Correlation between internal friction background and the concentration of carbon in solid solution in a martensitic steel

Tkalcec, I.; Mari, Daniele; Benoît, W.

doi:10.1016/j.msea.2006.03.115

Cited by 34 publications

(49 citation statements)

References 12 publications

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“…By contrast, the P1 maximum is frequency-independent (Fig. 2c) indicating that the associated mechanism is not thermally activated as reported by Tkalcec [32]. It is noted that the P1 maximum is not observed in the 820Q sample (Fig.…”

Section: Methodssupporting

confidence: 65%

“…The Snoek-Köster and dislocation-enhanced Snoek peak are used for evaluating the amount of foreign interstitial atoms and the dislocation density. It is important to emphasize that Snoek-Köster peak (or equivalently, the cold-work peak) [11][12][13][14][15][16] occurs both in deformed ferrite [11][12][13][14][15][16][17][18][19][20] and in martensite [11,[25][26][27][28][29][30][31][32][33][34][35][36][37][38][39].…”

Section: Introductionmentioning

confidence: 99%

“…However, the Snoek peak [49] and the dislocation-enhanced Snoek peak are absent in martenisite due to the tetragonality of the martensite. Instead, the carbon content in martensite may be assessed by the internal friction background [32]. It is recalled that carbon Snoek-Köster peak is frequently observed in ferrous martensite [25][26][27][28][29][30][31][32][33][34][35][36][37][38][39] in Fe-C alloys and numerous steels.…”

Section: Introductionmentioning

confidence: 99%

“…A few internal friction peaks were reported in high carbon tool steel (1.23 wt.%C) and in medium carbon high alloyed steel [31][32][33][34][35][36][37][38][39]. A non-thermally-activated internal friction P1 peak at 130 o C was first reported by Kê [25].…”

Section: Introductionmentioning

confidence: 99%

“…Lu [39] suggested that this peak stems from: (1) depletion of interstitial carbon due to the formation of transitional carbides or carbon segregations and abrupt decrease of the internal friction background [25,[34][35][36][37][38][39]; (2) hysteretic depinning of dislocations or twin boundaries [39]. But nevertheless the physical nature of the P1 phenomenon (referred to as the P1 maximum) is still unclear due to the large difference in alloy compositions and in the substructures of the quenched martensitic phases reported in the literature [11,[25][26][27][28][29][30][31][32][33][34][35][36][37][38][39].…”

Section: Introductionmentioning

confidence: 99%

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Mechanical Spectroscopy Of Bearing Steel

Lü

et al. 2015

Archives of Metallurgy and Materials

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This study presents mechanical spectroscopy of bearing steel subjected to different heat treatments. A non-thermally activated maximum, P1, was found at 130°C, in quenched martensitic samples, which were austenitized at 1050°C and 860°C, and presented twin martensite microstructures. It is suggested that the mechanism of the P1 maximum, observed on the lowtemperature side of Snoek-Köster peak, is related to the change of defect configurations in twinned martensite assisted with high mobility of the solute carbon atoms under an external harmonic stress field applied during mechanical loss measurements.Keywords: Bearing steel, twin martensite, carbon atoms, mechanical spectroscopy, internal friction, Snoek-Köster peak W pracy przedstawiono wyniki badań spektroskopii mechanicznej stali łożyskowej poddanej różnej obróbce cieplnej. W hartowanych martenzytycznych próbkach, które były austenityzowane w 1050°C i 860°C, i posiadały bliźniaczą mikrostrukturę martenzytu, występuje nietermicznie aktywowane maksimum P1 przy 130°C. Sugeruje się, że mechanizm maksimum P1, które występuje na niskotemperaturowym zboczu piku Snoek-Köstera, związane jest ze zmianą konfiguracji defektów w bliźniaczym martenzycie, przy wysokiej ruchliwości atomów węgla. Maksimum P1 ujawnia się pod wpływem działania harmonicznie zmiennego zewnętrznego pola naprężeń przyłożonego do próbki w trakcie badań metodą spektroskopii mechanicznej.

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Section: Methodssupporting

confidence: 65%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

See 3 more Smart Citations

Mechanical Spectroscopy Of Bearing Steel

Lü

et al. 2015

Archives of Metallurgy and Materials

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Global Techniques for Characterizing Phase Transformations – A Tutorial Review

2010

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To characterize phase transformations, it is necessary to get both local and global information. No experimental technique alone is capable of providing these two types of information. Local techniques are very useful to get information on morphology and chemistry but fail to deal with global information like phase fraction and size distribution since the analyzed volume is very limited. This is why, it is important to use, in parallel, global experimental techniques, that investigate the response of the whole sample to a stimulus (electrical, thermal, mechanical…). The aim of this paper is not to give an exhaustive list of all global experimental techniques, but to focus on a few examples of recent studies dealing with the characterization of phase transformations, namely (i) the measurement of the solubility limit of copper in iron, (ii) the tempering of martensite, (iii) the control of the crystallinity degree of a ultra high molecular weight polyethylene and (iii) a precipitation sequence in aluminum alloys. Along these examples, it will be emphasized that any global technique requires a calibration stage and some modeling to connect the measured signal with the investigated information.

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Tempering of Lath Martensite in Low and Medium Carbon Steels: Assessment and Challenges

Krauß

2017

steel research int.

156

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This paper is a directed review of the microstructures and the mechanisms, by which they are formed by tempering of lath martensite in low and medium carbon steels. As-quenched martensitic structure is first reviewed, then low-temperature tempering (LTT) that produces ultrahigh strength and good toughness, and high-temperature-tempering (HTT), which can produce excellent combinations of strength, ductility, toughness, and good resistance to hydrogen embrittlement in sour gas and oil environments, are covered. It is well known that hardness decreases continuously with increasing tempering temperature, but the superimposed multiple mechanisms of microstructural changes by which the softening and its retardation occur during various stages of tempering have received little attention on the integrated scales of microstructure, substructure, and nanostructure. Thus, earlier descriptions of the reasons for softening need deeper examination. In particular, the reasons for the changes in the very fine crystal size and high dislocation density of as-quenched lath martensite produced by high temperature tempering, sometimes producing a low dislocation density, un-recrystallized, fine lath-morphology ferritic grain size, sometimes producing an equiaxed, recrystallized ferritic grain size, are not clear. Deformation behavior and mechanical properties as related to the residual components of martensitic microstructure that survive tempering are discussed. Questions remain and the use of newer techniques, such as Electron Back Scatter Diffraction and atom probe tomography, in addition to light microscopy, transmission electron microscopy, Mössbauer effect spectroscopy, and Mechanical Spectroscopy used in characterizing quench and tempered structures are noted.

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Correlation between internal friction background and the concentration of carbon in solid solution in a martensitic steel

Cited by 34 publications

References 12 publications

Mechanical Spectroscopy Of Bearing Steel

Mechanical Spectroscopy Of Bearing Steel

Global Techniques for Characterizing Phase Transformations – A Tutorial Review

Tempering of Lath Martensite in Low and Medium Carbon Steels: Assessment and Challenges

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