Grain boundary precipitation in an Fe28.6Mn9.8Al0.8Si1.0C alloy

Chao, Chuen−Guang; Liu, T.F.

doi:10.1016/0956-716x(91)90464-c

Cited by 12 publications

(7 citation statements)

References 18 publications

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“…Hence, Fe-Al-Mn-C alloys are suitable for industrial use and in biomedical applications. The typical chemical compositions of Fe-Al-Mn-C alloys are in the ranges of Fe-(4.9-11.0) mass% Al-(23.7-35.0) mass% Mn-(0.5-1.5) mass% C [8][9][10][11][12]. Furthermore, it is generally concluded that Fe-Al-Mn-C alloys exhibit good oxidation resistance at high temperatures because a composition of Al between 8.5 wt.% and 10.5 wt.% results in the formation of a continuous protective Al 2 O 3 layer on the surface of the alloys [13][14][15].…”

Section: Introductionmentioning

confidence: 99%

Phase transformation of high temperature on Fe–Al–Mn–Cr–C alloy

Liu

Cheng

Chao

et al. 2009

Journal of Alloys and Compounds

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Section: Introductionmentioning

confidence: 99%

Phase transformation of high temperature on Fe–Al–Mn–Cr–C alloy

Liu

Cheng

Chao

et al. 2009

Journal of Alloys and Compounds

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“…[16] Evidence that silicon influences manganese partitioning comes from a study by Chao and Liu who reported manganese-rich grain boundary j-carbides in a Fe-28.6Mn-9.8Al-0.8Si-1.0C steel after aging for longer than 6 hours at 873 K (600°C). [17] The concentration of manganese in the j-carbide was determined by energy dispersive X-ray spectroscopy (EDS) to be 46.5 wt pct, which was almost 18 pct more manganese than the austenitic matrix composition. [17] However, manganeserich grain boundary j-carbides were also observed in a Fe-8Al-31.5Mn-1.05C alloy without silicon addition and b-Mn was not observed, even after extended aging for 24 hours at 823 K (550°C).…”

Section: Introductionmentioning

confidence: 99%

“…[17] The concentration of manganese in the j-carbide was determined by energy dispersive X-ray spectroscopy (EDS) to be 46.5 wt pct, which was almost 18 pct more manganese than the austenitic matrix composition. [17] However, manganeserich grain boundary j-carbides were also observed in a Fe-8Al-31.5Mn-1.05C alloy without silicon addition and b-Mn was not observed, even after extended aging for 24 hours at 823 K (550°C). [18] b-Mn is reported to precipitate on grain boundaries in the temperature range of 823 K to 1023 K (550°C to 750°C) in alloys without silicon.…”

Section: Introductionmentioning

confidence: 99%

An Atom Probe Study of Kappa Carbide Precipitation and the Effect of Silicon Addition

Bartlett

Aken

Medvedeva

et al. 2014

Metall Mater Trans A

103

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The influence of silicon on j-carbide precipitation in lightweight austenitic Fe-30Mn-9Al-(0.59-1.56)Si-0.9C-0.5Mo cast steels was investigated utilizing transmission electron microscopy, 3D atom-probe tomography, X-ray diffraction, ab initio calculations, and thermodynamic modeling. Increasing the amount of silicon from 0.59 to 1.56 pct Si accelerated formation of the j-carbide precipitates but did not increase the volume fraction. Silicon was shown to increase the activity of carbon in austenite and stabilize the j-carbide at higher temperatures. Increasing the silicon from 0.59 to 1.56 pct increased the partitioning coefficient of carbon from 2.1 to 2.9 for steels aged 60 hours at 803 K (530°C). The increase in strength during aging of Fe-Mn-Al-C steels was found to be a direct function of the increase in the concentration amplitude of carbon during spinodal decomposition. The predicted increase in the yield strength, as determined using a spinodal hardening mechanism, was calculated to be 120 MPa/wt pct Si for specimens aged at 803 K (530°C) for 60 hours and this is in agreement with experimental results. Silicon was shown to partition to the austenite during aging and to slightly reduce the austenite lattice parameter. First-principles calculations show that the Si-C interaction is repulsive and this is the reason for enhanced carbon activity in austenite. The lattice parameter and thermodynamic stability of j-carbide depend on the carbon stoichiometry and on which sublattice the silicon substitutes. Silicon was shown to favor vacancy ordering in j-carbide due to a strong attractive Si-vacancy interaction. It was predicted that Si occupies the Fe sites in nonstoichiometric j-carbide and the formation of Si-vacancy complexes increases the stability as well as the lattice parameter of j-carbide. A comparison of how Si affects the enthalpy of formation for austenite and j-carbide shows that the most energetically favorable position for silicon is in austenite, in agreement with the experimentally measured partitioning ratios.

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“…The Fe-Al-Mn-C alloy has a number of features that distinguish it from the other ironbased metals, which make its physical metallurgy both complex and interesting, with low density (nearly 6.6-6.9 g/cm 3 ), no or low magnetism, good atmosphere corrosion resistance, etc. In addition, the alloys could possess high strength and high ductility at room temperature with the fully austenite structure [3][4][5][6][7][8][9][10][11][12][13][14][15][16][17][18][19] and some coherent κ phase precipitates. Moreover, in order to improve the corrosion and high temperature oxidation resistance as well as strength, some alloy elements such as Si, Cu, Ti, V, Nb, Mo, W, etc.…”

Section: Introductionmentioning

confidence: 99%

Effects of Mn Contents on the Microstructure and Mechanical Properties of the Fe-10Al-xMn-1.0C Alloy

Chao

Liu

2002

Mater. Trans.

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The microstructures and mechanical properties of the Fe-10 mass%Al-(5-40)mass%Mn-1.0 mass%C alloys sheet castings have been investigated by using optical microscope (OM), transmission electron microscope (TEM), scanning electron microscope (SEM), experimental model analysis, tensile test and hardness test. Based on the present studies, the macroscopic microstructure of the present alloys are a mixture of austenite (γ ) and ferrite (α) duplex phases, and the α phase would decrease with the Mn content increased. In the meantime, according to the examination of TEM, the macroscopic γ phase is a mixture of the γ + fine(Fe, Mn) 3 AlC x (κ) + (Fe, Mn) 3 AlC x (κ ) phases and the macroscopic α phase is a mixture of the D0 3 + coarse(Fe, Mn) 3 AlC x (κ ) phases. The mechanical properties such as the ultimate tensile strength (UTS), yield strength (Y.S.), elongation of these alloys were in the range of 646-887 MPa, 575-824 MPa, and 16.3-29.2%, respectively. The hardness of these alloys were in the range of HR C 31-44. Moreover, the relationship between hardness and ultimate strength is UTS 20.93HR C . In addition, the damping ratios and Young's modulus of the present alloys were in the range of 0.0603-0.0417, and 139-165 GPa, respectively. It is noted here that the results have never observed by other research workers in the Fe-Al-Mn-C alloy system.

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Grain boundary precipitation in an Fe28.6Mn9.8Al0.8Si1.0C alloy

Cited by 12 publications

References 18 publications

Phase transformation of high temperature on Fe–Al–Mn–Cr–C alloy

Phase transformation of high temperature on Fe–Al–Mn–Cr–C alloy

An Atom Probe Study of Kappa Carbide Precipitation and the Effect of Silicon Addition

Effects of Mn Contents on the Microstructure and Mechanical Properties of the Fe-10Al-xMn-1.0C Alloy

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