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By Elaine Cristina de Azevedor

Em serviços de radioterapia são utilizados acessórios confeccionados com diversos tipos de polímeros para auxiliar no posicionamento dos pacientes durante o tratamento e na execução das rotinas de trabalho. A radiação gama pode causar nos polímeros degradação de sua estrutura molecular, dificultar a sua na assepsia e seu reduzir o tempo de vida útil. Neste trabalho é apresentado o estudo da degradação causada pela exposição à radiação gama em polímeros utilizados em serviços de radioterapia. Amostras de policarbonato (PC) e polipropileno (PP), foram expostas a doses de radiação gama de 5 kGy e 25 kGy, sendo analisadas por espectrometria de absorção na região do infravermelho e indentação instrumentada. O PC apresentou indícios de fragilização a partir de 5 kGy, reduzindo o tempo de vida útil e o PP apresentou se adequado para o uso em serviços onde haja exposição à radiação gama.

Aug 8, 2018

By Ana Clara Petrucelli

O reator EOF foi desenvolvido no Brasil nos anos 1980 com características únicas. O pré aquecedor de sucata e a distribuição dos pontos de injeção de gases oxidantes e combustíveis conferem estas características. O objetivo deste trabalho é reproduzir o comportamento do banho metálico de um EOF de 45 t comparando seus três pontos de injeção: lanças supersônicas, lanças atmosféricas e ventaneiras. A lanças supersônicas e ventaneiras promoveram uma grande agitação do banho quando comparado com os injetores atmosféricos uma grande oportunidade de melhoria.

Jul 29, 2018

By Larissa Rodrigues de Carvalho Rocha, Mauro Vivaldino Fernandes, Maurício Covcevich Bagatini, Beatriz Fausta Gandra, Adriano Cesar Carvalhido

O combustível com menor granulometria, denominado small, pode ser carregado juntamente com a carga metálica, em substituição ao coque, no intuito de melhorar as condições de permeabilidade do gás e a redutibilidade da carga no alto-forno. Na Usiminas, o equilíbrio na geração e no consumo desse material limita o seu uso em taxas abaixo da média nacional. Nesse sentido, foi avaliado o efeito do coque verde de petróleo (CVP) em substituição ao small coque no consumo de combustível e na estabilidade operacional do alto-forno. Os resultados do teste industrial indicaram a possibilidade de substituição até 45 kg/t gusa, com manutenção do fuel rate, da permeabilidade e da produtividade do alto-forno.

Oct 1, 2019

By Theron Wasson

The oil and gas fields of Michigan that have been under development since 1925 are in an area that extends across the middle of the lower peninsula from northeast to southwest, a distance of about 200 miles, and with a width of about 80 miles. In 19 years 70 fields have been discovered. Most of these are relatively small when compared with other oil-producing areas. This is borne out by the fact that since the first wells were drilled these fields have produced a total of only 204,000,000 bbl. However, Michigan is still maintaining its production, for during the past five years the annual production has remained fairly constant at approximately 20,000,000 bbl. Production for 1943, as reported by the Bureau of Mines, was 20,682,000 barrels. Roughly, one third oi Michigan's production in 1943 came from the Reed City field, which was discovered in 1941. During the year, 237 oil wells were completed in Michigan in 1943. The decrease of 56 from the 1942 total is probably due to the continuance of Government regulations requiring a 40-acre spacing pattern over most of the state. Fig. I shows the principal oil and gas fields of Michigan, and the columnar section, Fig. 2, shows the principal producing horizons in relation to the section drilled. The data of Table I and Table 2 have been carefully checked with previous reports to eliminate errors. Six new producing areas were discovered during 1943 and five areas discovered in 1942 were developed during the year. Both the new discoveries and the 1942 discoveries that were developed appear to be small and relatively unimportant. Goodwell Field.—The best discovery of the year is the Goodwell field, T. 14 N., R. 11 W., Goodwell township, Newaygo County. This small structure was located by core testing done by The Pure Oil Co. in 1942 and early 1943. The first producing well, C. R. Harris No. I, was completed on July 5, 1943, ill the Traverse limestone at a total depth of 2742 ft., with ail estimated potential of 1100 bbl. per day. By the end of the year, 18 wells had been completed in this field and approximately 281,000 bbl. of oil produced. The field operated under proration of 262 bbl. per day per well from Oct. I to Dec. I; 150 bbl. per day per well after that date. Woodville Field.—The small Woodville pool, T. 15 N., R. 11 W., 3 miles north of the Goodwell field, was discovered by core testing by the Ohio Oil Co. The discovery well was completed on May 5, 1943, flowing 650 bbl. of fluid, including 18 per cent salt water the first 18 hr., from the Traverse limestone at a depth of 2810 to 2815 ft. Seven wells had been completed by the end of the year and 67,000 bbl. of oil had been produced. Development is now practically at a standstill because further drilling does not aDDear economically iustified.

Jan 1, 1944

By Theron Wasson

The oil and gas fields of Michigan that have been under development since 1925 are in an area that extends across the middle of the lower peninsula from northeast to southwest, a distance of about 200 miles, and with a width of about 80 miles. In 19 years 70 fields have been discovered. Most of these are relatively small when compared with other oil-producing areas. This is borne out by the fact that since the first wells were drilled these fields have produced a total of only 204,000,000 bbl. However, Michigan is still maintaining its production, for during the past five years the annual production has remained fairly constant at approximately 20,000,000 bbl. Production for 1943, as reported by the Bureau of Mines, was 20,682,000 barrels. Roughly, one third oi Michigan's production in 1943 came from the Reed City field, which was discovered in 1941. During the year, 237 oil wells were completed in Michigan in 1943. The decrease of 56 from the 1942 total is probably due to the continuance of Government regulations requiring a 40-acre spacing pattern over most of the state. Fig. I shows the principal oil and gas fields of Michigan, and the columnar section, Fig. 2, shows the principal producing horizons in relation to the section drilled. The data of Table I and Table 2 have been carefully checked with previous reports to eliminate errors. Six new producing areas were discovered during 1943 and five areas discovered in 1942 were developed during the year. Both the new discoveries and the 1942 discoveries that were developed appear to be small and relatively unimportant. Goodwell Field.—The best discovery of the year is the Goodwell field, T. 14 N., R. 11 W., Goodwell township, Newaygo County. This small structure was located by core testing done by The Pure Oil Co. in 1942 and early 1943. The first producing well, C. R. Harris No. I, was completed on July 5, 1943, ill the Traverse limestone at a total depth of 2742 ft., with ail estimated potential of 1100 bbl. per day. By the end of the year, 18 wells had been completed in this field and approximately 281,000 bbl. of oil produced. The field operated under proration of 262 bbl. per day per well from Oct. I to Dec. I; 150 bbl. per day per well after that date. Woodville Field.—The small Woodville pool, T. 15 N., R. 11 W., 3 miles north of the Goodwell field, was discovered by core testing by the Ohio Oil Co. The discovery well was completed on May 5, 1943, flowing 650 bbl. of fluid, including 18 per cent salt water the first 18 hr., from the Traverse limestone at a depth of 2810 to 2815 ft. Seven wells had been completed by the end of the year and 67,000 bbl. of oil had been produced. Development is now practically at a standstill because further drilling does not aDDear economically iustified.

Jan 1, 1944

By Charles R. Keyes

PAGE. I Introduction,........674 11. Occurrence............ 676 III. Geology of Death Valley BoRate-Region,....677 1. Surface.Relief ......677 2. Geologic Formations,....680 3. Geotectonics,..684 IV. FURnace Canyon Deposits..686 1. General Features..686 2. Geologic Structure..688 3. Ores.....690 4. Typical Section ...691 V. Lost Valley Deposits...693 VI. Mojave Desert Deposits..693 1. Distribution....693 2. Geologic Structure ........694 3. Ores............ 696 VII. Santa Clara Valley Deposits .699 1. Distribution....699 2. Geologic Structure..700 3. Ores.....700 VIII. Ventura County Deposits..701 IX. Geologic Occurrence of Borax .701 1. Original Sources...701 2. Solfataric Borax...702 3. Lacustrine Borax...703 4. Marsh Borax....703 5. Terranal Borax...704 X. Chemistry of Natural Borates.... 705 1. General Considerations.....705 2. Composition of Saline Waters...706 3. Solubility of Components....707 4. Time-Element in Water.Concentrations . 707 5. Effect of Temperature.....708 6. Effect of Pressure......709 XI. Occurrence of Other Commercial Salines,.... 709 I. Introduction. A complete transforrnation has taken place in the borax industry during the year 1908. A most remarkable factor in

Jan 1, 1910

Addicks, L Ambler, J O Anderson, F B Armstrong, T Allen, L M, Jr Arnold, C E Adams, C E Adams, R E Anderson, A J Booth, E L Bernhardt, D I Boyd, W S Browning, W C Blake, D E Black, T B Bergman, Julius Bowen, H P Beckett, P G Blickensdefer, F C Bond, Josiah Butler, P P Bondlas. Y

Jan 1, 1923

By Y. A. Chang

Phase relationships in the system Cr-Si have been established based on the melting point, X-ray, metallo-graphic, and DTA studies. The three intermediate phases, Cr3Si, Cr5Si,, and CrSi,, melt congruently at 177V ± I@,Cr3Si, 1680"i 20°, and 1490" *20°C, respectively, while the fourth intermediate phase CrSi, melts peritectically at 1413" i 5°C to Cr5Si3 and a melt containing 51 at. pct Si. The temperatures and compositions of the four eutectic isotherms occurring in this system are given below: DTA and metallographic evidences indicate that Cr5Si, undergoes a phase transformation at 1505" i20°C. The high-temperature form of this phase could not be retained by the quenching techniques used in this study. TECHNOLOGICAL interest in the developing of composite systems, consisting of Sic on the one hand as a fiber-reinforced material and metallic substances such as chromium, nickel, or Cr-Ni alloys as a binding agent on the other hand, stimulated the present investigation of phase relationships in the binary system Cr-Si. Earlier works concerning this system have been evaluated and summarized by ansen and Anderko.' Their phase diagram was based mainly on the works of Kieffer, Benesovsky, and schroth2 and Kurnakov.~ According to these authors, the three intermediate phases Cr3Si, CrSi, and CrSi, all melt congruently at approximately 1730°, 1600°, and 1550°C. However, they did not agree on the compositional stability of the fourth intermediate phase between Cr3Si and CrSi. Later Parthe, Nowotny, and schmid4 determined the structure of this phase to be tetragonal T-1 type using the single-crystal method, and concluded that this phase had a formula of Cr5Si3. Since the compilation of Hansen and Anderko,' a new phase diagram for the system Cr-Si has been proposed by Elliott5 based on the works of Goldschmidt and rand,' Guseva and ~vechkin,~ and Trusova, Kuzev, and Ormont8 and the earlier works quoted by Hansen and Anderko.' According to this proposed phase diagram, all four intermediate phases have large ranges of homogeneity and all melt congruently. More recently, Svechnikov, Kocherzhinskii, and yupkog studied the system Cr-Si by the DTA-method. According to their findings, the three intermediate phases, Cr3Si, Cr5Si3, and CrSi,, melt congruently at 1700°, 1720°, and 1475"C, respectively, while the fourth intermediate phase, CrSi, melts peritectically at 1475°C to Cr5Si3 and a melt containing 50 at. pct Si. The temperatures and compositions of the four eutectic isotherms were found to be: In view of the discrepancies existing in the literature concerning the system Cr-Si, it was decided to rein-vestigate the phase relationships in this system. EXPERIMENTAL a) Starting Materials. Chromium disilicide and chromium or silicon powders were used in the present study to prepare the melting point and DTA samples. CrSi, was obtained by directly reacting cold-pressed elemental powders in an atmosphere of Hz at a temperature of about 1250°C. Chromium powder, purchased from Stark Chemical Co., had the following impurities in ppm: Fe, 200; Mg, 1000; and 0, 250; while silicon powder, purchased from the Welded Carbide Co., had the following impurities in ppm: Ca, 700; and Fe, 3500. b) Melting-Point Determination and Differential Thermal Analysis. Cylindrical melting-point samples of approximately 13 mm in diam and 30 mm in length with a rectangular groove in the center were prepared by hot-pressing of well-mixed powder mixtures in graphite dies. Before the melting-point determination, the hot-pressed samples were ground on a sand paper to remove any minute surface contamination of graphite. A small hole of 1 mm in diam, drilled on the center portion of the samples, served as a blackbody cavity for the temperature measurements. DTA samples approximately 13 mm in diam and 15 mm in length were prepared in a manner similar to the melting-point samples. Melting points were determined using the Pirani technique under a helium atmosphere of 40 psi. The design, performance, and operation of this apparatus have been described in detail by Rudy and ~ro~ulski.'~ The temperature measurements were carried out with a calibrated disappearing-filament-type micro-pyrometer. The measured temperature was corrected for losses from the quartz window of the melting-point furnace and for deviations from blackbody conditions of the observation hole. The procedure for temperature correction has also been previously described." The DTA method of Heetderks, Rudy and Eckertl' was also used to check any phase transformations of selected alloys in the system Cr-Si. It was not possible to make remated runs on the same sample once melt-

Jan 1, 1969

By Gabriela Grespan Câmara

O processo de galvanização a zinco utiliza como principal passivante o metal cromo na sua forma hexavalente. O presente trabalho estuda a remoção por zeólitas do íon cromo (VI) do efluente de uma indústria metalúrgica. Devido a grande concentração de Cr (VI) na amostra, primeiramente foi realizada uma redução deste metal utilizando metabissulfito de sódio, que é o agente redutor e de precipitação ideal para efluentes contendo concentrações de Cr(VI) acima de 100 mg L-1. Em concentrações menores o precipitado apresenta baixa cinética de sedimentação, necessitando de um polimento com um tratamento terciário. Este estudo foi realizado em coluna de leito fixo contendo zeólitas, onde foram filtradas soluções com concentrações de Cr(VI) variando de 0,5 a 10 mg L-1. O efluente tratado foi aplicado no topo da coluna e retirado pelo fundo. A partir dos dados de adsorção foram calculados as isotermas de adsorção (Langmuir e Freundlich). O modelo de Langmuir obtido mostrou-se significativo e preditivo com 97,93% de confiabilidade. A capacidade máxima da zeólita em remover cromo (VI) foi estimada em 0,02 mg de Cr(VI) g-1 de zeólita.

Aug 16, 2017

By M. E. Fine

IN the apparatus for measuring internal friction shown in fig. 1, a modification of that described by Kê,1,2 the parasitic energy loss or background is equivalent to a Q-1 of approximately 4x10-5. This low value of background was obtained by using a jeweler's collet of appropriate size for the upper support, eliminating lateral motion without immersing the bob in oil, and designing the bob to reduce air resistance. The pendulum is supported on the frame through a snug fitting, sliding rotary joint (fig. I-B). A slight twist of the top imparts essentially pure torsional motion to the pendulum. No evidence of energy loss in the sliding joint has been observed. In the bob (E) steel balls are used in the torsion arm, and the bottom is filled with lead giving a total weight of 94 g. A lighter bob may be used for small diameter specimens. Another bob was a solid disc with provision for adding discs to change the frequency. The oscillating image of the filament is recorded on a revolving drum camera (fig. 1-3) driven by a synchronous motor. This allows use of frequencies higher than can be measured visually on a glass scale. Samples varying in diameter from 0.020 to 0.075 in. have been measured, the frequencies have ranged from 1 to 12 cps, and the maximum strain varied from 0.5 to 10x10-5. With appropriate modification the sample may be placed in a thermostat. The apparatus may also be used to measure the shear modulus. In the examples of measurement given in table I the internal friction of Permendur and the 46.8 Ni-Fe alloy are due, for the most part, to magneto-mechanical hysteresis8 (elastic hysteresis accompanying stress-induced magnetostriction) which depends on strain amplitude and increases with annealing. The internal friction of most materials decreases with annealing. References IT. S. K6: Physics Review (1947) 71, 533. 2 T. S. Kê: Transactions AIME (1948) 176, 448; Metals Technology (June 1948) TP 23703. 3 R. Becker and W. Döring: Ferromagnetismus. 365 (1939). J. Springer.

Jan 1, 1951

By Reginald E. Hore

I. INTRODUCTION. SINCE the discovery of silver at Cobalt, Ontario, in 1903 more than 100,000,000 oz. of silver have been produced b: the mines in the Nipissing district, and there is reason to believe that at least as much more will be produced in the next five years. The estimated value of the aggregate output o ore to the end of 1910 is $48,327,280. The ore yielded 93,977,833, oz. of silver and was mined at a net profit of about $26,000,000. For 1910 the production was 30,558,825 oz. valued at $15,436,894, and yielding a profit of about $9,000',000 The details of the production of the Cobalt district for the years 1904 to 1909, inclusive, are given in Table I. TABLE I.-Silver-Production of the Cobalt District, 1904 to 1909 SMELTING-ORE. Production. Value. Silver-Content. Value Per Ton Ounces. Oz. Per Ton. 1904 206,875 $111,887 1,309 $708 1905.:.... 2,451,356 1,360,503 1,143 634 1906 5,401,766 3,667,551 1,013 687 1907 10,023,311 6,155,391 677 416 1908 18,022,480 8,468,293 736 363 1909 22,436,355 10,809,872 809 389 CONCENTRATES. 1908 1,415,395 $665,085 1,240 585 1909 3,461,470 1,651,704 1,174 559 The shipments from Cobalt are in the form of smelting-ore, concentrates from milling-ore, and bullion. The smelting-or( is largely high grade, averaging about 3,000 oz. per ton- A

May 1, 1911

By Priscila Graziela Melo Martins

O tamanho de grão austenítico é um parâmetro que influencia o desempenho de tratamentos térmicos em aços, assim como suas propriedades. Neste contexto, este trabalho investigou o uso de um reativo para ataque por imersão (240ml de água destilada, 2ml de HCl, 2g de ácido pícrico e 5 gotas de detergente neutro) para avaliar a influência da temperatura e do tempo de austenitização sobre o tamanho de grão austenítico de um aço ABNT1045 austenitizado nas temperaturas de 860ºC, 950ºC e 1100ºC por intervalos de tempo de 40, 90 e 180 minutos. As amostras austenitizadas foram temperadas em água, metalograficamente preparadas e atacadas com o reativo proposto com o objetivo de se revelar os antigos contornos de grãos austeníticos. Os tamanhos de grãos foram medidos com a utilização do software UMIAS de forma a possibilitar a determinação de distribuições estatísticas com quinhentas medidas para cada condição de tratamento. As amostras foram novamente preparadas e então atacadas com Nital 2%, sendo possível avaliar a influência do tamanho de grão austenítico sobre a morfologia da martensita. Pôde-se observar que, para o aço ABNT1045, a influência da temperatura de austenitização sobre o tamanho de grão austenítico é muito evidente e mais significativa do que a do tempo. Os valores de tamanho de grão se mostraram exponencialmente dependentes da temperatura, de forma que quanto maior o tamanho de grão austenítico, mais grosseira é a estrutura martensítica e menor é a dureza do material após a têmpera em água.

Aug 7, 2018

By J. S. Roberts

"Campbell mines has been in operation since 1948. Part of the process consists of roasting of a flotation concentrate which contains arsenopyrite.At present operation level the milling rate averages about 850 t.p.d. and about 48 t.p.d. of concentrate is roasted. The gas emissions at present contain between 3 and 3.5 t.p.d. of arsenic trioxide, about2 - 2.5 t.p.d. of particulate matter and between 19 - 25 t.p.d. of sulphur dioxide. The particulate is extremely fine calcine dust and it assays about 4 oz. Of gold per ton.Until 1974 the gas was discharged untreated through a 125' stack.UntreatedThe decision was made in 1972 to erect a gas treatment plant, construction ran through 1973 and operation began in 1974. The cost of the installation was about 1.3 million dollars.On investigation the process technology, it was apparent that the plant operated by giant Yellowknife for the same purpose was the model we should study. I would like to acknowledge the fine cooperation we had from giant, the plant that emerged is very similar to theirs and incorporates some improvements suggested by them and based on their operating experience.The plant is designed to remove arsenic and solid dust and it has no provisions to remove sulphur dioxide.We depend upon the 125' stack to assure adequate dilution. Because of the nearby airport the stack cannot exceed 125'. A stack burner is provided that can ""y used to heat the stack gas and carry it higher into the atmosphere when there is an inversion condition.The removal of arsenic from hot gas is fairly simple. The sublimation point is about 425°f, a few degrees above this point the arsenic is a gas and a few degrees below it condenses into a solid form. The arsenic could have been removed by simply dropping the temperature below the condensation point and collecting all the solids in a baghouse. This would have removed the possibility of recovering the gold in the calcine dust and would have produced an impure and more bulky arsenic material to be placed in safe storage. The decision was made to collect the solid dust in a hot electrostatic precipitator operating above the sublimation point and subsequently lower the temperature below the condensation point and collect the arsenic in a baghouse."

Jan 1, 1976

By Daniel N. Beshers, Ralph H. Condit

An expression for the diffusion coefficient of inlerstitial atoms in the bcc lattice is derived which takes account of jumps between tetrahedral and octahedral interstices. The results are applied to the case of carbon diffusion in iron to find values for jump frequencies of the types, octahedral-tetrahedral, tetra-hedral-tetrahedral, and tetrahedral-octahedral. ThERE has been renewed discussion1-5 concerning the mechanism of diffusion of interstitial atoms in the bcc lattice. This lattice has both octahedral and tetrahedral interstices, and it has been pointed out that the interstitial atoms may make jumps of the octahedral-octahedral type, hereafter called o-o, octahedral-tetrahedral, o-t, and tetrahedral-tetrahedral, t-t. Doubt has been cast on the applicability of snoek's8 model for internal friction to some interstitial migrations in bcc lattices wherein he proposed 0-0 jumps as the principal mechanism of migration. Also, the anomalous excess diffusion of carbon in iron at high temperatures4 has been ascribed to t-t jumps,2,3 even though the sites normally occupied are octahedral. In this paper an expression is derived for the diffusion coefficient, taking account of the three types of jump mentioned. The relationship of the coefficient to the corresponding internal friction relaxation time is found for the limiting case corresponding to Snoek's model. These results are applied to the case of carbon in iron. In Fig. 1, the structure is shown with the locations of the interstices. Each o site has four t site neighbors coplanar with it, and each t site lies halfway between two o sites. There are four t site first neighbors of a t site lying at the vertices of a tetrahedron. Let the average fraction of atoms occupying o sites and t sites be No and Nt, respectively. Since there are six o and twelve t interstices per unit cell having a lattice parameter, a, the concentration of interstitial atoms will It will be assumed that three types of jumps may be distinguished, t — t, t — o, o — t,for which the jump

Jan 1, 1968

By Matheus Porto Trindade, Marcos Menino de Macedo Filho, Isau de Souza Alves Junior, Sandro Griza, Brenno Lima Nascimento, Gustavo Dória Lima

O tratamento de oxidação térmica da liga Ti-6Al-4V foi realizado ao ar a 600 °C durante 2h, 5h e 10 h. O comportamento à fadiga foi analisado e comparado com aquele da liga não tratada. Foi feita caracterização através de análise por microscopia ótica e eletrônica, difração de raios-x e medição da rugosidade. Os resultados do DRX demonstraram crescimento dos picos de rutilo. Verificou-se um aumento na espessura média da camada formada de 0,12 μm para 1,09 μm ao elevar a duração do tratamento de 2 para 10 h. Os resultados apontaram redução de resistência a fadiga de 35 % para amostras oxidadas durante 2 h, 27 % para amostras oxidadas por 5 h e 29 % para as amostras tratadas durante 10 h, em relação ao ensaio com corpos de prova não submetidos ao tratamento. O efeito prejudicial causado pela camada formada após oxidação de 2 h foi tão danoso quanto o causado pela camada formada após 10 h, apesar da diferença entre as espessuras das camadas. A morfologia encontrada nas amostras fraturadas indicou fragilização na superfície das amostras oxidadas, contribuindo para a nucleação de trincas iniciais nos primeiros ciclos de fadiga na camada que favoreceram a propagação de fadiga, independendo da espessura de camada.

Oct 19, 2019

By Marcus Wolter Ferreira

O objetivo deste trabalho é desenvolver uma metodologia para aprovação de tubos com alta resistência a colapso de acordo com os requisitos da norma internacional API5CT grau N80, produzidos por tratamento térmico de tempera e revenimento, utilizando fornos de indução em tubos fabricados pelo processo de soldagem com resistência elétrica em alta frequência (ERW/HFIW). Neste trabalho são exploradas as principais propriedades mecânicas e dimensionais de um tubo de revestimento com diâmetro externo de 177,8 mm e parede 8,05 mm grau N80 processado para atingir alta resistência a colapso, onde serão apresentados os resultados do processo de qualificação para validação de sua produção em série.

Oct 30, 2017

By Bernardo Martins Braga

O desgaseificador RH é um reator de refino secundário bem estabelecido. Nesse equipamento, gás inerte é usado para promover a circulação de aço entre a panela de aciaria e uma câmara de vácuo. A predição correta da dispersão de gás na perna de subida do RH é importante para a modelagem confiável do processo. O presente trabalho estudou a penetração de gás na perna de subida do RH por meio de modelos físico e matemático. No estudo, foram considerados apenas um ou dois bicos injetores e vazões de gás, por bico, entre 5l/min e 50l/min. Para as condições com um bico injetor, os resultados das duas abordagens mostraram boa concordância qualitativa. Já para as condições com dois bicos injetores, a concordância só foi satisfatória para vazões de até 30l/min por bico. Adicionalmente, os resultados obtidos indicaram que o problema de penetração de gás em modelos matemáticos de desgaseificador RH identificado na literatura está relacionado com erros numéricos e não com falhas na modelagem da física do problema.

Aug 17, 2017

By Kirk Ellison, Sherif Elfass, Ramin Motamed, Kevin V. Stanton

"The determination of accurate load transfer curves are essential for estimating deep foundation loadsettlement response using t-z style analyses. While recently developed semi-empirical methods from Ashour et al. (2010) and Ashour & Helal (2012) have shown promise in preliminary studies, they have not yet been thoroughly benchmarked against a more widely accepted approach. To address this issue, these recent procedures are implemented in the computer program CGI-DFSAP to predict the results of four Osterberg-cell (O-Cell) load tests. These predictions are compared to outcomes obtained following the recommendations from Reese & O’Neill (1988) for t-z analyses of drilled shafts in sand and clay which are carried out with the program TZ-PILE. Overall, the results suggest that the new approach offers improved accuracy regarding predictions of drilled shaft response to axial loading.INTRODUCTIONThe behavior of axially loaded deep foundations is often analyzed using a technique known as the t-z method. In this method, deep foundation elements are broken into multiple segments which are supported by discrete nonlinear springs to capture the contribution of both side-friction (t-z springs) and end-bearing (Q-z springs). Hence, the t-z and Q-z relationships dictate the predicted load-settlement response. A number of different approaches have been developed to estimate load-transfer curves with some relying solely on empirical data from laboratory and field experiments (i.e. Coyle & Reese, 1966; Vijayvergiya, 1977) and others based mainly on analytical frameworks (i.e. Kraft et al., 1981; Randolph, 1994). Reese & O’Neill (1988) provide recommendations which are widely used for developing t-z and Q-z curves for analyzing drilled shafts. This method is hereafter referred to as Method 1 (M1). It should be noted that these empirically derived relationships are only applicable for problems associated with drilled shafts and are therefore not appropriate for developing load-transfer curves for other types of deep foundations (i.e. driven piles). This is because of the difference in the frictional resistance which can be developed between a circular concrete-soil interface as opposed to that of other materials (i.e. steel) and/or different cross sectional geometries.The M1 load-transfer curves form the basis for the t-z analysis of drilled shafts implemented in the computer program TZ-PILE (Ensoft, 2014). In light of this, TZ-PILE is employed herein as a reference to compare against the capabilities of another method of implementing t-z style analyses. This method is based on a semi-empirical framework for soil behavior developed by Norris (1986) and is implemented using the program CGI-DFSAP (Computers & GeoEngineering Inc., 2011). More information concerning this approach, hereafter referred to as Method 2 (M2), is given in subsequent sections."

Jan 1, 2017

By Beatriz Lemos Clemente

A maneira com que acontece a nucleação interfere diretamente na forma dos contornos de grão e também nas propriedades do material em questão. Para visualizar melhor, pode-se utilizar uma célula cúbica, na qual é possível notar que em cada eixo há diferença de textura e densidade entre os grãos já desenvolvidos. Neste trabalho, foram empregadas duas vias de estudo a fim de obter os resultados desejados. A primeira delas é a nucleação homogênea dos grãos e a outra, a nucleação não homogênea, ambas com velocidade constante. Esse fenômeno pode ser visto durante a recristalização de grãos. Rios e Villa [6] criaram um método efetivo para analisar a cinética das transformações homogêneas e não homogêneas a partir do método de JMAK[1-5]. Para comparar método analítico foi desenvolvida uma simulação computacional com base no modelo analítico Rios e Villa [6], foi utilizado a metodologia do Cone Causal (método estocástico). Os gráficos gerados confirmam a teoria de Rios e Villa [6] para esses casos particulares e comparam os resultados obtidos com o conceito de JMAK [1-5].

Oct 30, 2017

By D. N. Seidman

In the course of a study of the electronic and thermodynamic properties of Pb-Se alloys it was found necessary to have an accurate knowledge of the phase diagram. However, the literature is in disagreement as to whether or not a monotectic reaction occurs in the lead rich portion of the phase diagram. Pelabonl reported only a two-phase region consisting of lead-rich liquid and solid PbSe extending from almost pure lead to the compound PbSe, and gave the melting point of PbSe as 1065°C. The data of Friedrich and Leroux2 are in general agreement with this type of diagram, with the melting point of the compound being 1088°C. However, Nozato and Igaki by inverse rate thermal analysis observed a monotectic reaction isotherm exlacing at 860°C with a monotectic composition of 20.5 at. pct Se. The miscibility gap in the liquid state extends from 7.5 to 20.5 at. pct Se. Hansen and Anderko4 accepted Nozato and Igaki's phase diagram in the region of the lead-rich monotectic. To reinvestigate this portion of the phase diagram, both thermal analysis and metallographic examination of various compositions were performed. The thermal analysis apparatus was constructed according to the specifications of the National Bureau of Standards. A t/t-l pct Rh thermocouple was calibrated against the melting point of copper (NBS), zinc (NBS), and antimony (A. D. Mackay), the emf being measured with a Rubicon Type B potentiometer sensitive to lpv. The absolute accuracy of the thermal analysis obtainable with this system is ± 0.5oC. Starting materials were semiconductor grade lead and selenium purchased from the American Smelting and Refining Co. Both elements were 99.999 pct pure with only trace impurities detected upon spectroscopic examination. One hundred galloys were sealed in quartz crucibles with a central thermocouple well under a vacuum of less than 1 p. This procedure prevented any composition change due to vaporization during the run. Cooling curves were obtained on the alloys listed in Table I. Data was taken by the direct method at cooling rates ranging between 1/2 to 2°C per min. The alloys were heated well above the liquidus and shaken vigorously to insure homogeneity. No evidence of an arrest indicative of the monotectic reaction was observed, and the two-phase region reported by Pelabonl and Friedrich and Leroux? was confirmed in general, although our data give higher liquidus temperatures than Friedrich and Leroux. The melting point of stoichiomet-ric PbSe determined for two different samples was 1080.7 0.5oC. The results of this investigation are compared with Nozato and Igaki's data in Fig. 1. To Complement the thermal analysis data, an 86 at. pct Pb specimen was examined microscopically. This composition was in the center of the miscibility gap reported by Nozato and Igaki.3 The alloy was heated to 1000°C, held for 1/2 hr, and water quenched. The specimen was polished using standard metallographic techniques for lead. The alloy was etched with an acetic-nitric acid etchant for 10 min at 45°C. Microscopic examination did not indicate the existence of two separate layers or solidified droplets imbedded in a matrix, as would be expected if a miscibility gap were present. The mi-crostructure shown in Fig. 2 consists of uniformly dispersed, dendritic PbSe in a lead-rich matrix.

Jan 1, 1962