Object of this papers is to describe principle and mechanism of the X-ray Geiger Müller counter spectrometer, which was built up in our laboratory in coroperation with Mitsuoki Nakahira of Scientific Research Institute.
As the spectrometer stage we utlized the R. Fuess one circle crystal goniometer.
We attempted some focusing of diffraction patterns by adpotion of platy specimens.
Using partialy monochromati zed Cu-K_α radiations, measurements on some ceramic raw materials: Quartz, Kaolinite and Hydrated-Halloysite, were carried on.
Also some features of this apparatus and its useful appliance to ceramics' studies are noticed.

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While studying the relationship between strength of wet gypsum and its apparent specific gravity. I tried to set forth the relationship in mathematical formulae, such as I obtained before for dry gypsum.
The formulae are as follow:
log σ_x2/σ_x02=n₂log ρ₁/ρ₀ or log σ_x2=n₂ log ρ₁+log σ_x02/ρ₀ⁿ²when σ_x2 and ρ₁: compressive strength of wet gypsum and apparent specific gravity of dry gypsum.
n₂: experimental constant of wet gypsum.
σ_x02 and ρ₀: compressive strength of wet gypsum and apparent specific gravity of dry gypsum. Dry gypsum is supposed to be in an ideal condition, i.e. the quantity of water used is just the theoretical amount required to bring about the chemical change.
In order to ascertain the correctness of the formulae, experiments were conducted. Specimens were tested 3, 4 and 24 hours after the setting. These specimens were wet. The theoretical formulae indicate a straight line. The experimental logσ_x2-logρ₁ curves were almost similar to the theoretical line. Also in the case of dry gypsum, experiments endorsed the theoretical anticipation, as I described it in another report of mine. It is clear from the curves, that “n”, the experimental constant in the case of dry gypsum, is smaller than “n₂”.
When gypsum is wet, or when there is water in excess of the amount required for crystallization, its strength is about half that of dry gypsum.
This phenomenon is explained as follows.
When gypsum is wet, excess water exists among crystallized particles of gypsum. The quantity of this water does not affect the strength.
Crystallized particles of gypsum contact each other so that cohesive and frictional force works through these contacts. However, when there is water between two particles, the cohesive and frictional force is weakened because the water separates the two particles or, in other words, the distance between them increases a little. When gypsum is wet, it is easily broken if pressure is applied on it. Cleavage occurs along the part weakened by water, as described above.
When a specimen of dry gypsum is destroyed, the cleavage runs irregularly along the most vulnerable part of the specimen, but when the specimen is wet, it is cleft along the wet part where the cohesive and frictional force between particles is weakened.

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To find out the quantitative relationship between the port construction and the state of gaseous combustion in a glass tank furnace, a series of experiments has been carried out using the model tank of 1/20 size. Air and fuel gas were substituted by dilute solutions of hydrochloric acid and caustic soda respectively. The similarity of flow between the combustion gases and the solutions in the model was secured by the coincidence of Reynolds and Froude numbers. The solution of caustic soda was coloured by phenolphthalein in order to be able to measure the length of model flame. The results obtained are as follows:
(1) Comparing the model flame with actual one it was confirmed that the results of the model experiments run parallel with those of gaseous combustion.
(2) When the excess air ratio was kept constant the length of flame remained almost unaffected by the variation of Re as long as the flow was turburent.
(3) The length of flame (i.e., the distance from the point, where gas and air just begins to mix each other, to the top of flame) was not affected by the thickness and the length of partiton wall.

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一般に磐城粘土として知られている畑子澤粘土と木戸粘土とを比較檢討した。
1) 粘土を水簸分離して三つの粒子群に分ち, 各部分の鑛物組成と燒締りの關係を檢討した。
2) 兩粘土共主鑛物は未發達のカオリナイトで比較的よく似ている。
3) 畑子澤粘土中に含まれている曹達長石がこの粘土の特殊な燒締りに效果のあるものであろうと考えられる。
4) 木戸粘土に簡單な處理をして耐火物を造り, 畑子澤粘土を用いて造つたものと比較した結果は幾分劣るが, かなり優れた粘土質耐火物を造り得た。
研究は東京工業試驗所第1部第3課全員の協力によつて行われたものである。更に化學分析に協力して戴いた當試驗所小松崎技官, 又熱的試驗の一部に御協力戴いた東京工大山内教援と吉田講師, 並びに鑛物組成の一部決定に御協力下さつた山田助教授に厚く感謝する。又原料を御送附願った品川白煉瓦株式會社湯本工場にも厚く感謝する次第である。

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Magnesia was formerly produced by calcining magnesite (MgCO₃) or brucite (Mg(OH)₂) from Manchuria and Korea. But these raw materials are now entirely diffidult to obtain from these countries and our country itself. So that, magnesia or magnesium hydroxide, which is very important for various uses, e. g., basic magnesian refractories, magnesia cement. magnesium salt chemicals, etc., must be obtained directly from sea weter, or its evaporated brine or bittern from salt making plant.
In the pretent paper, vanious processes of makiug magnesium hydroxide or magnesia from the ore of magnesite and brucite, or sea water were fully discussed, and the proeesses of magnsia making by treating ses water, brine or bittern with calcined dolomite or lime from limestone calcining, were determined to be the best process in the present state of no production of magnesite or brucite, and these processes were preliminary tested with full discussion on the treating conditions and the chemical compositions, especially the relations between various conditions of treating method and the amount of intermixed lime to the principal component of magnesia. The best quality of magnesia was obtained by mixing dilute solution (Be 15-20°) of bittern or brine with slaked solution of calcined dolomite (700-800°C), in the following two steps: (1) small amount of calcined dolomite equivalent to SO₄ radical for precipitation of CaSO₄⋅2H₂O, and then (2) calculated sufficient amount of calcined dolomite equivalent to Mg radical for precipitation of Mg(OH)₂. Magnesium hydroxide or magnesia containing small amount of lime was also obtained by using dilute solution of quick lime or fresh slaked lime, by the same way in the two steps as above described.

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〓焼蝋石質坩堝 (900°焼成) の素地組織及びその焼締め過程をX線試驗, 鏡檢及び化學分析によつ精査し, 更に同樣の方法を用いて1.0Na₂O・1.0CaO・5.0SiO₂, 1.0Na₂O・1.0B₂O₃・5.0SiO₂及び1.0Na₂O 0.5CaO・0.5B₂O₃・5.0SiO₂の各硝子をこの坩堝で熔融した際における坩堝素地の, 温度あるいは時間變化による侵蝕状態を追究して, これらの硝子を熔融する際における坩堝の侵蝕機構に論及した。以下にその要約を記す。
1) 〓焼蝋石質坩堝の焼締め過程を通じて, 坩堝素地は白斑, 黄褐色部分及び黒斑の三つの部分から成つており, 白斑はパイロフィライトあるいはダイアスボアの各假像, 黄褐色部分はシャモットと粘土加熱分解物との混合した部分, しかして黒斑はFe₂O₃, TiO₂及びアルカリに富む硝子質の部分である。
2) 白斑中のパイロフィライトは1000-1100°間でムライト及びクリストバライトに分解する。しかして焼締め温度の上昇するに從つて上記の黄褐色部分から白斑の方へFe₂O₃, TiO₂アルカリ等の微量成分の移動があり, 白斑中のクリストバライトの量はこれらの成分と結合する爲に減少する。又黒斑は脈状に發達してその數と大きさを増す。
3) 坩堝が熔融硝子と接觸する部分には0.1-2.5mmの侵蝕層が出來ている。しかして侵蝕層内のクリストバライトは熔融硝子によつて選擇的に溶解され, この状態は侵蝕層に隣接した坩堝素地でも認められる。
4) 侵蝕層におけるパイロフィライト假像は, 化學的侵蝕には弱いが機械的破碎作用には強い。一方黄褐色部分はその逆である。又ダイアスポア假像は化學的侵蝕及び機械的破碎作用には強いが, 往々ブロックのまゝで熔解硝子中に脱落する。
5) 曹達石灰硝子の熔融に對しては坩堝の素地組織を, 又硼珪酸硝子の熔融に對しては坩堝の素地成分を侵蝕防止の際の問題に採り上げねばならぬ。終りに臨み本研究に必要な蝋石質坩堝の製作に協力して下さつた倉田高級耐火物製造所の御好意を感謝致します。又硝子の熔融及び顯微鏡寫眞の作製に當つて下さつた田邊昌之氏及び小坂丈予氏に謝意を表します。

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For Borosilicate glasses B₂O₃ anormalies are often seen. The author made an experiment of transformation point, softeming point and chemical durability in the ternary system of Na₂O-B₂O₃-SiO₂ and expressed them in ternary diagrams.
As the result, it was found that in the transformation points and chemical durabilities B₂O₃ anormaly appeared at the same position, but no anormaly was seen in softening points.
Also he pointed out that in the composition of borosilicate glasses the way of utilization of anormaly differ from each other and hence the composition should be changed naturally in the case of aiming the sealing glasses such as electric bulb glasses or chemical resisting glasses.

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In the author's previous paper, it was stated that due to the disposition that the cations of the modifying oxide do not approach to each other, atomic groups denominated as xy₄ are formed in glasses containing B₂O₃ at the viscosity of about 1.5×10¹² poises, i.e., near the contraction temperature of the glass. In this paper, further considerations concerning the xy₄-group formation in borosilicate glasses are given from the point of view of the ionic refraction of various oxygen in sodium borate glasses.
It is deduced that the B-O bonds in the BO₄ tetrahedron which is located in the central part of the xy₄-group is very strong, and this tetrahedron is formed at the expense of the loosening of the B-O bonds in the BO₃ triangles around it, i.e., these BO₃ triangles are unstable in comparison with those in the normal state. Accordingly, the predominance in number of the atomic groups xy₄ in comparison with other groups such as xy₃z, xy₂z₂, xyz₃, or xz₄, where x, y, and z represent BO₄ tetrahedron, BO₃ triangle and SiO₄ tetrahedron, respectively, is explained.
When the Na₂O content in the sodium borate glass is increased above 0.167, Na ions begin to cut the B-O bonds around xy₄-groups, and as the result, the unstable BO₃ triangles around BO₄ tetrahedron must be stabilized to some degree. It may be supposed that these Na ions should then be trapped in deep potential holes on cutting off the B-O bonds. These Na ions should not be so free as those added later, and they may be regarded as the so-called “enclosed” Na ions.
It may also be supposed that for each one xy₄-group, one Na ion could be the “enclosed” ion, i.e., free Na ions should begin to be produced at the composition 2Na₂O⋅5B₂O₃ or 28.6 mol% Na₂O. Thus the location of the maximum transition temperature curve in the ternary diagram Na₂O-B₂O₃-SiO₂, and the stability of the network of borosilicate glasses are discussed.

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Effects of the addition of chromium oxide on the properties of glass were studied with three kinds of base glass, determining specific gravities, thermal expansions, and chemical durabilities.
Maximum amounts of chromium oxide with which clear glass could be obtained were different by different kinds of base glass, being 8.5 weight percent of chromium oxide in a sodalime-silica glass and 5 percent in a soda- silica glass.

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Considering the trend of the frit composition of today towards softer, selected three ground glasses (Fig. 1) and added tenth of sodium fluoride and sodium silicofluoride respectively. By means of the heat balance, it was known the carbonic acid gas exhausting reaction in fluorine containing batches begins at about 120°C lower and ends at about 80°C lower temperature than that of fluorineless batches. The difference of effect was scarcely found between two fluorides.
100g batch of each was smelted in platinum basin, weight loss measured, chemically analysed from which escaping forms were deduced as just melted down and melted on as long as three hours. While in the former fluorine loss was attsibuted to NaF and F₂ (conveniently represents fluorine loss which accompanies no cation) for the most, SiF₄ for only one case, in the latter in no case to SiF₄.
In smelting of moderne type of titanium frit on plant scale, fluorine loss amounts to 15-20% and its increase with smelting period was relatively small reversely to the above mentioned results.

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本實驗結果より考察する限り次のような結論が得られた。
(1) 純藥を用いCaO-Al₂O₃-SiO.-MgO系においてゲーレナイト等の各種化合物とそれらを結ぶ中間の組成に相當する調合物を, 酸素アセチレン焔を以つて熔融し, 水中に滴下させ完全ガラス化させた試料を得た。
但しこの場合Zachariasenのガラズ式AmBnOのnが0.33以下のものと全くSiO₂を含まないものとは完全ガラス化が出來なかつた。
(2) これらのガラスを粉碎し, 各種刺戟劑を加えセメントとし小型モルタル壓縮強度試驗を行つた。
Ca(OH)₂を刺戟劑とする時ゲーレナイトガラスは著しく活性で刺戟劑の量と共に強度を増しゲーレナイトモルに對し約3.5モルの添加量の時 (重量で約50:50) 最高強度を示す。ウオラストナイトガラスやオケルマナイトガラスは活性に乏しく後者は自硬性を有するが微弱で刺戟劑によつても改善出來なかつた。
(3) CS-C₂S-C₂AS系の組成のガラスについても各組成のものについて同樣の實驗を行つた結果, 組成とCa(OH)₂の最適量, その場合の7日強度と28日強度の關係を示す式と圖を與えることが出來た。C₂ASがa%, C₂Sがb%, 従つてCSが (100-a-b)%の組成のガラスにおいて最高強度を與えるCa(OH)₂の量を調合物に對する重量%で示せば
49a+1b+11 (100-a-b)
となりゲーレナイトの量と共に増大する。ゲーレナイトの28日強度287kg/cm²を活性度100とすれば任意の組成の水滓の28日強度で表し得る活性度は
100a+96b+19 (100-a-b)
となり, 7日強度で現し得る活性度は
77a+96b+19 (100-a-b)
となる。これから初期強度はゲーレナイトの量と共に著しく, 長期強度はC₂C₂AS線上で著しくなることがわかつた。
(4) 結晶質のゲーレナイトは活性に乏しく, ガラスの1/5-1/10程度に過ぎず, この活性の低下は内部表面の減少によると考えられる。
(5) 一方ポルトランドセメントを刺戟劑とする場合にはゲーレナイトガラスは不規則性を示し, 後者が少量の場合は寧ろ初期強度を増加するが, 後者が前者と等量以上になると長期においてさえ全く硬化出來なくなる。これから見てもゲーレナイトのように高アルミナのガラスは水和する際に大量のCa(OH)₂を必要とすることがわかり, 充分刺戟劑が存在すればその優れた活性を發揮出來るが, 不充分の場合は性能を發揮し得ぬことを示すものである。
ウォラストナイトガラス及びオケルマナイトガラスはポルトランドセメとトの量と共に強度を増し, 不規則的な現象は見られなかつた。
附記本研究に當り, 文部省科學研究費の援助を得た。又多數の試驗片の熔融をお引受下さつた日本鋼管株式會社爐材工場長若林明氏及び貴重な文献を御貸與いたゞいた小野田セメント株式會社中央研究所長田中太郎氏に對し厚く感謝の意を表するものである。

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I investigated the relation of setting time and temperature or mixed ratio, and the relation of strength of the setting mass and mixed ratio.
This setting mass contained Al₂O₃⋅2SiO₂⋅2-3Na₂O⋅nH₂O gel and Na₂O⋅SiO₂⋅10H₂O crystal. The latter is strong but water soluble, which produces under the condition of excessive sodium silicate. The former is water in soluble and stable in water.

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