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Following is the personnel of the various society and national committees on which the A I M E is officially represented United Engineering Society Officers of the Board, 1921 JOHN VIPOND DAVIES, President CALVERT TOWNLEY, 1st Vice-president ALFRED D FLINN, Secretary WILLIAM L SAUNDERS, 2d Vice-president JOSEPH STRUTHERS, Treasurer Finance Committee House Committee CALVERT TOWNLEY, Chairman ALFRED D FLINN, Chairman GEORGE H PEGRAM . H S CROCKER WILLIAM L SAUNDERS BRADLEY STOUGHTON GEORGE M BASFORD CALVIN W RICE F L HUTCHINSON

Jan 1, 1923

By Persifor Frazer

The ore property of Mr. Augustus bop is situated about one and a half miles south of the New Windsor Station of the Western Maryland Railroad and is connected with the town of New Windsor by the Liberty and New Windsor Turnpike. It is about forty miles distant from Baltimore, and about seven miles west from the county town of Westminster, and a little more northeast from the celebrated Liberty Copper Mines. (See accompanying Map I and 2.) The property comprises about 140 acres, lying principally

Jan 1, 1881

By Robert Mehl

THE system cadmium-mercury has attracted much attention, chiefly because of its importance in the study of electrochemical standard cells. The constitutional diagram, as it is accepted today, is essentially that FIG. 1.-BIJL'S DIAGRAM FOR CADMIUM-MERCURY ALLOYS. developed by Bijl1 (Fig. 1), though there has been a great amount of work done on the system by other workers.2 A year ago the senior author published a paper on the crystal structure of the system, in which were described determinations of crystal structure

Jan 1, 1929

In accordance with the provision of the Constitution, notice is here given to all Members, Associates, and Junior Associates, that the dues of the year 1919 will be payable on Jan. 1, 1919, at the office of the Secretary. The clues for Members and Associates are $12 per year and the sum of. $2 additional is asked of those Members and Associates who desire to 'have the two volumes bound in the Institute's standard binding. The clues of Junior Associates are $5 per year.

Jan 12, 1918

By S. G. Lasky

Abraham Lincoln is reputed to have said that if you want to chart a course to some destination, you have to know where you are starting from. In this instance we have to define our starting point in a double manner: 1) What was the theoretical basis of the Paley predictions? 2) What actually did the Commission predict, so that we can see how the predictions have worked out up to now as a basis for considering how they may have to be changed.

Jan 3, 1960

BOSTON LOCAL SECTION Executive Committee HENRY L. SMYTH, Chairman ALFRED C. LANE, Vice-Chairman AUGUSTUS H. EUSTIS, Secretary-Treasurer, 131 State St., Boston, Mass. ROBERT H. RICHARDS ALBERT SAUVEUR Meets on the first Monday evening of each winter month, Twenty-third Meeting The Twenty-third Meeting of the Boston Local Section was held at the Engineers' Club, 2 Commonwealth Ave., on Monday evening, Nov. 30,- 1914. Prof. R. A. Daly addressed the meeting on The Iron Ores of Küruna; Sweden. AUGUSTUS H. EUSTIS Secretary.

Jan 1, 1915

By G. Cartaud, F. Osmond

WE have already devoted two previous memoirs to this question. In the first we collated and discussed the existing literature on the subject; in the second, we described the crystalline forms obtained by the reduction, at different temperatures, of ferrous chloride by hydrogen or by zinc-vapor. The conclusion from these researches was that the three allotropic states of iron-a, stable below A2; 19, stable between A2 and A3; and 7, stable above A3-all crystallize in the cubic system. The differences observed were such as are customarily encountered in the crystallographic records of many minerals of which allotropic varieties or isomerides are not known, but did not conform to the ordinary definition of polymorphism. It is, however, improbable that allotropic transformations, which are placed beyond doubt by a series of positive facts, do not involve some changes in the intimate structure. As a matter of fact, the crystals we did obtain were too small to allow of a precise examination, and this might introduce an element of uncertainty in the firm establishment of our conclusions. Professor H. Le Chatelier was even led to think from some of our results that iron could very well be a rhombohedron simulating a cube, and not a true cube, and it will be remembered that the crystalline form of bismuth was for a long time incorrectly regarded as cubic. Allotropy does not, however, necessarily involve such a deduction. Without departing from the cubic system at all, a whole

Nov 1, 1906

By Charles Austin

IN a recent paper the authors1 discussed the reactions to tempering of hypereutectoid steels quenched from 1000° C., as revealed by studies on changes in hardness, electrical resistivity, coercive force and metallo-graphic characteristics. The data, which related specifically to temper-ing temperatures of 550°, 650° and 710° C., for varying periods up to 125 hr., permitted the following important conclusions: 1. The rate of softening of the steels at the temperatures examined differed markedly although the steels were of "similar" general chemi-cal composition. 2. The temperature of maximum softening spread over a range from about 650° C. to the eutectoid inversion. 3. The divergence in behavior was ascribed, at least in part, to a profound difference in tendency to graphitization on annealing at sub-eutectoid temperatures. 4. The mode of spheroidization of the cementite, as revealed by metallographic studies, also varied considerably in the different steels. The purpose of the present investigation is to pursue further the study of the difference in behavior of the steels on tempering over a wider range of temperature. To this end the following features have received particular attention: 1. Comparison of temperatures of maximum softening of the various steels when the quenched samples were tempered for 5 hr. and for 75 hr. followed by furnace cooling and by quenching in water. 2. Determination of the effect of quenching temperature, prior to tempering, on the rate of softening. Quenching temperatures of 1000° and 850° C. were used in the investigations. 3. Examination of the microstructures obtained with the various heat-treatments employed.

Jan 1, 1938

By M. L. Samuels

In a recent paper the authors1 discussed the reactions to tempering of hypereutectoid steels quenched from 1000' C., as revealed by studies on changes in hardness, electrical resistivity, coercive force and metallo-graphic charaeteristics. The data, which related specifically to tempering temperatures of 550°, 650" and 710" C., for varying periods up to 125 hr., permitted the following important conclusions: 1. The rate of softening of the steels at the temperatures examined differed markedly although the steels were of "similar" general chemical composition. 2. The temperature of maximum softening spread over a range from about 650" C, to the eutectoid inversion. 3. The divergence in behavior was ascribed, at least in part, to a profound difference in tendency to graphitization on annealing at sub-eutectoid temperatures. 4. The mode of spheroidization of the cementite, as revealed by metallographic studies, also varied considerably in the different steels. The purpose of the present investigation is to pursue further the study of the difference in behavior of the steels on tempering over a wider range of temperature. To this end the following features have received particular attention: 1. Comparison of temperatures of maximum softening of the various steels when the quenched samples were tempered for 5 hi. and for 75 hr. followed by furnace cooling and by quenching in water. 2. Deterrnirlation of the effect of quenching temperature, prior to tempering, on the rate of softening. Quenching temperatures of 1000" and 850" C. were used in the investigations. 3. Examination of the microstructures obtained with the various heat-treatments employed.

Jan 1, 1938

By M. L. Samuels

In a recent paper the authors1 discussed the reactions to tempering of hypereutectoid steels quenched from 1000' C., as revealed by studies on changes in hardness, electrical resistivity, coercive force and metallo-graphic charaeteristics. The data, which related specifically to tempering temperatures of 550°, 650" and 710" C., for varying periods up to 125 hr., permitted the following important conclusions: 1. The rate of softening of the steels at the temperatures examined differed markedly although the steels were of "similar" general chemical composition. 2. The temperature of maximum softening spread over a range from about 650" C, to the eutectoid inversion. 3. The divergence in behavior was ascribed, at least in part, to a profound difference in tendency to graphitization on annealing at sub-eutectoid temperatures. 4. The mode of spheroidization of the cementite, as revealed by metallographic studies, also varied considerably in the different steels. The purpose of the present investigation is to pursue further the study of the difference in behavior of the steels on tempering over a wider range of temperature. To this end the following features have received particular attention: 1. Comparison of temperatures of maximum softening of the various steels when the quenched samples were tempered for 5 hi. and for 75 hr. followed by furnace cooling and by quenching in water. 2. Deterrnirlation of the effect of quenching temperature, prior to tempering, on the rate of softening. Quenching temperatures of 1000" and 850" C. were used in the investigations. 3. Examination of the microstructures obtained with the various heat-treatments employed.

Jan 1, 1938

By G. Cartaud, F. Osmond

We have already devoted two previous memoirs to this question. In the firstL we collated and discussed the existing literature on the subject; in the second: we described the crystalline forms obtained by the reduction, at different temperatures, of ferrous chloride by hydrogen or by zinc-vapor. The conclusion from these researches was that the three allo-tropic states of iron—a, stable below A2; , stable between A2 and A3; and , stable above A3—all crystallize in the cubic system. The differences observed were such as are customarily encountered in the crystallographic records of many minerals of which allotropic varieties or isomerides are not known, and did not conform to the ordinary definition of polymorphism. It is, however, improbable that allotropic transformations, which are placed beyond doubt by a series of positive facts, do not involve some changes in the intimate structure. As a matter of fact, the crystals we did obtain were too small to allow of a precise examination, and this might introduce an element of uncertainty in the firm establishment of our conclusions. Professor H. Le Chatelier mas even led to think from some of our results that r-iron could very well be a rhom-bohedron simulating a cube, and not a true cube, and it will be remembered that the crystalline form of bismuth was for a long time incorrectly regarded as cubic. Allotropy does not, however, necessarily involve such a deduction. Without departing from the cubic system at all, a whole

Jan 1, 1907

By William J. McCaughey, Richard L. Barrett

For sixty years—in fact, ever since the inception of the basic steelmaking process —basic slags have been the subject of study by chemists, metallurgists and petrog-raphers! with the purpose of providing a better understanding of the reactions between the slag and the metal during the refining process. The result of this work and of the researches of mineralogists and physical chemists into the chemistry of oxide systems is a considerable body of literature dealing not only with slags themselves but with equilibrium relationships in systems synthesized from pure components. Since any actual slag is a multicom-ponent system more complex than any yet worked out in the laboratory, a complete solution to the problem is still far away. The writers have recently published a paper1 which they believe sheds light on the role of the slag in the elimination of phosphorus and it is the purpose of the present paper to discuss the metallurgical applications of that work. Since the pioneer investigations on the constitution of basic slags carried on by Stead and Risdale, Carnot and Richards, Hilgenstock and others in the I88o's, a considerable body of literature on this subject has appeared. Many of the more important of these papers were summarized in the previous paper,l therefore they will not be reviewed here. PetRographic Study The present writers have had occasion, over a period of years, to examine petro-graphically a great number of basic steel-making slags having a very wide range of chemical compositions and made under various conditions of operating practice. Although certain of these slags exhibit some unusual features, it is a remarkable fact that the great majority of mature slags show certain typical characteristics, which persist throughout the wide range of chemical compositions. The typical mature slag usually appears under the microscope to consist of two phases. The phase of primary crystallization is light colored and doubly refracting. If separated mechanically and subjected to chemical analysis, it is found to consist essentially of SiO2, CaO, and P2O6. Sometimes, although not usually, two such silicate-phosphate phases are found. The other conspicuous phase is dark in color and optically isotropic, and occurs as the interstitial material between the grains of the light colored phase. This dark colored interstitial phase when analyzed is found to consist essentially of FeO, Fe2O3, MnO, and MgO. In some 'lags high in iron oxide, particularly those from low-carbon heats, dicalcium ferrite is found. This phase is dark reddish brown in color and anisotropic.

Jan 1, 1944

By William J. McCaughey, Richard L. Barrett

For sixty years—in fact, ever since the inception of the basic steelmaking process —basic slags have been the subject of study by chemists, metallurgists and petrog-raphers! with the purpose of providing a better understanding of the reactions between the slag and the metal during the refining process. The result of this work and of the researches of mineralogists and physical chemists into the chemistry of oxide systems is a considerable body of literature dealing not only with slags themselves but with equilibrium relationships in systems synthesized from pure components. Since any actual slag is a multicom-ponent system more complex than any yet worked out in the laboratory, a complete solution to the problem is still far away. The writers have recently published a paper1 which they believe sheds light on the role of the slag in the elimination of phosphorus and it is the purpose of the present paper to discuss the metallurgical applications of that work. Since the pioneer investigations on the constitution of basic slags carried on by Stead and Risdale, Carnot and Richards, Hilgenstock and others in the I88o's, a considerable body of literature on this subject has appeared. Many of the more important of these papers were summarized in the previous paper,l therefore they will not be reviewed here. PetRographic Study The present writers have had occasion, over a period of years, to examine petro-graphically a great number of basic steel-making slags having a very wide range of chemical compositions and made under various conditions of operating practice. Although certain of these slags exhibit some unusual features, it is a remarkable fact that the great majority of mature slags show certain typical characteristics, which persist throughout the wide range of chemical compositions. The typical mature slag usually appears under the microscope to consist of two phases. The phase of primary crystallization is light colored and doubly refracting. If separated mechanically and subjected to chemical analysis, it is found to consist essentially of SiO2, CaO, and P2O6. Sometimes, although not usually, two such silicate-phosphate phases are found. The other conspicuous phase is dark in color and optically isotropic, and occurs as the interstitial material between the grains of the light colored phase. This dark colored interstitial phase when analyzed is found to consist essentially of FeO, Fe2O3, MnO, and MgO. In some 'lags high in iron oxide, particularly those from low-carbon heats, dicalcium ferrite is found. This phase is dark reddish brown in color and anisotropic.

Jan 1, 1944

Not many accounts of mining methods or labor conditions in the mines in early days can be found; all that have seemed to be authentic have been included in the preceding chapters. In practically every field opened before 18.10 the first coal was recovered by quarrying, or strip mining, the operations, of course, being by hand and on a very small scale; new places were opened as soon as mining became difficult or expensive. Where it became necessary to drift into the hillsides, the first coal was taken out by sleds, and later by small wagons, the power being supplied by the miner, often assisted by dogs. Wooden rails then came into use with small cars running on them. These cars were very small, usually holding only a few bushels; in the Belleville, Illinois field as late as 1863 cars having capacities of 10, 12, 14 and some as large as 30 bushels were in use. It was not until late in the 1830's that horses or mules came into use for haulage purposes in the Pittsburgh region, although some had been used in the Richmond, Virginia field at an earlier date. Coal was usually undercut by hand and wedged down, until explosives came into general use, and in nearly every field the coal was forked into the cars, the fine coal, or slack, being left in the mine. Hours worked were very long, but few records remain to show what they were at different places and times; there was undoubtedly a great variation between districts and mines. Roy stated a miner could often produce 5 or 6 tons in a day of 8 or 9 hours in a 5 or 6 foot seam, but in another seam possibly could mine only 3 1/2 to 4 tons. He estimated an average day's work in a four foot seam at about 3 1/2 tons.1 In a strike in the Belleville field in 1863 it was found that an average skilled miner in the field could probably produce 4 to 5 tons a day.2 This was only the coarse coal loaded and did not include slack. In 1873, a coal undercutting machine was tried at a mine about two miles from Brazil, Indiana, said to be the first coal machine ever invented in the United States. It was run by a 5 H.P. steam engine (later to be changed to compressed air), and consisted of an iron rim, four feet in diameter with movable steel teeth placed about one foot apart. The rim

Jan 1, 1942

By J. H. Frye, C. P. Sun

A Frimary substitutional solid solution is a solution that has the same crystalline structure as the solvent metal, and in which solute atoms have replaced, solvent atoms at random on the host lattice. This replacement usually results in an increase in hardness as measured by conventional penetration tests. The factors controlling this hardness increase have been investigated in some detail for copper and silver alloys.1-5 It has been shown that at least four factors are involved: (1) concentration of solute, (2) row of the periodic table from which the solute is taken, (3) increase in lattice parameter of the solvent produced by the solute, and (4) work-hardening produced by penetration of the hardness indenter.2,4 The last factor is of the utmost importance. An investigation of the available data2,4 leads to the conclusion that the solutes that produce large hardness increases in copper or silver do so principally because they increase the rate of work-hardening. Furthermore, it is doubtful whether any solute produces appreciable hardening in the absence of plastic deformation and hence work-hardening. Thus it is clear that an understanding of the effect of solutes on rate of work-hardening is essential to an understanding of the hardness of solid solutions. This effect of solutes is also important in forming operations such as rolling or deep drawing. The presence of elements that confer rapid rates of work-hardening will increase power consumption and may well decrease the amount of deformation possible between anneals. This paper is the report of an investigation of the factors that control rates of work-hardening in copper and silver solid solutions. The silver and copper alloys considered are those in which all solutes are from the B subgroups or second short period of the periodic table. Experience with hardness, with structure of alloys, and with electrical conductivity has proved that results of a fundamental nature are most likely to be obtained if alloys are made up on the basis of the positions of the constituent elements in the periodic table. In previous work, Meyer analysis data on high-purity copper and silver solid solutions were obtained through careful measurements with fully calibrated equipment and these data were corrected to correspond to a standard grain size. From these corrected Meyer analysis data rates of work-hardening have now been calculated. Calculation of Rates as Work- HARDENING The Meyer analyses, on which this study of rates of work-hardening is based, consisted in determining impression

Jan 1, 1944

By J. H. Frye, C. P. Sun

A Frimary substitutional solid solution is a solution that has the same crystalline structure as the solvent metal, and in which solute atoms have replaced, solvent atoms at random on the host lattice. This replacement usually results in an increase in hardness as measured by conventional penetration tests. The factors controlling this hardness increase have been investigated in some detail for copper and silver alloys.1-5 It has been shown that at least four factors are involved: (1) concentration of solute, (2) row of the periodic table from which the solute is taken, (3) increase in lattice parameter of the solvent produced by the solute, and (4) work-hardening produced by penetration of the hardness indenter.2,4 The last factor is of the utmost importance. An investigation of the available data2,4 leads to the conclusion that the solutes that produce large hardness increases in copper or silver do so principally because they increase the rate of work-hardening. Furthermore, it is doubtful whether any solute produces appreciable hardening in the absence of plastic deformation and hence work-hardening. Thus it is clear that an understanding of the effect of solutes on rate of work-hardening is essential to an understanding of the hardness of solid solutions. This effect of solutes is also important in forming operations such as rolling or deep drawing. The presence of elements that confer rapid rates of work-hardening will increase power consumption and may well decrease the amount of deformation possible between anneals. This paper is the report of an investigation of the factors that control rates of work-hardening in copper and silver solid solutions. The silver and copper alloys considered are those in which all solutes are from the B subgroups or second short period of the periodic table. Experience with hardness, with structure of alloys, and with electrical conductivity has proved that results of a fundamental nature are most likely to be obtained if alloys are made up on the basis of the positions of the constituent elements in the periodic table. In previous work, Meyer analysis data on high-purity copper and silver solid solutions were obtained through careful measurements with fully calibrated equipment and these data were corrected to correspond to a standard grain size. From these corrected Meyer analysis data rates of work-hardening have now been calculated. Calculation of Rates as Work- HARDENING The Meyer analyses, on which this study of rates of work-hardening is based, consisted in determining impression

Jan 1, 1944

All the TECHNICAL PUBLICATIONS and CONTRIBUTIONS published in 1941 are available at Institute headquarters, unless otherwise noted They are also on file in many public, university and technical libraries and, when so indicated in the list, may be found in the TRANSACTIONS TECHNICAL PUBLICATIONS in Classes A-Metal Mining, 13-Milling and Concentration, H-Industrial Minerals, and I-Mining Geology are distributed in MINING TECHNOLOGY, which is issued every other month Technical Publications in Classes C-Iron and Steel Division, D-Nonferrous Metallurgy and E-Institute of Metals Division are distributed in METALS TECHNOLOGY, which is issued twice quarterly TECHNICAL PUBLICATIONS in Class G-Petroleum Division are distributed in PETROLEUM TECHNOLOGY, which is issued every other month TECHNICAL PUBLICATIONS in Classes F-Coal Division, J-Mineral Industry Education Division, K-Mining Administration, and L-Geophysics, are issued as separate pamphlets An Institute member is entitled to one copy of any printed TECHNICAL PUBLICATION or CONTRIBUTION Copies of TECHNICAL PUBLICATIONS listed have been mailed to members of the Institute according to their registration by classes CONTRIBUTIONS and other TECHNICAL PUBLICATIONS will be sent upon request A member may purchase an additional copy of a TECHNICAL PUBLICATION or a CONTRIBUTION at one cent a page, minimum charge, 25¢ Nonmembers may purchase any CONTRIBUTION or a TECHNICAL PUBLICATION of the F, J, K, or L classes at the same rate, but the nonmember price per copy for METALS TECHNOLOGY, MINING TECHNOLOGY or PETROLEUM TECHNOLOGY is $1 25 domestic, $1 35 foreign countries. TECHNICAL PUBLICATIONS (separate pamphlet form), $2 per annum domestic, $2 50 foreign. METALS TECHNOLOGY, $7 per annum domestic, $7 80 foreign (Iron and Steel Division and Institute of Metals Division ferrous and nonferrous papers) MINING TECHNOLOGY, $6 per annum domestic, $6 60 foreign (metal mining, milling and concentration, Industrial Minerals Division, and mining geology papers) PETROLEUM TECHNOLOGY, $6 per annum domestic, $6 60 foreign Bound volumes have been mailed to members that have requested them, and MINING and METALLURGY Is mailed each month A member is entitled to one volume a year on his membership and he may purchase for $2 50 one copy of a volume not already received, additional copies of the same volume, $5 Nonmembers in the United States may purchase the volumes listed at $5 each, outside of the United States and its possessions, $5 6o Extra single copies of MINING AND METALLURGY, 25¢ current issue, back numbers 500 each to members, to nonmembers 50¢ current issue and $1 each, back issues Subscription price to nonmembers and to members for extra copies, $3 per annum domestic, $4 00 foreign.

Jan 1, 1941

By B. Haimson, C. Fairhurst

One of the main functions of rock mechanics research has been to find ways of determining in-situ stresses. Many methods have been suggested, the most significant ones calling for measurements inside bore- holes. These methods usually employ some instrumentation for the purpose of measuring hole deformation. Several years ago, a new method was suggested by Scheidegger,l based on previous work by Hubbert and Willis.2 It was the method of "hydraulic fracturing," which had been introduced by the oil industry in 1948 for the purpose of oil-well production stimulation. Basically, hydraulic fracturing consists of sealing off a section of a borehole, pumping in a fluid, and pressurizing it until fracture occurs. If pumping is continued vigorously, the fracture is opened up and extended. In an oil field, such an artificial fracture increases the overall permeability of the formation and usually enhances production. During the entire operation, the variation of pressure with time is ordinarily recorded. Hubbert,2 Scheidegger,1 Kehle,3 and others have shown that the recorded pressures can be theoretically related to the magnitudes of the principal in-situ stresses; the orientation of the fracture can often be used to determine the direction of the principal stresses. The advantage of hydraulic fracturing over the present in-situ stress determination methods is simplicity: no sophisticated instrumentation is required inside the borehole; hence, the stresses can be measured at any depth. Moreover, if the formation is impermeable to the fracturing fluid, no elastic constants of the rock are required in calculating the stresses, a

Jan 1, 1970

By N. A. McKinnon, J. H. Auld, A. M. Marshall, R. A. Coyle

IN making a study of the slip deformation and strain hardening of single crystals of aluminum, it has been found that considerable information additional to that provided by the usual metal-lographic techniques can be obtained by the use of the microfocus X-ray method described by Schulz.1 This technique has been applied to crystals both in the state as-grown by the strain-anneal method and after they have been subjected to increasing amounts of plastic strain. Kelly and Wei" have recently reported the use of this method for a study of lineage structure in aluminum single crystals grown from the melt. The crystals, prepared from aluminum of 99.99 pct purity supplied by British Aluminium Co. Ltd., were grown in the form of flat tensile specimens with a gage section of 0.3 by 0.1 in. and a gage length of 2.3 in. The microfocus X-ray tube used provided a focus of approximately 50 half width. Examination of a large number of as-grown crystals showed no sign of any macroscopic defects in the majority of cases. However, occasionally crystals grown by the strain-anneal method did show defects similar in nature to those shown by Kelly and Wei to occur in crystals grown from the melt. In some other cases a more regular appearance of black and white lines, corresponding to valleys and ridges, respectively, in the lattice, was obtained, Fig. 1. This particular crystal was slightly deformed as the lines when present in the image of an as-grown crystal are only barely visible. The angle of tilt of the blocks is of the order of 3. It seems likely that these tilt boundaries arise during the growth of the crystal due to the specimen not being perfectly flat on the hearth of the furnace and straightening under its own weight at the elevated temperatures. For the deformation studies the crystals were strained in a Polanyi-type tensile machine. A typical photograph taken after 1.2 pct elongation of a single crystal oriented with its axis fairly close to the center of the stereographic triangle is given in Fig. 2. The reflection, which is from the (111) planes, is traversed by two systems of parallel lines. These have been identified as traces of the primary (111) slip plane and the (110) plane perpendicular to the primary slip direction. The latter lines correspond to kink bands which could not be detected by the ordinary techniques of

Jan 1, 1958

By George P. Hulst

Prior to 1914, there was little demand for antimony in this country; its use was limited almost entirely to the manufacture of type and bearing metals. Practically no antimony ore was mined here, the market being supplied principally from China, and the alloy was produced by a direct mixing of lead and antimony. The great world war, with its demand for shrapnel in hitherto undreamed of quantities, precipitated a great boom in the price of antimony. Nominally quoted at 6 c. to 7 c. in 1914, the price increased by leaps and bounds to 45 c. in March, 1916. Under the stimulus of high prices many small mines were opened, for it became profitable to work ores containing as low as 20 per cent. antimony. High-grade sulfide ores (stibnite), containing 55 per cent. to 60 per cent. antimony, were received from Bolivia, China, and Alaska. Low-grade sulfide ores, running from 20 per cent. to 45 per cent., were produced in Nevada, California, Idaho, Utah, and Mexico; much of this ore was fairly rich in silver. The principal oxide ores came from Mexico and Oregon. The following analyses are representative of various types of antimony ore: Sb Pb Cu AG AU SIO2 Be S CaO Zn As Oxide ore.......... 25.09 46.02 0.95 0.40 10.98 0.30 0.22 Sulfide ore......... 55.20 15.12 1.05 19.87 0.40 0.25 Sulfide ore......... 37.16 11.30 0.10 34.0 7.60 0.50 17.05 7.40 0.36 0.10 Sulfide ore......... 41.55 18.00 0.20 76.0 0.04 5.60 0.25 18.17 0.85 0.25 0.10 The International Lead Refining Co. fortunately was equipped to handle these ores through residue and blast furnaces. The charge consisted of a variety of sulfide ores containing Sb 20 to 60 per cent. and SiO2 6 to 45 per cent., oxide ores containing Sb 20 to 40 per cent. and SiO2 10 to 45 per cent. Secondary materials, such as battery plates, battery mud, lead oxide, paint, etc., together with refinery skims, softener skims, and other refinery byproducts, were treated along with the antimony ore to furnish the lead required. All silver-bearing antimony ores were treated in the residue furnace, the sulfur, iron, and copper forming matte that carried part of the silver, the balance going into lead bullion. The antimony slag produced was sufficiently low in silver to warrant being smelted in the blast furnace to antimonial lead.

Jan 1, 1921