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By Andreas G. Mueller

Gold-silver and copper-gold deposits with high-temperature wallrock alteration of Ca-Mg-Fe-Al silicates occur in ca. 3.0 Ga old greenstone belts of the Yilgarn Block, Western Australia. The deposits are hosted by amphibolite-facies komatiites, basalts and BIF, controlled by ductile shear zones and located within the contact-metamorphic aureoles of composite granodiorite-granite batholiths. Disseminated sulfides and free gold form foliation-parallel ore zones in a gangue of anhydrous silicates (garnet, clinopyroxene, olivine), hydrous silicates (amphibole, biotite) and calcite. The deposits may be classified on the basis of their dominant economic metals as: 1(1) Gold skarns with substantial silver as by-product, represented by the Marvel Loch mine (production: 2,200,000 t at 3.5 g/t Au), and characterized by the mineral association pyrrhotite, loellingite, arsenopyrite, galena, gold and magnetite. (2) Gold skarns with low silver contents, represented by the Nevoria mine (production:1,850,000 t at 3.4 g/t Au), and characterized by the mineral association pyrrhotite, chalcopyrite, arsenopyrite, gold, Bi-tellurides and magnetite. (3) Copper-gold skarns, represented by the Elverdton mine (production: 850,000 t at .7 5 Cu, 0.81 g/t Au), and characterized by the mineral association magnetite, chalcopyrite, pyrrhotite, pyrite, gold and Ag-Bi tellurides.

Jan 1, 1990

By Carlos Vinícius Domingos de Carvalho

As perdas geradas nos processos de uma Aciaria contribuem de forma significativa para a perda metálica do processo. Eventualmente, mesmo com uma operação correta, do ponto de vista de características do produto, pode ocorrer comprometimento do ponto de vista econômico, e uma forma de redução direta dos custos e aumento de performance é a redução das perdas geradas no processo. Desta forma, tornou-se importante realizar um estudo para reduzir as perdas metálicas na Aciaria. Foi utilizado a metodologia Seis Sigma, sendo estratificadas as perdas por processo na Aciaria, onde as maiores perdas na rota dos processos de Lingotamentos Contínuos foram: perda no Distribuidor (24,7%), corte de sequência (17,5 %), retorno de corrida por baixa temperatura do aço na panela (16,3 %); perda por obstrução da válvula da panela (8,8 %). A perda metálica foi reduzida em 50,8%. Além da redução expressiva das perdas, houve uma grande contribuição em relação à compreensão dos modos de falhas para apropriação correta das perdas, tornando as informações mais seguras e facilitando o tratamento de possíveis falhas no processo.

Oct 30, 2017

By Douglas Will Leite

O objetivo deste estudo é recuperar parte do alumínio empregado na fabricação das embalagens de medicamentos do tipo “blister”, por tratamento químico e térmico seguido de separação gravimétrica, resultando na obtenção de alumínio na forma de óxido (Al2O3). A caracterização do produto particulado metálico obtido constitui-se em um caminho para se chegar ao patamar de existência de coleta seletiva após seu descarte, diminuição deste tipo de embalagens nos aterros sanitários e/ou incineradores de lixo doméstico e posterior reaproveitamento com amplos benefícios ambientais. A caracterização morfológica do óxido de alumínio obtido foi realizada utilizando as técnicas instrumentais de ICP/AES e MEV/EDS.

Aug 7, 2018

By Hugo Montalvão Gontijo

O complexo de extração, beneficiamento e transporte de minério de ferro denominado Minas-Rio, de propriedade da Anglo American, consome na moagem primária uma grande quantidade de corpos moedores (bolas metálicas). Recentemente, foi desenvolvido em 4 etapas um trabalho para automatizar a reposição dos corpos moedores e estabilizar o grau de enchimento do moinho. Na etapa A, com a reposição sendo realizada com auxílio de um operador. Na etapa B, com a reposição sendo realizada automaticamente de acordo com uma taxa de reposição predefinida. Nas etapas C e D, com a taxa de reposição sendo alterada por meio do sistema de controle avançado OCS-4D©, considerando a potência do moinho como indicação indireta do grau de enchimento. É possível verificar após a implementação das modificações uma maior estabilidade da potência e consequentemente maior estabilidade do grau de enchimento.

Oct 30, 2017

By Paul A. Beck, John Towers, W. D. Manly

Recent work on grain growth in high purity aluminum and in a solid solution type alloy of aluminum and magnesium1 showed that the isothermal increase of the average grain diameter D with time follows the equation D = K(tg + A)2 Eq 1 Here tg is that portion of the total annealing time 1, which is available for grain growth, that is the annealing time less the time necessary for complete recrystallization. The parameters A and n depend only on the temperature. A has the dimension of time, and is usually of the same order of magnitude as the time for recrystallization: R. In some instances R may be substituted for A in Eq I. This is the case for example at long periods of annealing or at high temperatures, where both A and R become small in comparison with t. In such instances Eq I is simplified to D = K, tn Eq 2 For high purity aluminum the exponent n increases in the ratio of about I to 5 in. the temperature range of 350' to 6w°C. 70-30 brass has been long known to exhibit grain growth of the continuous type, such as occurs in pure metals. For this reason, it was of interest to determine whether grain growth in brass also follows Eq I and 2 as it does in aluminum. Isotherma1 grain growth data for 70-30 brass were published in recent years by R. S. French2 and by H. L. Walker.' Fig I shows a log D vs. log t plot of French's data, together with the 500, 600 and 700°C data by Walker for 42.8 pct reduction by rolling. In such a log D vs. log t plot Eq 2 corresponds to a straight line with a slope of n. As seen in Fig I, the data of French and the 600°C data of Walker can be represented by straight lines. However, the 500 and 7c0°C data of Walker give curved lines and the average slope of his 500°C line is very different from the slope of the line representing French's data for the same temperature. Furthermore the curvature of the 700°C line suggests a tendency for grain growth to stop after 8 hr. If confirmed, this would constitute a definite deviation from Eq 2, not explainable on the basis of the specimen thickness effect found in high purity aluminum.' Walker's specimens were 0.125 in., or 3.18 mm thick, while the deviation occurs at a grain size of approximately 0.4 mm. A further point of divergence arose recently, when J. E. Burke suggested4 on the basis of Walker's data, that, instead of Eq 2, grain growth in 70-30 brass follows the equation D - D, = K . tgn Eq 3 Here D, is the grain size as recrystallized at the temperature in question. Although it was possible to show5 that, for pure aluminum, for which isothermal grain growth has been carefully investigated, Eq 3 is incompatible with the experimental facts, the situation remained somewhat obscure with respect to 70-30 brass. In view of the discrepancies between the published data on brass from different

Jan 1, 1949

By John Towers, Paul A. Beck, W. D. Manly

Recent work on grain growth in high purity aluminum and in a solid solution type alloy of aluminum and magnesium1 showed that the isothermal increase of the average grain diameter D with time follows the equation D = K(tg + A)2 Eq 1 Here tg is that portion of the total annealing time 1, which is available for grain growth, that is the annealing time less the time necessary for complete recrystallization. The parameters A and n depend only on the temperature. A has the dimension of time, and is usually of the same order of magnitude as the time for recrystallization: R. In some instances R may be substituted for A in Eq I. This is the case for example at long periods of annealing or at high temperatures, where both A and R become small in comparison with t. In such instances Eq I is simplified to D = K, tn Eq 2 For high purity aluminum the exponent n increases in the ratio of about I to 5 in. the temperature range of 350' to 6w°C. 70-30 brass has been long known to exhibit grain growth of the continuous type, such as occurs in pure metals. For this reason, it was of interest to determine whether grain growth in brass also follows Eq I and 2 as it does in aluminum. Isotherma1 grain growth data for 70-30 brass were published in recent years by R. S. French2 and by H. L. Walker.' Fig I shows a log D vs. log t plot of French's data, together with the 500, 600 and 700°C data by Walker for 42.8 pct reduction by rolling. In such a log D vs. log t plot Eq 2 corresponds to a straight line with a slope of n. As seen in Fig I, the data of French and the 600°C data of Walker can be represented by straight lines. However, the 500 and 7c0°C data of Walker give curved lines and the average slope of his 500°C line is very different from the slope of the line representing French's data for the same temperature. Furthermore the curvature of the 700°C line suggests a tendency for grain growth to stop after 8 hr. If confirmed, this would constitute a definite deviation from Eq 2, not explainable on the basis of the specimen thickness effect found in high purity aluminum.' Walker's specimens were 0.125 in., or 3.18 mm thick, while the deviation occurs at a grain size of approximately 0.4 mm. A further point of divergence arose recently, when J. E. Burke suggested4 on the basis of Walker's data, that, instead of Eq 2, grain growth in 70-30 brass follows the equation D - D, = K . tgn Eq 3 Here D, is the grain size as recrystallized at the temperature in question. Although it was possible to show5 that, for pure aluminum, for which isothermal grain growth has been carefully investigated, Eq 3 is incompatible with the experimental facts, the situation remained somewhat obscure with respect to 70-30 brass. In view of the discrepancies between the published data on brass from different

Jan 1, 1949

By Camila Lourenço Soares

A produção de aço no mundo está a cada dia mais competitivo, com isso as indústrias siderúrgicas tem desenvolvidos projetos com foco na melhoria da qualidade dos aços e na redução dos custos dos processos de fabricação. Este trabalho descreve as melhorias realizadas no processo de lingotamento contínuo, com foco na redução do desvio de placas por desobstrução dos veios da MCC 2. Esta melhoria consistiu na modificação do sistema de controle e injeção de argônio dos veios durante o lingotamento. A implementação dessas ações propiciou um melhor controle na injeção de argônio no sistema de válvula gaveta, reduzindo significativamente as obstruções do veio por deposição de alumina. Hoje, com os resultados alcançados na MCC 2 perduramos entre as melhores práticas nacionais. O trabalho foi realizado sem investimento contribuindo com a redução do custo de transformação do aço em placa.

Aug 16, 2017

By T. R. Ingraham

When aluminum sulfate was decomposed in an evacuated apparatus and the sample cooled, Q alumina was found. The thermodynamics of the decomposition reaction were resolved by measurements of the total pressure of SO3, SO2, and O2 generated over the sample at various temperatures. The results were correlated with other published data to calculate the rmges of thermodynamic stability of the various compounds involved. The thermal decomposition of aluminum sulfate was studied by Wijhler, Pluddeman, and Wöhler1 and by Warner and Ingraham.2 The results of both studies were critically reviewed by Kellogg,3 who observed that "each set of data shows considerable scatter and strong curvature on a plot of log pso3 vs 1/T".3 He agreed with Warner and Ingraham2 that both the discrepancy in the two sets of results and their curvature may arise from the indefinite properties of the particular form of A12O3 which is formed during the decomposition. While studying the thermal stability of other sulfate systems, we had noted the presence of nonequilibrium oxide properties in both the cobalt4 and manganese5 systems, but neither had shown any appreciable curvature on a logPSO, vs 1/T relationship, and the data from both systems agreed reasonably well with prior work. It therefore seemed reasonable to reexamine the technique which had been used in our earlier work on aluminum sulfate.2 The principal difference was that a tightly compacted pellet had been used for the earlier aluminum sulfate work, whereas a loose powder, contained in a platinum boat, was used for our work on other sulfate systems. In addition, a better technique had been developed for dehydrating the samples. From work done on the nickel system,6 we had become aware of the highly protective nature of some sulfate layers on their oxjdes, and hence of the necessity of providing a large surface area of P3e sample when equilibrium was to be attained in a reasonable time. That observation suggested that perhaps a steady state, rather than equilibrium, had been reached in the earlier work on aluminum sulfate. This paper reports a repetition of the experimental work with large, finely divided samples of anhydrous aluminum sulfate. APPARATUS AND PROCEDURE The apparatus used in the experimental work was described in earlier papers.2,7 The source material was Anachemia reagent-grade Al2(sO4)3 - 18H2O which was first partly dehydrated by heating at 400°C for 48 hr and then completely dehydrated by repeated baking of an aluminum sulfate-oleum slush to dryness at 450°C. ? Alas was prepared by decomposing some of the sulfate in a muffle furnace at 800° C overnight. Approximately equal amounts of the 7) alumina and aluminum sulfate were used in the experiments. The finely divided samples were handled under dry box conditions, and in addition some of the aluminum sulfate was decomposed in the apparatus while it was under vacuum, to ensure its complete dehydration prior to sealing the apparatus. The samples were heated to a series of constant temperatures on both increasing- and decreasing-tem-perature programs. Two to three days were required to obtain steady readings of the total decomposition pressure on an increasing-temperature program, and 5 to 6 days on a decreasing-temperature program. Three samples were examined on both programs. Within experimental error, the results for each sample and each program could not be distinguished.

Jan 1, 1969

The Annual General Meeting of the Institute was held in Kelvin House, Johannesburg, on Wednesday, August 14th, 1974. Mr P. W. J. van Rensburg (President) was in the Chair. There were present 56 Fellows, 21 Members, 2 Graduates, 5 Associates, 16 Students, and 58 Visitors, making a total of 158. The President declared the Meeting open at 4.08 p.m. OBITUARIES The President: Ladies and gentlemen, before we start the business of the meeting, it is my sad duty to announce the deaths of the following members of the Institute since our last meeting: Dr O. A. E. Jackson, Honorary Life Fellow and Past President; C. Airth, T. L. Blunt, A. E. Frazer, C. L. Lamb, and K. Richardson, Life Fellows; and J. T. Beaumont, Fellow. As you know, there were a number of other deaths during the year, which were reported at previous General Meetings of the Institute. As a mark of respect to the memory of the deceased, and in sympathy with the bereaved, I ask you to rise and observe a few moments' silence. MINUTES The President: Ladies and gentlemen, the next item on your agenda is confirmation of the minutes of the General Meeting and Special General Meeting held on May 22nd, 1974. These will be published in the August issue of the Journal, and, since you have not yet received this, I must ask that they be held over to the next General Meeting. WELCOME The President: It is a very pleasant duty for me to welcome many members of our Institute and our guests, among whom we are particularly pleased to see the President of the Chamber of Mines, Mr Dolf Schumann, who is also Honorary President of this Institute. Mr Schumann, we are extremely pleased to have you with us today. And, we welcome an old friend of ours, Mr Dillon, Minister of Mines in Rhodesia, who has come down for our Annual General Meeting. Mr Dillon, we are very, very pleased to see you here this evening, and we look forward to seeing Mrs Dillon a little later. And we have with us, too, the presidents or representatives of many of our sister and brother associations, institutes, and societies. In particular, we welcome Mr Mike Gericke, President of the South African Council of Professional Engineers, and Professor Midgley, President of A. S. and T. S. We are also pleased to welcome the Presidents of the Mechanical Engineers, Electrical Engineers, Certificated Mechanical and Electrical Engineers, the Civil Engineers, the Joint Council of Scientific Societies, the Mine Ventilation Society, the South African Association of Consulting Engineers, the Association of Mine Managers, the Institute of Foundrymen, the Institute of Welding, the Federation of Societies of Professional Engineers, Mine Surveyors, Production Engineers (London), and the Institute of Production Engineering. We are very glad, too, to have with us a visitor from England, Professor Raynor and Mrs Raynor. Professor Raynor is Professor of Metallurgy at Birmingham University, and a very well-known metallurgist in Britain. We also have with us the Chairman of the Ferro-Alloys Association. We are expecting the Chairman of our Witbank/Middelburg Branch, the Chairman of the Engineers' Liaison Committee, Pretoria, the Director of the Witwatersrand College of Technical Education, and, of course, our old friend, Mr Eric Boden, the Manager of A.S. and T.S. It is a very great pleasure to have with us a number of persons who will receive honorary Life Fellowship at this meeting, and there are some Gold Medal winners and winners of our Student Prizes. We have apologies from a number of people who are away on business, and unfortunately some are ill. But we are extremely pleased to see those of you who are here, and we are also very pleased to see so many ladies. We expect to see many more of them later this evening, at our Cocktail Party. MEMBERSHIP The President: I have pleasure in announcing that, their names having been published in accordance with By-Law 5.2.2., the following have been elected by Council to membership in the following grades Fellows: B. Collins, D. W. Dixon, J. P. Dreyer, A. T. Hudson, and W. W. Pearce. Members: A. T. Fisher and I. F. Nagy. Associate Members : P. D. de Bruyn and H. C. Iverson. Graduates: D. P. O'Shaugnessy and M. F. Sadler. Associates: R. J. Bushell and A. MacDonald. Students : I. J. Barker, P. J. Charter, J. P. de Witt, G. S. Esterhuizen, N. Green, P. M. Jenner, M. J. R. Meyer, A. P. Nicol, W. J. C. Pothas, B. J. Robbetze, N. T. Sutherland, B. A. Statham, C. R. Thomas, N. C. Webb, M. Salamon, R. G. Jurd, and M. McChesney. Transfers to other grades of membership include the following: Member to Fellow: B. W. Holtzhousen. Graduate to Member: T. S. Schultz. Associate to Associate Member: C. L. Jordaan, H. J. L. Tomlinson, J. E. Forbes, G. H. S. Bamford, T. F. Carswell, J. W. Breidenhann, J. R. Garbutt, and L. S. Gibbs. Student to Graduate: C. J. Faueonnier and B. Lund. Student to Associate : G. P. Gooding. We welcome these new members

Jan 10, 1974

By Magnus Troilius

The heat-calculations of gas-analyses involve cumbrous multiplications, which are apt to lead into errors. The foliowing tables and formulae have been found useful as facilitating such calculations, and therefore I hope that they will be of interest to some of the members. By "heat-unit" will, in the following, be understood the amount of heat required to raise the temperature of 1 kilogram of water l° Cent. All the tables refer to cubic meters at O0 and 760 mm. pressure. The following gas is chosen as an example: C02, - 4.0 vol. per cent. co, = 20.0 " CHI, - 3.5 " H, - 7.0 " N, - 65.5 " " 100.0

Jan 1, 1884

Book new a Book reviews Economics of the mineral industries. 4th Edition. Society of Mining Engineers (Caler No. D, Litleton, CO 80127, U.S.A.). 660 pp. Reviewer: M.A. Ford Foundry technology, by P.R. Beeley. Durban, Buterworth Scientific, 1982. R124 + GST. Reviewer: A.P. van Wyk Underground Transport Symposium. Johannesburg, The South African Institute of Mining and Metallurgy Special Publication SP 1. 300 pp. R65 (Non-Member), R55 (Member), + GST. Reviewer: C.L. Workman-navies A summary of the Project DevelopmentSymposium as presented by The Australasian Institute of Mining and Metalurgy. $A 25.00. Reviewer: D.J. van Niekerk Geology of uranium deposits. Proceedings of the CIM-SEG Uranium Symposium, September 1981, edited by T. I. I. Sibbald and W. Petruk. Quebec, The Canadian Institute of Mining and Metallurgy, Special Volume 32, 1985.268 pp. Canadian $40 members, $50 non-members (plus $3 for postage and packaging). Reviewer: M.S. Toros Crushing and grinding process handbook. Chichester (England), Wiley, 1986. £49. Reviewer: M.P. Hay O'okiep's 50th birthday The 0'okiep Copper Company Limited, situated at Nababeep s,ome 35 km from Springbok, recently celebrated its fiftieth anniversary.

Jan 1, 1987

By R. G. Davies

WeERTMANI has shown that the high temperature steady state creep rate, i, in lead and indium-base alloys obeys an equation of the form where AH is the activation energy, o the applied stress, n the stress exponent, and R and T have their usual meanings. He observed a variation in n from 4.5 for pure metals to 3 for concentrated alloys, which he interpreted as due to Change in creep mechanism from the climb of dislocations in pure metals to a micro-creep mechanism in the alloys. The Cottrell-Jaswon microcreep mechanism of the moving dislocation taking its impurity atmosphere with it was considered to be the most likely process, although short-range order and the segregation of solute atoms to a stacking fault will also give a stress exponent of 3. Steady state creep has been investigated in a Au - 27 at. pct Cu alloy at temperatures above 1/2 TIM where TIM the absolute melting temperature. As the oxidation resistance of this alloy is excellent all tests were carried out in air with a furnace built to give a temperature variation of less than 1°C along the 60 mm gage length. A lever-arm arrangement applied the stress with a load being adjusted between each creep test to maintain a constant stress. As each test produced less than 0.5 pct creep strain, the variation in stress during the test was negligible. The creep strain was measured by a transducer at the end of one of the alloy-steel grips, with the out of balance potential being finally recorded on a variable speed chart recorder. A typical creep curve is shown in Fig. 1. The results, Fig. 2, confirm that n is nearer to 3 than to 4.5; the creep mechanism could be any of those given above. The activation energy, AH, which is independent of stress, is consistent with a diffusion controlled process; the activation energies for the self-diffusion of gold and for the diffusion of gold into Copper are both -45 kcal per ml., There is now considerable evidence, that, when the steady state creep is dependent upon diffusion, irrespective of the actual creep mechanism, the activation energy is independent of the stress. The author would like to acknowledge the financial assistance provided by the International Atomic Energy Agency, Vienna, and the Argentine Atomic Energy Commission.

Jan 1, 1962

By Fabiana da Silva Santos

O presente estudo fez uso de uma liga de NiTi, rica em Ni, elaborada em um forno de fusão por indução a vácuo - VIM e posteriormente refundida em fornos de arco elétrico com eletrodo não consumível de tungstênio – VAR. Com base nos resultados de Calorimetria Diferencial de Varredura (DSC), Difração de Raios-X (DRX) e Microscopia Eletrônica de Varredura (MEV) / Espectroscopia de Energia Dispersiva de Raios-X (EDS), foi possível observar a heterogeneidade composicional/ típica de fundido por processo convencionais, as inclusões de TiC e Ti4Ni2O provenientes da fusão no forno VIM, e o refinamento microestrutural e manutenção da sua composição original com uso de cadinho de cobre e câmara/atmosfera dos fornos VAR.

Oct 30, 2017

By Artur Camposo Pereira

Este trabalho tem como objetivo avaliar a microestrutura de cerâmica de argila incorporada com um lixo na forma de lodo gerado durante o tratamento de efluentes de uma indústria de fabricação de papel. A microestrutura de cerâmica incorporada com 0 e 10% em peso de lixo, e depois disparada a 600°C, foi avaliada por microscopia óptica, microscopia eletrônica de varredura e difração de raios X. Os resultados mostraram que o desperdício altera a microestrutura da cerâmica argilosa aumentando a porosidade, bem como formando novas fases cristalinas, principalmente com compostos de cálcio.

Oct 30, 2017

By Felipe Pereira Finamor

O aumento da razão da carga transportada por eixo tem sido fundamental para redução dos custos do transporte ferroviário, exigindo rodas de maior resistência mecânica, mas com tenacidade assegurada. Uma das estratégias é se adicionar aos aços microadições (< 0,5 % em massa) de nióbio e ou vanádio, os quais, em solução sólida na austenita atrasam sua decomposição em produtos difusionais, elevando a resistência mecânica dos aços. Neste trabalho foram avaliados dois aços com 0,7%C microligados ou não ao nióbio e molibdênio e produzidos pela MWL Brasil para a fabricação de rodas ferroviárias segundo a classe D da AAR (Association of American Railroads). Foram realizados ensaios dilatométricos em regime isotérmico com um dilatômetro Bähr DIL 805A do Laboratório de Transformação de Fases da Escola Politécnica da USP e análises metalográficas por microscopia eletrônica de varredura e microscopia ótica. Observaram-se atrasos na cinética de transformação austenita/perlita através da microadição de nióbio e molibdênio na ordem de 4 vezes, uma diminuição do espaçamento interlamelar da perlita transformada a 600ºC da ordem de 15% e um pequeno aumento da dureza dos produtos de reação no aço microligado.

Aug 16, 2017

By Rafael Oliveira Sena

A SMS Siemag tem oferecido ao mercado brasileiro novas tecnologias para Lingotamento Contínuo de Placas com objetivo de aumento de desempenho dos equipamentos. A SMS Siemag tem desenvolvido e otimizado o processo de revestimento de placas de cobre do molde que utiliza em conjunto com o processo de eletrodeposição a tecnologia thermal spray que proporciona um produto com alta propriedade de resistência ao desgaste. O revestimento cerâmico, mais conhecido como UniGuardTM, tem obtido resultados excelentes no mercado da América do Norte atingindo valores superiores a 300.000 toneladas. A utilização do revestimento UniGuardTM proporciona um aumento de produtividade e redução dos custos de manutenção do molde bem como redução de aquisição de novas placas de cobre.

Jul 29, 2018

By Oswaldo Delfim

Com o aumento da exportação do minério de ferro para os mercados asiáticos e consequentes novos parâmetros nas especificações, principalmente granulométricas para o minério com maior grau de pureza, viabilizaram-se importantes mudanças no processo produtivo, como por exemplo, a classificação do minério em sua umidade natural. Os ganhos adquiridos nesta nova condição de processo vão desde o aumento da recuperação mássica (de 90 a 95 para 100%), menor investimento no Capex e Opex, além dos ganhos na área ambiental como a eliminação da água na rota do processo e das barragens de rejeitos com consequente facilidade na obtenção do licenciamento ambiental. Neste artigo apresentamos os detalhes técnicos das condições dinâmicas ideais da peneira vibratória dedicada a esta nova aplicação.

Aug 16, 2017

By Carlos Bruno Eckstein, Cayo Vinicius da Silva Lima, Gabriela Ribeiro Pereira, Thiago Tôrres Matta Neves, Clara Johanna Pacheco, Laudemiro Nogueira Junior, Luiz Henrique de Almeida

Aços austeníticos HP atualmente são os materiais utilizados em tubos de fornos de reforma a vapor devido as suas propriedades superiores a altas temperaturas de operação. Por causa da exposição a ambientes oxidantes durante o serviço, na parede externa dos tubos é formada uma complexa camada de diferentes óxidos e, adjacente a esta, se forma região empobrecida de cromo. A presença de uma resposta magnética nesta região influencia diretamente o desenvolvimento de fermentas de inspeção não destrutiva para avaliação magnética da evolução microestrutural em fornos de reforma a vapor. Para caracterizar a resposta magnética desta camada transformada, foi utilizada uma amostra com estado de envelhecimento V utilizando-se a técnica de microscopia Kerr. Foram realizadas análises qualitativas por meio de imagens e análises quantitativas através do levantamento da curva de histerese. Os resultados permitiram identificar regiões com domínios magnéticos e correlacionar o seu comportamento com o valor do campo magnético aplicado.

Oct 29, 2019

By Isadora Pereira Nunes

O objetivo deste trabalho é estudar o efeito do recobrimento de níquel-nióbio por eletrodeposição na resistência à fadiga de um aço carbono SAE 1020. Os corpos de prova para os ensaios de fadiga foram extraídos de barras de diâmetro igual a 7,94 mm (5/16’’). Os ensaios de fadiga foram realizados por flexão rotativa com carregamento em balanço. Foi empregada uma velocidade de rotação de aproximadamente 1500rpm. Foram realizados ensaios de dureza do aço e da camada depositada de Ni-Nb. Análises microestruturais do aço e das fraturas de fadiga foram realizadas através de microscopia eletrônica de varredura (MEV). Os ensaios de fadiga foram realizados de forma a se obter curvas S-N (curvas de Whöler). Foram realizados três ensaios para cada carregamento. Foi observado que o recobrimento de Ni-Nb proporcionou tendência ao aumento do limite de resistência à fadiga do aço.

Aug 17, 2017

By P. R. Clark, M. D. Gleghorn

"IntroductionAt TransAlta Utilities Corporation&apos;s Highvale Mine, located west of Edmonton, Alberta (Fig. I and 2), dragline stripping has proved to be a practical and economical method of overburden removal and future plans have been based upon the continued use of draglines (Fig. 3) as the major stripping equipment (Williams, 1979, Nikols et al., 1986). However, long range planning has shown that the capacity of draglines alone will be exceeded in the early 1990s as mining progresses into deeper overburden cover (Tapics, 1983). Strip ratios will increase from I.3 bank m!/ t of coal in 1985to 4.5 bank m3 / t in 1995. During this period the depth of overburden will increase substantially and the areas to be mined will be characterized by weak soils including glacially displaced overburden. This increased overburden depth in relatively weak soils will make it impractical to _continue side casting by draglines without prestripping in advance. In 1983, a major investigation was initiated to determine what additional overburden removal equipment was appropriate to the Highvale operations, and recognizing the long delivery times of this major equipment. when it would be required. This paper describes studies and tests which were undertaken in 1983 and 1984 to select prestripping methods and equipment for the future operation of the mine.Previous planning studies have shown that with the current burn schedule and with the economies of progressing from low cover to high cover, as has been practiced in the past, overburden volumes will exceed the capacity of the existing draglines in the early 1990s (Fig. 4). These previous studies had placed reliance on (I tandem dragline operation for future overburden removal requirements up to a depth of 45 m throughout the Highvale Mine. New drilling together with the associated geotechnical studies and some detailed planning on the practicality of using tandem draglines, created concerns about their universal application. Even without considering geotechnical conditions there was a depth limitation to tandem dragJines and substantial prestripping would be required to achieve the ultimate depths."

Jan 1, 1987