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microstructure of the deposit, which in turn will affect the resulting properties of the CC product.
A typical photomicrograph of CVI carbon infiltrated into a PAN fiber preform is shown in figure 27. This micrograph shows the presence of large voids in some parts of the specimen. The CVI deposit consists of two structures: an isotropic phase immediately adjacent to the fiber surface (1 pm thick) and a second highly oriented lamellar structure. The extinction contours generated indicate that the basal planes of this second structure are circumferentially oriented approximately parallel to the fiber surface. The thickness of the deposit varies with fiber spacing and is thickest within the large open pores.
A higher magnification micrograph of the same composite is shown in figure 28, which shows more clearly the structure of the CVI deposits. In this particular region, the CVI deposit appears to have pinched off the pore so that subsequent infiltrations would not be expected to be effective. The bonding between the isotropic CVI layer and the fiber, and between the two CVI layers looks continuous, with no evidence of fissures or cracking.
The continuous nature of the interface between the fiber and the isotropic matrix is confirmed by the TEM dark-field micrograph (fig. 29). The SAD studies suggest that the isotropic layer is composed of small randomly oriented crystallites, while the laminar structure consists of larger highly oriented crystallites. It is interesting that the interface between PAN fibers and isotropic CVI and between pitch fibers and isotropic CVI is continuous. Thus, the development of such an interface appears to depend more on CVI structure than on individual fiber type. The laminar CVI carbon contains many narrow slit-shaped microfissures that are generally <1 pm in length and <0.1 pm in width. This type of cracking is similar to that observed in pitch matrices and indicates that the strength of the bonds between individual crystallite platelets within the lamellar matrix is weaker, in some places, than the bond between the isotropic CVI and the PAN fiber.
A photomicrograph of pitch fibers infiltrated with CVI carbon is shown in figure 30. In this case, conditions of deposition were such that no detectable isotropic layer was observed adjacent to the fiber surface. The CVI carbon exhibits optically anisotropic characteristics and has a rough lamellar structure. At this low magnification, it is difficult to observe if the interface between the fiber and matrix is microcracked, or if microcracks are present within the CVI deposit. Figure 31 shows an SEM micrograph of the same composite after etching with atomic oxygen. The interface between the fiber and CVI matrix is cracked. It should be noted that while the fiber matrix interface in this specimen is cracked, the corresponding interface shown in figure 29 is not. Since both composites were exposed to similar heat treatments, it can be concluded that the bonding between isotropic CVI and fiber is stronger than the bonding between lamellar CVI and fiber.
A TEM bright-field micrograph of the same specimen is shown in figure 32. Cracks are observed in both CVI layers. The interface between the two CVI layers appears relatively continuous, whereas extensive interfacial cracking occurs between the pitch fibers and the first CVI layer. Although etching preferentially attacks interfaces and can exaggerate the size of existing cracks, the technique is useful in detecting different structures and their boundaries. For instance, after etching the previously described specimen in atomic oxygen, examination with the SEM revealed the existence of two distinct CVI layers that were not detected optically (fig. 31). The effect of such a weak fiber-matrix bond is clearly shown in the fracture surface of this composite (fig. 33) where the fibers have been completely pulled out from their surrounding CVI matrix.