Anisotropy thermal

Fig. 4. Constraints exerted by the anisotropy field upon the orientation of the magnetization vector. (I) High anisotropy magnetization is almost locked onto the easy axis. (II) Low anisotropy thermal energy is sufficient to move the magnetization vector aside from the easy axis.

Reference (261a) reports uniaxial ([100] of pseudocell) antiferromagnetisra 81.5°K < T < 88.3°K, parasitic ferromagnetism due to canted spins T < 81.5°K as a result of different single-ion anisotropies, thermal hysteresis in the canted-spin uniaxial-spin transition, and an He 9000 oe for field-induced spin canting in the intermediate temperature range. 

Halpin-Tsai model [18] allows describing the thermal conductivity of composites containing fillers which have a fiber or disc shape. This model is used to take in consideration the composite anisotropy. Thermal conductivity could be given by the following equation (Eq 7) ... 

The flow-induced stress is generally considered smaller than the thermal-induced stress. However, it is not possible to neglect the former due to the frozen-in orientation of polymer molecules affects the mechanical anisotropy, thermal and optical properties, and the long-term dimensional stability. 

Below a critical size the particle becomes superparamagnetic in other words the thermal activation energy kTexceeds the particle anisotropy energy barrier. A typical length of such a particle is smaller than 10 nm and is of course strongly dependent on the material and its shape. The reversal of the magnetization in this type of particle is the result of thermal motion. 

Mechanical Properties and Structural Performance. As a result of the manufacturing process, some cellular plastics have an elongated cell shape and thus exhibit anisotropy in mechanical, thermal, and expansion properties (35,36). Efforts are underway to develop manufacturing techniques that reduce such anisotropy and its effects. In general, higher strengths occur for the paraHel-to-rise direction than in the perpendicular-to-rise orientation. Properties of these materials show variabiUty due to specimen form and position in the bulk material and to uncertainty in the axes with respect to direction of foam rise. Expanded and molded bead products exhibit Httie anisotropy. 

A summary of physical and chemical constants for beryUium is compUed ia Table 1 (3—7). One of the more important characteristics of beryUium is its pronounced anisotropy resulting from the close-packed hexagonal crystal stmcture. This factor must be considered for any property that is known or suspected to be stmcture sensitive. As an example, the thermal expansion coefficient at 273 K of siagle-crystal beryUium was measured (8) as 10.6 x 10 paraUel to the i -axis and 7.7 x 10 paraUel to the i -axis. The actual expansion of polycrystalline metal then becomes a function of the degree of preferred orientation present and the direction of measurement ia wrought beryUium. 

High-resolution dilatometric measurements have revealed the appearance of anisotropy in the cubic-phase thermal strain in the precursive temperature region for the soft-mode martensitic transformations in VaSi/ Ni-Al, In-Tl/ and SrTiOa In the case of Ni-Al and SiTiOa, the onset temperatures for the strain anisotropy are close to those at which the appearance of central peak behaviour occurs. 

It is the purpose of this paper to review briefly the thermal strain anisotropy data and to consider the implications for the central peak scattering. 

The precursive anisotropy in the thermal expansion for an In-26.5at%Tl alloy is shown in Figure 1 taken from reference 7, where for curve I the measurement direction becomes a c axis in the transformed crystal and for curve II it becomes an a axis. 

In order to reproduce the temperature variation of the lattice constants, the anisotropy of the lattice expansion has to be taken into account. For this purpose, the tensor of thermal expansion ot is introduced instead of the scalar a , and the tensor of deformation due to the HS <- LS transition is employed instead of the dilation (Fh — Fl)/Fl. Each lattice vector x T) can now be... 

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