally, hard particles of Al 2 O 3 can be associated with Metals 2021, 11, 1652 6 of 17 stress concentration around particle corners which tends to be reduced as a function of the reduction in the size of alumina particles, as was suggested by Mamoon [29]. In their studies about the effect of different sizes of Al 2 O 3 nanoparticles on 6066AA and 7005AA composites on mechanical properties, it was mentioned that 20 nm particle size enhances the best mechanical properties like UTS (Ultimate Tensile Stress). In this context, it is essential to note that the same size was used in the present work.

Microhardness Vickers Results
On the other hand, the nanoparticles concentration considered in this study (5 wt.%) produced a noticeable increase in the mechanical performance evaluated by hardness, significantly increasing the compressive strength. In this regard, Corrochano et al. [30] suggested that smaller reinforcement particles into aluminum matrix composites via powder metallurgy enhance their wear performance as a function of the hardness behavior.
In contrast, Ghasem et al. [31] showed that up to 3 h milled time, as was used in the present research work, promotes the excellent dispersion of fine particles of Al 2 O 3 into the aluminum matrix that contributes to increased mechanical properties. It is well known that fine nanoparticles increase dislocation density around the reinforcing particles, and simultaneously, grain refinement occurs due to particle stimulate nucleation mechanisms.
Likewise, Ramezanalizadeh [32] suggested that due to long milled time, reinforcing particles can be trapped into the metal matrix, promoting an increase in the local deformation and promoting the particle welding process, enhancing their final mechanical properties. Figure 5 shows the average wear rate of the specimens as a function of the applied load for the alloy and the composite (Al-6061 and Al-6061-Al 2 O 3 with 5 wt.% nanoparticles, respectively). Again, a similar trend in the wear behavior in both materials was observed: the average wear rate increased as load and sliding speed increased. In this regard, it was suggested that an increment in the applied load tends to increase the penetration of hard asperities of the counterface into the softer sample under evaluation, which generates the removal of particles in the softer material [33][34][35][36][37].

Average Wear Rate
Metals 2021, 11, x FOR PEER REVIEW 6 of 17 produces free path obstacles in the movement of dislocations in the subgrain structure, enhancing their hardness [28]. Additionally, hard particles of Al2O3 can be associated with stress concentration around particle corners which tends to be reduced as a function of the reduction in the size of alumina particles, as was suggested by Mamoon [29]. In their studies about the effect of different sizes of Al2O3 nanoparticles on 6066AA and 7005AA composites on mechanical properties, it was mentioned that 20 nm particle size enhances the best mechanical properties like UTS (Ultimate Tensile Stress). In this context, it is essential to note that the same size was used in the present work.
On the other hand, the nanoparticles concentration considered in this study (5 wt.%) produced a noticeable increase in the mechanical performance evaluated by hardness, significantly increasing the compressive strength. In this regard, Corrochano et al. [30] suggested that smaller reinforcement particles into aluminum matrix composites via powder metallurgy enhance their wear performance as a function of the hardness behavior.
In contrast, Ghasem et al. [31] showed that up to 3 h milled time, as was used in the present research work, promotes the excellent dispersion of fine particles of Al2O3 into the aluminum matrix that contributes to increased mechanical properties. It is well known that fine nanoparticles increase dislocation density around the reinforcing particles, and simultaneously, grain refinement occurs due to particle stimulate nucleation mechanisms.
Likewise, Ramezanalizadeh [32] suggested that due to long milled time, reinforcing particles can be trapped into the metal matrix, promoting an increase in the local deformation and promoting the particle welding process, enhancing their final mechanical properties. Figure 5 shows the average wear rate of the specimens as a function of the applied load for the alloy and the composite (Al-6061 and Al-6061-Al2O3 with 5 wt.% nanoparticles, respectively). Again, a similar trend in the wear behavior in both materials was observed: the average wear rate increased as load and sliding speed increased. In this regard, it was suggested that an increment in the applied load tends to increase the penetration of hard asperities of the counterface into the softer sample under evaluation, which generates the removal of particles in the softer material [33][34][35][36][37]. The Al-6061-Al2O3 significantly enhances the wear resistance of the composite in comparison with the reference alloy due to the nanoparticles acting as a third hard body The Al-6061-Al 2 O 3 significantly enhances the wear resistance of the composite in comparison with the reference alloy due to the nanoparticles acting as a third hard body that tends to reduce the counterface penetration. Similar trends were found by Sozhamannan et al. [37] in their studies about the wear performance of 6061 Al/nano ticp/Gr hybrid composites, where it was suggested that the presence of reinforcements in the Al matrix restrict the plastic deformation in the initial stage of loading, allowing a subsequent plastic Metals 2021, 11, 1652 7 of 17 deformation mildly. In addition, it is important to mention that there exist three important parameters that promote the current wear behavior: friction, temperature, and third body interaction. The researchers suggest that friction between contact surfaces promotes an increment in the temperature that stimulates oxide formations. This oxide formation can act as a solid lubricant that tends to reduce the friction coefficient. Therefore, its stability can be related to the specific conditions of load and sliding speed. Finally, additional reinforced particles well attached to the substrate can improve their mechanical properties as a function of their hardness increment. Parameters such as friction coefficient, oxide formations, and nanoparticle interaction will be discussed in other sections. that tends to reduce the counterface penetration. Similar trends were found by Sozhamannan et al. [37] in their studies about the wear performance of 6061 Al/nano ticp/Gr hybrid composites, where it was suggested that the presence of reinforcements in the Al matrix restrict the plastic deformation in the initial stage of loading, allowing a subsequent plastic deformation mildly. In addition, it is important to mention that there exist three important parameters that promote the current wear behavior: friction, temperature, and third body interaction. The researchers suggest that friction between contact surfaces promotes an increment in the temperature that stimulates oxide formations. This oxide formation can act as a solid lubricant that tends to reduce the friction coefficient. Therefore, its stability can be related to the specific conditions of load and sliding speed. Finally, additional reinforced particles well attached to the substrate can improve their mechanical properties as a function of their hardness increment. Parameters such as friction coefficient, oxide formations, and nanoparticle interaction will be discussed in other sections. Figures 6 and 7 show friction coefficients as a function of the applied load and sliding speed for both materials (Al-6061 and Al-6061-Al2O3).   that tends to reduce the counterface penetration. Similar trends were found by Sozhamannan et al. [37] in their studies about the wear performance of 6061 Al/nano ticp/Gr hybrid composites, where it was suggested that the presence of reinforcements in the Al matrix restrict the plastic deformation in the initial stage of loading, allowing a subsequent plastic deformation mildly. In addition, it is important to mention that there exist three important parameters that promote the current wear behavior: friction, temperature, and third body interaction. The researchers suggest that friction between contact surfaces promotes an increment in the temperature that stimulates oxide formations. This oxide formation can act as a solid lubricant that tends to reduce the friction coefficient. Therefore, its stability can be related to the specific conditions of load and sliding speed. Finally, additional reinforced particles well attached to the substrate can improve their mechanical properties as a function of their hardness increment. Parameters such as friction coefficient, oxide formations, and nanoparticle interaction will be discussed in other sections.      According to the XRD results, wear mechanisms observed in the aluminum composite indicate that removing fragments of the matrix is possible because of the material transferred to the counterface by adhesion [39]. The continuous cyclic loading tends to form harden asperities on the counterface (in this case, the sapphire ball), removing material from a sample made of aluminum (alloy and composite).

XRD Analysis of Wear Debris and Base Material
The detection of a second phase identified as MgO product of the high temperatures reached during the different test conditions can be observed in the XRD patterns. This phase is related to the formation of a tribolayer that reduces the friction coefficient, but cannot be well attached to substrate in order to reduce the wear rate [40]. This oxide formation seems to disappear as load and sliding speed increases. In a range from low load and sliding speed (1 N, 4 cm/s) to medium load and sliding speed (2 N, 7 cm/s), the MgO formation is evident, but in a range from medium load and high sliding speed (2 N, 10 cm/s) to high load and sliding speed (3 N, 10 cm/s), the MgO formation was not detected. This behavior suggests that under low and medium load and sliding speed (1 N, 4 cm/s to 2 N, 7 cm/s), more oxide formations are detached from the contact surface in comparison with a range from 2 N, 10 cm/s to 3 N, 10 cm/s.
It is essential to mention that only with oxygen atmosphere contact [41], the reaction: 2Mg + O 2 → 2MgO is promoted, and in this case intensified by the dry sliding conditions. In this context, it is evident that the oxide formation is another important parameter to be considered, as not all conditions showing the MgO formation or is not possible to be detected due to the low amount. Therefore, it is suggested that the oxide formation is related to the specific conditions of load and sliding speed that sometimes can act favorable (acting as solid lubricant) and other times unfavorable (acting as abrasive particles). In the same way, Cheng et al. [42] reported in their studies about the evolution of surface oxide film of typical aluminum alloys such as: 1060, 3003, 4032, 5052, 5083, and 6061, that MgO is one of the main stoichiometries formed in aluminum alloys, which is in good agreement with the obtained results. From Figures 9a-c and 10a-c, two main zones can be observed. The first one corresponds to a white zone identified as the base material, which is supported by the SEM-EDS analysis (Figures 9a-c and 10a-c (1)), where the low content of oxygen and several of the elements that constitute the aluminum matrix composite (Al, Zn, Mg, Cu) can be detected. In addition, a second dark zone depicts a mixture of delamination and fragmentation of a fine oxide layer; the morphology suggests particles of the counterface. Again, the SEM-EDS analysis supports the evidence (Figures 9a-c and 10a-c (2)) where it is possible to observe high oxygen content. It is evident that a change in tonality from white (base material) to dark (mixture of delamination and compaction of the suggested fine oxide layer) occurs as load and sliding speed increases, which reduces the friction coefficient, but cannot be sufficient to reduce the wear rate. This behavior is in concordance with the XRD results, wherein it was possible to detect MgO in the wear debris, mainly at low and medium load and sliding speed, which suggests high degradation of the fine oxide layer. (Figures 9a-c and 10a-c (2)) where it is possible to observe high oxygen content. It is evident that a change in tonality from white (base material) to dark (mixture of delamination and compaction of the suggested fine oxide layer) occurs as load and sliding speed increases, which reduces the friction coefficient, but cannot be sufficient to reduce the wear rate. This behavior is in concordance with the XRD results, wherein it was possible to detect MgO in the wear debris, mainly at low and medium load and sliding speed, which suggests high degradation of the fine oxide layer.  Additionally, the width of wear tracks increased as load and sliding speeds increased (see Figures 9a-c and 10a-c). These results are related to the increment in the penetration of the counterface as load and sliding speed increase. On the other hand, a diminution of the wear track thickness in the Al-6061-Al 2 O 3 with 5 wt.% nanoparticles was also observed (Figure 10a-c) in comparison with the Al-6061 without nanoparticles (Figure 9a-c), which suggests a protective behavior of the nanoparticles (Al 2 O 3 ) in the aluminum matrix composites. Additionally, the width of wear tracks increased as load and sliding speeds increased (see Figures 9a-c and 10a-c). These results are related to the increment in the penetration of the counterface as load and sliding speed increase. On the other hand, a diminution of the wear track thickness in the Al-6061-Al2O3 with 5 wt.% nanoparticles was also observed (Figure 10a-c) in comparison with the Al-6061 without nanoparticles (Figure 9a-c), which suggests a protective behavior of the nanoparticles (Al2O3) in the aluminum matrix composites.   Wear debris composed of the suggested fine oxide layer and the base material can be observed. A reduction in the fine oxide wear particles was detected as the load and sliding speed increased, which suggests a transition from oxidative to adhesive behavior, related to an initial high content of oxide wear debris and a long shallow crater surface. A wear map developed by Raghavendra and Ramamurthy [43] showed that in the Al 7075 reinforced with 5 wt.% of Al 2 O 3 , a transition of mild wear (oxidation) to severe wear (large crater and grooves) can occur as load and sliding speed increases. These observations are according to the presented results, the same behavior is shown in both materials (Al-6061 and Al-6061-Al 2 O 3 with 5 wt.% nanoparticles). Furthermore, it is observed that there is delamination and compaction of the suggested tribo-layer formed under the current conditions, a product of the different conditions of load, sliding speed, and the rotary ball-on-disc conditions. Metals 2021, 11, x FOR PEER REVIEW 12 of 17 Figure 11. Elemental mapping of worn surface at high magnification for the Al-6061 aluminum alloy (a1-c1) and aluminum composite (a2-c2), under low, medium, and high conditions of load and sliding speed (1 N and 4 cm/s, 2 N and 7 cm/s, 3 N and 10 cm/s).

Surface and Elemental Mapping Analysis
Wear debris composed of the suggested fine oxide layer and the base material can be observed. A reduction in the fine oxide wear particles was detected as the load and sliding speed increased, which suggests a transition from oxidative to adhesive behavior, related to an initial high content of oxide wear debris and a long shallow crater surface. A wear map developed by Raghavendra and Ramamurthy [43] showed that in the Al 7075 reinforced with 5 wt.% of Al2O3, a transition of mild wear (oxidation) to severe wear (large crater and grooves) can occur as load and sliding speed increases. These observations are according to the presented results, the same behavior is shown in both materials (Al-6061 and Al-6061-Al2O3 with 5 wt.% nanoparticles). Furthermore, it is observed that there is delamination and compaction of the suggested tribo-layer formed under the current conditions, a product of the different conditions of load, sliding speed, and the rotary ballon-disc conditions.
Differences are present on contact surfaces, mainly with fine oxide wear particles. In this context, it is possible to corroborate the high presence of fine oxide wear particles, whose content tends to be more pronounced at low and medium load and sliding speed (1 N and 4 cm/s) (2 N and 7 cm/s). Thus, the latest suggests the presence of a fine oxide film that reduces the friction coefficient, but it is not sufficient to generate wear protection. Differences are present on contact surfaces, mainly with fine oxide wear particles. In this context, it is possible to corroborate the high presence of fine oxide wear particles, whose content tends to be more pronounced at low and medium load and sliding speed (1 N and 4 cm/s) (2 N and 7 cm/s). Thus, the latest suggests the presence of a fine oxide film that reduces the friction coefficient, but it is not sufficient to generate wear protection. In the opposite way, at high load and sliding speed (3 N and 10 cm/s), the presence of oxide wear particles on worn surfaces was not detected, which is related to the low degradation of the suggested fine oxide layer. These results are in concordance with the XRD patterns applied on wear debris, where it is possible to detect oxide formations at low and medium load and sliding speed (1 N and 4 cm/s) (2 N and 7 cm/s), due to the high degradation of the suggested fine oxide layer. On the other hand, at high load and sliding speed (3 N and 10 cm/s), it was not possible to detect oxide formations, due to the low degradation of the suggested fine oxide layer.

Nanoparticle Analysis in the Wear Fragments
SEM images of the wear fragments after wear tests in the Al-6061-Al 2 O 3 with 5 wt.% nanoparticles show the distribution of alumina nanoparticles in the wear fragments (see Figure 12). Here, it is possible to observe that Al 2 O 3 particles appear embedded into the aluminum matrix composite. In this context, the literature suggests that the separation of abrasive particles such as oxides, carbides, nitrides, and others from the metal matrix can accelerate the removal of particles during wear tests which, as seen in this work, does not happen [34,35,38,39,44]. Particles embedded into the metal matrix can help enhance their wear performance due to an effective load transfer from the matrix to the reinforcement, as shown in the present study.
In the opposite way, at high load and sliding speed (3 N and 10 cm/s), the presence of oxide wear particles on worn surfaces was not detected, which is related to the low degradation of the suggested fine oxide layer. These results are in concordance with the XRD patterns applied on wear debris, where it is possible to detect oxide formations at low and medium load and sliding speed (1 N and 4 cm/s) (2 N and 7 cm/s), due to the high degradation of the suggested fine oxide layer. On the other hand, at high load and sliding speed (3 N and 10 cm/s), it was not possible to detect oxide formations, due to the low degradation of the suggested fine oxide layer.

Nanoparticle Analysis in the Wear Fragments
SEM images of the wear fragments after wear tests in the Al-6061-Al2O3 with 5 wt.% nanoparticles show the distribution of alumina nanoparticles in the wear fragments (see Figure 12). Here, it is possible to observe that Al2O3 particles appear embedded into the aluminum matrix composite. In this context, the literature suggests that the separation of abrasive particles such as oxides, carbides, nitrides, and others from the metal matrix can accelerate the removal of particles during wear tests which, as seen in this work, does not happen [34,35,38,39,44]. Particles embedded into the metal matrix can help enhance their wear performance due to an effective load transfer from the matrix to the reinforcement, as shown in the present study.

Schematic Illustration of the Wear Performance
Due to the depicted evidence, it is possible to suggest the next schematic wear evolution with the conditions presented: Figures 13 and 14 show that both materials (Al-6061 and Al-6061-Al 2 O 3 with 5 wt.% nanoparticles) form an oxide layer (MgO), which tends to reduce the direct contact between counterface and base material, showing the presence of fine and agglomerate particles coated with high oxygen content, as it was stated above. In this context, a reduction in the friction coefficient was evident as load and sliding speed increased, but not sufficient to generate wear protection. The wear protection is attained to the increment in hardness.
On the other hand, it is evident that degradation of fine wear particles at the initial stage of load and sliding speed occurs, which tend to be less pronounced as load and sliding speed increased. In this regard, it is important to mention that the addition of alumina nanoparticles significantly increases the wear resistance of the composites in comparison with the alloy, as a function of their hardness [25,45].

Schematic Illustration of the Wear Performance
Due to the depicted evidence, it is possible to suggest the next schematic wear evolution with the conditions presented: Figures 13 and 14 show that both materials (Al-6061 and Al-6061-Al2O3 with 5 wt.% nanoparticles) form an oxide layer (MgO), which tends to reduce the direct contact between counterface and base material, showing the presence of fine and agglomerate particles coated with high oxygen content, as it was stated above. In this context, a reduction in the friction coefficient was evident as load and sliding speed increased, but not sufficient to generate wear protection. The wear protection is attained to the increment in hardness. On the other hand, it is evident that degradation of fine wear particles at the initial stage of load and sliding speed occurs, which tend to be less pronounced as load and sliding speed increased. In this regard, it is important to mention that the addition of alumina nanoparticles significantly increases the wear resistance of the composites in comparison with the alloy, as a function of their hardness [25,45].

Conclusions
The analysis performed on the experimental results showed a significant improvement on the average wear rate of the aluminum matrix composite with 5 wt.% nanoparticles (Al-6061-Al2O3) compared with the aluminum base alloy without nanoparticles (Al-6061). This improvement in the wear rate is attributable to the hard nanoparticles of alumina (Al2O3) that act as a third hard body against wear, reducing the penetration of the counterface into the softer materials. Furthermore, the mechanical properties of the alu-

Conclusions
The analysis performed on the experimental results showed a significant improvement on the average wear rate of the aluminum matrix composite with 5 wt.% nanoparticles (Al-6061-Al 2 O 3 ) compared with the aluminum base alloy without nanoparticles (Al-6061). This improvement in the wear rate is attributable to the hard nanoparticles of alumina (Al 2 O 3 ) that act as a third hard body against wear, reducing the penetration of the counterface into the softer materials. Furthermore, the mechanical properties of the aluminum matrix composites were improved due to the addition of alumina (Al 2 O 3 ) nanoparticles. Strengthening mechanisms mainly lie in a nanometric size and homogeneous dispersion of particles offering an effective load transfer from the matrix to the reinforcement.
XRD results show the formation of a fine oxide (MgO) that tends to reduce the friction coefficient as load and sliding speed increases, due to acting as a solid lubricant. This oxide formation was especially detected on wear debris at low and medium load (1, 2 N) and low and medium sliding speed (4, 7 cm/s), where it was easier to detect this behavior, which is related to the high degradation of the suggested oxide film in these conditions. On the other hand, the oxide formation tended to disappear at high load and sliding speed (3 N and 10 cm/s), which suggests low degradation of the oxide film in this other condition.
SEM results showed fine oxide wear fragments on the contact surface, especially at low and medium load and sliding speed (1 N and 4 cm/s) (2 N and 7 cm/s), a product of the degradation of the suggested tribo-film, where this fine oxide wear fragments appeared to disappear as load and sliding speed increased. Finally, it was evident that alumina nanoparticles (Al 2 O 3 ) were maintaining embedded into wear fragments after wear tests, offering excellent wear properties.