The cassava starch used in this work for the production of plastic films was obtained from the market. Before use, it was dried on a metal plate until a constant mass was obtained.

The mineral filler was a kaolin purchased from the company DAMREC (France) its chemical and mineralogical compositions are given in Table 1 [12] . Metakaolin was obtained after heat treatment at 700˚C of this kaolin, for one hour with a rising rate of 5˚C/min in a programmable furnace of the NABER- THERM model.

*Ignition Loss.

The X-ray diffractograms were obtained using a Siemens equipment D5000 model equipped with a copper anti-cathode (λ = 1.54 Å). The analyzes were carried out on powder material with a grain size of less than 100 m in the range 5˚ < 2θ < 60˚ with a pitch of 0.02˚ and a counting time of 10.1 seconds per step.

Infrared (IR) spectra were obtained using a Fourier Transform spectrometer technique with Perkin Elmer Spectrum 1000 series. The spectral resolution was 4.0 cm⁻¹. The pellets are made from an intimate mixture of sample (1 mg) and potassium bromide (180 mg) then compressed under pressure. The microstructure observation of the samples was carried out using a scanning electron microscope the model Cambridge Stereo scan 260 series. The metallization was carried out by the deposition of layers on/Pd.

Tensile tests were carried out using a tensile dynamometer KERN CH Version 2.7. The device is provided with a fixing clip. The force is exerted vertically and the velocity is assumed to be constant (about 1 mm/min). The applied force is read on the screen of the device and the elongation on the scale incorporated in the device. The thermal resistance of the plastic films was determined at different temperatures using a furnace model NABERTHERM.

The procedure for the production of plastic films is similar to the ones commonly described in the literature [13] [14] . A sample starch (2.5 g) is mixed with 2 ml of glycerol (50% volume) in the presence of 3 ml of 0.1 M hydrochloric acid. The mineral filler (0.5 g) is added to the mixture. The whole is homogenized and then heated to 100˚C on a heating plate equipped with a magnetic stirrer for 10 min. The suspension is then neutralized by the addition of 2 ml of 0.1 M sodium hydroxide solution. Finally, the resulting viscous suspension is poured into petri dishes and then dried at room temperature in 72 hours. The non-reinforced bioplastic is named BP. The bioplastic reinforced with kaolin is named BPK and that reinforced with the metakaolin is named BPMK.

The presence of rays and diffusion halos on the starch powder diffractogram (Figure 1) highlight the semi-crystalline nature of this polymer.

The rays that characterized the three crystalline types of local starches (types A, B and C) are observed from a semi-crystalline material. Indeed, strong reflections are observed at 2θ = 16.43˚ (characteristic of polymorphic C) [15] 17.46˚;

18.28˚, 20.77˚ and 23.36˚ (characteristics of A and B) [16] [17] [18] . Weak reflections also occur at 2θ = 10.82˚, 22˚, 46.15˚.

Fourier transform Infrared spectroscopy (FTIR) was used to determine the functional groups present in starch, which is a carbohydrate formula C₆H₁₀O₅ (Figure 2). A strong and wide vibration band centered around 3400 cm⁻¹ is attributed to the bond stretch [19] while a less intense rays at 2930 cm⁻¹ is characteristic of the vibration of asymmetric stretching C-H of the aliphatic -CH₂ and -CH₂ groups [20] [21] [22] . At 1650 cm⁻¹, the vibration band of H₂O is observed. In the 400 cm⁻¹ - 1600 cm⁻¹ band, the IR spectrum of the starch is characterized by vibration bands at 1400 cm⁻¹; 1350 cm⁻¹; 1219 cm⁻¹ and 1150 cm⁻¹ attributed to the C-OH bond stretch vibrations due to the O-H alcoholic group and to the C-C bond. The vibration bands at 1145 cm⁻¹; 1072 cm⁻¹; 1005 cm⁻¹; 916 cm⁻¹ and 845 cm⁻¹ are relative to the groups; C-O-C, C-O and C-H.

Micrographs of starch obtained through scanning electron microscopy showed round, elliptical, angular and irregular particles with a flattened surface on one side with a tapered hole (Figure 3). As reported in the literature [23] , these particles tend to aggregate easily due to the strong interaction of intermolecular and intramolecular hydrogen bonds in the starch.

Figure 4 shows the X-ray diffraction patterns of kaolin and metakaolin. The characteristic rays of kaolinite (2θ = 12.42˚ and 24.71˚) and illite (2θ = 8.77˚ and 17.65˚) present on the kaolin spectrum are no longer visible on that of the Metakaolin. Only the rays at 2θ = 20.69˚ and 26.67˚ corresponded to the presence of quartz are always present. The kaolinite has lost its crystalline structure to become an amorphous material (metakaolinite). The model of layers, stacking along the c axis in metakaolinite is the same as that of kaolinite. On the other hand, the layer distance is shorter than that in kaolinite. This short range order

is not detectable by the X-ray, hence the absence of characteristic rays of kaolinite and illite.

Figure 5 showed the infrared spectra of kaolin and metakaolin. In the 3000 - 4000 cm⁻¹ bande, the spectrum of crude kaolin is characterized by the 3696 cm⁻¹, 3668 cm⁻¹, 3653 cm⁻¹ and 3620 cm⁻¹ bands due to the hydroxyl stretching vibrations. These bands have been the subject of several studies [24] [25] . The band located at 3696 cm⁻¹ was assigned to the hydroxyls of the edges of the interleaf. Those located at 3668 cm⁻¹ and 3653 cm⁻¹ are attributed to the surface hydroxyls of the octahedral layer in interaction with the base oxygen of the adjacent tetrahedral layer. The 3620 cm⁻¹ band is attributed to the internal hydroxyls. No band characterizing the presence of hydroxyl groups was observed on the metakaolin spectrum; expressing that the heat treatment of the kaolin at 700˚C in 1 hour resulted in a completely dehydroxylated metakaolin.

In the 600 - 1800 cm⁻¹ band range, the spectrum of the crude kaolin showed the absorption bands at 1112 cm⁻¹, 1019 cm⁻¹, 798 cm⁻¹, 754 cm⁻¹ and 698 cm⁻¹. The band at 1112 cm⁻¹ expressed the stretching vibrations of the Si-O apical bonds while that located at 1019 cm⁻¹ is corresponded to the stretching vibrations of the Si-O-Si bonds. The band located at 914 cm⁻¹ corresponded to the vibrations of the deformation of hydroxyls of the aluminum surface Al-O-H. The bands located at 798 cm⁻¹, 754 cm⁻¹ and 698 cm⁻¹ corresponded respectively to Si-O-Al vibrations and hydroxyls perpendicular to the (OH translational) surface [26] . The bands at 476 cm⁻¹ and 432 cm⁻¹ indicated the deformations of the Si-O groups while the band at 540 cm⁻¹ indicated the deformation of the Si-O-Al bonds. On the spectrum of metakaolin, profound changes were observed. The bands allocated to the OH groups and to Si-OH vibrations were no longer detectable. This indicated, in addition to dehydroxylation, a profound modification of the alumino-silicate structure of metakaolin. The relatively intense and acute peak at 798 cm⁻¹ observed in the case of kaolin becomes a reduced, wide and displaced towards 810 cm⁻¹ band of the metakaolin spectrum.

This broad band at 810 cm⁻¹ expressed the degree of structural disorder in metakaolin [27] . These modifications observed in metakaolin indicated a reduction in the cohesion of the layers by the weakening of the hydrogen bonds.

Kaolin is in the shape of hexagonal plates stacked one after the other (Figure 6(a)). Metakaolin platelets resulting from the heat treatment of kaolin have similar but more disordered morphology and more individualized platelets (Figure 6(b)). These observations reveal that the heat treatment of the kaolin at 700˚C for 1 hour results in dehydroxylation and disorganization of the crystalline structure of the material without a significant change on the morphology of the kaolinite platelets.

All elaborated samples have a homogeneous and smooth surface (Figure 7). The non-reinforced bioplastic (BP) is transparent whereas the two other bioplastics reinforced with kaolin (BPK) reinforced with metakaolin (BPMK) is opaque. This difference is due to the presence of the mineral load. The thickness of the samples was 50 μm after drying in Petrie dishes at ambient temperature.

The X-ray diffractograms of the various bioplastics (Figure 8) make it possible to observe the influence of the mineral load on their structural properties. The X-ray diffraction spectra of BP and BPMK showed similarities, leaving out the 2θ = 20.69˚ and 26.67˚ rays visible on the BPMK spectrum. Indeed, these rays indicated the presence of quartz in the plastic film reinforced with metakaolin. On the other hand, the X-ray diffraction spectrum of BPK revealed notable differences. The characteristic rays of kaolinite and quartz are present in thespectrum. This indicated that kaolin retains its structural integrity in the polymer- clay composite.

Figure 9 illustrates the infrared spectra of the reinforced or non-reinforced plastic films. The infrared spectra of BP and BPMK are similar. They are characterized by a strong and broad band centered at 3400 cm⁻¹ due to the stretching

vibrations of the OH groups. On the other hand, for the BPK spectrum, the absorption band centered at 3400 cm⁻¹, is thicker and is similar to that observed in the spectrum of starch. This indicates that the starch has not lost its granular structure despite heating in the presence of kaolin. The 3695 cm⁻¹ and 3670 cm⁻¹ bands, correspond respectively to the hydroxyls of the edges of the layers and to the hydroxides of the surface octahedral layer of the kaolin, are always present confirming the absence of interaction between the hydroxyls and the grains of starch. The absorption band centered on 1100 cm⁻¹ and attributed to the vibration of the C-O-C group of the polymeric chain undergoes profound and different modifications depending on whether the plastic film is reinforced with kaolin or metakaolin. This could be explained by an interaction between theedges of the plates of kaolin and metakaolin made up of cut bonds (Si-O and Al-O) and the polymer.

The micrograph of the plastic films obtained with the scanning electron microscope (Figure 10) showed similarity of structure between the BP and the BPMK. The BPK has a different structure than the other two fore-mentioned. Indeed, during heating of the starch-metakaolin mixture, the solvent penetrates inside the starch grains and causes their swelling. Continued heating of the mixture results in the swelling of the starch grains until they reach a stage where they lose their granular structure: large molecules (essentially amylose) emerge from the grain to be dissolved outside the latter and interact with the metakaolin particles. On the other hand, when the mineral load is kaolin, the solvent is not sufficiently available to allow for enough swelling of the starch grains. Therefore, it can’t lose its granular structure and solubilize.

The uniaxial tensile testing was carried out on samples of thickness e = 0.05 mm and of rectangular section (0.05 mm × 1.8 mm). Figure 11 showed the evolution of the applied stress (σ) as a function of the deformation of the test sample (ε). All the curves have a linear phase corresponding to an elastic deformation of the plastic films. According to Oudet [28] , the elastic deformation is probably due to

the deformation of the valence angle superimposed on the movements of some chains of the amorphous domain. After this phase, a loss of linearity due to a decrease in the cross section of the composites is observed. In this zone, which is referred to as a plastic deformation zone, stress weakening as a function of the deformation due to the occurrence of the intermolecular bond breakdown of hydrogen type is observed.

The physical parameters in tension are given in Table 2.

The Young’s modulus values changed from 19 MPa to 25 MPa when the plastic film is reinforced with metakaolin while it drops to 7 MPa when reinforced with kaolin. The maximum stresses and fracture changed from 4.4 MPa to 5.6 MPa and from 3.5 MPa to 4.7 MPa respectively with the metakaolin-polymer composites. On the other hand, when the kaolin is used for reinforcement, the maximum stresses and fracture drops from 4.4 MPa to 3.3 MPa and from 3.5 MPa to 2.5 MPa respectively. However, the tensile stress at break is the most important (56.3%) with kaolin-polymer composites. This break is progressive in non-reinforced and reinforced with metakaolin plastic films, whereas the break is brutal in the case of kaolin-reinforced plastic film. This improvement in the mechanical properties is attributed to the dispersion state of metakaolin and more precisely to the interactions between the metakaolin particles and the polymer chains. These interactions reduce the mobility of the chains and thus improve the macroscopic stiffness of the composite [29] [30] . Some researchers have found similar values using sepiolite and montmorillonite as reinforcements. They observe an increase in Young’s modulus and elongation at break [31] . But comparison is very difficult because starch mechanical properties strongly depend on the starch botanical source, the type and content of plasticizers as well as the storage relative humidity.

The behavior of the treated samples when heated was studied at different temperatures in a programmable oven (Figure 12). All plastic films remain

thermally stable up to 60˚C and 90˚C, the non-reinforced plastic film is highly softened while the other two remain slightly affected by heat up to 120˚C. At 150˚C, all the plastic films are totally softened. The heat effect is later felt when the plastic films are reinforced with kaolin and metakaolin. This indicates that the mineral load acts as a thermal barrier [32] .