Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching
Martensitic high carbon high strength AISI E52100 steel (JIS SUJ2) is one of the main alloys used in rolling contact applications when high wear and fatigue resistance are required. In this work, repeated induction heating and quenching of AISI E52100 is proposed and the refinement of the martensite...
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Фізико-механічний інститут ім. Г.В. Карпенка НАН України
2011
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irk-123456789-1382292018-06-19T03:03:07Z Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching Kida, K. Honda, T. Koike, H. Rozwadowska, J. Santos, E.C. Martensitic high carbon high strength AISI E52100 steel (JIS SUJ2) is one of the main alloys used in rolling contact applications when high wear and fatigue resistance are required. In this work, repeated induction heating and quenching of AISI E52100 is proposed and the refinement of the martensite structure and consequently improvement of the fatigue properties measured by rotating bending fatigue tests of steel parts is reported. Високовуглецеву високоміцну мартенситну сталь AISI E52100 (JIS SUJ2) найчастіше використовують за умов контактного кочення, де необхідні підвищені зносотривкість та втомна міцність. Запропоновано методи повторного індукційного нагріву та гартування сталі, внаслідок чого подрібнюється структура мартенситу та поліпшуються втомні властивості під час випробувань сталевих зразків за циклічного згину. Высокоуглеродистую высокопрочную мартенситную сталь AISI E52100 (JIS SUJ2) наиболее часто используют в условиях контактного качения, когда необходимы повышенные износостойкость и усталостная прочность. Предложены методы повторного индукционного нагрева и закаливания стали, вследствие чего измельчается структура мартенситна и улучшаются усталостные свойства во время испытаний стальных образцов при циклическом изгибе. 2011 Article Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching / K. Kida, T. Honda ,H. Koike, , J. Rozwadowska, E.C. Santos // Фізико-хімічна механіка матеріалів. — 2011. — Т. 47, № 5. — С. 96-100. — Бібліогр.: 7 назв. — англ. 0430-6252 http://dspace.nbuv.gov.ua/handle/123456789/138229 en Фізико-хімічна механіка матеріалів Фізико-механічний інститут ім. Г.В. Карпенка НАН України |
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Martensitic high carbon high strength AISI E52100 steel (JIS SUJ2) is one of the main alloys used in rolling contact applications when high wear and fatigue resistance are required. In this work, repeated induction heating and quenching of AISI E52100 is proposed and the refinement of the martensite structure and consequently improvement of the fatigue properties measured by rotating bending fatigue tests of steel parts is reported. |
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Article |
| author |
Kida, K. Honda, T. Koike, H. Rozwadowska, J. Santos, E.C. |
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Kida, K. Honda, T. Koike, H. Rozwadowska, J. Santos, E.C. Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching Фізико-хімічна механіка матеріалів |
| author_facet |
Kida, K. Honda, T. Koike, H. Rozwadowska, J. Santos, E.C. |
| author_sort |
Kida, K. |
| title |
Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching |
| title_short |
Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching |
| title_full |
Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching |
| title_fullStr |
Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching |
| title_full_unstemmed |
Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching |
| title_sort |
fatigue strength improvement of aisi e52100 bearing steel by induction heating and repeated quenching |
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Фізико-механічний інститут ім. Г.В. Карпенка НАН України |
| publishDate |
2011 |
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http://dspace.nbuv.gov.ua/handle/123456789/138229 |
| citation_txt |
Fatigue strength improvement of AISI E52100 bearing steel by induction heating and repeated quenching / K. Kida, T. Honda ,H. Koike, , J. Rozwadowska, E.C. Santos // Фізико-хімічна механіка матеріалів. — 2011. — Т. 47, № 5. — С. 96-100. — Бібліогр.: 7 назв. — англ. |
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96
Ô³çèêî-õ³ì³÷íà ìåõàí³êà ìàòåð³àë³â. – 2011. – ¹ 5. – Physicochemical Mechanics of Materials
FATIGUE STRENGTH IMPROVEMENT OF AISI E52100 BEARING
STEEL BY INDUCTION HEATING AND REPEATED QUENCHING
E. C. SANTOS, K. KIDA, T. HONDA, H. KOIKE, J. ROZWADOWSKA
Kyushu University, Motooka, Fukuoka, Japan
Martensitic high carbon high strength AISI E52100 steel (JIS SUJ2) is one of the main
alloys used in rolling contact applications when high wear and fatigue resistance are re-
quired. In this work, repeated induction heating and quenching of AISI E52100 is pro-
posed and the refinement of the martensite structure and consequently improvement of the
fatigue properties measured by rotating bending fatigue tests of steel parts is reported.
Keywords: induction heating; repeated quenching; high carbon steel.
Induction heating has become widely available as an alternative to furnace heating
for thermal processing of several materials, in particular steel parts [1]. Most steels
with carbon content higher than 0.3% (wt.%) are suitable for hardening by induction
heating. Compared to conventional gas furnace heating treatment, this process offers
several advantages such as fast heating rates, low energy consumption, and cost saving
[1]. The fast heating rates result in structure refinement and better mechanical proper-
ties. Unconventional heat treatment based on temperature cycling is known to reduce
prior austenite grain size (PAGS) in case of gas furnace treatment [2–5]; however there
is still little research about the effect of repeated quenching by induction heating. Mar-
tensitic high carbon high strength AISI E52100 steel (JIS SUJ2) is one of the main
alloys used in rolling contact applications when high wear and fatigue resistance are
required [6]. In this work, repeated induction heating and quenching is applied to
AISI E52100 samples and the influence of this combined process on the microstructure
and fatigue strength is investigated.
Test material and experimental procedures. Material and specimens. The che-
mical composition (wt.%) of the AISI E52100 steel bars was 1.0 C; 1.41 Cr; 0.35 Mn;
0.17 Si; 0.1 Cu; 0.016 Al; 0.02 Mo; 0.015 P; 0.006 Ni; 0.002 S; 59 N; 14Ti and 5 O
(Ti, O, N: ppm). Prior to induction heating the bars were annealed and the initial mic-
rostructure was confirmed to be formed by ferrite and spheroidized cementite particles.
Two types of specimens were prepared: fatigue specimens were machined to fit the
configuration shown in Fig. 1 and bar specimens of 20 mm in diameter were prepared
for metallurgical observation. In each of the fatigue specimens a stress concentrator
(slit of 0.8 mm length, 0.5 mm depth and 0.2 mm radius) was milled. The samples were
mechanically polished before testing. Both bars and rotating bending fatigue specimens
were processed by induction heating once (HT1), twice (HT2) and thrice (HT3). The
induction heating power varied from 40 kW to 50 kW and the frequency was kept
constant at 60 kHz. A photograph of the induction heating apparatus is shown in Fig. 2.
The samples rotated at a speed of 300 rpm as they passed through the coil at a transla-
tional speed of 35 mm/s. The rotating bending machine was designed in-house to test
sample as large as 10 mm to 30 mm in diameter and 20 cm to 50 cm in length. Photo-
graphs of the machine can be seen in Fig. 3.
Corresponding author: E. C. SANTOS, e-mail: santos@mech.kyushu-u.ac.jp
97
Fig. 1. Geometry of the rotating bending samples with a slit. All dimensions in mm.
Fig. 2. Fig. 3.
Fig. 2. Photo of the induction heating process.
Fig. 3. Photos of the rotating bending machine (a) and detail of the sample holder and load (b).
Fig. 4. Microstructure of the samples quenched once and etched by Nital 6% observed by laser
confocal microscope and scanning electron microscope: a – laser confocal microscope image
of the transformed area; b – FEG-SEM high magnification image of the martensitic
transformed area; c – FEG-SEM image of the microstructure of the ferrite + cementite core.
Microstructure and hardness. The martensite and retained austenite were obser-
ved by a laser confocal microscope (LCM) and scanning electron microscope (SEM).
The samples were etched by immersion in Nital 6% for 10 to 20 s. The prior austenite
grain size was observed in samples etched by immersion for 5 min in a Van Giesson
picral solution plus 2 ml of Teepol wetting agent and 2 drops of HCl followed by final
polishing with Buehler’s Mastermet 2 colloidal silica suspension. The martensitic
structure was also observed by electron backscatter diffraction using a Digiview TSL
detector in a Hitachi SU6600 FEG-SEM. The probe current was measured as 10 nA.
An area of 30×30 µm located at 0.2 mm from the edge of each sample was measured
by EBSD. The step size was 50 nm. The micro Vickers hardness profile of the samples
was also measured after repeated induction heating.
X-ray measurements. X-ray diffraction was used to measure the amount of
retained austenite and residual stress before and after the rotating bending tests. A
Bruker D8 discover with GADDS (2D detector) was used. The X-ray tube equipped
with CrKα radiation operated at 35 kV/40 mA. A graphite monochromator was positio-
ned at the incident beam. The detector distance was 15 cm, this corresponds to a ±15°
range from the centre of the detector. The measurements of retained austenite and resi-
98
dual stress were performed using a 100 µm collimator. During the retained austenite
measurements, the 2D detector was positioned at 2θ = 75° (measurement region from
60° to 90°) and ω was scanned from 30° to 45°. The collecting time was 1 hour. The
martensite α-Fe 110 and austenite γ-Fe 111, γ-Fe 200 peaks were fitted and quantified
by Rietveld refinement using TOPAS-academic. During the residual stress measure-
ments, the 2D detector was positioned at 2θ = –143° (measurement region from –128°
to –158°). The martensite α-Fe 211 at 156° was used as a standard. The residual stress
was measured by biaxial mode using 21 frames varying χ from 90° to 30° and ω from
0 to 180°. The collecting time was 7 h (1200 s per frame). Residual stress was calcu-
lated using Bruker’s Leptos 6.3, Pearson VII function.
Results and discussion. Fig. 4 shows the top surface of the once quenched bar
samples after etching in Nital 6%. By repeated quenching, the depth of transformation
increased slightly: from 1.16 mm (quenched once) to 1.25 mm (quenched thrice). Fig. 4a
presents the laser confocal microscope image of the transformed area. The transformed
area is composed of lath and plate martensite (Fig. 4b) while the core is formed by fer-
rite and sphereodized cementite (Fig. 4c). The cementite vol.% and inclusion average
size were measured by SIGMASIS software [7]. The cementite morphology and con-
tent remained unchanged by repeated quenching: the vol.% was around 12% and the
average size was 0.4 µm independent of the number of quenching steps. Several diffe-
rent etchants were used in the attempt to measure the influence of the repeated quen-
ching process on the prior austenite grain size. The best results were achieved by using
the picral solution specified in the experimental procedures. Fig. 5 shows the micro-
graphs of the samples after quenching once and thrice. The prior austenite grain size is
reduced by the repeated quenching process.
Fig. 5. Prior austenite grain size
of samples quenched once (a)
and thrice (b) showing
refinement of the structure.
The prior austenite grain size suggests that the microstructure was refined; howe-
ver, even comparing high resolution FEG-SEM microstructure, the refinement of the
martensitic structure is not clear. Fig. 6 shows the electron backscatter diffraction maps
(orientation image mapping) of samples HT1, HT2 and HT3. The micrographs clearly
indicate that the microstructure was refined by repeated quenching.
Fig. 6. Orientation image mapping (OIM) of samples HT1(a), HT2 (b) and HT3 (c) showing
refinement of the microstructure by repeated quenching.
99
Fig. 7 shows the diffraction pattern
of samples HT1, HT2 and HT3. The
amount of the retained austenite increa-
sed from 32% (HT1) to 41% (HT3). The
retained austenite content was slight
higher in sample HT3 compared to
HT2. Due to the competition between
nucleation of new austenite grains and
grain growth that occur simultaneously,
quenching more than two or three times
does not induce significant microstruc-
ture changes in the material.
The residual stress measurement at
the top surface of the samples can be
seen in Table. Stress σ11 was in the tangential and σ22 in the radial direction. In the
tangential direction (σ11), the stresses were always compressive. The residual stresses
in the radial direction (σ22) were close to zero.
Residual stress measurements
σ11, MPa σ22, MPa
HT1 –228.6 ± 10.4 43.0 ± 9.0
HT2 –149.7 ± 12.7 21.2 ± 11.0
HT3 –106.7 ± 13.3 13.1 ± 11.5
The hardness distribution remained unchanged by the repeated quenching process.
Fig. 8 shows the hardness distribution after quenching once, twice and thrice. The ma-
ximum hardness occurs around 0.3 to 0.6 mm inside the material. The lower hardness
at the surface might be a result of decarburization and/or non-uniform distribution of
the carbon content prior to induction heating. Austenite nucleation and grain growth
occurs when the temperature reaches Ac1 and due to temperature variation from the
surface to the core of the sample, the hardness will be non-uniform. It is important to
notice that even with a 9% increase in the retained austenite content, the hardness
distribution did not change possibly due to the structure refinement.
The S–N curves of the samples measured by rotating bending can be seen in Fig. 9.
The improvement of the fatigue strength as a result of the repeated quenching is clear.
The higher retained austenite content and the refinement of the martensite structure
were effective to increase the fatigue strength of the samples.
Fig. 8. Fig. 9.
Fig. 8. Hardness distribution in the samples quenched once HT1 (○), twice HT2 (●)
and thrice HT3 (□).
Fig. 9. S–N curve of samples after repeated quenching measured by rotating bending test.
Fig. 7. X-ray measurements of samples HT1,
HT2 and HT3 showing increase of retained
austenite content by repeated quenching.
100
CONCLUSIONS
Repeated induction heating and quenching was applied to AISI E52100 shafts.
The microstructure of the material was observed by laser confocal microscopy, scan-
ning electron microscopy and orientation image mapping. The hardness, retained aus-
tenite content, residual stresses and fatigue properties were measured. The repeated
quenching process decreased the prior austenite grain size and consquently refined the
martensitic structure of the samples. The retained austenite content increased. Residual
stresses were compressive in the tangential and close to zero in the radial direction. The
refinement of the martensitic structure and higher content of retained austenite after
quenching thrice increased the fatigue strength of the material.
РЕЗЮМЕ. Високовуглецеву високоміцну мартенситну сталь AISI E52100 (JIS SUJ2)
найчастіше використовують за умов контактного кочення, де необхідні підвищені зносо-
тривкість та втомна міцність. Запропоновано методи повторного індукційного нагріву та
гартування сталі, внаслідок чого подрібнюється структура мартенситу та поліпшуються
втомні властивості під час випробувань сталевих зразків за циклічного згину.
РЕЗЮМЕ. Высокоуглеродистую высокопрочную мартенситную сталь AISI E52100
(JIS SUJ2) наиболее часто используют в условиях контактного качения, когда необходи-
мы повышенные износостойкость и усталостная прочность. Предложены методы повтор-
ного индукционного нагрева и закаливания стали, вследствие чего измельчается структу-
ра мартенситна и улучшаются усталостные свойства во время испытаний стальных образ-
цов при циклическом изгибе.
Acknowledgements. The authors would like to thank Mr. Kinoshita from
Keyence and Dr. Saito from Bruker for the help with the laser confocal microscope
and x-ray measurements, respectively. We would also like to express our gratitude to
Dr. Suzuki from TSL Japan for the EBSD measurements and Mr. Shibukawa from
YSK, Co., Ltd., for providing the heat treated samples.
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Received 02.02.2011
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