Study on the Impact Resistance of Bionic Layered Composite of TiC-TiB2/Al from Al-Ti-B4C System

Mechanical property and impact resistance mechanism of bionic layered composite was investigated. Due to light weight and high strength property, white clam shell was chosen as bionic model for design of bionic layered composite. The intercoupling model between hard layer and soft layer was identical to the layered microstructure and hardness tendency of the white clam shell, which connected the bionic design and fabrication. TiC-TiB2 reinforced Al matrix composites fabricated from Al-Ti-B4C system with 40 wt. %, 50 wt. % and 30 wt. % Al contents were treated as an outer layer, middle layer and inner layer in hard layers. Pure Al matrix was regarded as a soft layer. Compared with traditional homogenous Al-Ti-B4C composite, bionic layered composite exhibited high mechanical properties including flexural strength, fracture toughness, compressive strength and impact toughness. The intercoupling effect of layered structure and combination model of hard and soft played a key role in high impact resistance of the bionic layered composite, proving the feasibility and practicability of the bionic model of a white clam shell.


Introduction
Ceramic reinforced Al matrix composite is a kind of strong vitality material, which meets the demand of modern scientific development and engineering technology. The combination between high strength, hardness, elastic modulus and wear resistance of ceramic [1][2][3] and the low density, high ductility and toughness of Al matrix results in the comprehensive characteristics of light weight, high strength and high wear resistance [4][5][6]. Therefore, ceramic reinforced Al matrix composite is treated as one of the most promising candidate materials in aviation, aerospace, weapons, vehicles, ships and other fields of engineering components. However, the addition of common ceramic reinforcements such as TiC, TiB 2 , Al 2 O 3 , SiC and B 4 C [7][8][9][10] increases the specific strength and specific modulus, and decreases ductility and tenacity of Al matrix composite, reducing the impact resistance and enlarging the possibility of brittle rupture. The shortcomings of the ceramic reinforced Al matrix composite greatly limit its application in working conditions of high impact, stress and pressure [11,12]. The fabrication of ceramic reinforced Al matrix composite with the characteristics of high strength, hardness, ductility, light weight, high strength and impact resistance is crucial to improve the comprehensive performance of engineering components.
In the actual industrial production, many kinds of technologies have been adopted to fabricate ceramic reinforced Al matrix composite, such as powder metallurgy, stirring casting technique, melt infiltration process and flux assisted synthesis [13][14][15][16]. Peng and co-workers [17] fabricated TiC and Al 2 O 3 reinforced Ni-Al matrix composite by hot pressed sintering. Compared with traditional ceramic/Al composite, the TiC-Al 2 O 3 /Ni-Al composite exhibited high strength and fracture toughness. Interface modification can improve the distribution of the ceramic and enhance bonding strength between reinforcement and matrix. In the scale of ceramic reinforcements, due to the high hardness, high elasticity modulus, good wettability, and relative stability with the Al matrix, TiC and TiB 2 are expected to be the best reinforcements for Al matrix composites [7]. Moreover, TiC and TiB 2 reinforced Al matrix composite can be fabricated from an Al-Ti-B 4 C system by self-propagating high temperature synthesis (SHS) directly. Shen and co-workers [18] analyzed the reaction mechanism and behavior of the Al-Ti-B 4 C system. The dissolution-diffusion-precipitation mechanism resulted in the perfect metallurgical bonding between TiC, TiB 2 and Al matrix. Zhou and co-workers [19] prepared B 4 C/2024Al composite with a volume fraction of 45% by a pressure infiltration method. Under the impact of 7.62 mm penetrator, B 4 C/2024Al composite exhibited high impact resistance. Choi and Rhee [20] investigated the effect of Al content on morphology of TiC fabricated from the Al-Ti-C system. When Al content increased from 0 wt. % to 40 wt. %, TiC morphology changed from sintered shape to sphere shape. Particle size of TiC decreased from 15 to 0.4 µm. These technologies focus on matrix modification, interface modification, ceramic phase modification and improvement of the fabrication method. Though the bonding strength, wettability and mechanical properties have been improved, the rigidity enhancement, strength and impact resistance under high impact force is limited.
With the progress of science and human society, bionic research has changed the development of technologies and human civilization. Many kinds of biology such as shells, desert lizard, wood, bamboo, bone and tooth of animals and so on have light weight, high strength and impact resistance properties, providing important references for improving properties of ceramic/Al composite. After investigating the microstructure of Crysomallon squamiferum, Yao and co-workers [21] found that the characteristic of layered structure enhanced its properties of impact resistance, crack arrest and heat insulation. The structure characteristic of Crysomallon squamiferum has been treated as a bionic model for anti-impact material. Weaver and co-workers [22] studied the dactyl club of Odontodactylus scyllarus which owned high-velocity impact characteristics. The characteristics of a multiphase composite of oriented crystalline hydroxyapatite and amorphous calcium phosphate and carbonate and characteristics of a highly expanded helicoidal organization of the fibrillar chitinous organic matrix played an important role in the biological property of Odontodactylus scyllarus, which built a bionic model for the fabrication of armor. The biologies with light weight, high strength and high impact resistance provide a solution method for structure design and combination between light weight and high anti-impact of impact resistance material.
In our previous study [23], the microstructure and mechanical properties of white clam shell has been investigated. White clam shell with perfect mechanical and crack arrest properties consisted of a horny layer, prismatic layer and nacreous layer. Compared with other kinds of shells with good mechanical property, the white clam shell displayed relative light weight and high flexure and compression strength, which met the need of a bionic model for design of bionic layered composites.
Based on the principle of bionics, a white clam shell is chosen as the bionic model of this paper. TiC/TiB 2 -Al composite fabricated from Al-Ti-B 4 C system is chosen as main material of bionic layered material. Based on the light weight, high strength and impact resistance characteristics of the white clam shell, a kind of bionic layered impact resistance material of Al-Ti-B 4 C system is fabricated by corporation method of combustion synthesis and hot pressing sintering. This bionic layered material possesses the capabilities of light weight, high strength and impact resistance and provides a new idea, approach and method for the application of ceramic/Al composite in engineering.

Material
The sample used for investigation of microstructure of white clam shell was purchased in the aquatic product market of Changchun, China. The soft tissues of white clams were removed by a scalpel carefully. Then the shells were rinsed by distilled water, and dried at room temperature for three days. Due to the low curvature and high mechanical properties, the sampling position was close to the wide marginal edge. The test sample for microstructure observation was prepared by breaking fragments from the white clam shells and observed scanning electron microscopy (SEM) (Model Evo18 Carl Zeiss, Oberkochen, Germany). More details about preparation of white calm shell samples can be found in our previous investigation [23].
The starting materials were purchased from commercial powders of aluminum (99.5% puritỹ 48 µm), titanium (99.5% purity~25 µm) and boron carbide (99.9% purity~13 µm), respectively. In this study, the molar ratio of Ti and B 4 C in Al-Ti-B 4 C system was 3:1. In order to realize bionic design and formability of bionic layered composite, the Al content of Al-Ti-B 4 C system varied from 30 to 50 wt. % of the total weight of the mixture. The reactant powders were mixed in a stainless steel container using stainless-steel balls at a low speed (~35 rpm) for 8 h to ensure homogeneity. According to the characteristics of white clam shell, a bionic model was built to guide the arrangement of Al-Ti-B 4 C layers with 30 wt. %, 40 wt. % and 50 wt. % Al contents. To meet the dimension demand of mechanical tests and practical fabrication feasibility, bionic layered composites with Φ 85 mm × 10 mm (30 g 40 wt. % Al-Ti-B 4 C, 10 g Al, 30 g 50 wt. % Al-Ti-B 4 C, 10 g Al and 30 g 30 wt. % Al-Ti-B 4 C) and Φ 85 mm × 6 mm (20 g 40 wt. % Al-Ti-B 4 C, 5 g Al, 20 g 50 wt. % Al-Ti-B 4 C, 5 g Al and 20 g 30 wt. % Al-Ti-B 4 C) were prepared. The 40 wt. % Al-Ti-B 4 C, Al, 50 wt. % Al-Ti-B 4 C, Al, 30 wt. % Al-Ti-B 4 C were laid into a graphite die and pressed into a plane surface successively. The arrangement mode of the layers of pure Al powder and the layers of Al-Ti-B 4 C powder was alternate. Al-Ti-B 4 C layers with different Al content were occupied the outer layer, middle layer and inner layer, respectively. Pure Al layers were arranged between arbitrary two Al-Ti-B 4 C layers, forming the layered pattern of precast block.
The combined precast block was pressed into cylindrical compact (about 85 mm in diameter) using a graphite die to obtain the density of 65% ± 2% theoretical density. Then the graphite die with compact was put into an intermediate frequency furnace under air atmosphere. The layered cylindrical compacts were heated to the ignition temperature of SHS reaction of Al-Ti-B 4 C systems. During the heating process, the temperature of graphite die was measured by an infrared temperature measuring sensor (Asmik, Hangzhou, China). The judge of occurrence of SHS in the ignition process was the sharp incensement of temperature sensor resulting from the heat released from reactions of Al-Ti-B 4 C systems. Then the graphite die was in progress of heat preservation for 5 min at ignition temperature of the infrared temperature measuring sensor. When the temperature decreased and was maintained at fixed point of Al for 5 min, the pressure of 6 t was applied on graphite die to increase the density of the composite. After 5 min of pressure preservation which followed by a cooling progress, the composite was prepared for metallographic and mechanical experiments. In order to exhibit changes in impact resistance property of bionic layered composite, the homogeneity Al-Ti-B 4 C composite was fabricated under the same preparation conditions.

Metallographic Experiment
Metallographic sample with dimension of 10 mm × 10 mm × 10 mm (Length × Width × Thickness) was prepared by a wire-electrode cutting machine to carry out metallography experiment. The samples were ground to get a smooth surface and etched by Keller's reagent (1 vol. % HF + 1.5 vol. % HCl + 2.5 vol. % HNO 3 + 95 vol. % H 2 O). After ultrasonically cleaning in alcohol for 10 min, the specimens were dried in hot air to obtain a clean surface.

Mechanical Practice
Flexural strength, fracture toughness, compressive strength and impact toughness are the key components of mechanical practices used to evaluate the impact resistance property. Therefore, the corresponding mechanical practices were conducted. Due to the ingredient diversity in axial direction of bionic layered composite, the loading direction of the mechanical tests was applied from the outer layer (40 wt. % Al-Ti-B 4 C) to inner layer (30 wt. % Al-Ti-B 4 C).

Microhardness Test
In order to understand hardness variation of different layers of bionic layered composite, a microhardness testing machine (HVS-1000, Shanghai Jujing Precision Instrument Manufacturing Co., Ltd., Shanghai, China) was used to measure hardness by applying a load of 100 g for 5 s on the vertical section. Five measurements were made for each specimen to get the average hardness value.

Flexural Strength Test
Three-point bending tests were used to obtain the flexure strength of bionic layered composite. The flexure strength was calculated by Equation (1).
where σ represented the flexure strength. P was the critical load during bending experiment process. L, b and h were the length of the support span, width and thickness of the samples, respectively. Combine the actual situation of fabrication of bionic layered composite and standard size requirement of flexural strength sample, homogeneity Al-Ti-B 4 C composite and bionic composite specimen were cut into dimensions of 30 mm × 10 mm × 10 mm (Length × Width × Thickness) by the wire-electrode cutting machine. After grounding to get the smooth surface, a universal testing machine (Model DDL-100, Changchun, China) with the constant loading rate of 0.2 mm/min was employed to test flexure strength. The loading span was 24 mm. Average value of flexural strength was calculated from three individual measurements.

Fracture Toughness Test
Ceramic reinforced metal matrix composites were sensitivity to crack. Fracture toughness can measure the crack arrest characteristic of the composite, especially for single edge notched beam method. Equation (2) was used to calculate fracture toughness. The selection of corresponding data was conducted in Reference [24].
where K I represented fracture toughness. Y was the geometry factor of the specimen. P was the critical load. L, b and h were the length of the support span, width and thickness of the samples, respectively. a was notch depth. Fracture toughness was tested by a universal testing machine with a loading rate of 0.2 mm/min (Model DDL-100, Changchun, China). Samples with dimension of 30 mm × 10 mm × 6 mm (Length × Width × Thickness) was cut off by a wire-electrode cutting machine, and grounded to get the smooth surface. The depth and width of notch was 1.3 mm and 0.2 mm, respectively. The loading span for three-point bending tests was 24 mm. Under the condition of 0 ≤ a/h ≤ 0.6, value of Y can be calculated by the following equation [24]. Value of A 0 , A 1 , A 2 , A 3 and A 4 are shown in Table 1. Fracture toughness was obtained from the average value of three parallel tests. The anti-compression property of bionic layered composite and Al-Ti-B 4 C composite was valued according to compression strength. The following equation was used to calculate the compression strength.
where σ represented the compression strength. P was the critical load during compression experiment process. A was the cross sectional area. The bionic and homogeneity composites were cut into a circular column of Φ5 mm × 10 mm by the wire-electrode cutting machine, and grounded to get the smooth surface. Compression strength was tested by a universal testing machine (Model DDL-100, Changchun, China). The constant loading rate was 0.2 mm/min. The average value of the compression strength was got from three individual tests.

Impact Toughness Test
Impact toughness is crucial to measure the impact resistance of bionic composite. Standard Charpy U-notch specimen was used for impact resistance experiment. The impact resistance sample with dimension of 50 mm × 10 mm × 10 mm (Length × Width × Thickness) was cut off by the wire-electrode cutting machine, and grounded to get the smooth surface. The impact toughness was calculated by the following equation.
where a represented impact toughness. A was ballistic work. b and h were width and thickness of specimen. A can be obtained from impact testing machine (Model RPK450, Changchun, China). The loading span for impact toughness tests was 40 mm. The average value of the compression strength was obtained from three individual tests. The metallography and fracture morphology of bionic composite were examined using scanning electron microscopy (SEM) (Model Evo18 Carl Zeiss, Oberkochen, Germany). The phase component was identified using X-ray diffraction (XRD) (Model D/Max 2500PC, Rigaku, Tokyo, Japan). Figure 1 shows the microstructure of a white clam shell. White clam shell can be divided into three layers: horny layer, prismatic layer and nacreous layer, as shown in Figure 1a-c, respectively. From Figure 1a, it can be found that the thickness of the prismatic layer occupies most of the whole thickness of the shell. The prismatic layer consists of various lamellae. The extension direction of a lamella crisscrosses the adjacent ones, exhibiting the typical characteristics of crossed-lamellar structure, as shown in Figure 1b. Compared with Figure 1a,b, the nacreous layer exhibits different surface morphology. The nacreous layer also consists of crossed lamellae, conforming to the characteristics of crossed-lamellar structure. Even though the extension direction of lamellae in the prismatic layer is different from that in nacreous layer, the microstructure of a white clam shell is characterized by crossed-lamellar structure.

Microstructure Characteristic of Bionic Model
In our previous study [23], the effect of microstructure, microhardness gradient on the mechanical properties of white clam shell was disclosed. The microhardness values of horny layer, prismatic layer and nacreous layer were 273 HV, 240 HV and 300 HV, respectively [23]. Different layers presented different hardness values, forming alternation combination model of hard and soft. The hardness value of outer layer was greater and less than that of middle layer and inner layer, respectively, constituting the typical characteristic of combination model of hard and soft. The coupling effect between layered microstructure properties and combination model of hard and soft played a key role in enhancing the mechanical properties of the white clam shell. Based on microstructure characteristics, white clam shell possessed light weight and high strength properties, which satisfied demands of a bionic model for designing a bionic layered composite.

Bionic Coupling Impact Resistance Model
According to the coupling effect between layered microstructure properties and the combination model of a hard and soft of white clam shell, a simplified diagrammatic sketch of a bionic coupling impact resistance model is built to guide the design of bionic layered composite, as shown in Figure 2. The bionic coupling impact resistance model consists of three hard layers and two soft layers. Soft layers space the contiguous two hard layers, connecting hard layers. Hard layers own different intensities of colors, which represents different hardness values. The hardness value of the outer layer is greater and less than that of middle layer and inner layer, respectively, which is consistent with the hardness tendency of white clam shell. The load is applied from outer layer to inner layer, which is

Bionic Coupling Impact Resistance Model
According to the coupling effect between layered microstructure properties and the combination model of a hard and soft of white clam shell, a simplified diagrammatic sketch of a bionic coupling impact resistance model is built to guide the design of bionic layered composite, as shown in Figure 2.

Bionic Coupling Impact Resistance Model
According to the coupling effect between layered microstructure properties and the combination model of a hard and soft of white clam shell, a simplified diagrammatic sketch of a bionic coupling impact resistance model is built to guide the design of bionic layered composite, as shown in Figure 2. The bionic coupling impact resistance model consists of three hard layers and two soft layers. Soft layers space the contiguous two hard layers, connecting hard layers. Hard layers own different intensities of colors, which represents different hardness values. The hardness value of the outer layer is greater and less than that of middle layer and inner layer, respectively, which is consistent with the hardness tendency of white clam shell. The load is applied from outer layer to inner layer, which is The bionic coupling impact resistance model consists of three hard layers and two soft layers. Soft layers space the contiguous two hard layers, connecting hard layers. Hard layers own different intensities of colors, which represents different hardness values. The hardness value of the outer layer is greater and less than that of middle layer and inner layer, respectively, which is consistent with the hardness tendency of white clam shell. The load is applied from outer layer to inner layer, which is similar to the loading direction of the white clam shell. Intercoupling the model between the hard layer and soft layer is identical to the layered microstructure property and hardness tendency of white clam shell. Moreover, the bionic coupling impact resistance model ensures the feasibility of the actual processing, establishing the connection between bionic design and bionic fabrication.   Figure 2. According to the distribution of different layers, Al-Ti-B4C composites and Al matrix can be organized into a layered structure in Figure 2. Namely, bionic layered composite with the characteristics of layered microstructure property and combination model of hard and soft can be fabricated in accordance with a bionic coupling impact resistance model, as shown in Figure 3.  The obvious layered phenomenon of bionic layered impact resistance can be found in metallography of Figure 3. Different hard layers exhibit different color depths, which represents different hardness. Combined with hardness values of 30-50 wt. % Al-Ti-B 4 C system, Al-Ti-B 4 C composites with 40 wt. %, 50 wt. % and 30 wt. % Al contents are the outer layer, middle layer and inner layer, respectively. The white layers are the soft layers of Al matrix. Bionic layered composite has high compactness and metallurgical bonding. From the point view of metallography, bionic layered composite is fabricated successfully in accordance with the bionic coupling impact resistance model. Figure 4 shows the fracture morphology of the outer layer, middle layer and inner layer in bionic layered composite. TiC ceramic particulate with near-spherical shape and TiB 2 ceramic particulate with a nearly rectangular shape exhibit a uniform particle size in every particular Al-Ti-B 4 C layer. Variation of Al content affects ceramic particle size. With the increase of Al content, ceramic particle size decreases. This phenomenon can be explained in the following way briefly. The SHS reaction mechanism of Al-Ti-B 4 C is called the dissolution-diffusion-precipitation mechanism [7,18], resulting in the formation of TiC and TiB 2 . The growth of TiC and TiB 2 is influenced by dwell time at high temperatures and maximum combustion temperature. The higher combustion temperature and longer dwell time promote the ceramic growth. The growth of TiC and TiB 2 is an exponential function of the combustion temperature. The increase of Al content decreases the dwell time at high temperature and increases the liquid metal surrounding the ceramic particulates, which reduces the driving force for ceramic particulates growth and prevents sintering among ceramic particulates to form larger particulates. Therefore, with the increase of Al content, the size of the TiC and TiB 2 particulates decreases. More details about the explanation for this phenomenon are given in previous studies [7,18,25]. Analysis of fracture morphology confirms that the TiC-TiB 2 reinforced Al matrix composite is prepared successfully in every hard layer of bionic layered composite, which builds a substantial base with high mechanical property. inner layer, respectively. The white layers are the soft layers of Al matrix. Bionic layered composite has high compactness and metallurgical bonding. From the point view of metallography, bionic layered composite is fabricated successfully in accordance with the bionic coupling impact resistance model. Figure 4 shows the fracture morphology of the outer layer, middle layer and inner layer in bionic layered composite. TiC ceramic particulate with near-spherical shape and TiB2 ceramic particulate with a nearly rectangular shape exhibit a uniform particle size in every particular Al-Ti-B4C layer. Variation of Al content affects ceramic particle size. With the increase of Al content, ceramic particle size decreases. This phenomenon can be explained in the following way briefly. The SHS reaction mechanism of Al-Ti-B4C is called the dissolution-diffusion-precipitation mechanism [7,18], resulting in the formation of TiC and TiB2. The growth of TiC and TiB2 is influenced by dwell time at high temperatures and maximum combustion temperature. The higher combustion temperature and longer dwell time promote the ceramic growth. The growth of TiC and TiB2 is an exponential function of the combustion temperature. The increase of Al content decreases the dwell time at high temperature and increases the liquid metal surrounding the ceramic particulates, which reduces the driving force for ceramic particulates growth and prevents sintering among ceramic particulates to form larger particulates. Therefore, with the increase of Al content, the size of the TiC and TiB2 particulates decreases. More details about the explanation for this phenomenon are given in previous studies [7,18,25]. Analysis of fracture morphology confirms that the TiC-TiB2 reinforced Al matrix composite is prepared successfully in every hard layer of bionic layered composite, which builds a substantial base with high mechanical property.

Phase Identification
Phase identification of the outer layer, middle layer and inner layer in bionic layered composite are shown in Figure 5. As indicated, the outer layer (40 wt. % Al-Ti-B 4 C system), middle layer (50 wt. % Al-Ti-B 4 C system) and inner layer (30 wt. % Al-Ti-B 4 C system) of bionic layered composite consist of Al, TiC, TiB 2 and Al 3 Ti, as shown in Figure 5a-c. The existence of Al 3 Ti enhances the metallurgical bonding between reinforcements and matrix. The reasons for the appearance of Al, TiC, TiB 2 in bionic layered composite can be briefly explained as follows. SHS reaction of Al-Ti-B 4 C system began with the formation of Ti x Al y compound via solid state diffusion. The C atom of B 4 C disassociated and diffused in Ti x Al y liquid phase, resulting in the formation of Al-Ti-B-C quaternary liquid with low consistence of the B atom. Due to the interface between B 4 C and Al-Ti liquid, there existed a high amount of C, TiC formed firstly on the surface of B 4 C particulate. With the increase of temperature, C and B dissolved and diffused into the liquid phase, forming the Al-Ti-B-C quaternary liquid with high consistence of B atom. TiC and TiB 2 precipitated from the quaternary liquid phase. Therefore, the product of Al-Ti-B 4 C system consisted of Al, TiC, TiB 2 . Moreover, details about the SHS reaction process can be found in previous studies [7,18]. Even though bionic layered composite was fabricated under air, no existence of oxides can be found in the XRD result.

Phase Identification
Phase identification of the outer layer, middle layer and inner layer in bionic layered composite are shown in Figure 5. As indicated, the outer layer (40 wt. % Al-Ti-B4C system), middle layer (50 wt. % Al-Ti-B4C system) and inner layer (30 wt. % Al-Ti-B4C system) of bionic layered composite consist of Al, TiC, TiB2 and Al3Ti, as shown in Figure 5a-c. The existence of Al3Ti enhances the metallurgical bonding between reinforcements and matrix. The reasons for the appearance of Al, TiC, TiB2 in bionic layered composite can be briefly explained as follows. SHS reaction of Al-Ti-B4C system began with the formation of TixAly compound via solid state diffusion. The C atom of B4C disassociated and diffused in TixAly liquid phase, resulting in the formation of Al-Ti-B-C quaternary liquid with low consistence of the B atom. Due to the interface between B4C and Al-Ti liquid, there existed a high amount of C, TiC formed firstly on the surface of B4C particulate. With the increase of temperature, C and B dissolved and diffused into the liquid phase, forming the Al-Ti-B-C quaternary liquid with high consistence of B atom. TiC and TiB2 precipitated from the quaternary liquid phase. Therefore, the product of Al-Ti-B4C system consisted of Al, TiC, TiB2. Moreover, details about the SHS reaction process can be found in previous studies [7,18]. Even though bionic layered composite was fabricated under air, no existence of oxides can be found in the XRD result.   The analysis of flexural appearance of bionic layered composite indicated that variation of Al content significantly affected flexural strength. Under the applied bend load, the outer layer of 40 wt. % Al-Ti-B4C composite endured the highest applied load, resulting in the existence of long and wide cracks. The addition of soft layer of Al absorbed some load and released damage of middle and inner layer. Therefore, no continuous and destructive cracks can be found in Figure 7b,c. The three layers of bionic composite defused the applied load by intergranular fracture, leading to the existence of a pit. With the increase of Al content, ceramic particle size decreased, which resulted in the decrease of the size of the pits in Figure 7. Combined with Figure 6, layered structure and combination model of hard and soft significantly enhance flexural strength of the bionic layered composite. There is no existence of continuous and destructive cracks on middle and inner layer. In the magnified microstructure of three layers, a number of pits with different size exist on flexural appearance. When Al content increases from 30 to 50 wt. %, the size of the pits decreases.
The analysis of flexural appearance of bionic layered composite indicated that variation of Al content significantly affected flexural strength. Under the applied bend load, the outer layer of 40 wt. % Al-Ti-B 4 C composite endured the highest applied load, resulting in the existence of long and wide cracks. The addition of soft layer of Al absorbed some load and released damage of middle and inner layer. Therefore, no continuous and destructive cracks can be found in Figure 7b,c. The three layers of bionic composite defused the applied load by intergranular fracture, leading to the existence of a pit. With the increase of Al content, ceramic particle size decreased, which resulted in the decrease of the size of the pits in Figure 7. Combined with Figure 6, layered structure and combination model of hard and soft significantly enhance flexural strength of the bionic layered composite.

Fracture Toughness
Fracture toughness is a key parameter to measure the crack arrest property of the material. Fracture toughness of bionic sample (12.2 MPa/m 2 ) is almost 4.7, 2.6 and 1.5 times as great as Al-Ti-B4C composite with 30 wt. % (2.6 MPa/m 2 ), 40 wt. % (4.7 MPa/m 2 ) and 50 wt. % (8.3 MPa/m 2 ) Al content, respectively, as shown in Figure 6. Identification of fracture appearance is beneficial to understand the crack arrest property of bionic layered composite. The corresponding result is shown in Figure 8a-f. Fracture appearance of three layers in bionic layered composite present irregular morphology and a number of small pits with different size and cracks. In the initial stage of bend progress, the applied load led to the extension of crack in the position of the crack presented in the specimen. During the process of crack extension, most TiC and TiB2 crystalline grains in three layers were extracted, leading to intergranular fracture phenomenon and irregular morphology. When the cracks reached the soft layers, the toughness fracture of Al restricted

Fracture Toughness
Fracture toughness is a key parameter to measure the crack arrest property of the material. Fracture toughness of bionic sample (12.2 MPa/m 2 ) is almost 4.7, 2.6 and 1.5 times as great as Al-Ti-B 4 C composite with 30 wt. % (2.6 MPa/m 2 ), 40 wt. % (4.7 MPa/m 2 ) and 50 wt. % (8.3 MPa/m 2 ) Al content, respectively, as shown in Figure 6. Identification of fracture appearance is beneficial to understand the crack arrest property of bionic layered composite. The corresponding result is shown in Figure 8a

Fracture Toughness
Fracture toughness is a key parameter to measure the crack arrest property of the material. Fracture toughness of bionic sample (12.2 MPa/m 2 ) is almost 4.7, 2.6 and 1.5 times as great as Al-Ti-B4C composite with 30 wt. % (2.6 MPa/m 2 ), 40 wt. % (4.7 MPa/m 2 ) and 50 wt. % (8.3 MPa/m 2 ) Al content, respectively, as shown in Figure 6. Identification of fracture appearance is beneficial to understand the crack arrest property of bionic layered composite. The corresponding result is shown in Figure 8a-f. Fracture appearance of three layers in bionic layered composite present irregular morphology and a number of small pits with different size and cracks. In the initial stage of bend progress, the applied load led to the extension of crack in the position of the crack presented in the specimen. During the process of crack extension, most TiC and TiB2 crystalline grains in three layers were extracted, leading to intergranular fracture phenomenon and irregular morphology. When the cracks reached the soft layers, the toughness fracture of Al restricted In the initial stage of bend progress, the applied load led to the extension of crack in the position of the crack presented in the specimen. During the process of crack extension, most TiC and TiB 2 crystalline grains in three layers were extracted, leading to intergranular fracture phenomenon and irregular morphology. When the cracks reached the soft layers, the toughness fracture of Al restricted crack extension and enhanced fracture toughness. Due to the intercoupling model between the hard layer and soft layer, the bionic layered composite exhibited the perfect crack arrest property and interlayer bonding.

Compressive Strength
Compression strength values of 30-50 wt. % Al-Ti-B 4 C composites and bionic layered composite can be found in Figure 6. Compressive strength of bionic sample is 137.4 MPa, which is higher than that of Al-Ti-B 4   During the compression progress, TiC and TiB2 particles were extracted and broken by the compression load, resulting in pits and cracks to defuse load. The existence of pits and cracks in Figure 9 indicated that the dominant fracture behavior of the three hard layers was the intergranular fracture. When cracks reached the soft layers, the high toughness of Al layers enhanced the compression strength of bionic sample and reset extension direction of cracks in the next layer. The layered structure and intercoupling model between the hard layer and soft layer led to a higher compression strength than that of traditional homogenous Al-Ti-B4C composite.

Impact Toughness
Compared with traditional homogenous Al-Ti-B4C composite, bionic layered composite possessed high mechanical properties including flexural strength, fracture toughness and During the compression progress, TiC and TiB 2 particles were extracted and broken by the compression load, resulting in pits and cracks to defuse load. The existence of pits and cracks in Figure 9 indicated that the dominant fracture behavior of the three hard layers was the intergranular fracture. When cracks reached the soft layers, the high toughness of Al layers enhanced the compression strength of bionic sample and reset extension direction of cracks in the next layer. The layered structure and intercoupling model between the hard layer and soft layer led to a higher compression strength than that of traditional homogenous Al-Ti-B 4 C composite.

Impact Toughness
Compared with traditional homogenous Al-Ti-B 4 C composite, bionic layered composite possessed high mechanical properties including flexural strength, fracture toughness and compressive strength, which builds its base of high impact resistance. Therefore, in order to investigate the impact resistance of bionic layered composite, the impact toughness and impact appearance were studied. The corresponding results are shown in Figures 6 and 10, respectively. Impact toughness of bionic layered composite is 17 J/cm 2 , which is higher than that of Al-Ti-B 4 C composites. Variation of Al content influences the impact toughness of Al-Ti-B 4 C composite with 30-50 wt. % Al content. Impact toughness values of homogenous 30 wt. %, 40 wt. % and 50 wt. % Al-Ti-B 4 C composites are 2.5 J/cm 2 , 3.6 J/cm 2 and 12.0 J/cm 2 , respectively. Figure 10a-f is the impact appearance and magnified microstructure of three layers in bionic layered composite. A large number of pits exist on the irregular impact appearance. It is worth noting that several dimples and cracked ceramic particles resulting from a certain degree of plastic deformation appear on the inner layer. In contrast to the inner layer, a crack is characteristic of the outer layer and middle layer of a bionic layered composite. Under the applied impact load, a bionic layered composite shows high interlayer bonding between the hard layer and soft layer. Analysis of impact appearance discloses the high impact resistance of the bionic layered composite. investigate the impact resistance of bionic layered composite, the impact toughness and impact appearance were studied. The corresponding results are shown in Figures 6 and 10, respectively. Impact toughness of bionic layered composite is 17 J/cm 2 , which is higher than that of Al-Ti-B4C composites. Variation of Al content influences the impact toughness of Al-Ti-B4C composite with 30-50 wt. % Al content. Impact toughness values of homogenous 30 wt. %, 40 wt. % and 50 wt. % Al-Ti-B4C composites are 2.5 J/cm 2 , 3.6 J/cm 2 and 12.0 J/cm 2 , respectively. Figure 10a-f is the impact appearance and magnified microstructure of three layers in bionic layered composite. A large number of pits exist on the irregular impact appearance. It is worth noting that several dimples and cracked ceramic particles resulting from a certain degree of plastic deformation appear on the inner layer. In contrast to the inner layer, a crack is characteristic of the outer layer and middle layer of a bionic layered composite. Under the applied impact load, a bionic layered composite shows high interlayer bonding between the hard layer and soft layer. Analysis of impact appearance discloses the high impact resistance of the bionic layered composite. After investigation of mechanical properties of bionic layered composite, it can be found that the bionic layered composite had relatively high flexural strength, fracture toughness, compression strength and impact toughness, which constructed a solid foundation for high impact resistance property. Under the applied impact load, due to mezzo mechanical properties, the outer layer of the bionic layered composite absorbed partial impact load in the form of an intergranular fracture. The soft layer of Al connected with the outer layer possessed high toughness, which restrained the appearance of the slabbing phenomenon. The middle layer of 50 wt. % Al-Ti-B4C composite possessed the lowest hardness and highest mechanical propertied among Al-Ti-B4C composites, which absorbed and defused most of the impact load. The soft layer connected with the middle layer absorbed impact load and reset the extension direction of cracks in next layer in the form of a ductile fracture. The highest hardness value of the inner layer of 30 wt. % Al-Ti-B4C composite played the role of fixing the position of the other layers and prevented delivery of the impact load. The intercoupling effect of the layered structure and combination model of hard and soft was the key point of the high impact resistance property of the bionic layered composite, which proved the feasibility and practicability of bionic design in Figure 2. After investigation of mechanical properties of bionic layered composite, it can be found that the bionic layered composite had relatively high flexural strength, fracture toughness, compression strength and impact toughness, which constructed a solid foundation for high impact resistance property. Under the applied impact load, due to mezzo mechanical properties, the outer layer of the bionic layered composite absorbed partial impact load in the form of an intergranular fracture. The soft layer of Al connected with the outer layer possessed high toughness, which restrained the appearance of the slabbing phenomenon. The middle layer of 50 wt. % Al-Ti-B 4 C composite possessed the lowest hardness and highest mechanical propertied among Al-Ti-B 4 C composites, which absorbed and defused most of the impact load. The soft layer connected with the middle layer absorbed impact load and reset the extension direction of cracks in next layer in the form of a ductile fracture. The highest hardness value of the inner layer of 30 wt. % Al-Ti-B 4 C composite played the role of fixing the position of the other layers and prevented delivery of the impact load. The intercoupling effect of the layered structure and combination model of hard and soft was the key point of the high impact resistance property of the bionic layered composite, which proved the feasibility and practicability of bionic design in Figure 2.

Conclusions
After summarizing the microstructure property of the white clam shell, a bionic coupling impact resistance model was established to guide the design of the bionic layered composite. The mechanical properties and impact resistance mechanism of the bionic layered composite fabricated by combination method of combustion synthesis and hot pressed sintering were investigated. The conclusions are described as follows: (1) White clam shell with characteristic of crossed-lamellar structure can be divided into three layers: horny layer, prismatic layer and nacreous layer. The coupling effect between layered microstructure and combination model of hard and soft layers played the key role in enhancing mechanical properties of the white clam shell, which satisfied demands of a bionic model for design of bionic layered composite.
(2) A simplified bionic coupling impact resistance model was built to guide the design of the bionic layered composite. The intercoupling model between the hard layer and soft layer was identical to the layered microstructure property and hardness tendency of a white clam shell.
(3) Combined with hardness values of 30-50 wt. % Al-Ti-B 4 C system, Al-Ti-B 4 C composites with 40 wt. %, 50 wt. % and 30 wt. % Al contents were the outer layer, middle layer and inner layer, respectively. The soft layers were Al matrix. As the role of the main material in bionic layered material, fracture morphology and phase identification confirmed the successful fabrication of TiC-TiB 2 reinforced Al matrix composite.
(4) Compared with traditional homogenous Al-Ti-B 4 C composite, high mechanical properties including flexural strength, fracture toughness and compressive strength formed the base of the high impact resistance of bionic layered composite. The intercoupling effect of layered structure and combination model of hard and soft layers was the key point of the high impact resistance property of the bionic layered composite, which proved to have the feasibility and practicability of bionic design contained in a white clam shell.