Effect of Boron Carbide Addition on Wear Resistance of Aluminum Matrix Composites Fabricated by Stir Casting and Hot Rolling Processes

: In this study, to evaluate the effect of boron carbide (B 4 C) addition on the wear performance of aluminum (Al), Al6061 and 5, 10, and 20 vol.% B 4 C/Al6061 composites were manufactured using the stir casting and hot rolling processes. B 4 C particles were randomly dispersed during the stir casting process; then, B 4 C particles were arranged in the rolling direction using a hot rolling process to further improve the B 4 C dispersion and wear resistance of the composites. Furthermore, a continuous interfacial layer between B 4 C and the Al6061 matrix was generated by diffusion of titanium (Ti) and chromium (Cr) atoms contained in the Al6061 alloy. Wear depth and width of the composites decreased with increasing B 4 C content. Furthermore, with B 4 C addition, coefﬁcient of friction (COF) improved as compared with that of Al6061. The results indicate that interface-controlled, well-aligned B 4 C particles in the friction direction can effectively increase the wear properties of Al alloys and improve their hardness. the stir casting process. Since it was manufactured by the casting process, defects were not observed at the B 4 C/Al interface. In the EPMA element mapping images, large amounts of the boron (B) and carbon (C) elements can be observed in the B 4 C areas, which indicates that the crystal structure of the B 4 C particles was maintained in molten Al during the stir-casting process. Elemental titanium (Ti) and chromium (Cr) appeared continuously along the interface between the B 4 C and Al matrix. It is known that AlB 2 and Al 3 BC precipitates form in the B 4 C/Al system [21]. However, these did not appear in the B 4 C/Al6061 compo- site manufactured by the stir casting process due to the Ti and Cr in the Al6061 alloy. Previous research has revealed the formation of multi-interfacial layers of Al 4 C 3 /(Ti,Cr)B 2 in the B 4 C/Al6061 composites [20]. The formation of interfacial layers can limit the decomposition of B 4 C reinforcements and promote their wettability in liquid Al in the stir casting process. There was no interfacial debonding between the Al matrix and B 4 C reinforcement. Therefore, B 4 C/Al6061 composites fabricated by stir casting followed by the hot roll- ing process have well-aligned B 4 C distribution along the rolling direction, with a continuous interfacial


Introduction
Aluminum matrix composites (AMCs) have many advantages over Fe-based alloys or composites, including high specific strength, high hardness, high stiffness, and wear resistance. AMCs are desirable materials for structural applications in the aircraft, automotive, and military industries and as neutron absorber materials in the nuclear industry [1][2][3][4]. Boron carbide (B 4 C) is currently considered the most promising ceramic reinforcement due to its attractive properties of high strength, low density of 2.52 g/cm 3 , high hardness (third hardest material after diamond and cubic boron nitride), and good chemical stability compared with other ceramic materials, such as silicon carbide and titanium boride [1,[5][6][7][8][9][10]. B 4 C has a high melting point and a good neutron absorbing property, so it has become a major focus in the field of nuclear shielding [11][12][13][14].
The inclusion of hard ceramic reinforcement in Al can improve the hardness and wear resistance of the soft Al matrix. Ortiz et al. reported that the lubricated sliding wear resistance of a fine-grained B 4 C composite fabricated by transient liquid-phase assisted spark-plasma sintering with Ti-Al additives under smooth conditions was comparable to that of the reference monolithic B 4 C ceramic [15]. It was shown that the Ti-Al-B 4 C composite has an excellent sliding wear resistance that exceeds that of monolithic B 4 C ceramic by one order of magnitude, and that is attributable to its greater hardness and densification. Kumar et al. manufactured an Al7075-B 4 C-rice husk ash (RHA) hybrid alloy composite using high vacuum casting [16]. The mechanical wear behavior, hardness, and flexibility were analyzed, and the conclusion was drawn that RHA and B 4 C particles improved the abrasion resistance of hybrid composites and reduced damage to the worn surface. Zhao et al. studied the wear behavior with increasing B 4 C content and changing load [17]. Augmentation of B 4 C content resulted in an increase in the friction coefficient and decrease in the wear mass loss. At a low load of 50 N, the dominant wear mechanisms of the B 4 C/Al5083 composites were microcutting and abrasive wear. At a high load of 200 N, the dominant wear mechanisms were microcutting and adhesion wear associated with the formation of delamination layers that protected the composites from further wear and enhanced the wear resistance under conditions of high load. Dou et al. found that with heat-treated B 4 C/Al6061 composites, the wear mass loss and coefficient of friction (COF) increased significantly under conditions of sliding time, applied load, and threshold of sliding speed [18]. Májlinger et al. reported that syntactic forms (hollow-sphere-reinforced Al matrix composites) would be promising materials for a moderately loaded sliding part because opened hollow inclusions during wear testing serve as lubricant reservoirs in Al composites [19].
To achieve better tribological properties, it is very important to prepare AMCs with uniform distribution of reinforcing particles. Furthermore, interfacial properties can dramatically alter the mechanical and wear properties of AMCs. In the case of AMCs fabricated by powder metallurgy, interfacial bonding with reinforcements can deteriorate due to surface oxide layers on the surfaces of Al powder. In our previous research, B 4 C/Al6061 composites having in situ interfacial layers produced by the reaction of the B 4 C and Al6061 matrix were successfully fabricated by the stir casting process [20]. A rolling process can also be used to fabricate AMCs with improved reinforcement dispersion. Thus, the purpose of this study was to evaluate the wear properties of low volumetric B 4 C/Al composites having uniform B 4 C dispersion and a controlled B 4 C/Al6061 interface manufactured using the stir casting and hot rolling processes. The ball-on-disk test was performed to observe the wear behavior under applied loads of 5 and 20 N. Phase analyses of microstructures and interface were performed through scanning electron microscopy (SEM) and electron probe microanalyzer (EPMA) analysis. Wear behavior according to the applied load and volume fraction of the B 4 C reinforcement was analyzed.

Materials and Methods
Al6061 alloy (ThyssenKrupp Materials Korea Co., Ltd., Seoul, Korea) was used as a matrix to fabricate metal matrix composites (MMCs). B 4 C powders (Dunhua Zhengxing Abrasive Co., Ltd., Dunhua, China) with commercial grades of F320 (Federation of European Producers of Abrasives (FEPA)-specified size distributions, 39.0 ± 1.5 µm) were used as reinforcements. The chemical composition of Al6061 provided by the company is shown in Table 1. B 4 C-reinforced Al6061 composites were prepared using the stir casting process comprising a pitched blade turbine type of impeller, which is suitable for suspending particles by strong down pumping. The size of the impeller was set to 2/3 of the diameter of the crucible. Baffles were installed to prevent swirling and to convert the horizontal flow of molten metal into a vertical flow when the impeller was rotating in the molten Al.
Al6061 alloy was melted in a graphite crucible by induction heating at a temperature of about 750 • C for 20-30 min. Degassing of the melt was performed with argon gas. After degassing, B 4 C particles preheated at 200 • C were added to the graphite crucible while continuing the stirring process. Stirring was maintained for 10 min at 800 rpm after finishing the B 4 C addition. After stirring, melt was poured into the preheated steel mold at 200 • C. The fabricated composites were cut into 100 mm × 100 mm × 10 mm pieces for the hot rolling process. For hot rolling, composites fabricated by the stir casting process were cross-rolled in atmospheric environments after preheating to 500 • C. A preheated composite plate was hot-rolled and then heat-treated again for 5 min per one pass. Twenty rolling passes were performed on each composite for fabricating a 1.6 mm thick plate from a 10 mm thick bulk composite. The fabricated hot-rolled B 4 C/Al6061 composites were cut into 250 mm × 350 mm sheets.
Wear test was performed using a ball-on-disk-type device (JLTB060, J&L Tech, Ansan, Korea) at 5 and 20 N loads with a 105 mm/s test speed. A Si 3 N 4 ball (Φ 6 mm) was used as the counterpart material. The size of the wear specimen was Φ 25 × 2 mm. An alpha step (DektakXT, Bruker, Billerica, MA, USA) was used to measure the wear depth and width, and a Vickers hardness tester (HM-122, Mitutoyo, Kawasaki, Japan) was used to measure the hardness of the composites. The measured load was 100 gf, and the holding time was 10 s. Each specimen was measured 5 times. The microstructures of the composites were observed with a scanning electron microscope (SEM, LEO-1450, Zeiss, Oberkochen, Germany), field emission-electron probe microanalyzer (FE-EPMA, JXA-8530F, JEOL, Akishima, Japan), and 3D X-ray tomography microscope (Zeiss, Xradia Ultra/Versa Hybrid Systems, Oberkochen, Germany).

Microstructures of B 4 C/Al6061 Composites Fabricated by the Stir Casting and Hot Rolling Processes
The microstructures of B 4 C/Al6061 composites are shown in Figure 1. In the case of the B 4 C/Al6061 composites fabricated by stir casting, most of the B 4 C particles were relatively well dispersed in the Al6061 matrix, as shown in Figure 1a-c. When the B 4 C/Al6061 composites were manufactured by stir casting, the B 4 C particles were randomly arranged in three dimensions. Some B 4 C particles (irregular shape) appeared like small particles because parts of them were exposed in the 2D SEM image. Figure 1d-f shows crosssectional SEM images of hot-rolled B 4 C/Al6061 composites. After hot rolling, the B 4 C reinforcement in the Al6061 matrix was arranged according to the rolling direction. This phenomenon is more clearly observed with increasing B 4 C content (Figure 1f). For hot rolling, composites fabricated by the stir casting process were cross-rolled in atmospheric environments after preheating to 500 °C. A preheated composite plate was hot-rolled and then heat-treated again for 5 minutes per one pass. Twenty rolling passes were performed on each composite for fabricating a 1.6 mm thick plate from a 10 mm thick bulk composite. The fabricated hot-rolled B4C/Al6061 composites were cut into 250 mm × 350 mm sheets.
Wear test was performed using a ball-on-disk-type device (JLTB060, J&L Tech, Ansan, Korea) at 5 and 20 N loads with a 105 mm/s test speed. A Si3N4 ball (Φ 6 mm) was used as the counterpart material. The size of the wear specimen was Φ 25 × 2 mm. An alpha step (DektakXT, Bruker, Billerica, MA, USA) was used to measure the wear depth and width, and a Vickers hardness tester (HM-122, Mitutoyo, Kawasaki, Japan) was used to measure the hardness of the composites. The measured load was 100gf, and the holding time was 10 s. Each specimen was measured 5 times. The microstructures of the composites were observed with a scanning electron microscope (SEM, LEO-1450, Zeiss, Oberkochen, Germany), field emission-electron probe microanalyzer (FE-EPMA, JXA-8530F, JEOL, Akishima, Japan), and 3D X-ray tomography microscope (Zeiss, Xradia Ultra/Versa Hybrid Systems, Oberkochen, Germany).

Microstructures of B4C/Al6061 Composites Fabricated by the Stir Casting and Hot Rolling Processes
The microstructures of B4C/Al6061 composites are shown in Figure 1. In the case of the B4C/Al6061 composites fabricated by stir casting, most of the B4C particles were relatively well dispersed in the Al6061 matrix, as shown in Figure 1a-c. When the B4C/Al6061 composites were manufactured by stir casting, the B4C particles were randomly arranged in three dimensions. Some B4C particles (irregular shape) appeared like small particles because parts of them were exposed in the 2D SEM image. Figure 1d-f shows cross-sectional SEM images of hot-rolled B4C/Al6061 composites. After hot rolling, the B4C reinforcement in the Al6061 matrix was arranged according to the rolling direction. This phenomenon is more clearly observed with increasing B4C content ( Figure 1f).    In the case of the 20 vol.% B 4 C composite, change in B 4 C dispersion after hot rolling was not observed well due to highly concentrated B 4 C particles ( Figure 2d). However, it was clearly observed in the 5 vol.% composite after hot rolling. After hot rolling of the stir-cast B 4 C/Al6061 composites, B 4 C particles were arranged according to the rolling direction as shown in Figure 2b. Partially agglomerated B 4 C particles of the stir-cast B 4 C/Al6061 composites were rarely observed in the 3D image of the hot-rolled B 4 C/Al6061 composite. In addition, it was confirmed that pores generated in the stir casting process decreased after hot rolling. In the case of the 20 vol.% B4C composite, change in B4C dispersion after hot rolling was not observed well due to highly concentrated B4C particles (Figure 2d). However, it was clearly observed in the 5 vol.% composite after hot rolling. After hot rolling of the stir-cast B4C/Al6061 composites, B4C particles were arranged according to the rolling direction as shown in Figure 2b. Partially agglomerated B4C particles of the stir-cast B4C/Al6061 composites were rarely observed in the 3D image of the hot-rolled B4C/Al6061 composite. In addition, it was confirmed that pores generated in the stir casting process decreased after hot rolling.

Interfacial Analysis of B4C/Al6061 Composites
EPMA was used to analyze the elemental distribution of B4C/Al6061 composites.

Interfacial Analysis of B 4 C/Al6061
Composites EPMA was used to analyze the elemental distribution of B 4 C/Al6061 composites. Figure 3 shows EPMA mapping images of the 5 vol.% B 4 C/Al6061 composite fabricated by the stir casting process. Since it was manufactured by the casting process, defects were not observed at the B 4 C/Al interface. In the EPMA element mapping images, large amounts of the boron (B) and carbon (C) elements can be observed in the B 4 C areas, which indicates that the crystal structure of the B 4 C particles was maintained in molten Al during the stir-casting process. Elemental titanium (Ti) and chromium (Cr) appeared continuously along the interface between the B 4 C and Al matrix. It is known that AlB 2 and Al 3 BC precipitates form in the B 4 C/Al system [21]. However, these did not appear in the B 4 C/Al6061 composite manufactured by the stir casting process due to the Ti and Cr in the Al6061 alloy. Previous research has revealed the formation of multi-interfacial layers of Al 4 C 3 /(Ti,Cr)B 2 in the B 4 C/Al6061 composites [20]. The formation of interfacial layers can limit the decomposition of B 4 C reinforcements and promote their wettability in liquid Al in the stir casting process. There was no interfacial debonding between the Al matrix and B 4 C reinforcement. Therefore, B 4 C/Al6061 composites fabricated by stir casting followed by the hot rolling process have well-aligned B 4 C distribution along the rolling direction, with a continuous interfacial layer between B 4 C and the Al matrix.
Metals 2021, 11, x FOR PEER REVIEW 5 of 10 the stir casting process. Since it was manufactured by the casting process, defects were not observed at the B4C/Al interface. In the EPMA element mapping images, large amounts of the boron (B) and carbon (C) elements can be observed in the B4C areas, which indicates that the crystal structure of the B4C particles was maintained in molten Al during the stircasting process. Elemental titanium (Ti) and chromium (Cr) appeared continuously along the interface between the B4C and Al matrix. It is known that AlB2 and Al3BC precipitates form in the B4C/Al system [21]. However, these did not appear in the B4C/Al6061 composite manufactured by the stir casting process due to the Ti and Cr in the Al6061 alloy. Previous research has revealed the formation of multi-interfacial layers of Al4C3/(Ti,Cr)B2 in the B4C/Al6061 composites [20]. The formation of interfacial layers can limit the decomposition of B4C reinforcements and promote their wettability in liquid Al in the stir casting process. There was no interfacial debonding between the Al matrix and B4C reinforcement. Therefore, B4C/Al6061 composites fabricated by stir casting followed by the hot rolling process have well-aligned B4C distribution along the rolling direction, with a continuous interfacial layer between B4C and the Al matrix.  Figure 4 is a schematic diagram showing the microstructure of the B4C/Al6061 composites manufactured by stir casting and hot rolling. As confirmed in the three-dimensional images, reinforcements in the composites manufactured by stir casting were randomly arranged in three dimensions. In addition, some pores existed in the Al matrix. Through the hot rolling process, the B4C reinforcement was arranged according to the rolling direction, forming several layers, and pores were remarkably reduced. Therefore, it is expected that well-aligned B4C particles along the wear direction, with decreased pores, could increase composite wear properties. Furthermore, the interfacial layer generated between B4C and the Al6061 matrix is expected to contribute to increasing the wear properties of the composites.   Figure 4 is a schematic diagram showing the microstructure of the B 4 C/Al6061 composites manufactured by stir casting and hot rolling. As confirmed in the three-dimensional images, reinforcements in the composites manufactured by stir casting were randomly arranged in three dimensions. In addition, some pores existed in the Al matrix. Through the hot rolling process, the B 4 C reinforcement was arranged according to the rolling direction, forming several layers, and pores were remarkably reduced. Therefore, it is expected that well-aligned B 4 C particles along the wear direction, with decreased pores, could increase composite wear properties. Furthermore, the interfacial layer generated between B 4 C and the Al6061 matrix is expected to contribute to increasing the wear properties of the composites.   Figure 5 shows SEM images of the wear track after the wear test of the Al6061 matrix and 5, 10, and 20 vol.% B4C/Al6061 composites tested under 5 and 20 N loads. It can be seen that the wear width decreases as the volume fraction of the B4C reinforcement increases. A similar tendency was observed in both conditions (5 N, 20 N). B4C reinforcement was observed around the wear track, but pull-out B4C from the Al matrix was net observed in the SEM images.    Figure 5 shows SEM images of the wear track after the wear test of the Al6061 matrix and 5, 10, and 20 vol.% B4C/Al6061 composites tested under 5 and 20 N loads. It can be seen that the wear width decreases as the volume fraction of the B4C reinforcement increases. A similar tendency was observed in both conditions (5 N, 20 N). B4C reinforcement was observed around the wear track, but pull-out B4C from the Al matrix was net observed in the SEM images.   Figure 6 shows 3D wear tracks and wear depth images obtained using alpha-step equipment. Through 3D mapping analysis, as shown in Figure 6a,b, we confirmed that there was a deviation in wear depth for each wear part. Therefore, cross-sectional analysis of the most worn parts was conducted in Figure 6c,d. At a low load of 5 N, the wear width of the Al6061 matrix was 1303 µm; this value showed a tendency to decrease as the volume ratio of reinforcement increased. The wear width of the 20 vol.% B 4 C/Al6061 composites was measured and found to be 720 µm. The wear depth decreased with increasing B 4 C content from 80 µm (Al6061) to 23 µm (20 vol.% B 4 C/Al6061 composites). Similarly, the wear width and depth also decreased with increasing B 4 C content of the composites tested at 20 N load. The 20 vol.% B 4 C/Al6061 composites had the smallest wear width and depth values of 856 and 36 µm, respectively, tested at 20 N load. These values are believed to have originated from the uniformly dispersed B 4 C particles and increased interfacial bonding with the Al matrix, resulting in increased resistance to wear. value showed a tendency to decrease as the volume ratio of reinforcement increased. The wear width of the 20 vol.% B4C/Al6061 composites was measured and found to be 720 μm. The wear depth decreased with increasing B4C content from 80 μm (Al6061) to 23 μm (20 vol.% B4C/Al6061 composites). Similarly, the wear width and depth also decreased with increasing B4C content of the composites tested at 20 N load. The 20 vol.% B4C/Al6061 composites had the smallest wear width and depth values of 856 and 36 μm, respectively, tested at 20 N load. These values are believed to have originated from the uniformly dispersed B4C particles and increased interfacial bonding with the Al matrix, resulting in increased resistance to wear.   Table 2 shows a summary of the wear width, wear depth, COF, and hardness of the Al6061 and B4C/Al6061 composites. The average COF values of Al6061 and of the 5 vol.%, 10 vol.%, and 20 vol.% composites are 0.35, 0.37, 0.28, and 0.31, respectively. Although the COF of the 5 vol.% sample was slightly higher than that of Al6061, the COF of the B4C/Al6061 composites decreased with the addition of B4C. In the case of 20 N load, the average COF values of Al6061 and of the 5 vol.%, 10 vol.%, and 20 vol.% composites are 0.39, 0.31, 0.33, and 0.38, respectively. The COF of the composites decreases with the increasing vol.% of B4C and reaches a minimum of 0.28 at 10 vol.% B4C. Therefore, it is difficult to say that the friction coefficient decreases as the volume ratio increases. However, the COF of the B4C/Al6061 composites tested at 20 N also slightly decreased with the addition of B4C. Vickers hardness of the composites increased from 116.5 to 139.9 as the B4C volume fraction increased. Therefore, the results reveal that the wear amount and hardness of the B4C/Al6061 composites are inversely proportional. When the load was increased from 5 to 20 N, the wear width of Al6061 increased from 1303 to 2101 μm, and the wear depth increased from 80 to 156 μm, which are 0.61 and 0.95 times increases, respectively. When the load was increased from 5 to 20, the wear width and depth of Al6061 increased 1.5 or 2 times, while that of the composite increased 0.5 times. However, when the load was increased from 5 to 20 N, the wear width of B4C/Al6061 increased from 720 to 856 μm, and the wear depth increased from 20 to 36 μm, which are 0.18 and 0.8 times increases, respectively. As a result, the wear rate was decreased with increasing the volume fraction of B4C. Furthermore, wear rate showed a tendency to   Table 2 shows a summary of the wear width, wear depth, COF, and hardness of the Al6061 and B 4 C/Al6061 composites. The average COF values of Al6061 and of the 5 vol.%, 10 vol.%, and 20 vol.% composites are 0.35, 0.37, 0.28, and 0.31, respectively. Although the COF of the 5 vol.% sample was slightly higher than that of Al6061, the COF of the B 4 C/Al6061 composites decreased with the addition of B 4 C. In the case of 20 N load, the average COF values of Al6061 and of the 5 vol.%, 10 vol.%, and 20 vol.% composites are 0.39, 0.31, 0.33, and 0.38, respectively. The COF of the composites decreases with the increasing vol.% of B 4 C and reaches a minimum of 0.28 at 10 vol.% B 4 C. Therefore, it is difficult to say that the friction coefficient decreases as the volume ratio increases. However, the COF of the B 4 C/Al6061 composites tested at 20 N also slightly decreased with the addition of B 4 C. Vickers hardness of the composites increased from 116.5 to 139.9 as the B 4 C volume fraction increased. Therefore, the results reveal that the wear amount and hardness of the B 4 C/Al6061 composites are inversely proportional. When the load was increased from 5 to 20 N, the wear width of Al6061 increased from 1303 to 2101 µm, and the wear depth increased from 80 to 156 µm, which are 0.61 and 0.95 times increases, respectively. When the load was increased from 5 to 20, the wear width and depth of Al6061 increased 1.5 or 2 times, while that of the composite increased 0.5 times. However, when the load was increased from 5 to 20 N, the wear width of B 4 C/Al6061 increased from 720 to 856 µm, and the wear depth increased from 20 to 36 µm, which are 0.18 and 0.8 times increases, respectively. As a result, the wear rate was decreased with increasing the volume fraction of B 4 C. Furthermore, wear rate showed a tendency to decrease as the applied load increased. The presence of hard B 4 C particles having good interfacial bonding with the Al matrix acts as an obstacle to wear of the soft Al matrix. Therefore, it is possible that the wear properties of the B 4 C/Al6061 composite will increase even further at a higher applied load. decrease as the applied load increased. The presence of hard B4C particles having good interfacial bonding with the Al matrix acts as an obstacle to wear of the soft Al matrix. Therefore, it is possible that the wear properties of the B4C/Al6061 composite will increase even further at a higher applied load.   Figure 8 shows worn surface images of the 20 vol.% B4C/Al6061 composites and Si3N4 ball. Large amounts of fine wear debris and grooves were identified in the B4C/Al6061 composites. In the case of AMCs, the weakly bonded particles with the Al matrix are easily separated from the matrix to create a wear groove on the surface of the specimen, which accelerates surface peeling as wear progresses. However, as a result of confirming the SEM images of the worn surface, it was found that most B4C particles are incorporated in the Al matrix. The surface of the ball had a worn trace and the B4C/Al6061 composite attached to it. Although partial adhesive wear was observed, abrasive wear was suppressed by well-aligned B4C, which had strongly bonded with the Al matrix. It is thought that due to the formation of a continuous interfacial layer between B4C and the Al matrix, pull-out of B4C particles hardly occurred. This is mainly because the interface was tightly bonded by a continuous (Ti,Cr)B2-based layer, and the protruded, well-aligned particles can bear the main wear force by abrasives and protect the surrounding Al matrix from further failure as shown in the schematic diagram in Figure 8f.   Figure 8 shows worn surface images of the 20 vol.% B 4 C/Al6061 composites and Si 3 N 4 ball. Large amounts of fine wear debris and grooves were identified in the B 4 C/Al6061 composites. In the case of AMCs, the weakly bonded particles with the Al matrix are easily separated from the matrix to create a wear groove on the surface of the specimen, which accelerates surface peeling as wear progresses. However, as a result of confirming the SEM images of the worn surface, it was found that most B 4 C particles are incorporated in the Al matrix. The surface of the ball had a worn trace and the B 4 C/Al6061 composite attached to it. Although partial adhesive wear was observed, abrasive wear was suppressed by well-aligned B 4 C, which had strongly bonded with the Al matrix. It is thought that due to the formation of a continuous interfacial layer between B 4 C and the Al matrix, pull-out of B 4 C particles hardly occurred. This is mainly because the interface was tightly bonded by a continuous (Ti,Cr)B 2 -based layer, and the protruded, well-aligned particles can bear the main wear force by abrasives and protect the surrounding Al matrix from further failure as shown in the schematic diagram in Figure 8f.

Conclusions
In this research, well-aligned, interface-controlled B4C/Al6061 composites were successfully fabricated by stir casting, followed by the hot rolling process. B4C particles were well aligned in the Al6061 matrix along the hot rolling direction. As the B4C content increased, the wear width and depth tended to decrease. Compared with that of Al6061, COF also improved via B4C addition. The B4C/Al6061 wear mechanism was mainly de-

Conclusions
In this research, well-aligned, interface-controlled B 4 C/Al6061 composites were successfully fabricated by stir casting, followed by the hot rolling process. B 4 C particles were well aligned in the Al6061 matrix along the hot rolling direction. As the B 4 C content increased, the wear width and depth tended to decrease. Compared with that of Al6061, COF also improved via B 4 C addition. The B 4 C/Al6061 wear mechanism was mainly delamination of Al6061 and the strong interfacial bonding between B 4 C and the Al matrix. The following conclusions can be drawn: • 5, 10, and 20 vol.% of the B 4 C particles were well dispersed by stir casting, and threedimensional irregular particles were arranged along the rolling direction through hot rolling. In addition, dispersion of the B 4 C particles was improved through hot rolling. Informed Consent Statement: Not applicable.

Data Availability Statement:
The data and analysis in this study are available on request from the corresponding author.

Conflicts of Interest:
The authors declare no conflict of interest.