ISOTHERMAL M2C CARBIDE GROWTH IN ULTRAHIGH STRENGTH HIGH Co-Ni STEELS

Lee, Hyuck Mo; Sohn, Hyunchul; Yoo, Choong Hwa

doi:10.1016/s1359-6462(97)00385-0

Cited by 3 publications

(1 citation statement)

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“…The peak strength of the secondary hardening for AerMet 100 steel could be obtained by tempering around 482 • C, which gives rise to the full precipitation of M 2 C carbides [10,11]. The M 2 C carbides in high Co-Ni secondary hardening steels are needle-shaped and coherent with a martensitic matrix at the stage of peak secondary hardening [10][11][12][13][14], and it has been proven that the M 2 C carbides have a hexagonal structure [15][16][17][18][19][20]. Recent research results indicate that [7] M 2 C carbides with a hexagonal structure firstly nucleated and then grew slowly in the case of AerMet 100 steel during tempering at 482 • C, and this process was dominated by needle-shaped precipitates when tempering for 7 h or less.…”

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confidence: 99%

The Evolution of a Microstructure during Tempering and Its Influence on the Mechanical Properties of AerMet 100 Steel

Wang,

Zhang,

Huang

et al. 2023

Materials

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In order to provide guidance for furthering the balance of strength and toughness of AerMet 100 steel through tempering treatment, the effects of the tempering time on microstructure and mechanical properties are investigated. The microstructure evolution, especially M2C precipitates and austenite in AerMet 100 tempered at 482 °C for 1~20 h, was characterized, and its influences on the mechanical properties were studied. The tensile strength decreases gradually, the yield strength increases first and then decreases, and the fracture toughness KIC increases gradually with an increasing tempering time. The strength and toughness matching of AerMet 100 steel is achieved by tempering at 482 °C for 5~7 h. Without considering the martensitic size effect, the influence of the dislocation density on the tensile strength is more significant during tempering at 482 °C. The precipitation strengthening mechanism plays a dominant role in the yield strength when tempering for 5 h or less, and the combined influence of carbide coarsening and a sharp decrease in the dislocation density resulted in a significant decrease in tensile strength when tempering for 8 h or more. The fracture toughness KIC is primarily influenced by the reverted austenite, so that KIC increases gradually with the prolongation of the tempering time. However, a significant decrease in the dislocation density resulting from long-term tempering has a certain impact on KIC, giving rise to a decrease in the rising amplitude in KIC after tempering for 8 h or more.

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