APFIM study of multicomponent M2C carbide precipitation in AF1410 steel

Olson, Gregory B.; Kinkus, T. J.; Montgomery, Jonathan S.

doi:10.1016/0039-6028(91)90421-n

Cited by 29 publications

(4 citation statements)

References 5 publications

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“…UHS Co-Ni steels all exhibit an excellent UTS/K 1C balance due to a M 2 C carbide precipitation during tempering in a highly dislocated lathmartensitic matrix [4,7,12,[15][16][17]. However, there is limited literature on the recently developed M54® steel [18][19][20][21].…”

Section: Introductionmentioning

confidence: 99%

Controlling the MC and M2C carbide precipitation in Ferrium® M54® steel to achieve optimum ultimate tensile strength/fracture toughness balance

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Déneux

Binot

et al. 2018

Materials Characterization

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Ferrium® M54® exhibits an excellent UTS/K 1C balance allowing its application in aeronautical structures. This steel belongs to the Co-Ni UHS steels family with M 2 C nanometer-size carbide precipitation during tempering. These steels provide very high strength with a very good fracture toughness thanks to the M 2 C fine precipitation during tempering, but also because coarse particles are dissolved during austenitizing without grain coarsening. The goal of this article is to identify the different carbide populations in M54®. A small addition of Ti in M54® forms a Ti-rich MC carbide precipitation that is stable at high temperature. Consequently, during austenitization at 1060°C, all other types of coarse carbides are dissolved in the matrix without grain coarsening. As a very small part of the initial carbon content is needed to form MC carbides, efficient and intensive nanometric M 2 C carbide precipitation takes place during tempering, leading to very high final strength. Due to this double precipitation of carbides in M54®, the steel achieves an outstanding UTS/K 1C balance.

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Section: Introductionmentioning

confidence: 99%

Controlling the MC and M2C carbide precipitation in Ferrium® M54® steel to achieve optimum ultimate tensile strength/fracture toughness balance

Mondière

Déneux

Binot

et al. 2018

Materials Characterization

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“…Where the LSW constant = 1.06 × 10 −30 m 3 s -1 was taken from [55]; this value was fitted for M2C in AF1410 aged at 510 °C, a steel with similar Cr and Mo contents as Cr2Mo; the same value for was assumed for M7C3 in 2CrMo, as no similar information was found in the literature. Similarly, B=0.456 and n=0.72 were fitted using data from [56] for the same steel.…”

Section: Predicting the Strength Of Multi-phase Maraging Steelsmentioning

confidence: 99%

“…The morphology of the reverted austenite in the 2CrMo was different from that in the Cr2Mo. Following the definition used widely in the literature [56][57], two morphologies of reverted austenite were observed: acicular  and globular Acicular  is nucleated at the martensite lath, block and packet boundaries, while globular  is nucleated at prior  boundaries as well as martensite block and packet boundaries. Fig.…”

Section: Ebsd Observationsmentioning

confidence: 99%

Effect of ageing on the microstructural evolution in a new design of maraging steels with carbon

et al. 2020

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A new maraging steel, based on carbide precipitation, is described. Two alloys were designed namely Fe-10Mn-0.25C-2Cr-1Mo wt% (2CrMo) and Fe-10Mn-0.25C-1Cr-2Mo wt% (Cr2Mo). These compositions were chosen to achieve ultra-high strength and high tensile elongation; the former and latter are promoted through the simulatenous precipitation of Cr-and Mo-rich carbides and Mn-rich reverted austenite. The alloys were manufactured through the standard melting, casting and hot working route. Following a solution treatment at 870 °C and quench, which gave a fully martensitic structure, the alloys were aged for various times at 510 °C. The microstructure and tensile properties were investigated in detail as a function of ageing time.The microstructure observed was dominated by micron scale and nanometer scale Mn segregation which determined the local Ac3 temperature. Austenite reversion occurred in both alloys, peaking at 16h in both cases. In the 2CrMo alloy, the reverted austenite was mainly globular in morphology due the Ac3 temperature being lower than the ageing temperature, but was acicular in the Cr2Mo with Ac3 similar to the ageing temperature of 510 °C. Moreover, acicular austenite was promoted by Mn segregation at martensite lath boundaries in Cr2Mo.In the 2CrMo steel, carbide precipitation (M3C and M7C3) occurred during heating to the ageing temperature, but the carbides gradually dissolved with further ageing. In contrast, in the Cr2Mo alloy, precipitation of carbides (M7C3 and M2C) occurred during ageing, the volume fraction of which increased with ageing time. In both alloys a TRIP effect was observed, but the extent of this was greater for the Cr2Mo alloy. The complex microstructure obtained after 16h led to an excellent combination of strength of 1.3GPa and elongation of 18%. Physics-based models for the microstructure in martensite, precipitation kinetics, as well as for TRIP in austenite were employed to explain and predict the individual strengthtening contributions of the microstructure to the total strength, confirming that the maximum strength-elongation relationship found after 16h is due to an optimal combination of a slightly overaged -but still strong-martensite and 30% of reverted austenite, for increased work hardening and ductility.

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“…AF1410 steel is a kind of high strength and high toughness secondary hardening steel, which has good welding performance and excellent corrosion resistance [28,29]. It is widely used in the manufacture of military equipment such as submarines, military aircraft, and artillery.…”

Section: Introductionmentioning

confidence: 99%

Multiobjective Optimization of Milling Parameters for Ultrahigh‐Strength Steel AF1410 Based on the NSGA‐II Method

Yan

et al. 2020

Advances in Materials Science and Engineering

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In this paper, ultrahigh-strength steel AF1410 was milled with the carbide tool, and a total of thirty experiments were performed based on central composite design (CCD) of response surface methodology. The prediction models of milling force and surface roughness are established, respectively. The influence of milling parameters (milling speed, each tooth feed, radial depth of cut, and axial depth of cut) on milling force and surface roughness is studied by ANOVA and established prediction model. Multiobjective optimization of milling parameters is accomplished based on nondominated sorting genetic algorithm II (NSGA-II) with milling force, surface roughness, and material removal rate as optimization objectives. The surface roughness, cutting force, and material removal rate are important indexes to measure the energy consumed in the process of product, the surface machining quality, and machining efficiency of processing, respectively. In order to minimize milling force and surface roughness and maximize material removal rate, NSGA-II was used for multiobjective optimization to obtain the optimal fitness value of the objective function. The NSGA-II has been applied to obtain a set of optimal combination of parameters from the Pareto-optimal solution set to enhance the machining conditions.

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APFIM study of multicomponent M2C carbide precipitation in AF1410 steel

Cited by 29 publications

References 5 publications

Controlling the MC and M2C carbide precipitation in Ferrium® M54® steel to achieve optimum ultimate tensile strength/fracture toughness balance

Controlling the MC and M2C carbide precipitation in Ferrium® M54® steel to achieve optimum ultimate tensile strength/fracture toughness balance

Effect of ageing on the microstructural evolution in a new design of maraging steels with carbon

Multiobjective Optimization of Milling Parameters for Ultrahigh‐Strength Steel AF1410 Based on the NSGA‐II Method

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