Efeitos das microestruturas bainíticas e multifásicas nas propriedades mecânicas de um aço AISI 4340

Coordenação de Aperfeiçoamento de Pessoal de Nível Superior (CAPES)

Aplicação do processo laser CO2 de soldagem em aço ARBL na fabricação de rotores para máquinas elétricas

Pós-graduação em Engenharia Mecânica - FEG

A influência da temperatura de pré-aquecimento e tecimento na microestrutura e propriedades mecânicas na soldagem MIG/MAG robotizada de aços SAE 8620 com ABNT LN28

Coordenação de Aperfeiçoamento de Pessoal de Nível Superior (CAPES)

Influência do tempo de imersão em solução aquosa contendo H2S sobre a tenacidade de tubo API 5L X65 sour avaliada a partir de ensaio Charpy

Com o decorrer dos anos o consumo de petróleo e seus derivados aumentou significativamente e com isso houve a necessidade de se investir em pesquisas para descobertas de novas jazidas de petróleo como o pré-sal. Porém, não apenas a localização dessas jazidas deve ser estudada, mas, também, sua forma de exploração. Essa exploração e extração, na maioria das vezes, se dão em ambientes altamente corrosivos e o transporte do produto extraído é realizado através de tubulações de aço de alta resistência e baixa liga (ARBL). Aços ARBL expostos a ambientes contendo H2S e CO2 (sour gas) sofrem corrosão generalizada que promovem a entrada de hidrogênio atômico no metal, podendo diminuir sua tenacidade e causar falha induzida pela presença de hidrogênio (Hydrogen Induced Cracking HIC), gerando falhas graves no material. Tais falhas podem ser desastrosas para o meio ambiente e para a sociedade. O objetivo deste trabalho é estudar a tenacidade, utilizando ensaio Charpy, de um tubo API 5L X65 sour após diferentes tempos de imersão em uma solução saturada com H2S. O eletrólito empregado foi a solução A (ácido acético contendo cloreto de sódio) da norma NACE TM0284 (2011), fazendo-se desaeração com injeção de N2, seguida de injeções de H2S. Os materiais foram submetidos a: ensaios de resistência a HIC segundo a norma NACE TM0284 (2011) e exames em microscópio óptico e eletrônico de varredura para caracterização microestrutural, de inclusões e trincas. As amostras foram submetidas a imersão em solução A durante 96h e 360h, sendo que, após doze dias do término da imersão, foram realizados os ensaios Charpy e exames fractográficos. Foram aplicados dois métodos: o de energia absorvida e o da expansão lateral, conforme recomendações da norma ASTM E23 (2012). As curvas obtidas, em função da temperatura de impacto, foram ajustadas pelo método da tangente hiperbólica. Esses procedimentos foram realizados nas duas seções do tubo (transversal e longitudinal) e permitiram a obtenção dos seguintes parâmetros: energias absorvidas e expansão lateral nos patamares superior e inferior e temperaturas de transição dúctil-frágil (TTDF) em suas diferentes definições, ou seja, TTDFEA, TTDFEA-DN, TTDFEA-FN, TTDFEL, TTDFEL-DN e TTDFEL-FN (identificação no item Lista de Abreviaturas e Siglas). No exame fractográfico observou-se que o material comportou-se conforme o previsto, ou seja, em temperaturas mais altas ocorreu fratura dúctil, em temperaturas próximas a TTDF obteve-se fratura mista e nas temperaturas mais baixas observou-se o aparecimento de fratura frágil. Os resultados mostraram que quanto maior o tempo de imersão na solução A, menor é a energia absorvida e a expansão lateral no patamar superior, o que pode ser explicado pelo (esperado) aumento do teor de hidrogênio em solução sólida com o tempo de imersão. Por sua vez, os resultados mostraram que há tendência à diminuição da temperatura de transição dúctil-frágil com o aumento do tempo de imersão, particularmente, as TTDFEA-DN e TTDFEL-DN das duas seções do tubo (longitudinal e transversal). Esse comportamento controverso, que pode ser denominado de tenacificação com o decorrer do tempo de imersão na solução A, foi explicado pelo aparecimento de trincas secundárias durante o impacto (Charpy). Isso indica uma limitação do ensaio Charpy para a avaliação precisa de materiais hidrogenados.

Corrosion resistance of steel with hot-dipped galvanized zinc and zinc alloy coatings in seawater

Hot-dipped galvanized zinc and zinc alloy coatings were used as the hot-dipped low alloy zinc coatings (aluminum content less than protective metallic coatings for steel structures in seawater in Chi- or equal to 10 wt%) is equal to or even lower than that of the pure na. Corrosion of the two coatings immersed in sea water in Qingdao zinc sheet, while the performance of the hot-dipped high alloy zinc and Xiamen for 6 years were introduced and analyzed, which pro-coatings is higher than that of the pure zinc sheet. The hot-dipped vides a basis for further development and applications of these coat- high alloy zinc coatings can be further developed for optimal tings in China. Tests proved that the anti-corrosion performance of formance in the future.

Light and electron microscopy of microstructure and fractography of an ultrahigh-strength martensitic steel

Microstructure, tensile properties and fractography have been examined in the oil-quenched samples of a low-alloy ultrahigh strength 4340 steel. Intergranular fracture was revealed to locate at the fracture origin. However, neither the quenched Charpy V-notched impact samples nor the tempered tensile samples showed such intergranular fracture behavior. The effects of loading rate and precipitation are discussed.

FeNbP in ultra-low carbon Nb-added steel containing high P

Precipitation of FeTiP is reported to occur in Ti-added IF steels containing high P during thermomechanical processing. An ultra-low carbon (ULC) Nb-added steel ingot containing a higher P content (< 0.8 wt-%) was produced via aluminothermic reduction of Fe2O3 followed by double electron beam melting (EBM). FeNbP coarse precipitates were observed in the as-cast microstructure. After soaking at 1050C for 1 h, the plate was hot rolled from 31 mm down to 7 mm in thickness (total reduction of 77%). During cold rolling of these hot bands we observed embrittlement. We believe that this embrittlement can be attributed to the presence of the FeNbP precipitates. Light optical and scanning electron microscopy (SEM/EDS) were used to characterize the microstructure of this ULC steel. (C) 2000 Elsevier B.V. All rights reserved.

Second Phase Precipitation in Ultrafine-grained Ferrite Steel

Fundação de Amparo à Pesquisa do Estado de São Paulo (FAPESP)

Defects in steel investment castings

A general investigation was performed, in an industrial environment, of the major types of defect specific to investment castings in steel. As a result of this work three types of metallurgical defect were selected for further study. In the first of these, defects in austenitic stainless steel castings were found to result from deoxidation by-products. As a result of metallographic investigation and the statistical analysis of experimental data, evidence was found to support the hypothesis that the other two classes of defects - in martensite stainless and low alloy steels -both resulted from internal or grain boundary oxidation of the chromium alloy constituent This was often found to be followed by reaction between the metal oxides and the ceramic mould material. On the basis of this study, proposals are made for a more fundamental investigation of the mechanisms involved and interim suggestions are given for methods of ameliorating the effect in an industrial situation.

Flexural–torsional buckling behaviour and design of cold-formed steel compression members at elevated temperatures

Current design rules for the member capacities of cold-formed steel columns are based on the same non-dimensional strength curve for both fixed and pinned-ended columns at ambient temperature. This research has investigated the accuracy of using current ambient temperature design rules in Australia/New Zealand (AS/NZS 4600), American (AISI S100) and European (Eurocode 3 Part 1.3) standards in determining the flexural–torsional buckling capacities of cold-formed steel columns at uniform elevated temperatures using appropriately reduced mechanical properties. It was found that these design rules accurately predicted the member capacities of pin ended lipped channel columns undergoing flexural torsional buckling at elevated temperatures. However, for fixed ended columns with warping fixity undergoing flexural–torsional buckling, the current design rules significantly underestimated the column capacities as they disregard the beneficial effect of warping fixity. This paper has therefore recommended the use of improved design rules developed for ambient temperature conditions to predict the axial compression capacities of fixed ended columns subject to flexural–torsional buckling at elevated temperatures within AS/NZS 4600 and AISI S100 design provisions. The accuracy of the proposed fire design rules was verified using finite element analysis and test results of cold-formed lipped channel columns at elevated temperatures except for low strength steel columns with intermediate slenderness whose behaviour was influenced by the increased nonlinearity in the stress–strain curves at elevated temperatures. Further research is required to include these effects within AS/NZS 4600 and AISI S100 design rules. However, Eurocode 3 Part 1.3 design rules can be used for this purpose by using suitable buckling curves as recommended in this paper.

Experimental Study of crack propagation in carbon steel using acoustic emission

Acoustic emission technique has become a significant and powerful structural health monitoring tool for structures. Researches to date have been done on crack location, fatigue crack propagation in materials and severity assessment of failure using acoustic emission technique. Determining severity of failure in steel structures using acoustic emission technique is still a challenge to accurately determine the relationship between the severity of crack propagation and acoustic emission activities. In this study three point bending test on low carbon steel samples along with acoustic emission technique have been used to determine crack propagation and severity. A notch is introduced at the tension face of the loading point to the samples to initiate the crack. The results show that the percentage of load drop of the steel specimen has a reciprocal relationship with the crack opening i.e. crack opening zones are influenced by the loading rate. In post yielding region, common acoustic emission signal parameters such as, signal strength, energy and amplitudes are found to be higher than those at pre-yielding and at yielding.

A solution framework for scheduling a BPM with non-identical job dimensions

A Batch Processing Machine (BPM) is one which processes a number of jobs simultaneously as a batch with common beginning and ending times. Also, a BPM, once started cannot be interrupted in between (Pre-emption not allowed). This research is motivated by a BPM in steel casting industry. There are three main stages in any steel casting industry viz., pre-casting stage, casting stage and post-casting stage. A quick overview of the entire process, is shown in Figure 1. There are two BPMs : (1) Melting furnace in the pre-casting stage and (2) Heat Treatment Furnace (HTF) in the post casting stage of steel casting manufacturing process. This study focuses on scheduling the latter, namely HTF. Heat-treatment operation is one of the most important stages of steel casting industries. It determines the final properties that enable components to perform under demanding service conditions such as large mechanical load, high temperature and anti-corrosive processing. In general, different types of castings have to undergo more than one type of heat-treatment operations, where the total heat-treatment processing times change. To have a better control, castings are primarily classified into a number of job-families based on the alloy type such as low-alloy castings and high alloy castings. For technical reasons such as type of alloy, temperature level and the expected combination of heat-treatment operations, the castings from different families can not be processed together in the same batch.

Laboratory studies on ball wear in the grinding of a chalcopyrite ore

Wear of high carbon low alloy (HCLA) cast steel balls during the grinding of a chalcopyrite ore was evaluated under different experimental conditions. The role of oxygen in enhancing ball wear during wet finding is brought out. The influence of pH on ball wear was also examined from the view point of acid production during grinding and reactivity of sulphides. Contributions from corrosion and abrasion towards ball wear are quantified in terms of ball wear rates as a function of time, particle size and gaseous atmosphere in the mill.

Studies on grinding media wear and its effect on flotation of ferrugenous phosphate ore

Marked ball grinding rests were carried out in the laboratory with a low grade phosphate ore under different experimental conditions. Two types of balls were used, namely high carbon low alloy (HCLA) cast steel and high chrome cast iron. Results of marked ball grinding tests indicated that ball wear increased with time and showed a sharp increase for wet grinding over dry grinding. Ball wear under wet grinding conditions was also influenced by the gaseous atmosphere in the mill. The grinding ball materials could be arranged in the following order with respect to their overall wear resistance: High chrome cast iron > HCLA cast steel balls Methods to minimize ball wear through control of mill atmosphere and addition of flotation reagents are discussed. Effect of grinding media and additions of flotation reagents during grinding on phosphate ore flotation are also discussed. (C) 1999 Elsevier Science Ltd. All rights reserved.

Mechanism of enhanced corrosion of alumina graphite refractories near slag/metal interface

All refractories show enhanced corrosion near the slag/metal interface due to Marangoni and convective flows. However, in the case of oxide refractories containing graphite flakes, corrosion is severe due to periodic oscillations in the contact angle at the slag/metal interface, resulting in cyclic dissolution of oxide and graphite into the slag and metal, respectively. Alumina--graphite (AG) refractories should be used only where they are not in simultaneous contact with slag (flux) and low carbon steel.