Mechanical and Thermal Neutron Absorbing Properties of B 4 C/Aluminum Alloy Composites Fabricated by Stir Casting and Hot Rolling Process

: In this study, to fabricate neutron shielding material, boron carbide (B 4 C)-reinforced aluminum (Al) alloy composites were successfully fabricated by stir casting followed by a hot rolling process. Microstructural analysis of B 4 C/Al6061 composites with different volume fractions (5, 10, 20, 25, and 30%) revealed that the composites had volume ratios similar to the target volume ratios of B 4 C. Furthermore, B 4 C reinforcements were uniformly dispersed in the Al matrix, forming multi-interfacial layers of Al 4 C 3 /(Ti,Cr)B 2 . The interfacial layer generated during stir casting maintained its own structure after the hot rolling process, indicating strong interfacial bonding strength. The tensile strengths of the B 4 C/Al6061 composites increased to 20 vol.% and stayed above the value for Al6061, even reaching 30 vol.%. The measured thermal neutron shielding rate increased with increasing B 4 C content, and the highest thermal neutron shielding rate was observed at 30 vol.% composite, which corresponds to 95.6% neutron shielding at 0.158-cm thickness.


Introduction
Aluminum matrix composites (AMCs), due to their high specific strength, thermal stability, good wear, and weldability, have many advantages in applications in the electronics, vehicle, aerospace, military, marine, and nuclear industries [1]. By changing the type of aluminum (Al) alloy and the reinforcing material, AMCs can be manufactured according to the needs of the application in question [1,2]. Recently, AMCs, which are lighter and more suitable than the conventional materials used in certain industries, have been replaced, and ceramic particles such as B 4 C [3], SiC [4], SiO 2 [5], TiC [6], TiB 2 [7], TiO 2 [8], Al 2 O 3 [9], MgO [10], AlN [11], Gd 2 O 3 [12], BN [13], etc., are used as reinforcement materials [1,14]. Among neutron absorber composites (NACs), B 4 C/Al composites are used as shielding materials in transportation baskets, storage racks, and storage casks for spent nuclear fuel. Materials with excellent neutron absorption include Gd (44,000 barn) [15], 149 Sm (41,500 barn) [16], 10 B (3850 barn) [17], and natural boron (760 barn) [15]. B 4 C has a considerable amount of 10 B (19.9%), and the neutron absorption cross-section is quite large [15]. It is reported that ceramics with excellent neutron absorption capacity, other than B 4 C, have high density and poor mechanical stability during the composite manufacturing process, as well as being expensive [17]. B 4 C, the reinforcing material used in this study, has the advantage of being easy to manufacture because its density is similar to that of aluminum (Al density: 2.7 g/cm 3 ; B 4 C density: 2.52 g/cm 3 ). For this reason, B 4 C-reinforced Al composites are often used in the nuclear shielding field.
Major fabrication methods of NACs include powder metallurgy, hot pressing, hot isostatic pressing, spark plasma sintering, coating, and stir casting [1,18]. Zhang et al. reported that B 4 C/Al composites could be prepared using a powder metallurgy process, i.e., ball milling, followed by pressing, sintering, hot extrusion, and hot rolling [19]. Microstructure analysis and neutron radiography revealed that high-energy ball milling induced homogeneous distribution of B 4 C particles in the Al matrix and good bonding between the Al matrix and the B 4 C particles. Tariq et al. used cold spray technology to deposit a neutron shielding B 4 C/Al composite coating on a 6061-t6 cylindrical substrate [20]. The microstructure, mechanical behavior, and neutron shielding performance of the coating were analyzed according to various heat treatment conditions. Abenojar et al. studied the effect of optimum compression pressure, internal density, and sintering atmosphere on powder metallurgy composite fabrication [21]. Harri Junaedi et al. investigated various strain rates and temperatures for the high-temperature deformation of the Al-15vol.% B 4 C composite [22]. The analysis showed the presence of threshold stress and that its value increases with decreasing the testing temperature.
Among the various fabrication process of NACs, stir casting is an attractive method because it is simpler than other manufacturing methods and has the advantage of easy mass production. However, the B 4 C content of stir cast composites was generally low (less than 20 vol.%) [23][24][25]. It is necessary to fabricate a B 4 C/Al composite containing high B 4 C content using a cost-effective stir casting process to increase functional properties such as neutron shielding, hardness, and modulus. Furthermore, uniform dispersion and precise content control of B 4 C are extremely difficult due to poor wetting between B 4 C/Al and loss of B 4 C particles during the stir casting process. In this study, B 4 C-reinforced Al6061 composites were manufactured by stir casting with the designed mold and stirring system followed by hot rolling.

Experimental Procedure
Al6061 alloy (ThyssenKrupp materials Korea Co., Ltd., Seoul, Korea) was used as a matrix to fabricate metal matrix composites (MMCs). The chemical composition of the Al6061 provided by the company is shown in Table 1. B 4 C powders (Dunhua Zhengxing Abrasive Co., Ltd., Dunhua, China) with a commercial grade of F320 (Federation of European Producers of Abrasives (FEPA)-specified size distributions, 39.0 ± 1.5 µm) were used as reinforcement. The particle size (D 50 ) of the B 4 C reinforcement, measured using laser diffraction spectroscopy (Sympatech HELOS, Clausthal-Zellerfeld, Germany), was 42.95 µm.  (5,10,20,25, and 30%) were prepared by stir casting process, a well-known approach used to fabricate MMCs. The theoretical volume fraction of B 4 C was calculated using the next equation.
where V is volume fraction, W is weight of the matrix and reinforcement, and ρ is the density of each material. We fabricated the stir casting equipment in a chamber system for environment control with the designed mold and stirring system. A schematic sketch of the experimental setup is provided in Figure 1. A pitched blade turbine type of impeller, suitable for suspending particles by strong down-pumping due to generation of axial flow with medium turbulence energy, was used in this research. Even though a propeller type impeller is more advantageous for stirring, a pitched blade turbine type was used due to  Al6061 alloy was melted in a graphite crucible by induction heating und tures of about 750 °C for 20-30 min. Degassing of the melt was performed with After degassing, B4C particles preheated to 200 °C were added to the graph while continuing the stirring process. Stirring was maintained for 10 min at 80 finishing B4C addition. After stirring, the melt was poured into the pre-heated at 200 °C. The fabricated composites were cut into 100 mm × 100 mm × 10 mm rolling process.
For hot rolling, the composites fabricated by the stir casting process were in atmospheric environments after preheating at 500 °C. A pre-heated com was hot rolled and then heat-treated again for 5 min per one pass. The rolling 10 meters per min (MPM) and the final degree of deformation was 84.2%. Th hot-rolled B4C/Al6061 composites were cut into 250 mm × 350 mm sheets.
The microstructures of the composites were observed with a scanning e croscope (SEM, LEO-1450, Zeiss, Oberkochen, Germany), a Cs-corrected fie transmission electron microscope (FE-TEM, JEM-ARM200F, JEOL, Akishima, a field emission electron probe microanalyzer (EPMA, JXA-8530F, JEOL, Ak pan). Sample densities were measured using Archimedes' principle. The ten the stir-cast B4C/Al6061 and the hot-rolled B4C/Al6061 composites were pe room temperature (RT) using a universal testing machine (5882 model, INST wood, MA, USA) with 5 × 10 −3 s −1 head speed. All specimens of the tensile tes pared in a dog bone shape (sub-size ASTM E8) and the test conditions were t all kinds of specimens. The B4C reinforcement volume fraction was calculat SEM images using an in-house code developed by the authors' group [3]. Th code automatically extracts reinforcement information from a given composite the volume fraction is calculated as the ratio between the reinforcement area a image area. Five images were used for each volume fraction calculation and percentage is expressed in this research. Al6061 alloy was melted in a graphite crucible by induction heating under temperatures of about 750 • C for 20-30 min. Degassing of the melt was performed with argon gas. After degassing, B 4 C particles preheated to 200 • C were added to the graphite crucible while continuing the stirring process. Stirring was maintained for 10 min at 800 rpm after finishing B 4 C addition. After stirring, the melt was poured into the pre-heated steel mold at 200 • C. The fabricated composites were cut into 100 mm × 100 mm × 10 mm for the hot rolling process.
For hot rolling, the composites fabricated by the stir casting process were cross-rolled in atmospheric environments after preheating at 500 • C. A pre-heated composite plate was hot rolled and then heat-treated again for 5 min per one pass. The rolling speed was 10 m per min (MPM) and the final degree of deformation was 84.2%. The fabricated hot-rolled B 4 C/Al6061 composites were cut into 250 mm × 350 mm sheets.
The microstructures of the composites were observed with a scanning electron microscope (SEM, LEO-1450, Zeiss, Oberkochen, Germany), a Cs-corrected field-emission transmission electron microscope (FE-TEM, JEM-ARM200F, JEOL, Akishima, Japan), and a field emission electron probe microanalyzer (EPMA, JXA-8530F, JEOL, Akishima, Japan). Sample densities were measured using Archimedes' principle. The tensile tests of the stir-cast B 4 C/Al6061 and the hot-rolled B 4 C/Al6061 composites were performed at room temperature (RT) using a universal testing machine (5882 model, INSTRON, Norwood, MA, USA) with 5 × 10 −3 s −1 head speed. All specimens of the tensile test were prepared in a dog bone shape (sub-size ASTM E8) and the test conditions were the same for all kinds of specimens. The B 4 C reinforcement volume fraction was calculated from the SEM images using an in-house code developed by the authors' group [3]. This in-house code automatically extracts reinforcement information from a given composite image, and the volume fraction is calculated as the ratio between the reinforcement area and the total image area. Five images were used for each volume fraction calculation and the average percentage is expressed in this research.
The neutron shielding test is designed to identify the thermal neutron density in a neutron absorber [21]. This test was performed by the Korea Research Institute of Standards and Science (KRISS). The neutron source was Am 241 -Be (α,n). The device produces about Metals 2021, 11, 413 4 of 12 60 neutrons, less than 0.6 eV, per second and irradiates neutrons on the surface of a neutron absorber for 20 min for each sample [21]. In neutron absorber composites, thermal neutron shielding is facilitated by 10 B isotope through the 10 B (nα) 7 Li transmutation reaction. Neutron shielding ability is defined as the 10 B isotope content present in B 4 C within the composite [2]. To estimate the neutron shielding ability according to the B 4 C content, the neutron transmittance for the B 4 C/Al composite was calculated using the Beer-Lambert law [7].
where I t and I o are the intensities of incoming and transmitted neutrons, respectively, ∑ is the macroscopic neutron transmission cross-section, and d is the thickness of the composite.
In the neutron shielding performance experiment, an SP 9 -He 3 proportional counter was installed in the neutron table weight, and neutron transmittance was determined by measuring the neutron coefficient before and after installation of the composite to be tested.

Microstructures of B 4 C/Al6061 Composites Fabricated by Stir Casting and Hot Rolling Process
Microstructures of the B 4 C/Al6061 composites are shown in Figure 2. For B 4 C/Al6061 composites fabricated by stir casting, some B 4 C particles were clustered (yellow circles), but most B 4 C particles were relatively well dispersed in the Al6061 matrix, as shown in Figure 2a-e. When B 4 C/Al6061 composites are manufactured by stir casting, the B 4 C particles are randomly and three-dimensionally arranged. Because part of the B 4 C particles (irregular shape) are exposed in the 2D SEM image, they look small. B 4 C aggregation in the B 4 C/Al6061 composites fabricated by stir casting has two main causes. First, when the turbulent energy dissipation rate, which is related to the size of the impeller and the revolutions per minute (RPM), is insufficient, B 4 C particles can be partially clustered in the Al6061 matrix. In addition, even if B 4 C is uniformly dispersed in the molten Al during the stir casting process, it can aggregate at the grain boundaries due to grain growth of the Al matrix during solidification. Therefore, it will be possible to improve the dispersibility of B 4 C through control of the stirring process and solidification condition. The measured volume fractions of the B 4 C reinforcement of the stir-cast B 4 C/Al6061 composites, obtained using an image tool program, were 4.89, 9.55, 19.25, 24.01, and 26.35% ( Figure 2). Microstructures of the B 4 C/Al composite plates after hot rolling are shown in Figure 2f-j. After the hot rolling process, the distribution of B 4 C particles was highly improved, with less agglomeration and fewer voids. Therefore, it is confirmed that uniformly dispersed B 4 C/Al6061 composites with negligible defects can be fabricated by a combination of stir casting and hot rolling. Measured volume fractions of B 4 C reinforcement were 4.82, 10.90, 20.02, 25.56, and 29.01% for 5, 10, 20, 25, and 30% B 4 C/Al6061 composites, respectively, values similar to the target volume ratios. The measured volume fractions of B 4 C were within 1% compared to the target volume ratios. This result revealed that B 4 C/Al6061 composites with relatively well controlled B 4 C volume fraction were successfully fabricated by self-designed stir casting followed by the hot rolling process.

Interfacial Analysis of B4C/Al6061 Composites
EPMA analysis was performed to analyze the elemental distributions of stir-cast B4C/Al6061 composites and hot-rolled B4C/Al6061 composites. Figure 3a shows the EPMA analysis results for the 5 vol.% B4C/Al6061 stir-cast AMCs. Since these were manufactured by the casting process, defects were not observed at the B4C/Al interface. The EPMA image shows large amounts of elemental boron (B) and carbon (C), indicating that the crystal structures of the B4C particles are maintained in molten Al during stir casting. Elemental titanium (Ti) and chromium (Cr) appeared continuously along the interface between the B4C reinforcement and Al matrix. It is known that AlB2 and Al3BC precipitates are formed in the B4C/Al system [26]. However, these did not appear in the B4C/Al6061 composite manufactured with the stir casting process due to the presence of Ti and Cr in the Al6061 alloy. Therefore, the interfacial layer entirely generated at the B4C/Al interface can limit the decomposition of B4C reinforcements and promote their wettability in liquid Al in the stir casting process. Figure 3b shows hot-rolled AMCs, indicating the presence of an interfacial layer after hot rolling. There was no interfacial debonding between the Al matrix

Interfacial Analysis of B 4 C/Al6061 Composites
EPMA analysis was performed to analyze the elemental distributions of stir-cast B 4 C/Al6061 composites and hot-rolled B 4 C/Al6061 composites. Figure 3a shows the EPMA analysis results for the 5 vol.% B 4 C/Al6061 stir-cast AMCs. Since these were manufactured by the casting process, defects were not observed at the B 4 C/Al interface. The EPMA image shows large amounts of elemental boron (B) and carbon (C), indicating that the crystal structures of the B 4 C particles are maintained in molten Al during stir casting. Elemental titanium (Ti) and chromium (Cr) appeared continuously along the interface between the B 4 C reinforcement and Al matrix. It is known that AlB 2 and Al 3 BC precipitates are formed in the B 4 C/Al system [26]. However, these did not appear in the B 4 C/Al6061 composite manufactured with the stir casting process due to the presence of Ti and Cr in the Al6061 alloy. Therefore, the interfacial layer entirely generated at the B 4 C/Al interface can limit the decomposition of B 4 C reinforcements and promote their wettability in liquid Al in the stir casting process. Figure 3b shows hot-rolled AMCs, indicating the presence of an interfacial layer after hot rolling. There was no interfacial debonding between the Al matrix and B 4 C reinforcement. This result indicates that only the Al matrix undergoes plastic deformation during the hot rolling process, and the B 4 C/Al interface maintains a strong bonding by the formation of an interfacial layer. and B4C reinforcement. This result indicates that only the Al matrix undergoes plastic deformation during the hot rolling process, and the B4C/Al interface maintains a strong bonding by the formation of an interfacial layer.  Figure 4 shows EPMA analysis results for the 30 vol.% stir-cast B4C/Al6061 and hotrolled B4C/Al6061 composites. Ti and Cr mapping images revealed that an interfacial layer was not perfectly generated at the B4C/Al interface. This is mainly due to insufficient Ti and Cr contents of the Al6061 matrix. Because the interfacial area is considerably increased with increasing B4C contents, the amount of alloying elements such as Ti and Cr required for interfacial layer generation also increases considerably. Further research is, therefore, required to totally generate an interfacial layer by controlling alloying elements according to B4C contents.  Figure 4 shows EPMA analysis results for the 30 vol.% stir-cast B 4 C/Al6061 and hotrolled B 4 C/Al6061 composites. Ti and Cr mapping images revealed that an interfacial layer was not perfectly generated at the B 4 C/Al interface. This is mainly due to insufficient Ti and Cr contents of the Al6061 matrix. Because the interfacial area is considerably increased with increasing B 4 C contents, the amount of alloying elements such as Ti and Cr required for interfacial layer generation also increases considerably. Further research is, therefore, required to totally generate an interfacial layer by controlling alloying elements according to B 4 C contents.    Figure 5 shows a TEM image and energy dispersive spectroscopy (EDS) element mapping images of the interfacial layer. Element mapping images of Al, B, C, Ti, and Cr provide information on the correlation and distribution of different elements. Ti, Cr, and B formed an approximately 200-nm thick layer surrounding B 4 C, and a small precipitate formed in the layer. Furthermore, an Al-based thin layer was observed between the B 4 C and Ti-Cr-B layers. FE-TEM observations were used to determine the nature of the B4C/Al6061 composite interface. Figure 5 shows a TEM image and energy dispersive spectroscopy (EDS) element mapping images of the interfacial layer. Element mapping images of Al, B, C, Ti, and Cr provide information on the correlation and distribution of different elements. Ti, Cr, and B formed an approximately 200-nm thick layer surrounding B4C, and a small precipitate formed in the layer. Furthermore, an Al-based thin layer was observed between the B4C and Ti-Cr-B layers.  Figure 6 shows a FE-TEM image and selected area electron diffraction (SAED) pattern of the interfacial layer. As a result of pattern analysis, the presences of TiB2 and Al4C3 were confirmed. From the EPMA and TEM results, the outer interfacial layer is known to be mainly composed of TiB2, with a small amount of CrB2. Therefore, because CrB2 is isomorphic to TiB2, it was expected that a substitutional solid solution would form with the same crystalline structure and similar lattice parameters [27]. It was predicted that molten Al in the casting process will react quickly with B4C. Indeed, the Al atom rapidly diffused toward B4C and reacted during the casting process to produce Al4C3. Thereafter, Ti and Cr atoms of the Al alloy diffused to B4C and reacted with the B atoms in the interface layer to form a thermodynamically stable and continuous (Ti,Cr)B2 layer on the Al4C3 layer.  Figure 6 shows a FE-TEM image and selected area electron diffraction (SAED) pattern of the interfacial layer. As a result of pattern analysis, the presences of TiB 2 and Al 4 C 3 were confirmed. From the EPMA and TEM results, the outer interfacial layer is known to be mainly composed of TiB 2 , with a small amount of CrB 2 . Therefore, because CrB 2 is isomorphic to TiB 2 , it was expected that a substitutional solid solution would form with the same crystalline structure and similar lattice parameters [27]. It was predicted that molten Al in the casting process will react quickly with B 4 C. Indeed, the Al atom rapidly diffused toward B 4 C and reacted during the casting process to produce Al 4 C 3 . Thereafter, Ti and Cr atoms of the Al alloy diffused to B 4 C and reacted with the B atoms in the interface layer to form a thermodynamically stable and continuous (Ti,Cr)B 2 layer on the Al 4 C 3 layer.  Table 2 summarizes the tensile strengths and relative densities of the Al6061 and B4C/Al6061 composites. The relative densities of the composites increased after hot rolling. It can be seen that the porosity in the composites significantly decreased after hot rolling. For the hot-rolled MMCs, the relative density was over 99%, indicating that the rolling process reduces the apparent porosity to less than 1%.   Table 2 summarizes the tensile strengths and relative densities of the Al6061 and B 4 C/Al6061 composites. The relative densities of the composites increased after hot rolling. It can be seen that the porosity in the composites significantly decreased after hot rolling. For the hot-rolled MMCs, the relative density was over 99%, indicating that the rolling process reduces the apparent porosity to less than 1%. When a B 4 C/Al6061 composite was manufactured by stir casting without additional heat treatment, the tensile strength decreased as the volume ratio increased due to casting defects such as pores and also due to particle agglomeration. However, B 4 C/Al6061 composites after hot rolling showed relatively higher tensile strengths than those of stir-cast B 4 C/Al6061 composites and Al6061. The tensile strength of the hot-rolled B 4 C/Al6061 composites clearly increased up to 20 vol.% and stayed above the value of Al6061, even increasing to 30 vol.%. This higher tensile strength of the composites than that of Al6061 means that applied load in the Al matrix is effectively transferred to the B 4 C in the composites. In the cases of 25 and 30 vol.% composites, the tensile strengths decreased compared to that of the 20 vol.% composite, even though the relative density was more than 99%. The viscosity of molten Al increased highly with the addition of over 20 vol.% B 4 C during the stir casting process, so more defects and B 4 C agglomeration were generated in the stir-cast 25 and 30 vol.% composites than were generated for the 5, 10, and 20 vol.% composites. In addition, even though the interfacial area increased with increasing B 4 C content, Cr and Ti contents of the Al6061 matrix were fixed. Therefore, interfacial layers were not fully generated at the B 4 C/Al interface in the 25 and 30 vol.% composites as shown in Figure 4. Therefore, if the stir casting process is optimized by controlling the dispersibility and alloying elements (Ti, Cr) of the composites, the tensile strength can be expected to improve.

Mechanical Properties of B 4 C/Al6061 Composites
The fracture surface of the 5 vol.% B 4 C/Al6061 composites after tensile testing using sub-size ASTM E8 specimens (Figure 7a) at room temperature was examined by SEM to study the fracture mechanism during tensile deformation. Figure 7b,c show typical SEM micrographs of the fracture surfaces of the tested B 4 C/Al6061 composites. It can be confirmed that fractured B 4 C particles are uniformly distributed on the fracture surfaces of the composites. Both ductile fractures of the Al matrix and brittle fractures of the B 4 C particles were observed. Although there were not many, dimples as large as the B 4 C particle size were also observed in the Al matrix, indicating the possibility of B 4 C pull-out. However, it can be clearly observed that most of the B 4 C incurred cleavage fracture. For intergranular fractures, the interfacial layer should be observed throughout the fractured B 4 C surface. Therefore, the presence of an interfacial layer at the B 4 C/Al interface in most fractured B 4 C samples is evidence of cleavage fracture. Large cracks on the fractured surface of B 4 C particles were occasionally observed. In the case of B 4 C/Al6061 composites, therefore, interfacial layer formation at the B 4 C/Al interface by reaction of B 4 C and Al, Ti, and Cr might cause an effective load transfer from the Al matrix to B 4 C, which would increase the tensile strength of the B 4 C/Al composites. granular fractures, the interfacial layer should be observed throughout the fractured B4C surface. Therefore, the presence of an interfacial layer at the B4C/Al interface in most fractured B4C samples is evidence of cleavage fracture. Large cracks on the fractured surface of B4C particles were occasionally observed. In the case of B4C/Al6061 composites, therefore, interfacial layer formation at the B4C/Al interface by reaction of B4C and Al, Ti, and Cr might cause an effective load transfer from the Al matrix to B4C, which would increase the tensile strength of the B4C/Al composites.  Figure 8 shows the neutron attenuation test facility, consisting of a graphite layer, an SP 9 -He 3 detector, and a neutron source. The graphite layer regulates fast neutrons and produces thermal neutrons. The SP 9 -He 3 detector ascertains the presence of thermal neutrons. The neutron attenuation test verifies the neutron absorption performance by comparing the measured thermal neutron density to the pre-irradiation thermal neutron density [21].   Figure 8 shows the neutron attenuation test facility, consisting of a graphite layer, an SP 9 -He 3 detector, and a neutron source. The graphite layer regulates fast neutrons and produces thermal neutrons. The SP 9 -He 3 detector ascertains the presence of thermal neutrons. The neutron attenuation test verifies the neutron absorption performance by comparing the measured thermal neutron density to the pre-irradiation thermal neutron density [21]. tured B4C samples is evidence of cleavage fracture. Large cracks on the fractured surface of B4C particles were occasionally observed. In the case of B4C/Al6061 composites, there fore, interfacial layer formation at the B4C/Al interface by reaction of B4C and Al, Ti, and Cr might cause an effective load transfer from the Al matrix to B4C, which would increase the tensile strength of the B4C/Al composites.  Figure 8 shows the neutron attenuation test facility, consisting of a graphite layer, an SP 9 -He 3 detector, and a neutron source. The graphite layer regulates fast neutrons and produces thermal neutrons. The SP 9 -He 3 detector ascertains the presence of thermal neu trons. The neutron attenuation test verifies the neutron absorption performance by com paring the measured thermal neutron density to the pre-irradiation thermal neutron den sity [21].    [20]. The measured neutron shielding ratios of B 4 C/Al composites in this research were similar to reported theoretical values. The results indicate that B 4 C/Al composites having superior neutron shielding properties similar to theoretical values are successfully fabricated by stir casting followed by rolling process.

Conclusions
In this paper, 5-30 vol.% B 4 C/Al6061 composites with relatively well controlled B 4 C volume fractions were successfully fabricated by self-designed stir casting followed by the hot rolling process. Microstructures, tensile strengths, and neutron shielding rates of the composites according to the volume fraction of B 4 C were investigated. As the B 4 C content increases, the values of the thermal neutron shielding rate tend to increase. However, strengthening effect of B 4 C was decreased at over 20 vol.% B 4 C content. The tensile strength is expected to be improved by controlling the dispersibility and alloying elements (Ti, Cr) of the composites. Process optimization for high volume fraction of B 4 C/Al composites is now under way. The following conclusions can be drawn:

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The interfacial layer generated during stir casting maintained its own structure after the hot rolling process, indicating strong interfacial bonding strength.

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The tensile strengths of the B 4 C/Al6061 composites clearly increased to 20 vol.% and stayed above the value for Al6061, even reaching 30 vol.% due to partial lack of an interfacial layer at high vol.% B 4 C/Al6061 composites. Institutional Review Board Statement: Not applicable.
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.