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Williams thickness of which does not increase rapidly compared to length. In ad­ dition, a study by Rhodes and Williams (1974) has shown that the laths in Fig. 25 actually consist of a large number of smaller particles, which even more strongly suggests that interface strengthening is important in this situation. The metastable β alloys, as in the case of the a + β alloys, can exhibit very high strengths, but typically become toughness limited before such strengths are attained. These alloys are also relatively susceptible to stress corrosion cracking.

Decker and Freeman (1960) have shown that these additions play a dramatic role in controlling constituent morphology near grain boundaries during creep. During the initial stages of creep, they find that the precipitation of 2 6 particles at grain boundaries causes the surrounding material to become depleted in chromium, re­ sulting in the grain boundary becoming coated by a continuous y' layer (Ni Al, Ti). At longer times, however, the γ ' layer dissolves on grain boundaries perpendicular to the stress axis and cracking then occurs at these boundaries.

Analysis of y' phases extracted from various superalloys (Kriege and Sullivan, 1968; Kriege and Baris, 1969) along with interpretations based 3 II High-Strength Nonferrous Alloys Ν I 5 I Μ S I I CO i n ο ο d 1 1 in Ο Ο ο in ο ο d d 00 i n co CO rH CO ο c o i n r-i d d in rH U rH I rH Ο in ο rH rH CO Ο Ο ο d d ο i n CO in i n i n i n Ο rH ο in ο c o CN CN CN CN CO CO rH I I I O Ο d q ^* rH oq i n d I I I I I 2 pj I I I I I I Β c ο U ο I 2 ο U "ί^Ί οο ο I I ΓΗ ι | Ο CO ο ιη Ο τ* ι I ο ο vD CO ιηΙ ο ο c o ΓΗ* d ο ο ιη ο pQpQpQpQCQpQpQpQpQpQ q O L n q i n i n o q q M I I I υ I I I I I Ο ο Ο ^ << ο οο D ιη co CN I° rH «β rH rH τ—I · ο Ο Ο σ\ Β ώ £ £ ^ 2 £ «53 ι7 ^ ΓΗ Η > q ο "tf rH 56 Stephen Μ.

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