Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants
The creep-fatigue of ferritic CrMo steel has been investigated by measuring the peak interval of the reversible magnetic permeability profile. The peak interval of reversible permeability was discussed in relation to the microstructural evolution during creep-fatigue. The peak interval decreased mon...
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Інститут проблем міцності ім. Г.С. Писаренко НАН України
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irk-123456789-1734312020-12-04T01:26:37Z Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants Kim, C.S. Научно-технический раздел The creep-fatigue of ferritic CrMo steel has been investigated by measuring the peak interval of the reversible magnetic permeability profile. The peak interval of reversible permeability was discussed in relation to the microstructural evolution during creep-fatigue. The peak interval decreased monotonously during creep-fatigue to 0.8N f and increased thereafter. The decrease in the peak interval with increasing fatigue life fraction was related to the coarsening of fine precipitates and recovery of martensite laths. There is a strong linear relationship between the hardness and peak interval of reversible permeability. 2016 Article Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants / C.S. Kim // Проблемы прочности. — 2016. — № 1. — С. 182-187. — Бібліогр.: 12 назв. — англ. 0556-171X http://dspace.nbuv.gov.ua/handle/123456789/173431 539.4 en Проблемы прочности Інститут проблем міцності ім. Г.С. Писаренко НАН України |
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Научно-технический раздел Научно-технический раздел Kim, C.S. Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants Проблемы прочности |
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The creep-fatigue of ferritic CrMo steel has been investigated by measuring the peak interval of the reversible magnetic permeability profile. The peak interval of reversible permeability was discussed in relation to the microstructural evolution during creep-fatigue. The peak interval decreased monotonously during creep-fatigue to 0.8N f and increased thereafter. The decrease in the peak interval with increasing fatigue life fraction was related to the coarsening of fine precipitates and recovery of martensite laths. There is a strong linear relationship between the hardness and peak interval of reversible permeability. |
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Article |
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Kim, C.S. |
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Kim, C.S. |
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Kim, C.S. |
| title |
Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants |
| title_short |
Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants |
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Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants |
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Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants |
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Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants |
| title_sort |
creep-fatigue behavior evaluation by reversible permeability of crmo ferritic steel for ultra-supercritical steem power plants |
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Інститут проблем міцності ім. Г.С. Писаренко НАН України |
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2016 |
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Научно-технический раздел |
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http://dspace.nbuv.gov.ua/handle/123456789/173431 |
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Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo Ferritic Steel for Ultra-Supercritical Steem Power Plants / C.S. Kim // Проблемы прочности. — 2016. — № 1. — С. 182-187. — Бібліогр.: 12 назв. — англ. |
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Проблемы прочности |
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AT kimcs creepfatiguebehaviorevaluationbyreversiblepermeabilityofcrmoferriticsteelforultrasupercriticalsteempowerplants |
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2025-07-15T10:05:28Z |
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2025-07-15T10:05:28Z |
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1837706960363847680 |
| fulltext |
UDC 539.4
Creep-Fatigue Behavior Evaluation by Reversible Permeability of CrMo
Ferritic Steel for Ultra-Supercritical Steem Power Plants
C. S. Kim
Department of Materials Science and Engineering, Chosun University, Gwangju, Republic of Korea
chs2865@chosun.ac.kr
The creep-fatigue of ferritic CrMo steel has been investigated by measuring the peak interval of the
reversible magnetic permeability profile. The peak interval of reversible permeability was discussed
in relation to the microstructural evolution during creep-fatigue. The peak interval decreased
monotonously during creep-fatigue to 0.8N f and increased thereafter. The decrease in the peak
interval with increasing fatigue life fraction was related to the coarsening of fine precipitates and
recovery of martensite laths. There is a strong linear relationship between the hardness and peak
interval of reversible permeability.
Keywords: ferritic steel, fatigue, creep, degradation, permeability.
Introduction. Ferritic steels are key materials in fossil fuel and nuclear power plant
components, such as boilers, steam pipes and steam turbines. The high chromium content
of these steels increases their oxidation resistance; therefore, they can be utilised at higher
temperatures than low alloy ferritic steels. These materials are developed in order to
improve their properties. However, they are inevitably softened during the exposure to
creep and fatigue at high temperatures [1–3]. Throughout the lifetime of a plant component,
the structural material is exposed to various types of loading and temperatures. The extent
of static or cyclic loading effects is normally taken into account during the design stage of
the structural components. Generally, the interaction of various influences, such as cyclic
loading and thermal history, can change the microstructure and mechanical properties upon
occurring. In addition, desirable or undesirable states may occur during service That may
influence the material state or behaviour. When the conventional destructive methods are at
use, material properties changes cannot be detected in facilities during operation due to the
fact that it is impossible to take specimens for microstructural examination and mechanical
tests. Therefore, to ensure the integrity and service life of structural components, it is
essential to understand their mechanical properties on a microstructural level. Many
researchers have studied microstructural characterisation using some nondestructive
evaluation techniques, such as acoustic, magnetic, electrical, and radiation methods [4–7].
However, the magnetic technique is sensitive to microstructural features, including grain
boundaries, precipitates, voids, and dislocations, which are the principal microstructures
contributing to the micromechanical properties of materials [8, 9]. The magnetic adaptive
testing (MAT) was studied by Vértesy et al. with a purpose of comparison with Vickers
hardness of cold rolled low-carbon steel. According to their report, the best linear relation
with the Vickers hardness. Takahashi et al. investigated the relationship between mechanical
and magnetic properties in cold rolled steel. They proposed a closed relation between the
minor loop parameters and the rolling reduction of steel.
Recently, numerous studies have reported the fundamental physics of magnetic
properties of materials in a research context. However, most reports and techniques may be
inapplicable to damage characterisation in the industrial field due to limitations of specimen
preparation and accessibility. The objective of this study is to examine the influence of
creep-fatigue damage on reversible permeability in CrMo ferritic steel and to develop a
nondestructive evaluation technique for damage characterisation.
© C. S. KIM, 2016
182 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
1. Experimental Procedure. The chemical composition of CrMo ferritic steel used in
this study is 0.09 C, 0.23 Si, 0.38 Mn, 0.015 P, 0.013 S, 0.065 Ni, 8.66 Cr, 0.9 Mo, 0.04 Cu,
0.21 V, 0.01 Al, 0.035 N, and 0.07 Nb by wt.%. The test materials were normalised at
1050�C and air cooled, followed by tempering at 760�C. The creep-fatigue test was
conducted at 550�C under load control using a servo-hydraulic fatigue test machine with a
resistance-heating furnace. The hold time at the maximum tensile stress was 600 s.
Cylindrical specimens were prepared, with gauge length of 16 mm, diameter of 10 mm and
shoulder radius of 20 mm. The microstructural observations were performed using field
emission scanning electron microscopy (FESEM) after chemical etching with Vilella’s
reagent. In order to observe the dislocation substructures, thin foils were prepared using
twin-jet polishing. Carbon replication was conducted in order to analyse the composition
and structure of precipitates using transmission electron microscopy (TEM). The reversible
permeability profile was obtained using a ferrite yoke probe.
The yoke probe was wound by pick-up coils: AC perturbing coils for modulating the
magnetic field and DC magnetising coils for magnetizing the test specimens, as shown in
Fig. 1. The specimen with a plate shape of 16 mm length, 5 mm width, and 1 mm thickness
were magnetised by a maximum magnetic field of 12 kA/m with a sinusoidal waveform of
0.05 Hz. A perturbation field of 80 A/m was applied as a reference signal at 40 Hz. The
induced first harmonic voltage in the pick-up coil was obtained using a lock-in amplifier.
The reversible magnetic permeability (� r ) is the limiting value of the incremental
permeability when the alternating field strength approaches zero. According to Ryu et al.,
the most appropriate technique of analysis is measuring the peak interval calculated from
reversible magnetic permeability [10].
2. Results and Discussion. The as-tempered (i.e., normalised and tempered, NT)
specimen exhibited a martensitic structure, containing a high dislocation density in the lath
interior and fine precipitates on the prior austenite grain boundary (PAGB) and martensite
lath boundary, as shown in Fig. 2. The PAG size was about 18 �m, and the width of the
martensite lath was 0.21 �m. Figure 2a represents the typical precipitate morphologies
observed by TEM, depicting tempered martensite, the triple point of PAGB and Cr23C6
precipitates on the PAGBs, as indicated by arrows. As observed by FESEM, well-
developed laths could be clearly seen in Fig. 2b. All precipitates are in line with the lath
boundaries. In Fig. 2c, the martensite lath structure is clearly seen to have elongated laths
and tangled dislocations. The precipitates of 9Cr–1Mo ferritic steel play an important role
in its mechanical properties. Extensive studies have shown two types of carbides, face
Fig. 1. Schematic diagram for the measurement of reversible magnetic permeability.
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 183
Creep-Fatigue Behavior Evaluation by Reversible Permeability ...
centred cubic (fcc) Cr23C6 and (Nb,V)C, and the as-tempered state in CrMo ferritic steel, as
shown in Fig. 2d.
Figure 3 represents the variation in peak interval of a symmetric double-humped curve
of reversible permeability and Vicker’s hardness as a function of the fatigue life fraction in
creep-fatigue damaged CrMo ferritic steel. The peak interval of reversible permeability
decreases during the creep-fatigue up to fracture. However, in the vicinity of the fracture
region denoted by gray square symbol in Fig. 3, it increased by approximately 5.6% more
than in the region far from the fracture. Due to coarsening of the fine precipitates and lath
recovery, the peak interval of reversible permeability is monotonously decreased. However,
the peak interval in near fracture region increases in the final failure as a result of the voids
generated on the packet and PAGB.
Fig. 2. TEM and FESEM micrographs of the as-tempered specimen: (a) TEM micrograph; (b)
FESEM micrograph of lath; (c) TEM micrograph of lath boundaries; (d) TEM micrograph of Cr23C6
and NbC precipitates.
a b
c d
Fig. 3. Peak interval of reversible permeability and Vickers hardness as a function of the fatigue life
fraction in creep-fatigue damaged CrMo ferritic steel.
184 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
C. S. Kim
Vickers hardness continuously decreased until failure, indicating softening. The
variation in reversible permeability and hardness in increasing fatigue life fraction was
related to the microstructural evolution during creep-fatigue, blocking the magnetic domain
wall and dislocation motions. To understand its microstructural effects on permeability and
hardness, microstructural evaluation of precipitates, dislocations, and martensite laths, was
conducted at every stage of creep-fatigue using electron microscope analysis. There was a
strong linear relationship between hardness (Hv) and peak interval (PI) of the reversible
permeability with a correlation coefficient of 0.95 and the following empirical equation.
Hv PI� �765 184. . (1)
Figure 4 shows the FESEM and TEM micrographs. They represent the precipitate
morphologies and dislocation substructures in creep-fatigue specimens at the maximum
tensile hold time of 600 s. The Cr23C6 phase precipitates on the PAGB and the lath
boundary were dominantly coarsened; therefore, the boundaries were unclear. The rapid
coarsening of the precipitates on the PAGB indicated that these boundaries play an
important part in the effective diffusion of solute atoms, such as Cr, Mo, and C. This
implies a diffusion-controlled coarsening mechanism. Diffusion-controlled Ostwald ripening
is expressed as r r kt3
0
3� � , where r and r0 are the average particle radius at times t and
t � 0, respectively. The coarsening rate can be calculated by solving this equation for k.
During creep-fatigue at 550�C, the coarsening rate of the Cr23C6 carbide for 600 s tensile
hold times was approximately 4 4 10 28. � � m3/s. In contrast, the NbC phase is very stable at
this testing temperature (e.g., Tm � �1100 C). The NbC precipitate size does not change
during creep fatigue damage. The number of fatigue failures was 950 cycles for tensile hold
times of 600 s.
The precipitates grew slightly after fatigue failure. The total increase in the precipitates’
average size was approximately 10% or less. The precipitates become effective pinning
sites, which prevent domain-wall motion in relation to a periodic array of coherent
precipitates with the matrix and have a close relationship with the volume fraction of the
Fig. 4. FESEM (a, b) and TEM (c, d) micrographs showing precipitates and dislocation substructures
of creep-fatigue damaged CrMo ferritic steel: (a) 0.2N f at a hold time of 600 s; (b) 0.8N f at a hold
time of 600 s; (c) 0.2N f at a hold time of 600 s; (d) N f at a hold time of 600 s.
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 185
Creep-Fatigue Behavior Evaluation by Reversible Permeability ...
precipitates [11]. In this study, the number of fine precipitates (i.e., Cr23C6) decreased with
the fatigue life fraction due to the coarsening phenomenon resulting in a decrease in the
peak interval of reversible permeability. Also, in this precipitate-hardened material, the fine
precipitates, namely NbC and Cr23C6, are obstacles to the motion of the grain boundary, lath
boundary and dislocation. However, loss of coherency (i.e., coherency strain) due to
coarsening during creep-fatigue can strongly influence softening, (see Fig. 3). Figure 4c
and 4d show typical TEM micrographs of the dislocation substructure in creep-fatigued
specimens prepared using thin foils. The dislocation density in the martensite lath interior
decreased with increasing creep-fatigue for both stress hold times. The as-tempered
specimen showed many elongated martensite lath structures, as previously shown in Fig. 2c.
There were high-density tangled dislocations within the martensite laths. Figure 4c and 4d
show the typical microstructures of 0.2N f and N f at a hold time of 600 s. The lath width
continuously grew during creep-fatigue, and the dislocation density within the lath interior
was lower than that of the as-tempered specimen (see Fig. 4c). The lath width’s growth is
attributed to the recovery of dislocations and the lath boundaries’ recombination. Grain
boundaries influence the domain wall’s motion via an effect related to the deflection of the
magnetic moment existing along the grain boundaries. Coercivity is inversely proportional
to grain diameter in materials where grain boundaries are the dominant obstacles to the
domain wall’s motion [12]. The peak interval of reversible permeability is two times the
coercivity. However, the PAG size does not change during creep-fatigue. Only the subgrain
(lath) size increased significantly after failure (see Fig. 4). This relationship between the
magnetic coercivity and grain size is similar to the present result, which showed a
decreasing peak interval as the martensite lath’s width decreases. The peak interval of
reversible permeability decreases monotonically due to coarsening of fine precipitates and
lath recovery up to 0.8N f of the fatigue life fraction. In contrast, the peak interval increases
in the final failure as a result of the voids generated on the packet boundary and PAGB.
Conclusions. The peak interval of a symmetric double-humped curve of the reversible
permeability reflects the microstructural effects on the domain wall motion. It is therefore
closely related to the fine precipitates, dislocations, laths and void evolution during
creep-fatigue damage. The peak interval of reversible permeability decreases monotonously
due to coarsening of the fine precipitates and lath recovery. However, the increase in the
vicinity of the fracture region was approximately 5.6% higher than that of the region far
from the fracture due to void generation on the packet and PAGB. There is a strong linear
relationship between the hardness and peak interval of the reversible permeability.
Consequently, the peak interval of reversible permeability is a potential parameter,
characterising creep-fatigue damage in fossil fuels and nuclear power materials.
Acknowledgments. This work was financially supported by the National Research
Foundation of Korea (NRF) Grant funded by the Korean Government (NRF-
2013M2A2A9043241).
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Received 03. 08. 2015
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 187
Creep-Fatigue Behavior Evaluation by Reversible Permeability ...
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/HRV (Za stvaranje Adobe PDF dokumenata najpogodnijih za visokokvalitetni ispis prije tiskanja koristite ove postavke. Stvoreni PDF dokumenti mogu se otvoriti Acrobat i Adobe Reader 5.0 i kasnijim verzijama.)
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/NLD (Gebruik deze instellingen om Adobe PDF-documenten te maken die zijn geoptimaliseerd voor prepress-afdrukken van hoge kwaliteit. De gemaakte PDF-documenten kunnen worden geopend met Acrobat en Adobe Reader 5.0 en hoger.)
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/ENU (Use these settings to create Adobe PDF documents best suited for high-quality prepress printing. Created PDF documents can be opened with Acrobat and Adobe Reader 5.0 and later.)
>>
/Namespace [
(Adobe)
(Common)
(1.0)
]
/OtherNamespaces [
<<
/AsReaderSpreads false
/CropImagesToFrames true
/ErrorControl /WarnAndContinue
/FlattenerIgnoreSpreadOverrides false
/IncludeGuidesGrids false
/IncludeNonPrinting false
/IncludeSlug false
/Namespace [
(Adobe)
(InDesign)
(4.0)
]
/OmitPlacedBitmaps false
/OmitPlacedEPS false
/OmitPlacedPDF false
/SimulateOverprint /Legacy
>>
<<
/AddBleedMarks false
/AddColorBars false
/AddCropMarks false
/AddPageInfo false
/AddRegMarks false
/ConvertColors /ConvertToCMYK
/DestinationProfileName ()
/DestinationProfileSelector /DocumentCMYK
/Downsample16BitImages true
/FlattenerPreset <<
/PresetSelector /MediumResolution
>>
/FormElements false
/GenerateStructure false
/IncludeBookmarks false
/IncludeHyperlinks false
/IncludeInteractive false
/IncludeLayers false
/IncludeProfiles false
/MultimediaHandling /UseObjectSettings
/Namespace [
(Adobe)
(CreativeSuite)
(2.0)
]
/PDFXOutputIntentProfileSelector /DocumentCMYK
/PreserveEditing true
/UntaggedCMYKHandling /LeaveUntagged
/UntaggedRGBHandling /UseDocumentProfile
/UseDocumentBleed false
>>
]
>> setdistillerparams
<<
/HWResolution [2400 2400]
/PageSize [612.000 792.000]
>> setpagedevice
|