carbon nanotube （CNT） is a type of carbon nanomaterial. Its diameter is on the nanometer scale, andits length is on the micron scale. CNT has remarkable properties. There are various types of CNT synthesismethods. However, it is difficult to disperse CNTs after synthesis; thus, dispersion techniques are vital. In thispaper, we introduce a CNT dispersion technique and present the characterization of CNT samples. To disperseCNTs, it is important to choose appropriate equipment and dispersants. Sonication and wet-jet milling aresuperior techniques for dispersing CNTs. Surfactants or polycyclic aromatic hydrocarbon compounds arewidely used as dispersing agents. However, designing and selecting dispersing agents is a serious challenge.Spectroscopy and microscopy are standard techniques for evaluating CNT dispersion. UV–Vis–NIR andRaman spectroscopies, atomic force, scanning electron and transmissionelectron microscopies are widelyused to characterize and dispersed CNTs. CNTs are applied broadly in various fields; for example, in materialsengineering, they are useful for achieving high mechanical performance in polymer composites and forpreparing rubber compounds with low electrical resistivity, as well as many other applications. Furthermore,CNTs are also applied in sensors, transistors, and high transparent/low surface resistivity films.

In this study, nylon microcapsules were prepared on a paper surface using an interfacial polymerizationreaction for the preparation of a functional paper. After impregnation with ethylenediamine　（EDA） solution,filter paper was placed in a beaker containing organic solvent（ cyclohexane, chloroform, or cyclohexanechloroformsolvents （volume ratio = 3:1, 1:1, 1:3）, a terephthaloyl chloride. When cyclohexane was usedas the organic solvent, a nylon capsule structure formed on the paper surface. Then, a pressure-sensitiveadhesive paper that did not require release paper, and a functional paper with a polyamide film containingvolatile essential oil composites （VEO） using this interfacial polymerization reaction. The pressure-sensitiveadhesive paper prepared employing the interfacial polymerization did not require the use of release paper. Thepaper prepared using this technique adhered sufficiently to the alumna foil after a hot-press treatment. EDAconcentration of 5％ and a 60-mL volume of the 35％ SIS–cyclohexane solution maximized the adhesivenessof paper. This successfully fixed the nylon film containing the VEO on the paper surface. Release of VEOfragrance from the paper surface was studied, and the paper showed sustained release of the VEO.

The effect of a surface texture of a single lap joint bonded with cyanoacrylate resin on the adhesive strengthwas experimentally investigated. The surface was shot blasted to make the target texture surface by using theabrasive media which had different sizes and shapes. Sdr（developed interfacial area ratio of the scale-limitedsurface） was adapted in the surface texture parameters to investigate a relation between the adhesive areaand the wetting tension. These result revealed that the increase of adhesive strength of shot blasted surfacewas able to be estimated by the developed interfacial area.

In-situ modified epoxy resins with polyurethanes （U-BAEs） were synthesized and measured the propertiesof the cured blends in order to improve the low fracture toughness derived from the brittleness withoutdecreasing the strength and heat-resistant. U-BAEs were synthesized in changing contents of a bis-phenolA type epoxy resin （BAE）, and then the cured blends were prepared by using an anhydride as a hardener,after that effects of BAE's contents on the morphologies of the cured blends, properties of them and therelationships between them were inspected. As the results of that, in the cured blends of U-BAEs synthesizedin a 20 wt. ％ content of BAE, flocks with a size of a few micro-meter formed by cohesion of polyurethane（ PU）domains with a size of sub-micro-meter and spherical epoxy matrices（ EMs） domains with a size of a fewmicro-meter were found.In the cured blends of U-BAEs synthesized in a 40 wt.％ content of BAE, flocks with a size of a few micrometerformed by cohesion of PU domains with a size of sub-micrometer were found but spherical EM domainswith a size of a few micro-meter were not found. Furthermore, in the cured blends of U-BAEs synthesized ina 60 wt.％ content of BAE, just PU domains with a size of sub-micro-meter dispersed uniformly in EM werefound. As BAE contents in synthesizing U-BAEs are lower, the amount of PU components with high molecularweight and without an ability to cross-links because of their ends not blocked with n=1 components in BAEis increased more. On the other hand, as BAE contents in synthesizing U-BAEs are higher, the amount ofPU components with low molecular weight and with an ability to cross-links because of their ends blockedwith n=1 components in BAE is increased more. The compatibility of the latter to EMs could be better thanthat of the former and then the above change of morphologies was caused. Fracture toughness （K_1C） ofall cured U-BAEs show maximum values at an about 16 wt. ％ of modification rate of PU. As for the abovephenomena, 2 mechanisms were considered from the morphologies and the stress-strain（S-S） curves of thecured U-BAEs. The first is that the K_1C's of the cured U-BAEs could increase when the EMs are plasticized andthen the brittleness is decreased. However, the K_1C's of them could be changed to decrease when the EMs areplasticized too much and then the progress of cracks get easy. The second is that the K_1C's of them could beincrease by absorbing deformation energy when the PU domains form the above flocks and then the EMs haveplastic deformation locally. However, the K_1C's of them could change to decrease when the flocks disappearand then the local plastic deformation in EMs does not occur.