Effect of Morphology of Calcium Carbonate on Toughness Behavior and Thermal Stability of Epoxy-Based Composites

In this study, the modification of an epoxy matrix with different amounts of cube-like and rod-like CaCO3 nanoparticles was investigated. The effects of variations in the morphology of CaCO3 on the mechanical properties and thermal stability of the CaCO3/epoxy composites were studied. The rod-like CaCO3/epoxy composites (EP-rod) showed a higher degradation temperature (4.5 ◦C) than neat epoxy. The results showed that the mechanical properties, such as the flexural strength, flexural modulus, and fracture toughness of the epoxy composites with CaCO3 were enhanced by the addition of cube-like and rod-like CaCO3 nanoparticles. Moreover, the mechanical properties of the composites were enhanced by increasing the amount of CaCO3 added but decreased when the filler content reached 2%. The fracture toughness Kic and fracture energy release rate Gic of cube-like and rod-like CaCO3/epoxy composites (0.85/0.74 MPa m1/2 and 318.7/229.5 J m−2, respectively) is higher than the neat epoxy (0.52 MPa m1/2 and 120.48 J m−2).


Introduction
Epoxy resin is a kind of thermosetting resin with a molecular structure containing at least two epoxy groups.Due to the good adhesive properties, electrical insulation performance, low dielectric constant and dielectric loss, good heat resistance, and chemical resistance of these resins, they have been widely used in adhesives, electronic instruments, the light industry, coatings, electronics, electrical appliances, electronic packaging, aerospace applications, and other fields [1][2][3].However, the application of cured epoxy in the more-demanding fields is limited by its brittleness and poor crack and impact resistance.The commonly used toughening methods include elastomer modification and adding materials with soft molecular structures and epoxy curing agents.These methods effectively improve the toughness of epoxy resins but at the expense of the mechanical modulus and heat resistance of the curing material.
Studies show that incorporating inorganic nanoparticles into the epoxy resin matrix effectively improves the properties of the composite material.The toughening effect of inorganic nanoparticles on epoxy resins is derived from three main aspects.First, the inorganic nanoparticles dispersed in the epoxy resin play a role of transferring stress and reducing stress concentration, thus preventing destructive microcracks from appearing.Second, elongation of the inorganic rigid particle is negligible under the tensile stresses, causing voids on the interface between the matrix and inorganic particles.This blunts the microcracks and impedes the propagation of cracks into destructive cracks.Finally, inorganic nanoparticles have a high specific surface area and active functional groups on the surface of the particles.These functional groups are combined with epoxy resin molecular chains to form a network structure that improves the physical and chemical properties of the epoxy resin.Carbon-based materials, such as carbon nanotubes (CNTs), graphite, and carbon black [4][5][6][7][8][9] can improve the thermal conductivity of the composites due to their intrinsic high thermal conductivity; however, the higher conductivity of this kind of carbon-based composite limits its application in the electronics component packaging field.In order to solve these problems, Zotti et al. [10] used metal-core carbon-shell nanoparticles as nanofiller to fabricate epoxy resin nanocomposites.The metal core/polymeric shell structure nanofiller with magnetic properties enhanced the fracture behaviors significantly.The results show that the effect of nanoparticles on dynamic flexural modulus is negligible (only a 3.6% increase) at room temperature, but this change is more pronounced at higher temperatures.In recent years, researchers have paid attention to the synthesis and modification of epoxy resins through the use of inorganic nanoparticles, such as SiO 2 [11][12][13][14], TiO 2 [15][16][17][18], Al 2 O 3 [19][20][21][22], ZrO 2 [23][24][25][26], CaCO 3 [27][28][29][30] and ZnO [31][32][33][34], as fillers.These inorganic nanoparticles are physically or chemically combined with polymers, which enhances the interfacial bonding between the particles and polymer matrix, and thus improves the toughness and strength.Nanometer calcium carbonate is a common inorganic filler that has been widely used in organic macromolecular materials due to its low cost, low toxicity, and low environmental impact.In addition, its low aspect ratio and large surface area may lead to a strong interfacial interaction between the filler and polymer matrix.Li et al. [35] studied the influence of nano-CaCO 3 on the mechanical properties of an epoxy resin composite and demonstrated that the impact strength and flexural modulus of the nano-CaCO 3 composites improved remarkably when 6 wt.% of nano-CaCO 3 was added.He et al. [36] prepared nano-CaCO 3 /epoxy/carbon fiber composites that showed higher thermal stability and mechanical strength.The results showed that a small amount of nano-CaCO 3 (2−6 wt.%) in the epoxy matrix could significantly increase the thermal stability and mechanical properties.Li et al. [37] modified epoxy resin with ground calcium carbonate (GCC), and the results indicated that the flexural strength and the ratio of the flexural strength to the compressive strength of the epoxy resin mortar were enhanced via the incorporation of GCC.The morphology, size, and amount of nanoparticle dopant directly affect the interfacial interaction between the matrix resin and filler.Zotti et al. [38] reported a sepiolite/epoxy system with different type of sepiolite (hydrated and dehydrated).Compared to the neat epoxy, the sepiolite/epoxy composites show higher T g (≈6 • C) and enhanced modulus at 35 • C.Moreover, its thermo-mechanical properties and fracture properties were enhanced remarkably with 10 wt.% of nanofiller.To date, much research has focused on epoxy/inorganic nanoparticle composites, but seldom on the effects of the nanoparticle morphology on the mechanical and thermal properties of epoxy resins.In addition, the distribution of the nanoparticles with different morphologies (such as spherical, fibrous, lamellar, etc.) in the matrix is also different.
In this work, rod-like and cube-like CaCO 3 were prepared.Nano-CaCO 3 /epoxy composites are subsequently produced by embedding nano-CaCO 3 with different morphology into epoxy resin.The influence of nano-CaCO 3 morphology on the thermal and mechanical properties of the nano-CaCO 3 /epoxy composites was investigated.

Materials
The epoxy resin with bisphenol A diglycidyl ether (185-190 g eq −1 ) was used as the matrix for the composites and purchased from Kukdo Chemical Company (Seoul, Korea).4,4'-diaminodiphenylmethane (DDM) was used as the hardener in this work, which was purchased from TCI Company (Tokyo, Japan).Cube-like calcium carbonate (CaCO 3 ) was obtained from Sigma-Aldrich Company (Seoul, Korea).All chemicals were not further processed except when mentioned specifically.

Synthesis of Nano-CaCO 3 Nanorods
Typically, 2 g CaCO 3 nanoparticles were dispersed in 100 mL acetic acid solution by agitating magnetically at 60 • C for 2 h.Second, 4 g citric acid was added into the clarified solution and stirred for 12 h at 60 • C. The clear solution turned into a milky colloid during the process of stirring.The milky colloid was then filtered and washed several times with ethanol and water.The precursor was dried overnight at 40 • C. Finally, the dried precursor was calcinated at 450 • C for 2 h.

Preparation of Nano-CaCO 3 /Epoxy Composites
The CaCO 3 /epoxy mixture was prepared by pre-dispersing different morphology and amounts of CaCO 3 in acetone under sonication for 30 min.Subsequently, the epoxy resin was added in the above solution under intense electromagnetic stirring at 60 • C.After removing the acetone from the above solution, 17 wt.% of hardener was added to the CaCO 3 /epoxy resin solution under mechanical mixing at 60 • C for 15 min, and then the mixture underwent a degassing process in a vacuum oven at 60 • C for 30 min.Finally, the samples were cured according to the following procedure: 110 • C for 1 h, 140 • C for 2 h, and post-cured at 170 • C for 1 h.The preparation process was shown in Scheme 1.
above solution, 17 wt.% of hardener was added to the CaCO3/epoxy resin solution under mechanical mixing at 60 °C for 15 min, and then the mixture underwent a degassing process in a vacuum oven at 60 °C for 30 min.Finally, the samples were cured according to the following procedure: 110 °C for 1 h, 140 °C for 2 h, and post-cured at 170 °C for 1 h.The preparation process was shown in Scheme 1.

Characterization of Synthetic Compounds
Thermogravimetric analysis of CaCO3 and nano-CaCO3/epoxy composites were carried out using NETZSCH (TGA, TG 209 F3, Bavarian, Germany) with a heating rate of 10 °C min −1 under a N2 atmosphere from room temperature to 800 °C.The structures of CaCO3 inorganic nanomaterials were characterized using X-ray diffraction (XRD, Panalytical Incorporated, Netherlands) with Cu Kα radiation (λ = 1.5405Å ).The cross-sectional of the nano-CaCO3/epoxy composites were conducted by using scanning electron microscopy (SEM, Model SU8010, Hitachi Co., Ltd., Japan).The critical stress intensity factor (Kic) of the epoxy and CaCO3/epoxy was carried out on a universal test machine (Instron Model 1125 mechanical tester, USA) via three-point bending flexure tests and calculated according to the ASTM D5045-95 standard.The schematic of main dimensions of single-edge notch (SEN) samples for the test are shown in Figure S1.The size of the SEN bending sample was 5 × 10 × 50 mm 3 , each with a pre-crack (5 mm) at the center.The sample was pre-cracked with an electric knife, where the length of pre-crack was measured using Vernier calipers and thickness gauges.Moreover, each group of samples contained at least five samples, and the results were averaged after removing the highest and lowest values during the test.The real photos of the prepared (before testing) and tested sample are shown in Figure S1.Scheme 1. Preparation of CaCO3/epoxy composites with different morphology of calcium carbonate.

Results
Scheme 1. Preparation of CaCO 3 /epoxy composites with different morphology of calcium carbonate.

Characterization of Synthetic Compounds
Thermogravimetric analysis of CaCO 3 and nano-CaCO 3 /epoxy composites were carried out using NETZSCH (TGA, TG 209 F3, Bavarian, Germany) with a heating rate of 10 • C min −1 under a N 2 atmosphere from room temperature to 800 • C. The structures of CaCO 3 inorganic nanomaterials were characterized using X-ray diffraction (XRD, Panalytical Incorporated, Netherlands) with Cu Kα radiation (λ = 1.5405Å).The cross-sectional of the nano-CaCO 3 /epoxy composites were conducted by using scanning electron microscopy (SEM, Model SU8010, Hitachi Co., Ltd., Japan).The critical stress intensity factor (K ic ) of the epoxy and CaCO 3 /epoxy was carried out on a universal test machine (Instron Model 1125 mechanical tester, USA) via three-point bending flexure tests and calculated according to the ASTM D5045-95 standard.The schematic of main dimensions of single-edge notch (SEN) samples for the test are shown in Figure S1.The size of the SEN bending sample was 5 × 10 × 50 mm 3 , each with a pre-crack (5 mm) at the center.The sample was pre-cracked with an electric knife, where the length of pre-crack was measured using Vernier calipers and thickness gauges.Moreover, each group of samples contained at least five samples, and the results were averaged after removing the highest and lowest values during the test.The real photos of the prepared (before testing) and tested sample are shown in Figure S1.
The effect of different morphologies and different amounts of CaCO3 on the mechanical properties of epoxy resin were investigated.The formula of flexural strength (σf) and elastic modulus (Eb) values are as follows: Figure 2 shows SEM images of CaCO 3 nanorods and nanocubes.The SEM shows that the particles of Figure 2a were cubes with a side length of around 400 nm, while the particles of Figure 2b were rods with diameters of 50-100 nm and lengths of around 500 nm.Compared with the cube-like CaCO 3 , the interface of the rod-like CaCO 3 is clearer, the lamination phenomenon was weakened, and the dispersibility was improved.A good dispersion property meant the nanoparticles were uniformly dispersed in the epoxy resin matrix, and the composite material generated more microcracks and plastic deformation when subjected to impact, thereby absorbing more impact energy to achieve an enhanced toughening effect.Figure 2 shows SEM images of CaCO3 nanorods and nanocubes.The SEM shows that the particles of Figure 2a were cubes with a side length of around 400 nm, while the particles of Figure 2b were rods with diameters of 50-100 nm and lengths of around 500 nm.Compared with the cubelike CaCO3, the interface of the rod-like CaCO3 is clearer, the lamination phenomenon was weakened, and the dispersibility was improved.A good dispersion property meant the nanoparticles were uniformly dispersed in the epoxy resin matrix, and the composite material generated more microcracks and plastic deformation when subjected to impact, thereby absorbing more impact energy to achieve an enhanced toughening effect.
The effect of different morphologies and different amounts of CaCO3 on the mechanical properties of epoxy resin were investigated.The formula of flexural strength (σf) and elastic modulus (Eb) values are as follows:

∆P ∆m
Processes When the content of CaCO 3 was 2%, its mechanical properties decreased mainly due to the crowding effect, which was caused by the excessive amount of CaCO 3 additive.When the content of CaCO 3 reached 3%, a large number of aggregation points were generated inside the epoxy resin composites.These aggregation points acted as cracks in the material.When the material was subjected to an external force, stress concentration occurred near the tips of the cracks, and subsequently reduced the mechanical properties.
Processes 2019, 7, x 5 of 11 where P is the applied load (N), L is the span length (mm), b is the sample width (in mm), d is the sample thickness (mm), ΔP is the force change in the linear portion of the load-deflection curve (N), and Δm is the corresponding deflection change (mm).
The σf and Eb of CaCO3 nanotubes/epoxy composites with different contents of CaCO3 are shown in Figure 3.All composite materials showed better properties than neat epoxy resin.The CaCO3 nanotubes/epoxy composites shows increased σf and Eb with the increased CaCO3 content, and then decreased when the CaCO3 content went up to 2%.The enhanced σf and Eb properties due to the CaCO3/epoxy interface interactions transferred the mechanical loads from the matrix to the filler.When the content of CaCO3 was 2%, its mechanical properties decreased mainly due to the crowding effect, which was caused by the excessive amount of CaCO3 additive.When the content of CaCO3 reached 3%, a large number of aggregation points were generated inside the epoxy resin composites.These aggregation points acted as cracks in the material.When the material was subjected to an external force, stress concentration occurred near the tips of the cracks, and subsequently reduced the mechanical properties.The fracture toughness K ic and fracture energy release rate G ic of neat epoxy and its composites were determined via K ic and G ic measurements.The K ic and G ic of the composites with different CaCO 3 content was shown in Figure 4.The K ic value can be calculated as follows: where α is the pre-crack width (mm), and Y is the geometrical factor.
The critical strain energy release rate (G ic ) can be calculated as follows: where the Poisson ratio v for the epoxy is v = 0.3; and E is Young's modulus, which obtained from the fracture testing.
As can be seen from the Figure 4, the pure resin was very brittle, where its K ic and G ic values were 0.52 MPa m 1/2 and 120.48 J m −2 , respectively, while that of the EP-rod and EP-cube reached 0.85/0.74MPa m 1/2 and 318.7/229.5 J m −2 at 1.5 wt.%, respectively.The results show that when the content of CaCO 3 increased, the K ic and G ic of the composites increased in the range of less than 1.5 wt.%.This increase in fracture properties can be caused by many toughening mechanisms, such as crack path deflection, crack pinning, plastic void growth, etc. [39,40].However, the K ic and G ic of the composite decreased when the content of CaCO 3 was more than 1.5 wt.%.This indicates that excessive nano-CaCO 3 particles could lead to aggregation in the epoxy resin and reduce the mechanical properties of the epoxy composites, while epoxy composites with a small amount of nano-CaCO 3 exhibited enhanced mechanical properties.The result shows that the fillers were expected to lead to higher fracture toughness and fracture energy than neat epoxy, which means that they could withstand stronger shocks and were more durable than neat epoxy.Furthermore, the dispersed nanoparticles formed Van der Waals bonds between the epoxy group of the epoxy resin and the CaCO 3 particles, enhancing the constraints between the particles/polymer chain and the polymer chain itself [41].Thus, the good dispersion of rod-like CaCO 3 led to a better mechanical property than cube-like CaCO 3 .
effect, which was caused by the excessive amount of CaCO3 additive.When the content of CaCO3 reached 3%, a large number of aggregation points were generated inside the epoxy resin composites.These aggregation points acted as cracks in the material.When the material was subjected to an external force, stress concentration occurred near the tips of the cracks, and subsequently reduced the mechanical properties.The SEM fractographs of neat epoxy, EP-cube-1.5, and EP-rod-1.5 are shown in Figure 5. Figure 5a shows a smooth cross-section and is a typical brittle fracture morphology of neat epoxy resin.In comparison, the EP-cube-1.5(Figure 5b) and EP-rod-1.5 (Figure 5c) show rough surfaces, indicating that the crack path of EP-cube-1.5 and EP-rod-1.5 was more complex than neat epoxy resin, which were caused by the crack deflection mechanism.The addition of CaCO 3 filler led to crack deflection or crack pinning on the fracture surface.Here, nanoparticles could be considered as an obstacle to crack propagation during the material fracture process, such that this kind of crack propagation will leads to higher energy absorption when the epoxy resin breaks [42][43][44], which is consistent with the result of Figure 4. Furthermore, the EP-rod-1.5showed a more undulated surface than EP-cube-1.5,and there were some agglomerates of CaCO 3 particles distributed on the fracture surface of EP-cube-1.5.However, this was not found in EP-rod-1.5,indicating that the rod-like CaCO 3 had a good dispersing effect in the matrix and formed interface with the epoxy resin.
Processes 2019, 7, x 6 of 11 where α is the pre-crack width (mm), and Y is the geometrical factor.
The critical strain energy release rate (Gic) can be calculated as follows: where the Poisson ratio v for the epoxy is v = 0.3; and E is Young's modulus, which obtained from the fracture testing.
As can be seen from the Figure 4, the pure resin was very brittle, where its Kic and Gic values were 0.52 MPa m 1/2 and 120.48 J m −2 , respectively, while that of the EP-rod and EP-cube reached 0.85/0.74MPa m 1/2 and 318.7/229.5 J m −2 at 1.5 wt.%, respectively.The results show that when the content of CaCO3 increased, the Kic and Gic of the composites increased in the range of less than 1.5 wt.%.This increase in fracture properties can be caused by many toughening mechanisms, such as crack path deflection, crack pinning, plastic void growth, etc. [39,40].However, the Kic and Gic of the composite decreased when the content of CaCO3 was more than 1.5 wt.%.This indicates that excessive nano-CaCO3 particles could lead to aggregation in the epoxy resin and reduce the mechanical properties of the epoxy composites, while epoxy composites with a small amount of nano-CaCO3 exhibited enhanced mechanical properties.The result shows that the fillers were expected to lead to higher fracture toughness and fracture energy than neat epoxy, which means that they could withstand stronger shocks and were more durable than neat epoxy.Furthermore, the dispersed nanoparticles formed Van der Waals bonds between the epoxy group of the epoxy resin and the CaCO3 particles, enhancing the constraints between the particles/polymer chain and the polymer chain itself [41].Thus, the good dispersion of rod-like CaCO3 led to a better mechanical property than cube-like CaCO3.The SEM fractographs of neat epoxy, EP-cube-1.5, and EP-rod-1.5 are shown in Figure 5. Figure 5a shows a smooth cross-section and is a typical brittle fracture morphology of neat epoxy resin.In comparison, the EP-cube-1.5(Figure 5b) and EP-rod-1.5 (Figure 5c) show rough surfaces, indicating that the crack path of EP-cube-1.5 and EP-rod-1.5 was more complex than neat epoxy resin, which were caused by the crack deflection mechanism.The addition of CaCO3 filler led to crack deflection The thermal stability of the as-prepared neat epoxy resin, EP-cube composites, and EP-rod composites was measured with a TGA measurement and presented in Figure 6.According to the method proposed by Doyle [45], the integral procedural decomposition temperatures (IPDT) of the samples was analyzed.From the IPDT, we could derive the inherent thermal stability of polymer composites during its thermal degradation.The formula for calculating IPDT is as follows [46,47]: A 1 where A* is the area ratio of the total experimental curve divided by the total TGA thermogram, K* is the coefficient of A*, and T i and T f are the initial and final experimental temperature.A 1 , A 2 , and A 3 are the areas of the divided regions of the TGA curve, which are indicated in Figure S2.
Processes 2019, 7, x 7 of 11 samples was analyzed.From the IPDT, we could derive the inherent thermal stability of polymer composites during its thermal degradation.The formula for calculating IPDT is as follows [46,47]:  In addition, the decomposition activation energy of epoxy resin composites (Et) were obtained from the TGA analysis.The Et of epoxy composites was calculated by using the integral method of Horowitz and Metzger [48].
where α is the decomposition fraction; Tmax is the temperature at the maximum weight loss rate; R is the gas constant; θ = T−Tmax; and Wt, W0, and W∞ are the actual, initial, and final masses of the sample.The thermal stability parameters of the as-prepared samples, including IPDT and Et values, are shown in Table 1.The three samples showed similar TGA curves; however, compared with neat epoxy, the epoxy resin with 1.5% CaCO3 nanorods (EP-rod-1.5)showed a higher degradation temperature (4.5 °C) than pure epoxy resin.The T5% of EP-cube composites and EP-rod composites were significantly higher In addition, the decomposition activation energy of epoxy resin composites (E t ) were obtained from the TGA analysis.The E t of epoxy composites was calculated by using the integral method of Horowitz and Metzger [48].
where α is the decomposition fraction; T max is the temperature at the maximum weight loss rate; R is the gas constant; θ = T−T max ; and W t , W 0 , and W ∞ are the actual, initial, and final masses of the sample.The thermal stability parameters of the as-prepared samples, including IPDT and E t values, are shown in Table 1.
The three samples showed similar TGA curves; however, compared with neat epoxy, the epoxy resin with 1.5% CaCO 3 nanorods (EP-rod-1.5)showed a higher degradation temperature (4.5 • C) than pure epoxy resin.The T 5% of EP-cube composites and EP-rod composites were significantly higher than neat epoxy.However, the temperatures at T 50% increased slightly.This result shows that the modification of the epoxy resin enhanced the chemical stability of the polymer composites.The IPDT of neat epoxy resin was 476.8 • C, while the EP-rod-1.5sample showed the highest IPDT value (533.6 • C), indicating an increase in thermal stability.Furthermore, the E t for the decomposition of the EP-cube composites and EP-rod composites were higher than the neat epoxy resin, which meant higher thermal stability and it need more energy for the thermal decomposition process.In addition, the EP-rod composites showed higher T 5% and E t than the EP-cube composites because rod-like CaCO 3 can be more evenly dispersed in the EP resin than cube-like CaCO 3 , thus the network structure of EP resin was more denser and the interaction between the CaCO 3 and EP molecular chains was enhanced, which limited the thermal motion of the molecular chain of EP, increasing the energy required for thermal decomposition of materials, and enhancing the thermal stability of composites.The EP-rod composites showed higher char yields at 800 • C than the neat epoxy and EP-cube composites, which indicated that rod-like CaCO 3 promoted char formation, which prevented heat transfer and enhanced the thermal stability [49].

Conclusions
The mechanical properties and thermal stability of epoxy resin with different morphologies and contents of CaCO 3 nanoparticles were investigated in this work.The results show that the toughness behavior and thermal stability of epoxy composites with CaCO 3 were significantly better than that of neat epoxy resin.Due to the better dispersing effect of rod-like CaCO 3 than cube-like CaCO 3 , the EP-rod CaCO 3 composites showed better mechanical properties and thermal stability than that of neat epoxy and EP-cube CaCO 3 composites.Observation of the fractured surface using SEM revealed that the EP-rod-1.5showed a more undulated surface than EP-cube-1.5 and neat epoxy resin, and when cracking occurred, the binding force between the nanoparticles and the polymer chains offset more energy, thus the fracture surface exhibited greater toughness.

Supplementary Materials:
The following are available online at http://www.mdpi.com/2227-9717/7/4/178/s1, Figure S1: Dimensions of the sample for fracture toughness test (all dimensions are in mm) and the real picture of the prepared (before testing) and tested sample, Figure S2: Schematic representations of A 1 , A 2 , and A 3 .

Figure 2 .
Figure 2. SEM images of (a) CaCO 3 nanocubes and (b) CaCO 3 nanorods.The effect of different morphologies and different amounts of CaCO 3 on the mechanical properties of epoxy resin were investigated.The formula of flexural strength (σ f ) and elastic modulus (E b ) values are as follows: where P is the applied load (N), L is the span length (mm), b is the sample width (in mm), d is the sample thickness (mm), ∆P is the force change in the linear portion of the load-deflection curve (N), and ∆m is the corresponding deflection change (mm).The σ f and E b of CaCO 3 nanotubes/epoxy composites with different contents of CaCO 3 are shown in Figure3.All composite materials showed better properties than neat epoxy resin.The CaCO 3 nanotubes/epoxy composites shows increased σ f and E b with the increased CaCO 3 content, and then decreased when the CaCO 3 content went up to 2%.The enhanced σ f and E b properties due to the CaCO 3 /epoxy interface interactions transferred the mechanical loads from the matrix to the filler.

Figure 3 .
Figure 3. (a) Flexural strength and (b) elastic modulus of CaCO3 nanocubes/epoxy composites and CaCO3 nanorods/epoxy composites as a function of CaCO3 content

Figure 4 .Figure 3 .
Figure 4. Fracture toughness (Kic) and fracture energy (Gic) of neat epoxy and its epoxy composites with different content of CaCO3.

Figure 3 .
Figure 3. (a) Flexural strength and (b) elastic modulus of CaCO3 nanocubes/epoxy composites and CaCO3 nanorods/epoxy composites as a function of CaCO3 content

Figure 4 .Figure 4 .
Figure 4. Fracture toughness (Kic) and fracture energy (Gic) of neat epoxy and its epoxy composites with different content of CaCO3.The fracture toughness Kic and fracture energy release rate Gic of neat epoxy and its composites were determined via Kic and Gic measurements.The Kic and Gic of the composites with different CaCO3 content was shown in Figure 4.The Kic value can be calculated as follows:   =   3 2 ⁄
=  *  * (  −   ) +   is the area ratio of the total experimental curve divided by the total TGA thermogram, K* is the coefficient of A*, and Ti and Tf are the initial and final experimental temperature.A1, A2, and A3 are the areas of the divided regions of the TGA curve, which are indicated in FigureS2.