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De Gennes (1975) proposed the possibility of using LCEs as arti cial muscles, by taking advantage of their substantial uniaxial contraction in the direction of the director axis. The alignment of mesogens can be coupled with polymer network structures in LCEs; thus, if one heats nematic LCE lms toward the nematic isotropic phase transition temperature, the nematic order will decrease, and when the phase transition temperature is exceeded, one observes a disordered state of mesogens. Through this phase transition, the LCE lms show a general contraction along the alignment direction of the mesogens, and if the temperature is lowered back below the phase transition temperature, the LCE lms revert to their original size by expanding. This anisotropic deformation of the LCE lms can be very large, and along with good mechanical properties, thus providing the LCE materials with promising properties as arti cial muscles.

This irreversible polarization curve also has the shape of a wave (see Fig. 5.13, curve 3) with the limiting current density yd. The half-wave

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Anisotropic deformation of monodomain LCEs by a thermal phase transition from an LC to an isotropic state was rst reported by Kupfer and Finkelmann (1994) A nematic LCE prepared by the two-step process contracted by about 26% owing to the change in order parameter as a result of the change in molecular alignment of mesogens This anisotropic deformation behavior of LCEs has been a subject of extensive experimental and theoretical studies (Stenull and Lubensky, 2005; Mao et al, 2001; Warner et al, 1988) Warner and Terentjev established a relation between the nematic order parameter S and the effective backbone anisotropy of polymer chains forming the rubbery network The relation is expressed by a dimensionless ratio of the principal step lengths parallel and perpendicular to the nematic director (R8/R>) (Warner and Terentjev, 2003, 1996) In the nematic phase, this ratio is larger than unity (R8/R>E1.

(5.4.27)

17

3) (Warner and Terentjev, 1996), but after a nematic isotropic phase transition, this ratio approaches unity as a result of the formation of a random coil of polymer chains, which makes the polymer material contract along the director axis of LCEs In the smectic A phase, the ratio R8/R> is in general smaller than unity because the polymer chains are likely to exist between the smectic layers (Cotton and Hardouin, 1997) There have been a number of efforts to develop arti cial musclelike materials (Buguin et al, 2006; Mol et al, 2005; Saikrasun et al, 2005; Stenull and Lubensky, 2005; Li et al, 2004; Naciri et al, 2003; Clarke et al, 2001; Mao et al, 2001; Thomsen et al, 2001) LCE lms with a splayed or twisted molecular alignment display a well-controlled deformation as a function of temperature (Fig 3.

/-* o \

12) (Mol et al, 2005) The twisted lms show a complex macroscopic deformation owing to the formation of saddlelike geometries, whereas the deformation of the splayed structure is smooth and well controlled (Mol et al, 2005) Wermter and Finkelmann (2001) reported a new type of LC coelastomers composed of LC side chains and LC main-chain polymers (Components 10a c) as network strands Thanks to the direct coupling of the LC main-chain segments to the network anisotropy, the thermoelastic response was increased remarkably with an increase of the concentration of these segments An elongation in the direction of the director by up to a factor of 4, relative to the length of the networks in an isotropic state, was observed in the nematic state (Fig 313) (Wermter and Finkelmann, 2001).