Solubility Limit Of Carbon Research Articles

The Solubility Limit of Carbon in Alumina at 1,600°C.

The solubility limit of carbon in α-Al2O3 (alumina) equilibrated at 1,600°C under He in a graphite furnace was measured by wavelength-dispersive spectroscopy. Undoped alumina and alumina containing carbon at a concentration resulting in the precipitation of a second phase were prepared and equilibrated at 1,600°C. The undoped alumina was used to quantify the amount of carbon deposited on the surface of samples because of hydrocarbon contamination in the electron microscope, and this background level was removed from the signal measured from carbon-doped samples. The solubility limit of carbon in alumina was found to be 5,300 ± 390 at. ppm, and it is believed that carbon substitutes oxygen as an anion and is charge-compensated by oxygen vacancies. Doping alumina with carbon at concentrations below the solubility limit does not impede densification and reduces grain growth. Doping above the solubility limit hinders densification during sintering.

Microstructure and mechanical properties of Ti–45Al–2W–xC alloys

The microstructure and mechanical properties of five alloys with nominal compositions of Ti–45Al–2W–xC (in at.%), where x is ranging from 0.4 to 2.0 at.%, were studied. The alloys were prepared by vacuum induction melting in graphite crucibles, followed by centrifugal casting into a graphite mould. The as-cast alloys were subjected to hot isostatic pressing and heat treatment consisting of solution annealing, cooling at a constant rate and stabilisation annealing. The microstructure of the heat-treated alloys consists of equiaxed α2(Ti3Al) + γ(TiAl) lamellar grains surrounded by γ grain boundaries with a small amount of β/B2 particles. The α2-α2 interlamellar spacing λ decreases with increasing carbon content until a solubility limit of carbon is achieved. The increase in carbon content above the solubility limit leads to the formation of primary Ti2AlC particles during solidification and an increase in the amount of γ phase at grain boundaries. Vickers microhardness of lamellar grains depends on the carbon content and interlamellar spacing λ. The studied Ti–45Al–2W–0.8C and Ti–45Al–2W–1.2C alloys show improved creep resistance at 800 °C compared to that of the reference carbon-free TiAl–W and carbon-containing TiAl–Nb based alloys with fully lamellar, nearly lamellar, convoluted or pseudo-duplex microstructure.

Study of the Effect of Carbon on the Deformation Behavior and Microstructure of a Ti–10V–2Fe–3Al Alloy

Scanning electron microscopy (SEM) and X-ray diffraction (XRD) analysis are used to study the structure, phase composition, and deformation behavior of a titanium Ti–10V–2Fe–3Al alloy with different carbon contents. It is shown that as the carbon content in the alloy increases to the maximum carbon solubility, the dispersity of the secondary α-phase increases and, therefore, the strength of the alloy increases. After reaching the carbon solubility limit, titanium carbide particles are observed in the alloy structure; the morphology of the particles and their sizes are similar to those of the primary α-phase. The titanium carbide particles do not affect the strength and plasticity characteristics of the alloy during tensile tests and retain their initial shape after deformation. At the stage of strain localization, titanium carbide particles are sites of micropore nucleation.

Behavior of Al4C3 Particles During Flotation and Sedimentation in Aluminum Melts

Al4C3 particles form during the primary production of aluminum via molten salt electrolysis due to the carbon solubility and direct contact between bath, metal, and carbon anodes. Additional Al4C3 may form during melt processing through direct contact between the melt and carbonaceous materials. As a result of their small size and similar density to aluminum, removal of aluminum carbide particles can be challenging. If not removed, carbides can produce inclusion defects or poor surface condition in aluminum products. The current work studies the removal and behavior of Al4C3 particles during flotation with different gas mixtures, as well as sedimentation. The interaction between carbide particles and Al2O3 films during the melt treatment processes was also studied and reported. Factsage thermochemical software was used to model the interactions at the interface of inclusions and bubbles covered by films. The highest degree of carbide removal was obtained after flotation with an H2O-containing argon gas mixture, where the carbide concentration dropped below the measured solubility limit of carbon at the corresponding temperature. Strong interaction between Al4C3 particles and Al2O3 films was observed during sedimentation which worked as an efficient removal method for the particles. Oxidation of carbides and formation of oxycarbides were suggested as the mechanisms promoting the attachment of carbides on oxide films.

Solubility of carbon, manganese and silicon in γ-iron of Fe-Mn-Si-C alloys

The study was performed on alloys with a carbon content of 0,37-0,57 % (wt.), silicon 0,23-0,29 % (wt.), manganese 0,7-0,86 % (wt.), the rest– iron. To determine the phase composition of alloys used microstructural, microanalysis and X-ray analysis. In addition, the physical characteristics of the alloys studied in this paper were determined, such as alloy chemical dependence of extension and contraction ratio, impact toughness and hardness. The results obtained in this paper showed that the iron-based alloy with the content of carbon of 0.57 % (wt.), silicon of 0.28 % (wt.) and manganese of 0.86 % (wt.)) had the superior microstructure and physical properties. It was determined that after a number of crystallization and phase transformation the alloy phase structure includes two phases: a-iron and cement magnesium doping Fe2.7Mn0,3C..
 For the first time using the method quasichemistry received an expression of the free energy of a γ-iron alloyed with silicon and magnesium, and determined the solubility limit of carbon, manganese and silicon. The maximum content in γ-iron can reach: carbon 6,8 % (at.), manganese – 67,5 % (at.), silicon – 2,3 % (at.).

Modelling of structure forming in structural steels

The study showed that the influence of alloying elements on the secondary structure formation of the steels containing from 0.19 to 0.37 wt. % carbon; 0.82-1.82 silicon; 0.63-3.03 manganese; 1.01-3.09 chromium; 0.005-0.031 nitrogen; up to 0.25 wt.% vanadium and austenite grain size is determined by their change in the content of vanadium nitride phase in austenite, its alloying and overheating above tac3, and the dispersion of ferrite-pearlite, martensitic and bainitic structures is determined by austenite grain size and thermal kinetic parameters of phase transformations. Analytical dependencies are defined that describe the experimental data with a probability of 95% and an error of 10% to 18%. An analysis results of studying the structure formation of structural steel during tempering after quenching show that the dispersion and uniformity of the distribution of carbide and nitride phases in ferrite is controlled at complete austenite homogenization by diffusion mobility and the solubility limit of carbon and nitrogen in ferrite, and secondary phase quantity in case of the secondary phase presence in austenite more than 0.04 wt. %. Equations was obtained which, with a probability of 95% and an error of 0.7 to 2.6%, describe the real process.

Solubility of Carbon, Manganese and Silicon in α-Iron of Fe-Mn-Si-C Alloys

The study was performed on alloys with a carbon content of 0.37-0.57% (wt.), silicon 0.23-0.29% (wt.), manganese 0.7‑0.86% (wt.), the rest– iron. To determine the phase composition of alloys used microstructural, microanalysis and X-ray analysis. In addition, the physical characteristics of the alloys studied in this paper were determined, such as alloy chemical dependence of extension and contraction ratio, impact toughness and hardness. The results obtained in this paper showed that the iron-based alloy with the content of carbon of 0.57 % (wt.), silicon of 0.28 % (wt.) and manganese of 0.86 % (wt.)) had the superior microstructure and physical properties. It was determined that after a number of crystallization and phase transformation the alloy phase structure includes two phases: a-iron and cement magnesium dopingFe2.7Mn0,3C. For the first time using the method quasi-chemistry received an expression of the free energy of a solid solution α-iron alloyed with silicon and magnesium, and determined the solubility limit of carbon, manganese and silicon. In δ-iron may dissolve to 0.09% (wt.) carbon, manganese up to 3.5% (wt.), silicon – 0.25% (wt.). The maximum content in α-iron can reach: carbon – 0.017% (wt.), manganese – 21% (wt.), silicon – 1.3% (wt.).

A Determination of Carbon Solubility Limit in Bcc-Iron from Low-Temperature Age Hardening by Bayesian Inference

A Determination of Carbon Solubility Limit in Bcc-Iron from Low-Temperature Age Hardening by Bayesian Inference

Solubility of boron and carbon in γ-iron of Fe-B-C alloys

It is known that solubility of elements affects the phase composition of alloys that are formed in the solidification process. To predict the phase composition of alloys, it is necessary to determine the solubility limit in the phases. In the paper the structural properties of austenite of alloys in the system of Fe-B-C are studied and the solubility limit of boron and carbon is determined. The investigation is carried out for the specimens with carbon content of 0.0001–2.3 wt.% and boron content of 0.0001–1.0 wt.%, the rest is iron. To determine the physical properties of alloys, we use the microstructure analysis, X-ray microanalysis, X-ray structure analysis and differential thermal analysis. It is shown experimentally that the maximum shift of the eutectoid point is observed when boron content is up to 0.004 wt.%. When boron content of the alloy increases to 0.01 wt.%, the eutectoid point shifts to the left to 0.21 wt.%-carbon and the austenite area decreases. Further increase in the numerical value of boron content in the alloy is hardly caused the eutectoid point to shift. In this paper, the vertical section of the Fe-B-C system state diagram is obtained from experimental data. For the first time we obtain temperature dependence of the free energy of γ-iron solid solution, using the quasi-chemical method, and determine the solubility limit of carbon and boron. The maximum weight fraction of boron in the austenite can be up to 0.0136 wt.%, and that for carbon – up to 1.12 wt.%.

Co–Cr–Mo alloys: Improved wear resistance through low-temperature gas-phase nitro-carburization

UNS R31538, a Co–Cr–Mo alloy for biomedical applications, was surface-engineered by LTNC (low-temperature nitro-carburization), leading to co-infusion of concentrated interstitially dissolved carbon and nitrogen. LTNC was performed by encapsulating the alloy together with solid urea in a silica ampoule, evacuated and backfilled with Ar. Upon heat treatment, pyrolysis of the urea generates molecular species that provide carbon and nitrogen to diffuse into the alloy and, at the same time, “activate” the surface for carbon and nitrogen infusion by removing the alloy's native surface oxide and forming a micrometer-scale nitride layer. The treatment generates an outer zone rich in nitrogen and an inner zone rich in carbon. While the outer zone contains nitride precipitates, the inner zone consists of a uniform solution of interstitially dissolved carbon with atom fractions up to 0.035, orders of magnitude higher than the equilibrium solubility limit of carbon in UNS R31538. The treatment increases the surface hardness of UNS R31538 to 16 GPa, twice as high as that of the as-received state. Moreover, it improves the wear resistance (wear-loss volume) and the accompanying acoustic emissions (“squeaking”) by one order of magnitude. Accordingly, surface engineering by LTNC has potential to improve the performance of load-bearing Co–Cr–Mo components, e.g. in medical implants.

Effect of Corbon Content on the Structure and Mechanical Properties of TI-10V-2Fe-3Al Alloy

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Solubility of Boron and Carbon in Ferrite of the Fe-B-C System Alloys

Investigation was carried out for Fe-B-C alloys with carbon content of 0.0001–0.01 % (wt.) and boron content of 0.0001–0.01 % (wt.), the rest is iron. To determine the structural state of alloys we use the microstructure analysis, X-ray microanalysis and X-ray structure analysis. The level of microstraines, dislocation density and the coercive force of ferrite is determined, and it is shown that structure imperfection grows with boron content increase in the alloy. The obtained results enable to suggest that boron atoms in a solid solution of α-iron occupy substitutional-interstitial positions depending on boron content. In the paper it is shown experimentally, that at room temperature solubility limit of boron and carbon in the ferrite is 0.00012 % (wt.) and 0.006 % (wt.). When boron and carbon content increases further, the following phases are formed: Fe2B, Fe3(CB) and Fe23(CB)6. In this paper by means of quasi-chemical method we obtain for the first time temperature dependence of the free energy for α-iron solid solution, as well as solubility limit of carbon and boron. Maximum mass fraction of carbon may be up to 0.016 % (wt.), and maximum boron mass fraction – up to 0.00025 % (wt.). At room temperature the boron solubility limit in ferrite is 0.0001 % (wt.), and carbon one is 0.004 % (wt.). The calculated numerical values of the solubility of boron and carbon in ferrite of the Fe-B-C system alloys are less than that of the experimental results. This can be explained by the fact that boron atoms interact more actively with structure imperfections than carbon atoms. At high temperatures the solubility of carbon and boron in given phase increases.

EFFECT OF CARBON ON PHYSICAL AND STRUCTURAL PROPERTIES OF FеB IRON MONOBORIDE

In this paper we study effect of carbon on structural and physical properties of FeB iron monoboride in Fe-B system alloys with carbon content of 0,05-0,90% (wt.) and boron content of 9,0-15,0% (wt.), the rest is iron. To determine the physical properties of alloys we use microstructure analysis, X-ray microanalysis and X-ray structural analysis. Carbon doping of FeВ iron monoboride leads to a feeble lattice strain and effects on the physical characteristics of boride. Using the quasi-chemical method we estimate the temperature dependence of the boride free energy and carbon solubility limit in FeB monoboride. Carbon can substitute up to 4% ofboron atoms in FeB phase depending on the temperature. At high temperatures the carbon solubility in this phase increases. The obtained estimated data is in good agreement with experiment.

Effect of Carbon on the Physical and Structural Properties of Boride Fe2B

For Fe-В and Fe-В-С system alloys one of the structure constituent is iron boride Fe2B but in the literature there is no information on carbon solubility limit in iron boride Fe2В. The object of this paper is to reveal the effect of carbon on the physical and structural properties of boride Fe2В.
 Investigation was performed for the specimens with carbon content of 0,05 - 0,80 % (wt.) and boron content of 9,0 - 15,0 % (wt.), the rest is iron. To determine the physical properties of alloys we use microstructure analysis, X-ray microanalysis and X-ray structural analysis.
 It is found that carbon doping of boride Fe2В leads to a feeble lattice strain and effects on the physical characteristics of boride. We estimate the free energy of boride Fe2B and carbon content in Fe2B phase. Carbon can substitute up to 3 – 8 % of boron atoms in Fe2B phase depending on the temperature which is verified by experimental data. The carbon solubility in this phase is also examined.

Modeling of poly-crystalline silicon ingot crystallization during casting and theoretical suggestion for ingot quality improvement

Finite element (FE) and cellular automaton (CA) models are used in order to predict the microstructure of Poly-Crystalline Silicon (PC-Si) ingots during casting in a directional solidification furnace. During solidification, the 3D-FE model is used to simulate thermal field inside the furnace, while the nucleation and growth of PC-Si are simulated by the modified version of CA model. In this model both nucleation at silicon-crucible interface and nucleation of equiaxed grains on impurities are modeled. The origin of impurity is considered SiC particles when carbon segregates during the solidification and precipitates as SiC particles if carbon solubility limit is reached. The model is evaluated with experimental data for different parameters, such as: the temperature profile at the top and bottom of the PC-Si, grain size, and the height of solidified silicon during solidification. A one-dimensional form of grain growth is observed at the crucible-silicon interface, while a more two-dimensional form of growth is predicted at higher silicon height. The microstructure of PC-Si shows that the grain size increases as a function of PC-Si ingot height. The effects of the cooling rate and competitive growth on the final microstructure of PC-Si are also investigated. The results show that less nucleation sites are formed at the bottom of the crucible with a slower cooling rate, which leads to a larger grain size. Furthermore, the grains at the crucible side walls tend grow inward at a lower cooling rate, which can significantly change the microstructure of PC-Si. This study shows that the competitive growth phenomena plays an important role in the final microstructure of silicon ingots. A simulated model is proposed which shows that by changing the density and location of nucleation sites it is possible to achieve more effective control on final PC-Si micro structure. This simulation helps to explain the crystal behavior observed in ingots cast under different conditions.

Comparative study and quantification of cementite decomposition in heavily drawn pearlitic steel wires

Heavily cold-drawing was performed on a pearlitic steel wire and on an ultra-low carbon (ULC) steel wire in order to highlight and quantify the microstructural changes caused by this type of deformation. Both global techniques (thermoelectric power, electrical resistivity, internal fiction background) and local techniques (Atom Probe Tomography) were combined for this study. It was shown that two distinct stages have to be taken into account during the cold-drawing of pearlitic steels. The first stage (below a true strain of 1.5) was attributed mainly to the lamellar alignment, while the second stage (above a true strain of 1.5) was unambiguously interpreted as being due to a gradual enrichment of the carbon content of ferrite arising from the strain induced cementite decomposition. The carbon content in solid solution in ferrite was assessed as a function of the true strain. All the techniques showed that this carbon content exceeds the solubility limit of carbon in the ferrite above a true strain of 2.2. A correlation between the increase in the carbon content of ferrite and the increase in yield strength was also highlighted. Moreover, a scenario was proposed to explain the microstructural changes caused by drawing.

Preparation of graphene on Cu foils by ion implantation with negative carbon clusters**Project supported by the National Natural Science Foundation of China (Grant Nos. 11105100, 11205116, and 11375135) and the State Key Laboratory of Advanced Welding and Joining, Harbin Institute of Technology, China (Grant No. AWJ-M13-03).

We report on few-layer graphene synthesized on Cu foils by ion implantation using negative carbon cluster ions, followed by annealing at 950 °C in vacuum. Raman spectroscopy reveals IG/I2D values varying from 1.55 to 2.38 depending on energy and dose of the cluster ions, indicating formation of multilayer graphene. The measurements show that the samples with more graphene layers have fewer defects. This is interpreted by graphene growth seeded by the first layers formed via outward diffusion of C from the Cu foil, though nonlinear damage and smoothing effects also play a role. Cluster ion implantation overcomes the solubility limit of carbon in Cu, providing a technique for multilayer graphene synthesis.

Effects of dilute substitutional solutes on interstitial carbon inα-Fe: Interactions and associated carbon diffusion from first-principles calculations

By means of first-principles calculations coupled with the kinetic Monte Carlo simulations, we have systematically investigated the effects of dilute substitutional solutes on the behaviors of carbon in $\ensuremath{\alpha}$-Fe. Our results uncover the following. (i) Without the Fe vacancy the interactions between most solutes and carbon are repulsive due to the strain relief, whereas Mn has a weak attractive interaction with its nearest-neighbor carbon due to the local ferromagnetic coupling effect. (ii) The presence of the Fe vacancy results in attractive interactions of all the solutes with carbon. In particular, the Mn-vacancy pair shows an exceptionally large binding energy of $\ensuremath{-}$0.81 eV with carbon. (iii) The alloying addition significantly impacts the atomic-scale concentration distributions and chemical potential of carbon in the Fe matrix. Among them, Mn and Cr increase the carbon chemical potential, whereas Al and Si reduce it. (iv) Within the dilute scale of the alloying solution, the solute concentration- and temperature-dependent carbon diffusivities demonstrate that Mn has a little impact on the carbon diffusion, whereas Cr (Al or Si) remarkably retards the carbon diffusion. Our results provide a certain implication for better understanding the experimental observations related with the carbon solubility limit, carbon microsegregation, and carbide precipitations in the ferritic steels.

Solubility limit of carbon in Rh measured by graphene growth on the surface

A method to measure carbon solubility limit in Rh is proposed based on dissolution of surface carbon. Achieving of the solubility limit gives rise to a new surface phase: graphene islands, which can be easily registered by surface sensitive methods, like Auger spectroscopy and thermionic emission. The method can be applied to a platinum metal which does not produce a bulk carbide, and contains carbon in a form of bulk solid solution. The carbon solubility limit in Rh was found by the equation log( n Lim [at.%]) = 2.2 – 4600/ T (K) for the temperature range 1200–1800 K.

Physical ambiguity of the notion of the solubility limit by the example of its determination using the formation of graphene on the surface in the Re-C system

Results obtained during the determination of the solubility limit of carbon in metal based on the detection of the time instant of the nucleation of the new phase, graphene, have been considered. Graphene is easily detected by the surface-sensitive methods of thermionic emission and electron Auger spectroscopy. It has been shown that the nucleation of the first graphene islands and the formation of the graphene monolayer covering the whole surface and even the multilayer graphite film on it can be used as the time instant of the phase transition depending on the sensitivity of the method. The solubility limits differ by many times depending on the determination method. This indicates the physical ambiguity of this physical characteristic of the double systems analogous in physical meaning to the pressure of the saturated vapor for the phase transitions in the one-component systems.