Many anomalous physical properties are experimentally observed during the superlattice formation in Fe-Al alloys. Such anomalies have not yet been completely explained in spite of extensive iesearches.
According to the author's investigation about the ferromagnetic superlattice, such anomalies must be due to the interrelations between the superlattice formation and the origination of the spontaneous magnetization. The origin of the singular properties of Fe-Al system can also be reduced to this fundamental idea.
With this general point of view, the phase diagram concerning superlattice formation in these binary alloys are reviewed.

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The _??__??__??__??_e_??_ure and accuracy in the determination of crystal orientation of hexagonal metal single crystals by the simple, rapid, and accurate light-figure method are fully explained for the case of zi_??_c single crystals of a cylindrical-rod form as an example.

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The two assumptions under which a thermodynamical theory of plastic deformation has been develoted by us in the preceding report, were discussed from a view point of the dislocation model.
i) Slip in a crystal occurs through a movement of dislocation in the slip plane, in which the potential field can be represented approximately by a sinus function with a period of one at mic distance in the simple cubic lattice only, but additionally a field with a period of a quarter of one atomic distance must be added to it in the face centred lattice.
Provided that the dislocation passes through positions of the minimum potential in such a field whea it moves, lattice in the neighbourhood of dislocation centre must transform to the different type of lattice at every. quarter of one atomic distance four times, while the dislocation moves one atmic distance, in the following way; face centred lattice→body centred→face centred→body centred→face centred. In the narrow region arround the dislocation centre such a transformed lattice corresponds to a heavily deformed state which is far over the elastic limit.
ii) From the above consideration a mechanical energy E=f.l dissipated for gliding one atomic distance l is equal to the free energy 4 ΔG for the fourhold transformations. Consequently the following, equation is satisfactory
ΔG=^l/₄•f=0.306f.
which is the firit assumption in the previous report.
iii) The second assumption in the previous report, crystals having no actual transformation raise the lattice transformation under so high a stress that its magnitude is greater than the critical shear stress, can be immediately satisfied in the restricted region arround the dislocation centre from the above model.
iv) The line dislocation in our modified model is not always perpendicular to its moving direction, but it is at the angle of 60° in the slip plane of face centred lattiec.
v) W hen such dislocation moves, there exists the posibility that vacant holes at the lattice points are left behind it. Existence of these holes gives a resistance against movement of a following dislocation, and results in hardening the crystal.

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The curves of (degree of cold work)-(anomalous temperature) which were drawn from the experimental data of S. Satô [Heat evolution. Sci. Rep. 27 (1939), 278] and those of T. Suzuki [True Specific heat. MS.], were extended to the point where the above degree is zero, and the temperatures were determined, as 230° and 277°, expecting that they are anomalous ones for annealed Cu. Further, from the result of investigation on the diffusion between Cu and An, carried out by S. Tanaka and C. Matano [Mem. Kyoto Univ., 13 (1930), 343], it was confirmed that 230° is really an anomalous temperature for the annealed specimen. Finally, from the experimental result obtained by A. Avaramescu [True Specific heat. Zeits. tech. Phys. 20 (1939) 213]., it was found that, approximately, 550° is also an anomalous temperature of Cu. Thu-, it was concluded that the anomalous temperatures are 230°, 277°, 550° and 1083° (m, p.), in Cu, and that there exists the following regularity in them; namely,
(0°K_??_277°):(277°_??_1080°)=1:1.46
=2:3.
(0°K_??_230°):(230°_??_550°)=1.56:1
=3:2.

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The critical point of hypereutectoid steel (its composition is 1.18% C, 0.23% Si, 0.28% Mn, 0.017% P, 0.023% S) was measured by the Sato's self-recording dilatometer when it was quenched in oil, after being coiled slowly (lamellar pearlite specimen), annealed (globular pearlite specimen), quenched in oil (martensite specimen) or cooled in air (sorbit specimen) from 950°. The Ar''-points do not appear on the latter two while they appear on the former two when they are quenched in oil from 780°. The more the quenched temperature rises, the more the Ar''-point decreases on the martensite specimen. This chance is due to the numbar of cementite nucleus in austenite by the quenching temperature.

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The vapour pressure of Cd, Mg, Se, Te and Zn, which ranges from a few mm. Hg up to 1 atomospheric pressure, was measured by the boiling point method devised by the present author. The results obtained are shown in Fig. 3. From these data the empirical formulae of the relation between vapour pressure and temperature were determined as follows:
Cd ………… log p=-⁵⁶⁶⁰/_T+8.32
Mg ………… log p=-⁹²³⁰/_T+9.87
Se………… log p=-⁵⁵³¹/_T+8.58
Te………… log p=-⁵⁸³³/_T+7.54
Zn………… log p=-⁶²⁷¹/_T+8.19
By utilizing the above relations, the latent heat of vaporization and changes of internal energy and entropy glue to vaporization of these metals were calculated and discussed thermo dynamically.

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For a fundamental datum for refining crude Se by distillation, the vapour pressure of Se alloys containing another element was determined with the following results:
(a) The vapour pressure of Se-Sn and Se-Bi alloys decreases with the increase of Sn or Bi content, but each system has a monovariant range in its isobaric and isothermal diagram.
(b) The isobar and isotherm of Se-Te alloy show the minimum and maximum respectively, therefore separation of Te by distillation is difficult. (c) Se-Hg alloy is difficult to be separated due to high vapour pressure of the intermetallic compound (Hg. Se) which exists in this system. (d) The vapour pressure of Se-S alloy increases monotonously with increasing of S content. (e) Se-Cd alloy contains the intermetallic compound (Se•Cd) having low vapour pressure, so that it is possible to remove Cd from Se by distillation. Se-Zn alloy is similar to Se-Cd alloy. (f) Spectrographic examination of distillated Se was also carried out.

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Behaviours in tempering of high speed. tels quenched into hot bath. were investigated as to hardness. specific gravity, microstructure, dilatometric and specific resistance measurements.
Firstly, the change of hardness and specific gravity for hot bath quenched specimens followed by tempering were dealt with, Secondly, the tertiary Ar'' transformation revealed in 650°C tempering was described. Lastly a decomposition at 650°C tempering for but bath quenched specimens and their Ar'' traneformation were discussed.

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As was stated in the first report, a number of metals superior to 18/8 S. S. in mechanical and physical properties were found among them Nos, 4, 5, 15 and 22, were selected as fundmental compound metals-for ttlhe 2 nd research, taking also the results of corrosion tests into consideration.
The aim of the present research is to find compound metals not inferior to 18/8 S. S. in chemical propety, from the metallurgic stand point especially in corrosion resistance, by the addition of a proper amount of the fourth elements to the fundamental compound metals. As the fourth elements eight kinds were taken into consideration and among them 5 kinds are easily obtainable; there were first selected for investigation.
Of the five elements-Ti, Mo, V, Si, Al, fourkinds of metal were produced by affixing different quantities to each one of them, of which two or three kinds of metal were proved to be superior to 18/8 S. S. not only in mechanical and physical properties, but also in corrosion resistance.

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It has been shown that multiple tempering is superior to single tempering in hardness and tool life, and that these properties are signitieant in hich cobalt high speed steels and not in low cobalt steels.
This paper also treats with the multiple tempering and single tempering on low tungsten high speed steels. It was clarified that the above facts are evident of them, in which the retained austenite of quenched steels is comparatively stable and of large quantity. The effect of aluminum, vanadium and titanium on the properties of the low tungsten high speed steels were also studied.

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