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Metal-metal type amorphous wires with a good ductility were produced in the M-Zr (M = Cu, Cu-Nb and Cu-Ta) alloy systems by a technique using melt spinning into rotating water. The formation of the amorphous wires is limited to a narrow range of 35 to 40 at % zirconium where the critical sample thickness for the formation of an amorphous phase is above about 100#m and the amount of copper replaced by niobium or tantalum is less than about 7 and 5 at %, respectively. The wires have a circular crosssection and a rather smooth peripheral surface. Their diameters are in the range of 0.07 to 0.15 mm. The Vickers hardness, Hv, and tensile strength, of, are of the order of 425 to 440 DPN and 1670 to 1810 MPa. The elongation to fracture, el, is about 2.4 to 2.7%. Cold drawing to about 30% reduction in area results in increases in of and 6f by about 10% and 35%, respectively. Furthermore, the addition of 5at % niobium results in decreases in of and Hv by about 14% and 4%, respectively, without detriment to the good bending ductility. Owing to the faster quench rates of the wire samples, caused by the inherent differences in the solidification process of the ejected melt as well as in the manner of cooling after solidification, the amorphous wires have been found to exhibit a considerably higher relaxation enthalpy value, AH, and a lower temperature for the onset of structural relaxation as compared with the amorphous ribbon having the same thickness as the diameter of the wire, demonstrating that the amorphous wires possess a higher degree of structural disorder.

Thin films of FeC were deposited onto a polymer substrate by reactive DC magnetron sputtering, using an argon and hydrocarbon gas mixture. The polymer web is wound by a roll coater, and an individual thin film with a constant thickness is piled up by increasing a number of passes up to a desired thickness. Uniaxial films with Hk= 4000Nm and low dispersion were obtained. The coercive force was a function of thickness; it was Hc= 8A/m for films 0.8pm thick. The easy axis of the uniaxial anisotropy was along the direction transverse to the rolling direction of the polymer web. The origin of the uniaxial amsotropy is the anisotropic thermal shrinkage of the polymer web is discussed by a model.