The process of precipitation of Mn from supersaturated solid solution of Al rich Al-Mn alloys was examined mainly by the X-ray diffraction methods. The changes in the electrical resistance, corrosion velocity in 20% HCl and Vickers hardness were also measured. The composition of specimen used are given in Table 1. By the experiments of Laue method it was shown that he specimen No. 1 precipitate metastble phase in early stage of precipitation. The amounts of the metastable and equilibrium phases (MnAl
6) present in annealed alloys varied with annealing time, the metastable phase being gradually transformed into equilibrium one as annealing was prolonged, and finaly all the precipitates transformed into equilibrium phase MnAl
6. So far examined, the Laue photographs of speicmen No. 2 showed the spots of metastable phase but no spot of MnAl
6 was found. From Debye-Sherrer method, it is assumed, that this metastable phase is the “G” phase denoted by Hume-Rothery and his co-workers. The orientational relation of precipitated MnAl
6 crystal with matrix crystal was assumed as follows: (315)_Al \varparallel(001)_MnAl
6; [1\bar30]_Al \varparallel[100]_MnAl
6 The metastable phases also have certain orientational relation, but it has not yet been found possible to determine. The presence of small amount of Fe or Si accelerates the velocity of precipitation markedly. In high purity Al-Mn alloys the metastable phase is very persistent, especially within the grains, and it requires very long time to occur the precipitation of MnAl
6. The temperature of initial precipitation is assumed about 400°.
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