low-cost source of laminar particles. However, delamination, dispersion, and distribution of talc within the polymer and matrix-particle interface all have a significant effect on the performance of PP/talc composites. Untreated talc tends to agglomerate when it is compounded with PP, resulting in poor dis- persion. Moreover, low compatibility between PP and the talc surface leads to poor interfacial adhesion and results in a composite with poor mechanical properties.1–3
Composite performance can be improved by modifications in the matrix, the filler’s surface, or both. Matrix modification has been carried out using peroxides, but the final properties are generally impaired because of molecular-weight degradation by chain scission.4 Enhancing the filler-matrix interphase can be achieved by modify- ing the filler surface. Using coupling agents has been suggested as a way to reduce agglomeration and improve particle dispersion and distribution.5, 6 However, these agents are more costly than talc. Here, we propose grafting acetoxy groups to the talc surface as a cost-effect alternative.
We have developed a process, based on a particular acidic treatment of talc, that enables delamination, particle size reduction, and surface functionalization. Hydroxyl groups on the borders of talc laminar parti- cles react with the acidic protons, grafting acetoxy groups (-COOCH3/ to the surface. The acetoxy groups render the talc surface more hydrophobic so that talc stacks break down into thin, individual platelets. This favors talc delamination and preserves the laminar morphology. In addition, particle size is reduced to the nanometer scale (platelet thickness).7
We compared the performance of the composites containing either untreated (A10) or treated (A10A) talc. We observed the influ- ence of the talc surface treatment on composite morphology by its
Figure 1. Cross-section of a composite of polypropylene (PP) and 10% by weight treated talc (A10A) showing the orientation of talc parti- cles in an injected specimen and scanning electron microscopy (SEM) images (2000 ) at different points.
particle dispersion and distribution (see Figure 1). We attribute these characteristics to the hydrophobic nature of the surface-grafted acetoxy groups.7 Also, the preferred talc particle orientation, which strengthens the matrix, is a consequence of the motion of talc platelets in a viscous medium during the injection-molding process.
Another benefit of incorporating modified talc is the improvement of talc-PP adhesion compared with the adhesion between untreated talc and PP: compare Figure 2(a) and (b). We attributed this improvement to the particle-polymer links that remain after cryogenic fracture of the composites.
Stress-strain curves of PP and PP/talc composites reveal the effect of talc modification, supported by the clear evidence from the photographs of the specimen after mechanical testing (see Figure 3). The modulus of the PP/A10A composite is slightly higher than that of the PP/A10 (untreated) composite. We tentatively attribute this to the extremely small particle size and better dispersion in the treated- talc composites, which both contribute to an increase in modulus by forming an interconnected particle network.8 However, major improve- ments are observed in yield stress (21%), elongation at break (44%),
low-cost source of laminar particles. However, delamination, dispersion, and distribution of talc within the polymer and matrix-particle interface all have a significant effect on the performance of PP/talc composites. Untreated talc tends to agglomerate when it is compounded with PP, resulting in poor dis- persion. Moreover, low compatibility between PP and the talc surface leads to poor interfacial adhesion and results in a composite with poor mechanical properties.1–3Composite performance can be improved by modifications in the matrix, the filler’s surface, or both. Matrix modification has been carried out using peroxides, but the final properties are generally impaired because of molecular-weight degradation by chain scission.4 Enhancing the filler-matrix interphase can be achieved by modify- ing the filler surface. Using coupling agents has been suggested as a way to reduce agglomeration and improve particle dispersion and distribution.5, 6 However, these agents are more costly than talc. Here, we propose grafting acetoxy groups to the talc surface as a cost-effect alternative.We have developed a process, based on a particular acidic treatment of talc, that enables delamination, particle size reduction, and surface functionalization. Hydroxyl groups on the borders of talc laminar parti- cles react with the acidic protons, grafting acetoxy groups (-COOCH3/ to the surface. The acetoxy groups render the talc surface more hydrophobic so that talc stacks break down into thin, individual platelets. This favors talc delamination and preserves the laminar morphology. In addition, particle size is reduced to the nanometer scale (platelet thickness).7We compared the performance of the composites containing either untreated (A10) or treated (A10A) talc. We observed the influ- ence of the talc surface treatment on composite morphology by itsFigure 1. Cross-section of a composite of polypropylene (PP) and 10% by weight treated talc (A10A) showing the orientation of talc parti- cles in an injected specimen and scanning electron microscopy (SEM) images (2000 ) at different points.particle dispersion and distribution (see Figure 1). We attribute these characteristics to the hydrophobic nature of the surface-grafted acetoxy groups.7 Also, the preferred talc particle orientation, which strengthens the matrix, is a consequence of the motion of talc platelets in a viscous medium during the injection-molding process.Another benefit of incorporating modified talc is the improvement of talc-PP adhesion compared with the adhesion between untreated talc and PP: compare Figure 2(a) and (b). We attributed this improvement to the particle-polymer links that remain after cryogenic fracture of the composites.Stress-strain curves of PP and PP/talc composites reveal the effect of talc modification, supported by the clear evidence from the photographs of the specimen after mechanical testing (see Figure 3). The modulus of the PP/A10A composite is slightly higher than that of the PP/A10 (untreated) composite. We tentatively attribute this to the extremely small particle size and better dispersion in the treated- talc composites, which both contribute to an increase in modulus by forming an interconnected particle network.8 However, major improve- ments are observed in yield stress (21%), elongation at break (44%),
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