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By Mônica Aline Magalhães Gurgel

Este trabalho avaliou a evolução estrutural e mecânica dos ciclos térmicos realizados em uma chapa laminada a frio de aço baixo carbono com micro adição de molibdênio e nióbio destinado para a indústria automobilística, associado a classe dos aços bifásicos. Para realização do estudo foi feita a caracterização microestrutural e mecânica, por intermédio de amostras retiradas após a laminadas a frio produzidas em escala industrial, com auxílio das técnicas de microscopia óptica, e avaliação da dureza via Nanoindentador Instrumentado. Os ciclos térmicos foram feitos com o intuito de observar os processos de recuperação, recristalização, e transformação de fases no aquecimento e após resfriamento, com encharque em distintas temperaturas do campo intercrítico, via análise de dilatometria em um equipamento de análise termomecânica (TMA) em amostras extraídas da chapa laminada a frio “Full- Hard”.

Aug 16, 2017

By R. J. Caro

The Anaconda phosphate plant was put into operation in the fall of 1923. Its present daily operating capacity is approximately 170 tons of treble superphosphate and 16 tons of phosphoric acid analyzing 42 pct P2 O5 and 52 pct P2 Os, respectively. As a result of the continued increased demand for phosphates, Anaconda decided in 1947 to expand the plant's daily output to 270 tons of treble superphosphate and 54 tons of phosphoric acid. The present daily plant intake is 335 tons of wet (footwall) phosphate rock analyzing 31.7 pct P² O5 and 0.28 pct V² O5. The rock is shipped from Anaconda's mine at Conda, Idaho, in open railroad cars, having been crushed to pass 3/8 in. mesh at the mine.' The expansion program will require an increased intake of 300 tons of rock per day. The hanging-wall rock anaIj-ses approximately 30.5 pct P2 O5 and 0.11 pct V² O5, and will be beneficiated in a new washing plant under construction

Jan 1, 1950

By G. R. Tostengard

"The paper identifies functional areas which frequently can yield significant productivity improvement. Emphasis is placed on the repair and maintenance, material supply and training functions. Successful approaches are discussed in some detail, and typical results which have been achieved are reviewed.IntroductionA challenge which at all times confronts the manager o f any mineral operation is the potential to improve his operation no matter how effective it might be a t the present time. The challenge has been present through my entire lifetime and I suspect a good many years prior to that and, I expect, will continue many year s and decades in the future. The competitive and economic situation in which we in the minerals industry find ourselves today makes the challenge eve n more important during the 1980s. In many cases it’s a question of survival, not simply pr of it improvement.There are, of course, many avenues to improving profitability; technological changes, new equipment and facilities, improved products, improved mine plans, etc. All of these are important and must be addressed by each manager. This paper focusses on just one avenue to improvement and that is ""improved management"", not so much of management at the boardroom level but of improved management o f the facilities and workforce as the y currently exist. Management implies control. There are three areas where control is often found lacking:1, Repair and maintenance of equipment and facilities;2. Material supply including procurement, inventory control and warehousing; and3. Training.These three areas are all complex and difficult to manage and they are all but ignored in the formal education which our industry's manager s normally receive. They are areas which can be improved with relatively small investments and therefore, they represent especially attractive improvement targets during the 80s when, for most of us, investment dollars are very difficult to come by."

Jan 1, 1983

By Pedro Sampaio Cotta

O mercado de Siderurgia no Brasil vive um momento de pressão causado pelas quedas dos preços internacionais e agravado por fatores internos como a redução no consumo, aumento do custo de energia e tributação elevada. Tendo em vista que, ao menos no curto prazo, não há perspectiva de melhoria, as indústrias do setor se mobilizam para adequar a esta nova realidade. A sobrevivência em um cenário de alta competitividade é garantida reduzindo custos de produção e manutenção e buscando aumentar a produtividade sem, entretanto, expandir a capacidade produtiva. Para atingir estes objetivos as indústrias focam em pequenas melhorias operacionais, com investimentos em pequenas modernizações e otimizações de processos existentes, em detrimento de grandes investimentos em expansões. Neste contexto observa-se um aumento na relevância do software de automação, que surge como alternativa para realização de melhorias, pois possuem custo relativamente baixo em comparação com reformas a nível mecânico e podem proporcionar ganhos importantes de eficiência e qualidade. Este artigo apresenta um estudo da utilização de metodologias ágeis de desenvolvimento de software para realização de melhoria contínua em processos industriais. Como exemplo de aplicação é apresentado o trabalho de otimização do software de automação de um laminador de alumínio com foco no aumento de sua taxa de utilização. A meta foi buscar um ganho de produtividade garantindo os mesmos padrões de segurança originais dos equipamentos e com impacto mínimo nas atividades produtivas.

Aug 17, 2017

By Fabiana da Silva Santos

Neste trabalho foram estudados os efeitos da laminação a frio com baixo percentual de redução e a cinética de recristalização em um aço médio carbono e alto manganês. O aço em estudo foi laminado a frio com percentual de redução de 10%, seguido de um tratamento térmico de recozimento nas temperaturas de 650 e 700°C, em tempos de 10, 15, 20, 25 e 30 minutos. A caracterização microestrutural e avaliação da fração recristalizada foram avaliadas por microscopia óptica e a dureza Vickers (avaliada em um macrodurômetro e um microdurômetro). De acordo com os resultados pode-se observar um efeito combinado de recristalização e crescimento de grão em função da microestrutura parcialmente encruada pelo baixo percentual de redução imposto, que se acentua com aumento do tempo e da temperatura de encharque.

Aug 16, 2017

By Jackson de Brito Simões

As ligas com memória de forma (LMF) apresentam características funcionais de recuperação de deformações plásticas aparentes e mudança de suas propriedades mecânicas quando submetidas a variações de temperatura, proporcionando um crescente interesse para aplicações de engenharia e originando uma nova maneira de projetar sistemas mecânicos. Nesse contexto, é importante desenvolver novos métodos de fabricação de componentes e dispositivos a partir de LMF. Infelizmente essa fabricação pode ser ainda extremamente complexa e dispendiosa, principalmente para LMF do sistema Níquel-Titânio (Ni-Ti). No final do século XX, a fundição de precisão se tornou uma alternativa eficaz para a conformação de componentes de titânio e suas ligas em aplicações de alta tecnologia. Entretanto, não existem informações da utilização desse processo para fabricação de componentes mecânicos de LMF. Assim, o objetivo deste trabalho foi avaliar o processo de fundição de precisão para o desenvolvimento de novos, produtos principalmente miniatuadores ativos de LMF Ni-Ti. Para isso, foi realizada a fabricação de diferentes formatos de miniatuadores de LMF Ni-Ti (de composição nominal em peso de 54,9Ni-45,1Ti) pelo processo de fundição de precisão com molde sólido, e ainda sua caracterização térmica e por ensaios não destrutivos. Foram obtidos quatro miniatuadores distintos, nos formatos de minitubo duplo, arruela Belleville, mola e parafuso, com bom acabamento superficial. A presença da transformação de fase característica das LMF foi avaliada por técnicas de calorimetria diferencial exploratória (DSC) e resistência elétrica em função da temperatura (RET) nos quatros tipos de miniatuadores. As técnicas não destrutivas de raios X e tomografia computadorizada foram empregadas para avaliar a qualidade dos miniatuadores produzidos, sendo importantes na detecção da presença de defeitos de processo. Ficou evidente a eficiência do novo processo proposto, porém ainda se faz necessário mais investigações principalmente com relação ao comportamento termomecânico dos miniatuadores obtidos por esse processo.

Aug 16, 2017

By David Bassanelli Sampaio

Com a crescente demanda por sistemas distribuídos e multiplataformas, houve uma larga proliferação de métodos, linguagens e tecnologias com o objetivo de atender aos mais diversos requisitos desse ambiente. Com isso, a TI de corporações que possuem desenvolvimento interno de aplicações enfrentam um grande desafio de gerir conhecimento dos profissionais mais experientes e integrar novos profissionais de forma a garantir a qualidade e agilidade na tratativa de incidentes, bem como a capacidade de evolução e criação de novas soluções. Neste trabalho, apresentaremos as diretrizes, tecnologias e processos desenvolvidos na Usiminas, consolidados em uma arquitetura. Esta arquitetura propiciou, entre outros, a estabilidade e continuidade dos sistemas existentes, a padronização da experiência final do usuário, a agilidade na construção das soluções Java, evoluindo a qualidade dos sistemas mantidos pela TI, com resultados efetivos.

Oct 30, 2017

By Amanda de Vasconcelos Varela

A Inconel 718 tem sido usada por décadas nas indústrias aeroespacial e nuclear por sua boa combinação de resistência mecânica e resistência a oxidação. No entanto, entre aproximadamente 650 e 850ºC, observa-se uma mudança indesejável no modo de fratura da superliga, que caracteriza a fratura intergranular assistida por oxidação. Com as temperaturas de operação em cada vez maiores e uma alta demanda por eficiência energética, a fragilização pelo ambiente é uma grande limitação a aplicação da superliga. Por isso, o objetivo deste trabalho é caracterizar o fenômeno através de ensaios de tração a quente em diferentes taxas de deformação e por microscopia eletrônica de varredura e EDS. A faixa de temperatura de ocorrência do fenômeno, segundo a evidência de fratura frágil intergranular variou conforme a taxa aplicada, manifestando-se entre 650 e 750ºC até 900ºC em todos os casos. O efeito da disponibilidade de oxigênio foi observado e o elemento não demonstrou ser determinante na perda de propriedades mecânicas avaliadas em tração. O nióbio, presente em quantidade considerável na liga, apareceu predominantemente como NbC nos contornos e interior dos grãos, incorporado ao titânio na região de fratura, com aspecto fragmentado. Acredita-se, portanto, que este tenha papel decisivo no processo de fragilização.

Oct 30, 2017

By Bart Blanpain, Tom Peter Jones, Muxing Guo, Liugang Chen, Huayue Shi

Fayalite based slag is formed during the smelting process of secondary copper resources. It was found that with the presence of high ZnO, the slag became viscous, causing a slag tapping problem. In the present paper, the phase relations of the slag system ZnO-“FeO”-SiO2-Al2O3- CaO (ZnO = 0-12 wt%, Al2O3% = 0-15 wt%, CaO = 0-1.5 wt%, with iron saturation) at 1150 °C is studied by using quenching technique followed by phase identification and compositional analysis of equilibrated samples. The dependence of FeO and Al2O3 solubility in the liquid slag on the chemical composition of slag is characterized. Based on the experimental data, the solid fraction of the slag, which may considerably, influences the slag viscosity, at the tapping temperature can be reasonably estimated and, therefore an appropriate modification of the slag composition can be made.

Jan 1, 2016

By Kamila Kazmierczak

Neste estudo utiliza-se o processo de metalurgia do pó para a elaboração de compósitos a base de alumínio reforçados com nanopartículas de TiO2. O compósito é obtido através de moagem de alta energia assim como a obtenção da liga AA2014 utilizada como matriz. A consolidação dos pós obedeceu à seguinte sequência: mistura dos pós segundo proporções específicas, compactação uniaxial, extrusão a quente e tratamento térmico. O material produzido foi estudado microestruturalmente mediante microscopia ótica e caracterizado quanto à dureza.

Aug 7, 2018

By W Y. Kim, Y B. Kang, Y J. Park

The phase equilibria in the Al2O3–TiOx system were investigated in wide ranges of temperature and oxygen partial pressure: 1300~1600°C and 10-16.6~10-8 atm, respectively. The equilibrium phases and their compositions were identified using X-ray diffraction (XRD) and electron probe microanalysis (EPMA), respectively. Most noticeably, a wide range of pseudobrookite solid solution was found in equilibrium with almost pure alumina. At each temperature, the cationic ratio expressed as RTi = nTi/(nAl + nTi)) of the pseudobrookite solid solution showed a noteworthy dependency on the oxygen partial pressure. This resulted in the formation of a broad range of pseudobrookite solid solutions, ranging from Al2TiO5 (RTi = 1/3) to Ti3O5 (RTi = 1.0). Complete miscibility within the pseudobrookite solid solution was observed at 1600°C, with only a minor miscibility gap becoming evident below 1500°C. Based on the results obtained in the present study, the behaviours of Al2TiO5 pseudobrookite have implications in two key domains: (1) understanding changes in the physical properties of the materials, and (2) elucidating the evolution of Al–Ti complex oxide inclusions in liquid steel which can deteriorate the steel cleanliness.

Aug 21, 2024

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 Roland C. Walker

Traditional headed rebar has existed in the mining industry as a ground support product for many years. The head of a rebar bolt is most commonly produced by hot upset die forging. Upset die forging produces a rugged, simple head that performs well. Certain elements of the head must comply with regulatory standards, such as ASTM F432-95, which offers a standard test procedure to ensure quality of the product. The head style produced by all major manufacturers has been optimized to reduce manufacturing costs, provide greater miner safety and provide an excellent performing product. Observations were made in some mines of heads failing under in-situ loading. These observations could not be replicated according to the ASTM testing method. This paper highlights the problem and how a solution was developed. The development includes pictures of in-situ failures from the underground operations, laboratory replication tests indicating how this loading occurs, and then the use of this calibrated test method to validate the new design created.

Jan 1, 2009

By Adriano Alex de Almeida

Dois aços de grão não orientado com 2,45 e 3,3 %Si com 7 amostras para cada liga, foram estudados para compreensão do efeito do teor de silício nas perdas histeréticas. As amostras foram recozidas com diferentes temperaturas de recozimento final, resultando em diferentes tamanhos de grão. As perdas histeréticas e B50 foram medidos. Os resultados de B50 mostraram que não houve variação de textura entre as ligas com diferentes %Si. Por fim, os resultados não mostraram variações da energia dissipada pela perda histerética com adição de %Si.

Aug 7, 2018

By Kimio Itagaki

The distribution ratios of Ag, Pb, As, Sb and Bi for the Cu2S-FeS or Ni3S2-FeS matte / FeOx SiO2, FeOx-SiO2-CaO or FeOx-CaO slag equilibration in a MgO crucible were determined experimentally at 1523~1573K under controlled partial pressures of S2 and O2 at given PSO2 of 10.1, 50.7 and 101.3 kPa (0.1, 0.5 and 1 atm) and be observed dependency of distribution ratio on the matte grade, SO2 pressure and slag basicity were analyzed on the basis of thermodynamics,

Jan 1, 2003

By F. N. Rhines, W. S. Pellini

In many of the otherwise well established alloy phase diagrams the solidus curves (temperatures at which liquid first appears upon melting) have not been located accurately, chiefly because the experimental techniques that have been most popular for determining solidus temperatures have been both cumbersome and subject to large errors. C. E. Homer and H. Plummerl have described a sensitive and at the same time a very simple technique for locating the solidus curves in a number of alloys of tin. Their method consists simply in noting the temperature at which a specimen of the alloy ruptures under the influence of a light bending force. Although this method is not new, it has been little used for this purpose in the past; nevertheless, it appears so attractive in its possibilities of speed, simplicity, and precision that the investigations presently to be described were undertaken to verify its merits. The redetermination of the solidus and eutectic temperatures of the lead-antimony system was employed as a medium of experimentation. New values obtained in this way are believcd to be sufficiently precise to warrant a revision of the currently accepted lead-antimony phase diagram (Fig. I). Determinations of the solidus of the lead-rich lead-antimony alloy series have been published by X. S. Dean2 and by E. E. Schumacher and F. C. Nix. Their points are represented in Fig. I. In their work the solidus was not located at antimony collcentrations greater than 2 per cent; the curve was presumed to meet the eutectic horizontal at an antimony concentration of about 2.5 per cent. In the present studies the solidus has been traced to 3.5 per cent, where the eutectic horizontal is intersected (Table I and Fig. I). Within the range investigated by Dean and by Schumacher and Nix the agreement with their values is good. H. Seltz and B. De Witt,4 on the basis of activity measurements, have calculated that the intersection of the solidus and the eutectic reaction horizontal should lie at 3.86 per cent of antimony. The following determinations of the eutectic temperature have been reported: Roland-Gosselin,5 228°C.; Ewen,6 228OC.; J. E. Stead,7 24g°C.; Campbell,8 228°C.; W. Gontermann,9 245' to 252°C.; R. Loebe,lo 245°C.; E. Heyn and 0. Bauer,ll 245°C.; H. Endo,12 250°C.; R. S. Dean,= 247' to 258°C.; E. Abel, O. Redlich, and J. Adier,13 245°C.; W. Broniewski and L. Sliwowski,14 250' to 252°C.; H. Seltz and B. De Witt,4 25o°C. A temperature of 247°C. appears to have been generally accepted in recent years; it is the value most frequently obtained by the method of cooling curves. Values below 247°C. have usually been obtained by inferior cooling-curve techniques; those above 250°C., by the method of heating

Jan 1, 1943

By W. S. Pellini, F. N. Rhines

In many of the otherwise well established alloy phase diagrams the solidus curves (temperatures at which liquid first appears upon melting) have not been located accurately, chiefly because the experimental techniques that have been most popular for determining solidus temperatures have been both cumbersome and subject to large errors. C. E. Homer and H. Plummerl have described a sensitive and at the same time a very simple technique for locating the solidus curves in a number of alloys of tin. Their method consists simply in noting the temperature at which a specimen of the alloy ruptures under the influence of a light bending force. Although this method is not new, it has been little used for this purpose in the past; nevertheless, it appears so attractive in its possibilities of speed, simplicity, and precision that the investigations presently to be described were undertaken to verify its merits. The redetermination of the solidus and eutectic temperatures of the lead-antimony system was employed as a medium of experimentation. New values obtained in this way are believcd to be sufficiently precise to warrant a revision of the currently accepted lead-antimony phase diagram (Fig. I). Determinations of the solidus of the lead-rich lead-antimony alloy series have been published by X. S. Dean2 and by E. E. Schumacher and F. C. Nix. Their points are represented in Fig. I. In their work the solidus was not located at antimony collcentrations greater than 2 per cent; the curve was presumed to meet the eutectic horizontal at an antimony concentration of about 2.5 per cent. In the present studies the solidus has been traced to 3.5 per cent, where the eutectic horizontal is intersected (Table I and Fig. I). Within the range investigated by Dean and by Schumacher and Nix the agreement with their values is good. H. Seltz and B. De Witt,4 on the basis of activity measurements, have calculated that the intersection of the solidus and the eutectic reaction horizontal should lie at 3.86 per cent of antimony. The following determinations of the eutectic temperature have been reported: Roland-Gosselin,5 228°C.; Ewen,6 228OC.; J. E. Stead,7 24g°C.; Campbell,8 228°C.; W. Gontermann,9 245' to 252°C.; R. Loebe,lo 245°C.; E. Heyn and 0. Bauer,ll 245°C.; H. Endo,12 250°C.; R. S. Dean,= 247' to 258°C.; E. Abel, O. Redlich, and J. Adier,13 245°C.; W. Broniewski and L. Sliwowski,14 250' to 252°C.; H. Seltz and B. De Witt,4 25o°C. A temperature of 247°C. appears to have been generally accepted in recent years; it is the value most frequently obtained by the method of cooling curves. Values below 247°C. have usually been obtained by inferior cooling-curve techniques; those above 250°C., by the method of heating

Jan 1, 1943

By R. M. Asimow

Both smith1 and wells2 have shown that the dif-fusivity of carbon in austenite increases rapidly with increasing carbon concentration. Smith has shown, in addition, that part but not all of this increase can be attributed to the concentration dependence of the activity coefficient of carbon in austenite. From the work of Eshelby', it is known that, because of the image displacements, there is a uniform dilatation of the material in a body containing random centers of dilatation. It is thus tempting to explain the enhanced diffusivity as resulting from this apparent negative pressure caused by the interstitial carbon atoms.* That is, the activation free energy for diffusion is not directly a function of concentration if we consider that the alloy is subjected to a concentration-dependent pressure. To proceed with a quantitative solution, it is necessary to determine the activation volume AV for the diffusion process. An exact calculation of AV is quite a difficult problem and does not appear to have been solved as yet. A simpler procedure is to use the semiempirical, macroscopic theory of seyes' which relates the activation free energy AG to AV. Keyes has shown that for many types of diffusion processes the following relationship is valid Where p is the Gruneisen constant and x the compressibility. This relationship is based on the assumption that AG can be identified with strain-energy terms. In general there will also be contributions to AG due to a change in the energy of the valence electrons of the metal; thus the relation must be considered largely empirical. Surprisingly, for self-diffusion where it is well-known that the electronic contribution is quite important,' the Keyes relation works quite well for many systems. For interstitial diffusion where it might be expected that the relationship is on a firmer theoretical basis, the limited experimental data available is not in particularly good agreement as can be seen from Table I. However, it must be remembered that besides the uncertain basis of the Keyes formula there is considerable uncertainty in some of the experimental values of AV. The only real justification for using the Keyes formula in the present analysis is that it gives a result which satisfactorily solves the problem at hand and, further, there are no more reliable procedures for calculating AV available. The coefficient 3 in Eq. [I] is determined such that the room-temperature value for x is to be used. The activation entropy AS is estimated as 8.95 x 10"3 kcal per OK mole using the values in Table I1 and the Zener" relation AS = PAHIT, where p is a dimensionless thermal coefficient of Young's modulus which is to be evaluated at low values of T/T,, aH is the activation enthalpy, and T, is the melting temperature of the alloy. The resulting value of AG at 1000°C is 25.6 kcal per mole. The Gruneisen constant (p = 3cup/XC,), where p is the density, is evaluated from the room-temperature data in Table I1 after calculating C, from the relation. A value of p = 8.32 g per cu cm based on the value of a. in Table I is used. The result is C, = 5.0 x lo6 erg per g, H = 2.32, and AV = 3.41 cu cm per mole at 1000°C and infinite carbon dilution. It is assumed that the activation volume is not a function of carbon concentration. The theory could be refined to consider AV a function of concentration, but due to the uncertainties in the parameters there seems little justification for this. Carbon dissolved in austenite forms a nonideal solid solution, so that in writing an equation for. the diffusivity of carbon it is necessary to take into account the change in activity coefficient with concentration. The resulting equation is16

Jan 1, 1964

By J. E. Dutrizac, Alba Sunyer

The factors affecting the precipitation of arsenic-free alunite (KAl3(SO4)2(OH)6) were investigated in a series of laboratory experiments. Although the amount of alunite precipitated increased with increasing retention time, temperature, solution pH and the concentrations of Al(SO4)1.5 or K2SO4, the composition of the products remained nearly constant. The preferred conditions identified for the precipitation of arsenic-free alunite were then used to assess the behaviour As(III) and As(V) during alunite precipitation at 98°C. Increasing additions of As(III), as NaAsO2 or As2O3, resulted in a slight increase in the amount of precipitate formed at pH 2.80. However, X-ray diffraction analysis showed all the precipitates to be alunite, and <0.2% As(III) was detected in the products. In contrast, increasing additions of As(V), as KH2AsO4 or As2O5, resulted in significant increases in the amount of precipitate formed at pH 2.80 or 3.00. Furthermore, the arsenate (AsO43-) contents of the precipitates increased up to 15%, and the sulphate contents decreased, as the As(V) concentration of the synthesis solution increased from 0 to 9 g/L. X-ray diffraction analysis of the products detected only alunite, but there was a progressive expansion of the alunite cell with increasing arsenate content. The implication is that arsenate substitutes for sulphate in the alunite structure. Preliminary observations on the environmental stability of the arsenate-bearing alunite using the TCLP protocol gave solubilities <0.4 mg/L from a precipitate containing 8.5% AsO4 and 7.8 mg/L from a product containing 19.5% AsO4. Thus, it appears that alunites containing less than -10% AsO4 would be an acceptable vehicle for the disposal of arsenic from hydrometallurgical processing solutions.

Jan 1, 2011

By O. D. Gonzalez

Existing measurements for the steady-state permeation of hydrogen in a iron above 100°C have been examined for contribution of determinate errors. The analysis leads to a recommended equation for the permeability of hydrogen in a iron: o= (2.9 ±0.5) x 10-3 exp - (8400 ± 400)/RT cu cm (ntp H2) cm-1 sec-1 atm-1/2 THE permeability of a iron to hydrogen has been the subject of numerous investigations over the past 40 years, and at present there are thirteen sets of published results for the rate of steady-state permeation of hydrogen in a iron above 100°C. The numerical values in each set of results are entirely self-consis-tent, but the spread among the sets is too large to be attributed solely to experimental error, i.e., to error other than in the specimen itself. Several reasons have been advanced to explain the disparities, but to date the relative importance of experimental inaccuracy to the spread remains uncertain. The purpose of this report is to examine in detail the sources of determinate errors inherent in the experiments and to assess as far as possible the contribution of the errors to the results. The ultimate goal is the selection of values for the permeability and heat of permeation most nearly representative of hydrogen in a iron. The analysis is limited to those experiments in which the permeation rate was observed at steady state—a condition in which traps for hydrogen within the metal are filled to a fixed level15 so that the trapping mechanism is not reflected in the rate of passage of the gas. Furthermore only data are examined in which surface processes are judged to have little or no influence on the flow. It is hoped with these restrictions to obtain values of the permeability and the heat of permeation which will be as closely related as possible to the mechanism of lattice diffusion. I) DEFINITION OF TERMS; UNITS In this report the data for permeation are given in terms of a coefficient oj permeability, ?, which is defined by the equation: jt=?A/?x{p1/2-po1/2) [1] where jt is the total flow of gas normal to the surface of a membrane of planar geometry, e.g., a disc, of area A and thickness ?x; pi and po are the pressures in the input and output sides, respectively. For flow radial to the walls of a membrane of cylindrical geometry, e.g., a tube, the corresponding equation is: where 1 is the length of the cylinder, and ri and ro are the inner and outer radii, respectively. The flux normal to the surface is given by Fick&apos;s law: j= -D(dc/dx) [3] At steady state the concentration gradient will be constant, and integration of Eq. [3] gives for the total flow through a disc of area A and thickness Ax: h =-DA(co - ci) [4] where c, and ci are the concentrations of solute at the output and input surfaces, respectively. When surface control is absent, co and ci are given by Sievert&apos;s law c = Kp1/2, and substitution therewith into Eq. [4] gives directly Eq. [I] where ? = DK. Integration of Fick&apos;s Eq. [3] in cylindrical coordinates will give Eq. [2] where again ? = DK and is thus shown to be independent of geometry (provided that surface control is negligible). The coefficient of permeability, or simply the permeability,* must be expressed in proper units. In *The term permeability will refer in this report always to the coefficient defined above; permeation will be used to specify the general phenomenon of gas passage through a membrane. this report ? will be expressed in the units of cu cm (ntp H2) cm-1 sec-1 atm-1/2. The variations of D and K with temperature are given by D = Do exp(-Ea/RT) and K = KO exp(-?Hs/RT) where E, is the activation energy for diffusion and AH, the heat of solution, each usually expressed in calories per mole of solute. The variation of permeability with temperature will thus be given (for conditions where surface control is negligible) by ? = ?o exp(-?Hp/RT) where ?0 = DoKo and ?Hp = Ea + ?Hs. The units of ?0 are the same as those of 6, and??Hp will be expressed in calories per mole H. 11) SUMMARY OF PERMEABILITY RESULTS Table I gives the values reported to date for the permeability of H2 in a iron in terms of ?o and ?Hp. Except where noted the parameters listed were taken directly from the numbers reported by the various investigators with only a change in units. The temperature limits within which the listed ?o and ?Hp hold are given in column 7; the limits marked in parentheses in this column indicate the entire temperature range covered in each investigation. The listed values of ?o and ?Hp are those giving a linear plot of ln? against T-1 at the higher temperatures in each set of measurements, and thus presumably represent the case for which surface control was negligible. Column 6 gives values of 9 at a representative tem-

Jan 1, 1970