The annealing texture of highly rolled Aluminium Plate (99.98% purity) consists of the (100) [001] texture and the (123) [112] type texture retained of rolling texture.
After recrystallization process became complete, the charpening of annealing texture was observed with the passage of annealing time.
It is assumed that the cubic orientation may bd corresponds to an orientation which is gained by 43° rotation around [111] pole of the (123) [112] type textare and that is approximately coincident to the pole of a cubic orientation.
The retained (123) [112] type texture may be result from a mechanism of pol ygonization during annealing, or reorientation by 48° rotation around two common [111]pole of the (123) [112] type component.
We discussed that "oriented nucleation phenomena" may be more important factor to the mechanism of formation of primary recrystallization texture, and moreover "oriented growth" will be affect in a sense of additional factor.

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In order to study the mechanism of age-hardening in Al-Cu-Sn alloy, a study was made on alloys containing 2 to 5 percent copper and 0 to 5 persent tin quenched from 500° in water after being heated at that temperature for I/2 hour, and tempering for various hours at 100°, 150°and 175°respectively;
The variation in hardness of the alloys due to the above heat treatment has been studied by means of hardness tester. When a small amount of tin is added to the alloys, the artificial age-hardening property was vigorously accelerated compared with Al-Cu alloy for instance, the degree of hardening of some alloys reached to two hundred percent.

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In the previous report, the authors had reported the results measured electro de-p°etential of pure Al as one of its electro-chemical properties. The results obtained in an investigation of flowing current of pure Al are given in this paper. Samples of 99.9-pureity Al were used and electrolyte used was 3%NaCl+0.1%H₂O₂, and 0.1%HCl, and measuring time was 0.5, 1, 1.5 and 2 minutes. Samples were heated at 100, 150, 200, 250, 300, 350, 400, 450, 500, and 550°C with following air cooling, and after that treatment, samples were prepared by buff-polish or usual polish with flannel.
conclusion:
It is obtained that there is a trend which the flowing current of the sample which dipped in the electrolyte used was 3%NaCl+0.1%H₂O₂, differs from that of sample which dipped in the electrolyte used was 0.1%HCl. Sample which used was the electrolyte 3%NaCl+0.1%H₂O₂ indicates immediately after dipping the decreasing flowing current, but the case of 0.1%HCl used, has a tendency to increase flowing current with increasing of time.

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The experiments were carried out from befor deformation to after break down by tensile pull in order to obtain some considerations about the plastic deformation of circular-rod specimens which consist of 99.5 pct aluminum. Two specimens were prepared by the strain-anneal method, one of which has one boundary and the other three of them. The orientations of the crystals and its boundaries were determined by the rotation photographs and the method of stereo graphic projection.
The results obtained are as follow: (1) The variation of the specimen axises at the boundaries or its neighbourhood cannot be determined by the relations between the its crystallographic planes and directions and the resolved shearing stresses, as in the case of single crystals. (2) We suppose that the producing process of distorted spots and spots elongated to circular directions are in relation with the Laue patterns produced with deformation.

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61S材のCu量を0.05より0.7%迄変えた5号試験片を以て迅速腐蝕液に200日間全浸漬し,夫等の機械的性質の変化からCu量の耐蝕性に及ぼす影響に就て検討した結果を次に要約する。
1) 10日間にして各試料とも腐蝕し,外観の観察から侵蝕の状況は孔蝕性である。
2) 浸漬後約50日間は急激に侵蝕し,それ以後の作用は緩慢である。
3) 侵蝕に伴う伸びの変化が抗張力の変化より急激であり,主として孔蝕性の侵蝕が行われる。
4) 従つて耐蝕性の比較を抗張力の減少率を以て判定したが,何れの質別もCu量の増加に伴つて耐蝕性を低下する。
5) 耐蝕性はT₄,H,O及びT₆の順に低下し,O材とT₆材はCu量が0.56%を越すと急激に劣化する。
6) O材とT₆材の耐蝕性の不良は固溶体の他にMg₂Siの析出しているためである。
7) Cu量の上限は0.5%迄の範囲で決めることが妥当と判断した。
8) 以上の事は第1報の結果と共に61SのCu量が0.15-0.40%の範囲に決められている事の妥当なことを確認したことになる。

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Aluminum containing 0.5, 0.9, 1.4, 2.0, 4.0, 6.0%, Si, 0.2, 0.3, 0.5, 0.8, 1.0, 1.6, 2.0, 2.9%Fe, and 1.0, 2.0, 3.0, 4.4, 5.5%Cu respectively were investigated. The tendency of Al-Si system alloys to form stresses under the influnce of composition and cooling velocity was sharply reduced by increasing the addition of Si up to 2%. The influnce of Fe was weaker compared with that of Si, but increased the tendency to form stresses up to 0.6%Fe. Inregard to the influnce of Cu, the addition of Cu showed a greater tendency to form stresses than did the alloys containing Si and Fe individually.

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The experiments were carried out in order to obtain the minimum inner radii for 90° or 180° cold bends applied parallel or perpendicular to the rolled direction of the following sheets.
We also experimented on mechanical properties of them, And the results are shown in Fig. 1, 2, 3, 4, 5, 6, 7 and 8.
There is no rule about the span of the supporting points in the bend test standard, but it is illustrated that the influence of them on the bending radius are essential.
Then we studied about it. The results show that when the span of supports is made too wide the minimum inner radius of bend test becomes uncorrect as shown in Fig. 11.
It is very difficult to keep the correct bending radius, for the bending load tends to concentrate to a line. Therefore, we examined that if it was bent with accurate radius by compressing a test piece from outside with such ductile material as lead late how we could decrease the inner radius of bend test, and we got the results showing smaller bending radius as Fig. 13 in the case of lead plates. The results which we measured the deforming conditions of the test pieces showed more uniform deformatiom compared to the case without lead plate.

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Here is no doubt about that the swell of annealed aluminum sheets is caused by gas contained in the molten metal, the material of sheets. However, we cannot positively declare that more fact of having made no mistake in the manufacturing of slabs can eliminate the swell. Of course, the swell is considered to be brought about by mistaken process of annealing or by hot or cold rolling process preceeding to the annealing. The swell of aluminum sheets is often found also in the case of hard sheet a study of the causes of swell has been made with the following results.
At the meeting of last autumn, we reported on the casting of genuine ingots by eliminating the gas peculiarts aluminum by means of so-called "Candle melting process". Ever in such an ingot, there is absorbed gas in excess of saturation point, because the ingot is casted from the molten metal which absorbed gas while being exposed to high temperature after having been melted by above mentioned process and is suddenly quenched. If this ingot is superheated by solutioni heat-treatment to be made before hot rolling process resulting in it partial buring and derolution, then the gas contained in the ingot excess of satulation point is released to make something like pin-holes consequently, this is considered without donbt to be one of the cause as in the case of pin-holes appearing at the time of casting. The statistical date at the plant show that the super-heating in solution heat-treatment is one of the causes of swell.
Special consideration is nesessary about the state of gas in solid things. The absorbed gas is considered to be in the state of free gas or of solid gas swell, which occurs when there is no mistaken processing in hot rolling, is considered cheefully the result of free gas contained in ingots. And swell which occurs in the ingots, containing no free gas is considered to result from the liberation of solidfy gas in excess of satulation point due to mistaken processing in hot rolling.

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Orang peel was found by deep drawing recrystallized, at comparatively lower temperature, 2S sheet. This is thought of duing to a peculiar surface with coarse grains by the annealing and particularly, that a incubating coarsen property of Fe in 2S will be important factor.

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The studies on the effects of tack welds of aluminum plate were carried out. The results obtained are as follows.
Using closely spaced tack welds.
(1) Buckling and distortion can be minimized and welding work is easy.
(2) The cracking occurs in thick plates, but it can be reduced by choosing proper welding condition and material composition.

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Generally, 3S alloy can not be satisfactorily produced as fine grain sheet unless rapidly annealed in a salt bath, that is, the annealing temperature should be raised as rapidly as possible through the germination range.
Therefore, 3S sheet is not so much used for deep drawing in Japan as in other countries. The work has been carried out with a view to ascertaining the influence of preheating of ingot on the grain size and the mechanical properties of 3S sheet. Then, it was ascertained that preheating the ingot at over 550°C for a long time, the finer grain sheet could easily be produced same as 2S. And it was found that the sheet rolled from preheated ingot can be fully annealed at 350°C even in an electric air furnace without any grain growth. On the other hand, one rolled from un-preheated ingot can not be annealed at less than 450°C in an air bath and futhermore its grain size becomes too large to use for deep drawing.
It was also ascertained that the preheating of ingot is effective to prevent the germination of grain even if heated in a salt bath.
Futhermore, it was recognized that the modified 3S alloy containing 1.0%Mn and 0.2%Mg does not give rise to the germination whether preheated or not.
Therefore, it is commendable from practical viewpoint that 3S ingot should be by all means preheated at 600°C-550°C in order to get the finer grain sheet suitable for deep drawing.

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The procced paper describes the tolerance for die-casting and gravity, castings.
But we know that these tolernces are differance of shrink ratio of Castings.
So that we messured the net shrinkage. Namely that is shrinkage coefficent of castings.
This shrinkage coefficert are messured that 5.0×10^-3 to die-castings and 5.0×10^-3 to gravity castings at Alumminum Alloys.
But at die-castings shrinkage coefficent varieite between 4.0×10^-3 to 6.0×10^-3 and at graivty castings that varieite between 5.0×10^-3 to 7.0×10^-3.
And we know that shrinkage coefficent are not regard to thickness of castings but that are regard to cooling radio C_A.
C_A=surface are of castings/weight of castings
thet Pelation between shrinkage coeffcient and cooling ratio C_A is a liniar one.
If we put thrinkage coefficent ΔL.
ΔL=α(t_s-20)-α_f(t_f-20)
α_f. t_j: expansion coefficent and temperature of dies.
t_s: temperature of the eastings begin to shrink.
α: expansion coefficent of the eastings.
We have known temperatule of dies and shrinkage coeffcient of castings by this messurement, so that by above formura we can determine the casting conditions, and we can draw casting diagrams.

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There is no need to seuy that the use of aluminum alloy as a material of super-structure of sea-going vessel much contributes to the increase in loading capacity and improvement of transverse stability of the vessel. In this case, however, it is required that any appropriate measure should be taken to prevent the galvanic corrosion on the surface of the aluminum where steel material contacts with.
Thri is to report the results of the several tests which have been made by ourselves to know what kind of treatment shoued be made on the surface of steel material to avoid the occurauce of the corrosion on aluminum most effectivly.
The lists made by contacting galvanized steel sheet, steel sheet plated with zinc, one plated with cadmium, ziuc metalicon, aluminum metalicon and non-treated steel sheet each with anodized 52S aluminum alloy and non-treated one.
Dipping each of the above mentioned test-piece, as contacted with aluminum alloy, into the solution of 1mol MaCl+3%H₂O₂, we measured the decrease in volume and lowering of stress by corrosion of the aluminum alloy. The results showed that the zinc plated steel is the most favorable material for this purpose, and next comes zinc metalicon, Al metalicon, galvanized steel, and cadmium plated steel in orders. We found that the non-treated steel was not suitable for the purpose. And we confirmed, in this test, that the anodized aluminum loss much stronger corrosion resistanse than non-treated one.

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It is usual with anodized wares that the shade of net-like pattern appear on them, to the detrement of their commercial value. This shade books like bondary line of macrostructure at the first glance. However the investigation seems to prove that it has nothing to do with the bondary line of macrostructure.
We have found out that the appearance of the shade cannot be prevented by polishing the surface of aluminum sheets, rinsing with alkaline water not by changing the annealing method.
Further, it has been found out that ever high quality metal of around 99.93 percent pure cannot escape the appearance of shades the change in the anodizing method is of no avail in combatting the shades. Because they appear in both cases of employing the sulphuric acid method and the on alic acid method. When the sulphuric acid method is emproyed, the shades are not so evident, but this is simply due to the film of metal being opaque. The shades cannot be elased neither by the treatment of the gas eliminated from the molten metal nor of the solvent. But the use of N₂ Gas in the treatment of the eliminated gas makes the shade less prominent than to use of Cl gas.
Next, when the sheet rolled from virgin ingots is anodized, it show also the shades. From this phenmenon, it is concei vable that the net-like pattern results from the cause inherent in aluminum ingots. As the composition of aluminum sheets is thus considered to be the main cause of the shades, we have conducted the experiment, changing iron and silicon confents within the limit of 99 persent of aluminum. The result of this experiment shows that the shades change pretty much depending upon the contents of iron and silicon.
The shades disappear when the purity of metal is below 93 percent, white, in the case of the metal being 99 percent or upwards, the patterns look like scattered bamboo leaves when the iron content is large, and perlight sesigne when siliconcontents is large. Further, in the metal of comparatively higher purity, net-like patterns are ovident and in the metal of lower parity, white, round specks appear instead of net-like patterns.
These change in the patterns cannot be explained out simply by balanced starte diagram.
When the metal of this grade is casted, the macrostructure is very peculiar. Specifically, when it is anodized, various flower patterns come to apper. Further, these flower patterns exist perpendicularly in pillar shapes and their boundary lines are dotted with iron particle. Although the substance of the patterns is net to be ascertained, we submit the reports on the results of investigation conducted into the mutual relation relative to the various patterns

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In the Part 1 (1) of this report, we discussed about the effects of voltage and concentration, and then, introduced the simple experimental formulae which showed the relations between the properties of anodic oxid film and these factors.
In succession to the preceding experiments, we examined the effects of time and concentration on oxid film in sulphuric acid process. In this experiments, the type of current is D. C. only and the other factors are held in constant, i. e., voltage is 15V and temperature of bath is 16-17°C. The inspection process for the properties of oxid film is the method soecified in. JIS P10431, 1951, which was used in preceding experiments.
The results of experiments are as follows.
(1) The relation between thickness of film and time and concentration is shown by following experimental formula.
(See Fig. 1, Fig. 2, Fig 3, Fig. 4, Table 1.)
1/T=1.52C^-1.326+0.0053+5.6-0.13C/t
[10<C<30 20<t<60]
T=Thickness (μ)
C=Concentration (%)
t=Time (min)
(2) The relation between thickness of film and electric power is shown by following farmula. (See Fig. 5, Fig. 6, Table 2.)
T=b₄+a₁W
T=Thickness (μ)
W=electric power (A/dm²×V)
Coefficients, a₄ and b₄, vary with time as hown in Table 2.
(3) The relation between corrosion resistance and time and concentration is shown by fallowing experimental formula. (See Fig. 7, Fig. 8, Fig. 9, Table 3.)
1/S=7.56C-0.714-0.36/t
[10<C<30 20<t<60]
S=Corrosion Resistance (sec.)
C=Concentration (%)
t=Time (min)
(4) The relation between thickness of film and corrosion resistance is shown by the same experimental formula as that of the preceding report. (See Fig 10)
S=180T_0.253-239
T=Thickness (μ)
S=Corrosion Resistance (sec.)
(5) The relation between abrasion resistance and time is not able to be shown by the simple experimental formula although, the degreasing inclination is not so remarkable as film thickness or corrosion resistance, the increasing rate of abrasion resistance decreases gradually with time. (See Fig. 11)
(6) Specific abrasion resistance, abrasion resistance for each 1μ of film thickness, is improved greatly as time becomes long. (See Fig. 12)

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For aluminum and its alloys are cmployed for constructional materials contact with steam, they must have superior corrosion resistance in it, but the investigations on the action of steam vapor on aluminum and its alloys almost have not been canied out in the past. This corrosion test were made on usual trade aluminum alloys to determine the resistance to corrosion in steam atmosphere by measuring the weight loss, and the decreasing of tensile strength and elongation during test.
(1) As compared with Fe, aluminum and its alloys has become established high resistance to corrosion in steam.
(2) High-purity aluminum, under steaming stmosphere, surpasses the other aluminum and its alloys in resistance to corrosion. This resistance increases with increase in purity. However, the effects of a few impurity, Fe and Cu, to the resistance to corrosion are to be considered.
(3) It is unexpected that the resistance of 52S is following to high-purity aluminum.

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We built a boat with out-board engine for trial from light alloy 56S. The following data is ofintersest: L. O. A. 5.000m; beam 1.486m; depth 0.678m; weight of hull only, 100kg. This weightis about a half compared with the same type wooden one.
In future sails will be fitted. The form of the boat is suitable for motor boat trimming by the stern and is suitable for yacht when the boat is even keel except engine.
The maximum speed was 27 knots with 22 HP out-board engine.
This boat has been and will be used to study work, strength, vibration, corrosion etc.

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We can think of a number of factors that affect the dielectric property of an electolytic condenser, but by far the most important one is the purity of aluminum used as its anode. In Japan today aluminum of 99.9% up purity is usually used for the anode of an electrolytic condenser, but as to which one of its main impurities such as Fe, Si, Cu, etc. is the biggest factor of affecting the dielectric property, the question has been left urclarified. In this connection, the authors conducted, back in 1950, an experimental investigation with a view to ascertaining which one of those fine impurities had the most unfavorable influence on the formation of dielectric film, when it was found that Cu, Si, Mg, Mn, etc. dissolved in small qnantity in solid solution had little or nothing to do with the question, but that Fe or Ti that exists in precipitated form, no matter how little, exereises an unfavorable influence. On the other hand, it was also ascertained then that if 0.1% or less Zn and Mg or 0.05% or less Mn was added to the aluminum of 99.99% purty, its dielectric property was rather improved.
In their latest examination the authors made further scrutiny into the similar influence of those impurities contained in aluminum ranging in purity from 99.9 to 99.99%. Consequently, it was found that even the 99.99% grade aluminum sometimes proves inferior to 99.9% one in point of its dielectric property and that the dielectric property solely depends on its iron content. The conclusion thus obtained is that in specifying the purity of aluminum to be used for an electrolytic condenser, it is more important to specify the limit of allowing the iron to be contained in it than its synthetic purity.
Besides, since the annealing operation is usually made in an electric air furnace, which causes an oxide film to appear on the surface of aluminum foil, it is natural that the higher the annealing temperature goes up, the poorer its dielectric property should become. This time we have made an anuealing test by means of vacuum heating so as to prevent the oxide film coming out on the surface of the testing material, for which we have used 99.99% aluminum. Nevertheless, we have found that the higher the annealing temperature rises, the poorer, though slightly, its dielectric property becomes, and that the size of recrystallized grains seems to have something to do with it. t follows therefore that the annealing temperature for aluminum of high purity (99.9 to 99.99%) should be held as low as it is required for the recrystallization temperature (300°C), and in this connection, it is commendable from practical viewpoint that the annealing should be conducted at around 350°C so that the aluminum foil may be prevented from getting smeared with oil on the surface.

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Factors which are seemed to affect on the strength of thin sphere under little concentrated load are radius of sphere, height or length of chord, thickness and mechanical properties of material (elastic and plastic properties), etc. In these factors, that resulted from the shape of the test-piece were already reported in the part 1 of this paper. Then, in this report, we will discuss about the effects of thickness and material.
The typical thickness of test-pieces are 0.6, 0.8, 1.0 and 1.2mm. On each test-pieces, relation between deflection (δ) and load (P) is examined by the same method as used in the Part 1 of this paper. The results are as follows.
(1) The relation between deflection (δ) and load (P) is shown by the parabolic curve. When the sheet is thinner than 0.5. 0.6mm, the relation is shown by the single parabolic curve. When the sheet is thicker than 0.5 0.6mm, however, it is shown by one parabolic curve up to the certain` value of load which varies with the thickness, and then, when load passes over this value it is shown by the other parabolic curve which differs from the former.
(2) In each curve, the angle of inclination (tanα) is proportional to thickness (t), and the value which is compensated identically for the shape of test piece and the material-property (a/rh/tanα) is inversely proportional to the second power of thickness (t²). After all, the relation between deflection and thickness is generally shown by the following experimental formula.
δ=AγhP^b/Ept³
In the range in which load is light and the sheet is thin, b is approximately 1. Then diflection (δ) is shown as follows.
δ=AγhP/Ept³
(3) When the sheet is thicker than 0.6mm, a jump phenomenon is revealed. We desire to study on this jump phenomenon still more.
(4) The above formula may be applied even for aluminum alloys.

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