There has been much confusion evident in the literature in terms of the influence of impurity elements on grain refinement of magnesium alloys. This thesis addresses how impurity elements such as iron, manganese, carbon and beryllium affect grain refinement in magnesium alloys. The thesis starts with an investigation into the effect of the uptake of iron on grain refinement of Mg-Zr alloys. The highly detrimental influence of the uptake of iron on grain refinement in Mg-Zr alloys has been confirmed. The gradual loss of grain refinement of Mg-Zr alloys partly arises from the consumption of Zr by the formation of Fe2Zr via the reaction between soluble Zr and Fe picked up from mild steel crucibles. (Settling of undissolved Zr particles also partly attributes to the gradual loss of grain refinement.) The morphological evolution of Zr-rich cores from circular to rosette-like has been reported here for the first time. In contrast to the detrimental effect in Mg-Zr alloys, a positive effect of iron has been observed in grain refinement of Mg-Al based alloys. The addition of iron in the form of anhydrous FeCl3 produces significant grain refinement of high-purity Mg-Al alloys. Obvious grain refinement was also achieved through the uptake of iron from steel crucible surfaces; however, the addition of Fe powder in the form of an ALTABTM Fe75 powder compact (75%Fe, 15%Al and 10% Na-free flux) did not give rise to grain refinement. The results obtained from both the grain refinement tests conducted in aluminium titanite crucibles and an ultra-low carbon 316L stainless crucible indicate that the grain refinement of Mg-Al alloys by iron inoculation has little to do with the Al4C3 hypothesis. The nucleant particles have been clarified to be Fe- and Al-rich intermetallics. The effect of manganese on the grain refinement of high purity Mg-Al based alloys and commercially available AZ31 alloys has been investigated using an Al-60%Mn master alloy splatter at 730 „aC in aluminium titanite crucibles. Grain refinement was readily achievable in these alloys. Electron microprobe analyses revealed that prior to the addition of extra manganese the majority of the intermetallic particles found in AZ31 are of the Al8Mn5 type. However, after the addition of extra manganese in the range of 0.1% to 1.0%, the predominant group of intermetallic particles changed to the metastable AlMn type. This leads to a hypothesis that the metastable AlMn intermetallic particles are more effective than Al8Mn5 as nucleation sites for magnesium grains. The hypothesis was supported by the observation that a long period of holding at 730 „aC led to an increase in grain size, due probably to the transformation of the metastable AlMn to the stable Al8Mn5. Native grain refinement in magnesium alloys has been clarified. Based on the fact that native grain refinement is an exclusive feature of high purity Mg-Al alloys, it is hypothesized that Al4C3 particles act as nucleation centres. This is also the mechanism of carbon grain refinement of Mg-Al alloys. A trace of beryllium leads to dramatic grain coarsening in Mg-Al alloys at normal cooling rates. Apart from Mg-Al alloys, a trace of beryllium also causes considerable grain coarsening in Mg-Zn, Mg-Ca, Mg-Ce, Mg-Nd and also hinders grain refinement of magnesium alloys by Zr. Modelling grain refinement to predict the final grain size has been made on the basis of understanding of existing models. The modified model has resolved a fundamental gap in the relative grain size model using a more universal expression of solute concentration in the liquid.

Due to recent legislation aimed at reducing carbon emissions into the environment through weight reduction, the automotive and aerospace industries are using light alloys such as aluminium silicon (Al–Si) and aluminium zirconium (Al–Zr) instead of steel due to their excellent mechanical properties and low weight to strength ratio. In order to further improve mechanical and metallurgical properties in these alloys, grain refinement is usually used in industry. However, the current and most widely used grain refiner Al–5Ti–B is unable to refine Al–Si alloys with silicon content greater than 3 wt.%., and Al–Zr alloys due to poisoning of the refiner by silicon and zirconium. The Al–5Ti–B refiner also contains larger Al3Ti particles and agglomerates of TiB2 which affect its efficiency and suitability in industrial applications where thin sheets are required. In this study, a new technique which improves the microstructure and efficiency of the Al–5Ti–B refiner has been developed. This involves the reaction of potassium tetrafluoroborate (KBF4) and potassium hexafluorotitanate (K2TiF6) salts at shorter reaction time before ultrasonic processing during solidification. This leads to the formation of a new Al3Ti morphology and de-agglomeration of TiB2 particles which enhances its grain refinement efficiency by 20%. Secondly, through phase diagram analysis of Al grain refining systems and crystallography studies, it was observed that Al3Ti and Al3Nb display similar lattice parameters with atomic misfit of 4.2% and would undergo a peritectic reaction with α-Al at low contact angles. Based on this, and using the duplex nucleation theory and poisoning by Si and Zr, a new quaternary grain refiner containing aluminium, titanium, niobium and boron (Al–4Ti–Nb–B) has been developed. This novel grain refiner has been found to be efficient in Al–Si alloys and Al–Zr, both at laboratory and industrial scales, and to improve the mechanical properties of the alloys despite the presence of Ti in the alloy. It was observed that the addition of Nb to an Al–Ti–B system leads to the formation of solid solution phases of Al3Ti1-xNbx, Al3Nb1-xTx, and (Ti1-xNbx)B2 which prevents poisoning by Si and Zr. Experimental simulations showed that Al3Nb1-xSix rather than Ti(Al1-xSix)3 are formed in Al–Si alloys, and Al3(Ti1-xNbx) and (Al3Ti1-xNbx)B2 phases are formed in Al–Zr alloys rather than Al3(Zrx,Ti1-x), B2(Zrx,Ti1-x) or ZrB2 phases. A new grain refining mechanism, ‘The Quad Nucleation Theory’ based on four nucleation events in Al–4Ti–Nb–B has been proposed. Other newly developed quaternary and ternary novel grain refiners capable of refining aluminium silicon alloys are also presented in this thesis. This includes a novel method of refining Al–Si alloys using phosphorus and niobium.

Student Number: 9400670E School of Chemical and Metallurgical Engineering Faculty of Engineering and Built Environment / The selection of a particular steel grade for an application is extremely important to ensure that the final components have a long serviceable life. The chemical compositions of the steels are critical, and minor changes in chemistry can make substantial differences. Aluminium and vanadium are used in heat treatable steels as grain refining agents. These elements affect the properties of the steels. Two steels with identical chemical composition except for the aluminium and vanadium additions were comparatively tested to determine the better steel for a particular automotive coil spring. The tests included mechanical testing and on site fatigue testing. Fatigue resistance is extremely important especially for automotive coil springs. The mechanical properties revealed superior tensile strength in the vanadium grain refined spring steel while the aluminium grain refined spring steel had superior ductility and fatigue resistance.

The industrial use of recycled aluminium is greatly limited by the degraded mechanical properties due to the increased impurities. Fe, one of the common impurity content in Al alloys, is difficult to eliminate once introduced into aluminium during primary production or recycling processes. Due to the low solid solubility of Fe in Al, the formation of Fe-rich intermetallic compounds (Fe-IMCs) is inevitable, which is one of the main causes for the deterioration of mechanical properties in various cast Al alloys. In order to obtain desirable mechanical properties of recycled Al alloys, modification and refinement of the Fe-IMCs are urgently required as the compact and refined morphologies of such intermetallics are generally non detrimental to Al alloy's performance. However, manipulating the solidification behaviour of the Fe-IMCs phases, including nucleation and growth, is very challenging because of the inherently more difficult heterogeneous nucleation of the Fe-IMCs compared with that of a pure metal or a solid solution; and the strong growth anisotropy. Limited understanding on mechanisms of nucleation and growth of the multicomponent Fe-IMCs is available in the literature. The aim of this study is to gain a deeper understanding on the heterogeneous nucleation and growth behaviour of Fe-IMCs in various Al alloys. The nucleation and growth of both primary and eutectic Fe-IMCs have been investigated during various solidification conditions including a number of different cooling rates and casting temperatures. Based on the experimental results of the solidification of several ternary and quaternary alloys, effect of Mg on the solidification behaviour of Fe-IMCs was investigated. Further the surface modified TiB2 particles were used to enhance the heterogeneous nucleation of Fe-IMCs in order to refine the Fe-IMCs particles. The dominant Fe-IMC in Al-5Mg-2Si-1.2Fe-0.7Mn alloy is identified, using transmission electron microscopy (TEM), as α-AlFeMnSi with a body centred cubic (BCC) lattice structure and lattice parameter of 1.256nm. In the current alloy system, the nucleation of primary α-AlFeMnSi occur at lower cooling rate (≤0.8K/s) when required nucleation undercooling is reached, as the slower cooling rate allows longer diffusion time for the solute to form a stable nucleation embryo. When casting with 20K superheat, the size of primary α-AlFeMnSi increases gradually from 24.5±3.1μm (870K/s) to 251.3±75.3μm (0.02K/s) and the size of α-AlFeMnSi eutectic increased gradually from 102.0μm (870K/s) to 623.3μm (0.02K/s). The Fe and Mn concentration in α-AlFeMnSi appears to reduce with the increased cooling rate due to the relatively insufficient solute supply when solute concentration is low (1.2wt.% Fe and 0.7wt.% Mn). Microstructure observation reveals that the {011} plane, especially on <111> orientation, is the preferred growth orientation of BCC primary α-AlFeMnSi, resulting in rhombic dodecahedral in 3D. The eutectic α-AlFeMnSi, prefers to initiate on the primary α-AlFeMnSi. In addition to the substantial nucleation undercooling, the research revealed that the nucleation of primary α-AlFeMnSi also rely on the local solute concentration and the solute diffusion. Compared with α-Al, the growth of α-AlFeMnSi is less sensitive to the cooling rate changes due to the complexities in multi-components interaction and different diffusion efficiency of different elements. The addition of Mg to Al-1.2Fe-0.7Mn and Al-2Si-1.2Fe-0.7Mn alloys was found to lead to a morphology change of Fe-IMCs. Al6(Fe,Mn), the predominant Fe-IMC in the Al-1.2Fe-0.7Mn-xMg alloy, changed from needle morphology to interconnected lamellar morphology when Mg composition increased from 0.004wt.% to 6.04wt%. A Mg-rich layer at about 5-20nm in thickness was commonly observed on the Fe-IMC/α-Al interface in the alloys with Mg content. The eutectic lamellar spacing for Al6(Fe,Mn) increases from 1.8±0.3μm to 4.5±0.8μm when Mg content increased from 0.004wt.% to 6.04wt.%. In the case of α-Al12(Fe,Mn)3Si, the predominant Fe-IMC in Al-2Si-1.2Fe-0.7Mn-yMg alloys, its lamellar spacing of the eutectic increased from 1.4±0.3μm to 3.25±0.8μm when Mg increased from 0.04wt.% to 5.41wt.%. Owing to the strong anisotropy of the Fe-IMC crystals, the segregation of solute Mg on preferred growth orientation is higher, causing greater growth restriction on this orientation. Consequently, the growth velocity on other orientations becomes relatively more significant. To optimise the morphology of Fe-IMCs in Al alloys, a novel Αl-Ti-B(Fe) grain refiner for Fe-IMCs has been developed to enhance the heterogeneous nucleation of Fe-IMCs. The addition of the novel grain refiner to an Al-5Mg-2Si-1.2Fe-0.7Mn alloy under controlled solidification condition results in a considerable refinement of the primary Fe-IMCs from 251.3±75.3μm to 110.9±45.5μm and from 127.3±36.2μm to 76.5±18.2μm at cooling rates of 0.02K/s and 0.15K/s, respectively. TEM investigations on the refiner reveal a Fe-rich adsorption monolayer in a zigzag fashion on the prismatic planes on the boride particles. This surface modification is beneficial for the heterogeneous nucleation of the Fe-IMCs. Further investigation of the Al alloy with this grain refiner addition revealed that there existed specific orientation relationships (ORs) between TiB2 and Fe-IMCs: (001)[020]Al13Fe4 // (11-20)[10-10]TiB2, and (001)[120]Al13Fe4 ∠6.05˚ (11-20)[10-11]TiB2; (0-11)[100]α-AlFeMnSi // (0001)[-2110]TiB2, and (0-11)[111]α-AlFeMnSi ∠4.5˚ (0001)[10-10]TiB2. The Fe adsorption on substrate particle, the observed ORs between TiB2 and Fe-IMCs, and the refinement of primary α-AlFeMnSi with the addition of modified TiB2 provide evidence of structure templating and composition templating required by heterogeneous nucleation of Fe-IMCs. This research has delivered contribution to the understanding and new approach for optimizing the morphology of Fe-IMCs in the Fe-containing Al alloys. Using the slow cooling rates (≤0.15K/s), the formation compact primary α-AlFeMnSi can be considerably encouraged. With a lower casting temperature, the size and volume fraction of large Chinese-script α-AlFeMnSi can be significantly reduced. With addition of reasonable Mg content the morphology of Fe-IMC can be modified. Particularly, with the addition of the Al-Ti-B(Fe) grain refiner in well-controlled condition, the primary α-AlFeMnSi can be significantly refined. Thus, by implementing these approaches, the optimized Fe-IMC morphology in the microstructure of Fe-containing Al alloy is able to offer promising mechanical performance.

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The system of upper high nickel alloying steel seal ring and lower high nickel alloying steel seal ring, installed in the grooves of turbine, can extend out and fit with the wall of valve cage, resulting in forming a good seal under the pressure. In the project, the failure steel seal ring is considered. This situation had threatened the safety of the whole steam turbine system. The purpose of this study is to identify the failure cause of the steel seal ring used in nuclear steam turbines. New high nickel steel alloy seal ring was compared with the failed seal ring. The dimensions of macroscopic ring with clearly plastic deformation were measured using calipers. Surface morphology of ring was observed by optical microscopy through metallographic analysis. There is a lot of precipitation in the grain boundaries of used seal ring, along with smaller grain size than the new seal ring. To explore the composition of precipitation, scanning electron microscopy (SEM) with energy-dispersive spectrometer (EDS) were used. The results indicated that the concentration of titanium (Ti) and molybdenum (Mo) was higher in the precipitation of used seal ring. At the same time, the hardness and elastic modulus of used seal ring were reduced, measured by nanoindentation test. In-situ SEM tensile testing were used to record and analyze the generation of crack source and crack development under applied load. The reasons of the seal ring failure can be answered because of these experimental results at both macroscopic and microscopic scales. The main reason of the seal ring failure is a combination of long-term stress and elevated temperature during turbine operation. Complex work environment caused recrystallization and recovery, resulting in grain refinement and secondary phase precipitation. Further embodiment, recrystallization and recovery caused the elastic modulus and hardness of used seal ring decrease. Moreover, a lot of secondary phase precipitates appeared at grain boundaries during use. The appearance of secondary phase precipitates become the weakest part of used seal ring. The applied load lead to seal ring failure from the formation of microvoids to microvoids aggregated becoming microcracks until to the appearance of cracks at macroscopic scale. These changes of microscopic structure ultimately reflected in critical plastic deformation of used seal ring.

Magnesium alloys have been extensively used for structural and functional applications due to their low densities. In order to improve the mechanical properties, grain refinement of the microstructures of magnesium alloys has been studied for many years. However, an effective and efficient grain refiner or refinement technique hasn’t been achieved yet, especially for those with aluminium contained. In this study, solution for this problem has been discovered through further understanding of the solidification process, including the potency and the efficiency of nucleation particles, the role of solute, and the role of casting conditions. First of all, the study suggested that MgO particles can act as nuclei in magnesium alloys by measuring and analyzing the differences in cooling curves with various amount of endogenous MgO particles. The differences indicated that the number density of MgO particles has a huge influence on the microstructure. This idea has been fatherly proved by the inoculation of MgO particles in magnesium alloys because the microstructures have been significantly refined after the inoculation. A new kind of refiner (AZ91D-5wt%MgO) has been developed based on such understandings. Secondly, the study discovered that the role of solute has much smaller effect on the grain size than it was suggested in traditional understandings. The inverse-proportional relationship between the grain size and the solute is highly suspected and the major role of solute is to cause columnar- equiaxed transition. The role of casting conditions has also been studied in order to provide experimental evidence for the existence of melt quenching effect in magnesium alloys. It is shown that various casting conditions, such as pouring temperatures and mould temperatures, have large influence on the critical heat balance temperature after rapid pouring. In this study, a theoretical model based on the analysis of cooling curves is presented for grain size prediction. An analytical model of the advance of equiaxed solidification front is developed based on the understanding of the role of casting conditions. Eventually, all these understandings have been applied to magnesium direct-chill (DC) casting. The refined microstructure of DC cast ingots can further assist in understanding the mechanism of advanced shearing achieved by MCAST unit. The comparison of the ingots with and without melt shearing indicated that the advance shearing device can disperse MgO film into individual particles.

The industrial practice of grain refinement of aluminium alloys involves the addition of inoculant particles to initiate alpha-aluminium grains at small undercoolings. This results in a uniformly fine, equiaxed as-cast microstructure and is commonly achieved using Al-Ti-B additions. The phase responsible for initiation of grains in aluminium melts inoculated with Al-Ti-B was determined during the 1990s; since that time, scientific understanding of grain refinement has advanced rapidly. However, one of the main problems of addition inoculants is impurities which is added to the melt and may affect the desired characteristics of the product. With regards to this problem other methods of refinement and the mechanisms of refining have not been fully understood and prediction of as-cast Microstructures in aluminium alloys has much scope for improvement. In this thesis: 1-Factors in establishing equiaxed microstructure were analysed and the origin of equiaxed grains were explored. Then the nucleation process and the involved mechanisms were investigated in depth and control of nucleation process to achieve a fine and uniform structure was set as target. 2-Refinement of microstructure with introduction of shearing was evaluated and the process of refinement in the mushy zone (semisolid state) as a base line was established. Then introduction of shearing above liquidus as a development was analysed and outstanding refinement was seen with shearing above liquidus which have not been investigated properly elsewhere. 3- The mechanisms of refinement by introducing shearing were investigated and the refining mechanisms below and specifically above liquidus were investigated systematically. As results an appropriate understanding about the mechanisms of nucleation and refinement above liquidus was established. 4- Finally, with simulation the most dominant factor in approaching fine grain size by applying shear was identified and the results of experimental examination was verified by simulation.

Aluminetos de ferro pertencem a uma classe de materiais interessantes por combinarem excelente resistência à oxidação com boas propriedades mecânicas em temperaturas moderadas a altas (até 500°C). Estes materiais, contudo, em temperatura ambiente, possuem baixa ductilidade (menos de 5% de alongamento à tração), característica correlacionada a efeitos ambientais, o que dificulta seu processo de conformação. A fundição é uma via de processamento tradicionalmente aplicada às ligas frágeis (por exemplo, ferro fundido cinzento), sendo necessário conhecer as propriedades termoquímicas da liga para que as peças fundidas sejam livres de defeitos atribuídos ao processo, como a formação de poros e rechupes. Neste trabalho foram investigadas três ligas distintas de intermetálicos, Fe28Al, Fe28Al6Cr e Fe28Al6Cr1Ti, sob a influência de diferentes condições de solidificação. Para estas três composições de liga, observou-se a redução do tamanho de grão em até 60% pela adição de Al-5Ti-1B como inoculante ao metal fundido. As ligas foram produzidas em condições laboratorias (forno de indução com capacidade máxima de 2 kg e proteção sob fluxo de Ar), bem como em escala industrial (forno de indução com capacidade de 100 kg). O processo em escala industrial resultou em peças de fundição com pequena quantidade de defeitos, sendo este um indicativo da capacidade de produzir peças destes aluminetos de ferro diretamente pelo processo de fundição. A técnica de tomografia de raios X auxiliou na mensuração da contração linear (~6%) e tendência à formação de defeitos. Além da caracterização microestrutural das ligas produzidas, este trabalho, ao relatar processo de fundição em escala industrial, inclui uma discussão sobre a reatividade do metal fundido e o material refratário que reveste o forno de indução. Dessa forma, os dados obtidos permitem averiguar a fundibilidade de ligas da família FeAl pelo uso de forno de indução. / Iron aluminides are good candidates for applications at moderate to high temperatures (up to 500 °C) because they combine excellent oxidation resistance with good mechanical properties. However, these materials have low ductility at room temperature (less than 5% traction elongation), a characteristic correlated to environmental effects, which hinders their conformation process. Casting is a processing route traditionally applied to brittle alloys (eg, gray cast iron), it is necessary to know the thermochemical properties of the alloys to reduce the formation of defects attributed to the casting process, such as the formation of pores, scar and blows. In this work, three different alloys of intermetallic (Fe28Al, Fe28Al6Cr and Fe28Al6Cr1Ti) were investigated under the influence of different solidification conditions. For these three alloy compositions, grain size reduction by up to 60% was observed by the addition of Al-5Ti-1B as an inoculant to the molten metal. The alloys were produced under laboratory conditions (induction furnace with a maximum capacity of 2 kg and protection under Air flow), as well as industrial scale (induction furnace with capacity of 100 kg). The industrial scale process resulted in castings with a small number of defects, which is an indication of the ability to produce mechanical parts of these iron aluminides directly by the casting process. The X-ray tomography technique assisted in the measurement of linear contraction (~ 6%) and tendency to defect formation. In addition to the microstructural characterization of the alloys, this work includes a discussion about the reactivity of the molten metal and the refractory material coating the induction furnace. In this way, the obtained data allow to investigate the FeAl alloys castability by the use of induction furnace.

As ligas Al-Si hipoeutéticas têm grande importância na indústria de fundição de peças devido às excelentes propriedades de fundição, como baixo ponto de fusão e alta fluidez. A análise térmica das curvas de resfriamento medidas durante a solidificação destas ligas pode ser utilizada para controlar a formação da macroestrutura de grãos. Esta análise envolve a determinação das temperaturas de início e final de solidificação, bem como a evolução da fração de sólido com o tempo a partir da chamada análise térmica de Fourier. Apesar desta técnica ter sido aplicada a diversas ligas comerciais, existem poucos dados referentes às ligas Al-Si binárias. Os dados são ainda mais escassos quando se deseja examinar o efeito do tratamento de inoculação do metal líquido para refino de grão. O objetivo do presente trabalho é investigar o efeito do tratamento de inoculação nas ligas binárias Al-3%Si, Al-7%Si e Al-11%Si através da análise térmica e metalográfica. Foram obtidos lingotes cilíndricos a partir do vazamento da liga Al-Si líquida com ou sem a adição de inoculante na forma da liga mãe Al-3%Ti-1%B, adicionada para se obter um teor nominal de 0,05%Ti. Curvas de resfriamento foram medidas a partir de termopares inseridos no interior da cavidade do molde, composto de areia de sílica ligada com resina fenólica. Os lingotes foram seccionados e as suas micro e macroestruturas examinadas por metalografia óptica. A análise térmica das curvas de taxa de resfriamento e a análise térmica de Fourier foram aplicadas para determinar os instantes de início e final de solidificação, a magnitude da recalescência, a evolução da fração de sólido com o tempo e a fração de sólido no momento da coesão dendrítica. Os resultados mostram que o inoculante, apesar de adicionado na mesma quantidade em todas as ligas, é mais efetivo em diminuir o tamanho de grão da liga Al-3%Si do que das ligas Al-7%Si e Al-11%Si. Esta perda de eficiência é chamada de envenenamento do inoculante pelo Si. A evolução da fração de sólido mostra que a fração de coesão diminui com o aumento do teor de Si, como observado por alguns autores. A adição do inoculante diminui a fração de sólido durante a solidificação, diminuindo também a fração de coesão. Este efeito contraria dados da literatura para o ponto de coesão medido através de métodos mecânicos. / The hypoeutectic Al-Si alloys are extremely important to the foundry industry owing to their excellent fluidity and castability. The thermal analysis of the cooling curves measured during solidification of these alloys can be used to control the formation of the grain macrostructure. This analysis consists of the determination of the temperatures at the beginning and end of solidification, as well as the calculation of the time evolution of the solid fraction by more elaborate techniques, such as, the Fourier thermal analysis. Although this technique has been applied to several aluminum commercial alloys, there are very few data about binary Al-Si alloys. Available data related to the effect of melt inoculation to decrease grain size are even scarcer. The objective of the present work is to study the effect of the inoculation treatment of the binary alloys Al-3%Si, Al-7%Si, and Al-11%Si by thermal analysis and metalography. Cylindrical ingots were cast by pouring Al-Si melts with or without the addition of inoculant in the form of Al-3%Ti-1%B to obtain 0,05%Ti. Cooling curves were measured by thermocouples located within the mold cavity, made of silica sand and phenolic resin. The ingots were sectioned and their micro and macrostructures examined by optical metalography. The simple thermal analysis and the Fourier analysis were used to determine the time of beginning and end of solidification, the size of the recalescence, the time evolution of solid fraction and the solid fraction at the dendrite coherency point. The results show that, although the same amount of inoculant is added to all melts, it is more effective to decrease the grain size of the Al-3%Si than that of the Al7%Si and Al-11%Si alloys. This fading of efficiency is referred to as poisoning of the inoculant by Si. The evolution of solid fraction shows that the solid fraction at the coherency point decreases with an increase in the Si content, as observed by other authors. The addition of inoculant also causes a decrease in the solid fraction at dendrite coherency, which disagrees with some published coherency fraction obtained by mechanical methods.