Developing bearing steels combining hydrogen resistance and improved hardness

Szost, Blanka A.; Vegter, R. H.; Rivera-Dı́az-del-Castillo, P.E.J.

doi:10.1016/j.matdes.2012.07.030

Cited by 45 publications

(41 citation statements)

References 28 publications

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“…Therefore, there are more large-size undissolved cementite particles in condition #1, and the mean diameter of undissolved cementite particles of the experimental steel in condition #1 is larger than that in other conditions. In addition, on the whole, the mean diameter of undissolved cementite particles increases with the increasing of austenitizing time (Figure 10(d)), which is consistent with the calculation results of Szost et al [42] and Zhang et al [43] It means that the cementite particle coarsening occurs simultaneously with its dissolution.…”

Section: Cementite Dissolution Behavior During the Partial Austenitizingsupporting

confidence: 89%

Microstructure of Hot Rolled 1.0C-1.5Cr Bearing Steel and Subsequent Spheroidization Annealing

Liu

Zhang

et al. 2016

Metall Mater Trans A

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The effect of final rolling temperature and cooling process on the microstructure of 1.0C-1.5Cr bearing steel was studied, and the relationship between the microstructure parameters and subsequent spheroidization annealing was analyzed. The results indicate that the increase of water-cooling rate after hot rolling and the decrease of final cooling temperature are beneficial to reducing both the pearlite interlamellar spacing and pearlite colony size. Prior austenite grain size can be reduced by decreasing the final rolling temperature and increasing the water-cooling rate. When the final rolling temperature was controlled around 1103 K (830°C), the subsequent cooling rate was set to 10 K/s and final cooling temperature was 953 K (680°C), the precipitation of grain boundary cementite was suppressed effectively and lots of rod-like cementite particles were observed in the microstructure. Interrupted quenching was employed to study the dissolution behavior of cementite during the austenitizing at 1073 K (800°C). The decrease of both pearlite interlamellar spacing and pearlite colony size could facilitate the initial dissolution and fragmentation of cementite lamellae, which could shorten the spheroidization time. The fragmentation of grain boundary cementite tends to form large-size undissolved cementite particles. With the increase of austenitizing time from 20 to 300 minutes, mean diameter of undissolved cementite particles increases, indicating the cementite particle coarsening and cementite dissolution occuring simultaneously. Mean diameter of cementite particles in the final spheroidized microstructure is proportional to the mean diameter of undissolved cementite particles formed during partial austenitizing.

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Section: Cementite Dissolution Behavior During the Partial Austenitizingsupporting

confidence: 89%

Microstructure of Hot Rolled 1.0C-1.5Cr Bearing Steel and Subsequent Spheroidization Annealing

Liu

Zhang

et al. 2016

Metall Mater Trans A

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“…Such traps have higher binding energies to hydrogen than those of regular interstitial sites within the matrix and can trap hydrogen either reversibly or irreversibly, depending on the magnitude of the binding energy [42]. It is these hydrogen traps, and their ability to prevent further hydrogen migration, leading to potentially detrimental interactions, which show most promise in the search for hydrogen-resistant steels [42] [15]. The following two sections outline these trapping mechanisms, as presented within the literature, identifying suitable traps for future investigation along with the modelling techniques available to evaluate said suitability.…”

Section: Ingress Due To General Corrosion and Internal Decarburisatiomentioning

confidence: 99%

“…This paper provides a review of the current literature regarding hydrogen embrittlement of relevance to designing hydrogen embrittlement resistant bearing steels, including the fundamentals of rolling contact fatigue (RCF) [14], microstructural design [15] and the experimental techniques available for the assessment of hydrogen embrittlement [16]. Included, is a description of the primary mechanisms of hydrogen ingress and proceeding embrittlement as postulated in the literature, identifying corresponding experimental evidence, discrepancies and relevant knowledge gaps.…”

Section: Introductionmentioning

confidence: 99%

Hydrogen embrittlement in bearing steels

Stopher

Rivera-Dı́az-del-Castillo

2016

Materials Science and Technology

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Hydrogen embrittlement is, and has been for over a century, a prominent issue within many sectors of industry. Despite this, the mechanisms by which hydrogen embrittlement occurs and the suitable means for its prevention are yet to be fully established. Hydrogen embrittlement is becoming an ever more pertinent issue. This has led to a considerable demand for novel hydrogen embrittlement resistant alloys, notably within the bearings industry. This paper provides an overview of the literature surrounding hydrogen embrittlement in bearing steels, and the means by which manufacturers may optimise alloys and accompanying processes to prevent embrittlement. Notably, novel steels combining both high strength and hydrogen embrittlement resistance are reviewed with respect to their design, evaluation methods, and required future work.

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“…TDA is one of the more popular methods, where negligible differences in measurable hydrogen concentrations between TDA methods and the primary mercury methods have been found [37,38], and thus TDA methods are consequently recognised in the BS ISO 3690 [32] for measuring hydrogen in steel welds. Consequently, TDA has been used to measure the concentration of diffusible hydrogen in bearing steels in a number of studies [10,17,28,29,33,[39][40][41][42].…”

Section: Introductionmentioning

confidence: 99%

Thermal Desorption Analysis of Hydrogen in Non-hydrogen-Charged Rolling Contact Fatigue-Tested 100Cr6 Steel

et al. 2017

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Hydrogen diffusion during rolling contact fatigue (RCF) is considered a potential root cause or accelerator of white etching cracks (WECs) in wind turbine gearbox bearing steels. Hydrogen entry into the bearing steel during operation is thought to occur either through the contact surface itself or through cracks that breach the contact surface, in both cases by the decomposition of lubricant through catalytic reactions and/or tribochemical reactions of water. Thermal desorption analysis (TDA) using two experimental set-ups has been used to measure the hydrogen concentration in non-hydrogen-charged bearings over increasing RCF test durations for the first time. TDA on both instruments revealed that hydrogen diffused into the rolling elements, increasing concentrations being measured for longer test durations, with numerous WECs having formed. On the other hand, across all test durations, negligible concentrations of hydrogen were measured in the raceways, and correspondingly no WECs formed. Evidence for a relationship between hydrogen concentration and either the formation or the acceleration of WECs is shown in the rollers, as WECs increased in number and severity with increasing test duration. It is assumed that hydrogen diffusion occurred at wear-induced nascent surfaces or areas of heterogeneous/patchy tribofilm, since most WECs did not breach the contact surface, and those that did only had very small crack volumes for entry of lubricant to have occurred.

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Developing bearing steels combining hydrogen resistance and improved hardness

Cited by 45 publications

References 28 publications

Microstructure of Hot Rolled 1.0C-1.5Cr Bearing Steel and Subsequent Spheroidization Annealing

Microstructure of Hot Rolled 1.0C-1.5Cr Bearing Steel and Subsequent Spheroidization Annealing

Hydrogen embrittlement in bearing steels

Thermal Desorption Analysis of Hydrogen in Non-hydrogen-Charged Rolling Contact Fatigue-Tested 100Cr6 Steel

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