ABSTRACT
In 1983, I supplemented [8] my earlier review [3) by including subsequent studie and those reported in two more (RQ3 and RQ4) international conferences.
G lezer et a l. [9] reviewed some aspect of mechanical properties of amorphou alloys including some test methods such as tension, loop bending, tearing, an1 microhardness. They also briefly summarized the strength , Young's modulus, hard ness , plastic flow, and fracture . The effects of quenching rate, applied magneti, field, cold-rolling, irradiation , hydrogen charging, and annealing are brie fly men tioned also. In the atomistic mechanism of inhomogeneous plastic deformation they mentioned that the radial distribution function of amorphous state compute1
om x-ray data cannot be described in terms of a dislocation model even though .e dislocation density may be as high as 1014-1015 /cm2• While they did not cite .e source for this statement it was in direct contradiction to the fi ndings of Ni->miya and Koizumi [10,11] who introduced 1014-1015/cm2 dislocations into a fcc ttice and relaxed with a Morse potential. The calculated radial distribution agreed ith x-ray data and the bond angle distribution agreed with that of a dense randomlcking model of the amorphous structure . Rao and Radhakrishnan [12) made a survey of mechanical properties of metall ic
asses. They tabulated the hardness, ultimate strength, and Young's modulus of >out 40 compositions. They also listed the fracture toughness of 32 compositions. 1tigue of Pd80Si20 was reviewed in some detail. An elastic-crack-opening displaceen! (COD) approach was found applicable to the crack extension per cycle for is material and for Ni39Fe38P 14 B6AI3. Exponents for power law creep were listed ·r 14 compositions. For Fe40Ni40P 14B6 , they found that the steady state creep rate inversely proportional to the rupture time raised to a 0.8 power, ba ed o n the
1ta collected by G ibeling and Nix [13]. They also briefly reviewed stress relaxation, homogeneous flow, and computer simulation of micromechanisms. A bout the j stence of dislocations, they said that well-defined line defects are unlikely in etallic glasses because of the lack of long range o rder. However, the type of slocations envisioned is of Volterra of Somigliana [14] type and not the Burgers slocations and hence long-range order is not needed. Egami and Vitek [15] reviewed their calculations on the atomic level stresses.
