A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
837–843
THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN
X5CrNi18-10 STEEL AFTER ITS STRAIN-INDUCED
MARTENSITIC TRANSFORMATION
MIKROSTRUKTURA METASTABILNEGA AVSTENITA PO
PRETVORBI V NAPETOSTNO INDUCIRANI MARTENZIT V
JEKLU X5CrNi18-10
Agnieszka Kurc-Lisiecka1, Wojciech Ozgowicz2, El¿bieta Kalinowska-Ozgowicz3,
Wojciech Maziarz4
1Rail Transport Department, University of Dabrowa Gornicza, Cieplaka Str. 1C, 41-300 Dabrowa Gornicza, Poland
2Institute of Engineering Materials and Biomaterials, Silesian University of Technology, Gliwice, Poland
3Fundamentals of Technology Faculty, Lublin University of Technology, Nadbystrzycka Str. 38, 20-618 Lublin, Poland
4Institute of Metallurgy and Materials Science of the Polish Academy of Sciences, Reymonta Str. 25, 30-059 Krakow, Poland
akurc@wp.pl
Prejem rokopisa – received: 2015-05-19; sprejem za objavo – accepted for publication: 2015-11-05
doi:10.17222/mit.2015.102
The performed investigations concerned the influence of the degree and temperature of deformation on the microstructure of
metastable austenite in the stainless steel X5CrNi18-10 after its strain-induced martensitic transformation. Samples of steel strip
were cold rolled within a degree of deformation from 20 % to 70 % and stretched at a low temperature of -196 °C. The
microstructure was observed by means of scanning electron microscopy (SEM) and transmission electron microscopy (TEM,
HREM). It wasen found that after cold rolling with a small degree of deformation (20 %) in the tested steel, generally a
single-phase microstructure of the matrix  is found with a high density of dislocations and numerous deformation bands
morphologically characteristic of stainless steel with a low stacking-fault energy. After rolling with a 50 % thickness reduction,
however, the microstructure displayed deformation twins as well as refined morphologic formations of the phase ’, mostly
localized in the vicinity of the grain boundaries of the metastable matrix , and also trace amounts of carbide precipitates. In
samples stretched at a temperature of -196 °C the microstructure of the matrix displayed a considerable density of dislocations
with lath areas of the martensite ’ and precipitations of the carbides M23C6. Moreover, the tested steel revealed a
crystallographic dependence of the planes and directions on the identified phases  and ’, corresponding to dependences of the
Kurdjumov-Sachs type, independent of the method and temperature of the plastic deformation. Tests carried out in the TEM
proved that the typical sites of nucleation induced by the plastic deformation of martensite are the shear bands, particularly their
intersection. The preferred mechanism of transformation, observed in the conditions of cold rolling is, however, a direct
transformation of the type  (fcc)  ’ (bcc).
Keywords: austenitic stainless steels, cold rolling, microstructure, phase transformation, strain- induced martensite
Izvedene so bile preiskave vpliva temperature in stopnje deformacije na mikrostrukturo metastabilnega avstenita po njegovi
pretvorbi v napetostno inducirani martenzit v jeklu X5CrNi18-10. Vzorci v obliki trakov so bili hladno valjani s stopnjo
deformacije od 20 % do 70 % in natezani pri nizki temperaturi – 196 °C. Mikrostruktura je bila opazovana s pomo~jo vrsti~ne
elektronske mikroskopije (SEM) in s presevno elektronsko mikroskopijo (TEM, HREM). Ugotovljeno je, da je po hladnem
valjanju z majhno stopnjo deformacije (20 %) v preizku{anem jeklu dobljena enofazna mikrostruktura z osnovo , z visoko
gostoto dislokacij in {tevilnimi deformacijskimi pasovi, ki so morfolo{ka zna~ilnost nerjavnega jekla z nizko energijo napake
zloga. Po valjanju s 50 % zmanj{anjem debeline, se v mikrostrukturi poka`ejo deformacijski dvoj~ki, kot tudi drobni nastanki
faze ’, ve~inoma v bli`ini mej zrn metastabilne osnove  in tudi sledi izlo~kov karbidov. V vzorcih natezno obremenjenih pri
temperaturi –196 °C je mikrostruktura osnove pokazala precej{njo gostoto dislokacij z latastimi podro~ji martenzita ’ in
izlo~ki karbidov M23C6. Poleg tega je preiskovano jeklo pokazalo kristalografsko odvisnost usmerjenosti ravnin in ploskev v
identificiranih fazah  in ’, ustrezno odvisnosti vrste Kurdjumov-Sachs, neodvisno od metode in temperature plasti~ne
deformacije. Preiskave izvedene na TEM so potrdile, da so zna~ilna mesta nukleacije martenzita, inducirane s plasti~no
deformacijo, stri`ni pasovi, posebno {e njihova kri`anja. Prednostni mehanizem premene, opa`ene pri hladnem valjanju, je
neposredna premena vrste  (fcc)  ’ (bcc).
Klju~ne besede: avstenitna nerjavna jekla, hladno valjanje, mikrostruktura, fazna premena, napetostno inducirani martenzit
1 INTRODUCTION
Austenitic stainless steels are widely used in many
engineering applications, such as in the chemical, machi-
nery, food, automotive, nuclear and shipbuilding indus-
tries, due to their excellent corrosion resistance, weld-
ability, and mechanical properties. However, some of
these austenitic steels with a lower content of Ni can
undergo a transformation to martensite during cold
working.1 A different martensite morphology can be
formed due to these processes, mainly strain-induced or
stress-induced martensite.2 In austenitic stainless steels
two types of martensite can form spontaneously, i.e.,
body-centered cubic (bcc) martensite ’ and hexagonal
close-packed (hcp) martensite . The amount of  and/or
’ martensite depends on the chemical composition,
stacking-fault energy, phase stability and processing
parameters, such as stress state, temperature, strain rate.
Materiali in tehnologije / Materials and technology 50 (2016) 6, 837–843 837
UDK 669.112.227.34:669.15-194.5:669.112.227.1 ISSN 1580-2949
Original scientific article/Izvirni znanstveni ~lanek MTAEC9, 50(6)837(2016)
During the deformation process different transformation
sequences take place, such as:     ’ or   ’. In
the transformation mode     ’,  martensite acts as
the precursor phase of ’. The formation of ’ is closely
related to the shear bands, which are planar defects
associated with the overlapping of stacking faults on
111. Depending on the nature of the overlapping,
twins,  martensite or stacking-fault bundles may be
formed. Twins are formed when stacking faults overlap
on successive {111} planes, whereas  martensite is
generated if the overlapping of the stacking faults occurs
on alternate 111 planes. Stacking-fault bundles arise
from the irregular overlapping of stacking faults.1–6
The presence of deformation-induced martensite may
be a harmful phenomenon and may cause a delayed
cracking of deep-drawn austenitic stainless-steel compo-
nents. On the other hand, the formation of martensite
resulting from the plastic deformation of metastable
austenite is of great interest for the production of high-
strength and ductile austenitic stainless steels.2,3
The aim of the present study was to analyze the
morphological details of strain-induced martensite in
cold-rolled Cr-Ni steel.
2 MATERIAL AND EXPERIMENTAL
PROCEDURE
The investigations concerned austenitic stainless steel
of the type X5CrNi18-10 in compliance with PN-EN
10088:1-2007 7 with the chemical composition quoted in
Table 1. The input material in the form of steel strip,
2 mm thick, 40 mm in width and 700 mm long was
supersaturated in water after its austenitizing for 1 h at a
temperature of 1100 °C and cold rolled with a 20 %,
50 % and 70 % thickness reduction. After rolling with a
draft of 70 %, samples of the tested steel were subjected
to a tensile test at a low temperature of –196 °C with a
strain rate  of about 10–5 s–1.
Table 1: Chemical composition of the investigated steel
Tabela 1: Kemijska sestava preiskovanih jekel
Elements content, in mass fractions (w/%)
C Mn Si P S Cr Ni Ti Al Fe
0.024 1.32 0.43 0.028 0.005 18.53 7.8 0.010 0.01 bal.
The hardness measurements of the investigated
cold-rolled steel were carried out with a microhardness
tester FM 700 produced by Future-Tech (Japan),
according to the standard PN-EN ISO 6507-1:2007.8 The
hardness was also determined in the case of the sample
after 70 % degree and stretched at a low temperature of
–196 °C with a strain rate  of about 10–5 s–1. The
measurements were made using the Vickers method on
metallographic samples with a load of 50 N for a time of
30 s.
The microstructural investigations were performed
with scanning (SEM) and transmission electron micro-
scopy, as well as high-resolution electron microscopy
(HREM). Applying SEM, a metallographic polished sec-
tion after cold rolling with a draft of 20 % and stretching
at the temperature of liquid nitrogen was detected. These
observations were made by means of SEM of the
SUPRA type from Zeiss (Germany) with a magnification
of 15.000×.
The section that was mechanically polished was
etched in the reagent Mi17Fe.9 TEM observations were
carried out using thin foils on the samples of strip after
cold rolling with a draft of 50 %, and on samples
stretched at a temperature of –196 °C. The preparation of
the foils comprised a cutting out of disks, 3 mm in dia-
meter, from a strip with a thickness of 1.0 and 0.6 mm,
grinding with abrasive paper until the samples reached a
thickness of 0.1 mm. The Tenupol-5 double jet electro-
polisher was used for thin foil preparation from the
samples in an electrolyte containing nitric acid and
methanol (1:3). The microstructure was observed by
means of TEM of the type Technai G2 F20 applying an
accelerating voltage of 200 kV equipped with high-angle
annular dark-field (HAADF) and energy-dispersive
(EDS) detector. The phases were identified based on
electron diffraction. The procedure was aided by the
A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
838 Materiali in tehnologije / Materials and technology 50 (2016) 6, 837–843
Figure 1: Microstructure of investigated steel X5CrNi18-10: a) after
20 % of deformation, b) after cold-rolling with 70 % and tensile test at
–196 °C, etching- Mi17Fe
Slika 1: Mikrostruktura preiskovanega jekla X5CrNi18-10: a) po 20
% deformaciji, b) po hladnem valjanju s 70 % in nateznim preizkusom
pri –196 °C, jedkano z Mi17Fe
computer software Gatan and a crystallographic data-
base.
3 RESULTS AND DISCUSSION
In the supersaturated state the investigated steel dis-
plays a single-phase austenite structure with a diameter
of the average grains in the matrix  amounting to about
75 ìm and a hardness of about 125 HV0.5, containing
many annealed twins and single clusters of non-metallic
inclusions. After cold rolling in the range 20–30 %
metallographically distinctly elongated grains of the
matrix  with a hardness of 323 HV5 (Table 2) could be
detected with numerous effects of work hardening in the
form of fine parallel and intersected lines and slip bands,
as well as shear bands, which are probably sites of mar-
tensite ’ nucleation.
Table 2: Results of the hardness measurement of the investigated
cold-rolled and stretched steel
Tabela 2: Meritve trdote preiskovanih hladno valjanih in natezanih
jekel
No. Material condition
Hardness, HV Hard-
ness,
HV 5
Number of measurement
1 2 3
1 supersaturated 144.7 148.5 145.8 146.3
2 cold rolled zh=20% 321.5 322.7 325.9 323.4
3 cold rolled zh=50% 411.5 410.8 408.7 410.3
4 cold rolled zh=70% 418.5 417.4 418.6 418.1
5
cold rolled with
zh=70% and
stretched at –196C
460.1 461.3 459.2 460.2
The results of the observation of the microstructure
of the investigated steel after cold-rolling with a degree
of deformation of 20 % and 70 % and after stretching at
a temperature of –196 °C carried out on a scanning elec-
tron microscope (SEM) are presented in the micrographs
A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
Materiali in tehnologije / Materials and technology 50 (2016) 6, 837–843 839
Figure 3: TEM micrograph structure of X5CrNi18-10 steel after 50 %
of deformation: a) microstructure of the matrix  containing
microtwins and martensite ’, b) dark field taken of reflection (200) ,
c), d) diffraction pattern
Slika 3: TEM-posnetek strukture jekla X5CrNi18-10 po 50 %
deformaciji: a) mikrostruktura osnove , ki vsebuje mikrodvoj~ke in
martenzit ’, b) temno polje pri odsevu (200) , c), d) uklonska slika
Figure 2: TEM micrograph of X5CrNi18-10 steel after 50 % of deformation: a) a band of austenite containing microtwins, b) diffraction pattern
Slika 2: TEM-posnetek jekla X5CrNi18-10 po 5 % deformaciji: a) pas avstenita, ki vsebuje mikrodvoj~ke, b) uklonska slika
A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
840 Materiali in tehnologije / Materials and technology 50 (2016) 6, 837–843
Figure 5: TEM micrograph structure of X5CrNi18-10 steel after 50 %
of deformation: a) cell microstructure of austenite containing a
variable dislocation density and ultra-fine lath of martensite ’, b)
diffraction pattern
Slika 5: TEM-posnetek strukture jekla X5CrNi18-10 po 50 % defor-
maciji: a) celi~na mikrostruktura avstenita vsebuje razli~no gostoto
dislokacij in ultra drobni latasti martenzit ’, b) uklonska slika
Figure 4: TEM micrograph structure of X5CrNi18-10 steel after 50 %
of deformation: a) subgrain of austenite containing a high density of
dislocations and ’, bright field, b) dark field taken of the reflection
(110)’, c) diffraction pattern
Slika 4: TEM-posnetek strukture jekla X5CrNi18-10 po 50 %
deformaciji: a) podzrna avstenita vsebujejo veliko gostoto dislokacij
in ’, svetlo polje, b) temno polje pri odsevu (110) ’, c) uklonska
slika
Figure 6: High-resolution (HREM) micrograph: a) dislocation structure of the matrix  of steel B after cold rolling (zh=50 %) and Fourier
transform (FFT), b) detail A of Figure 6a – modulated structure (IFFT) with microtwins bands and Fourier transform (FFT), c) solution of
Fourier transform in Figures 6a and 6b
Slika 6: Visokolo~ljivi posnetek (HREM): a) struktura dislokacij v osnovi  jekla B po hladnem valjanju (zh=50 %) in Fourierjeva pretvorba
(FFT), b) detajl A na Sliki 6a modulirana struktura (IFFT) s pasovi mikro tvoj~kov in Fourierjeva pretvorba (FFT), c) re{itev Foirierjeve
pretvorbe na Slikah 6a in 6b
in Figure 1. In the structure of the steel, complex effects
of deformation inside the grains  and at the boundaries
are revealed (Figure 1a). Plastic deformation leads to a
distinct elongation of the grains in the direction of roll-
ing and to the formation of numerous slide bands and
shear bands, in which probably the martensite ’ is loca-
lized (Figure 1b). The hardness of the examined steel
increases with an increasing degree of deformation. With
the increase of the cold rolling degree from 50 % to 70
% the hardness of the investigated steel increases from
410 to 418 HV5, respectively (Table 2). As suggested
in10,11 the twins, the dislocation density, the nucleation of
martensite ’ and the increase of the volume fraction of
martensite ’ phase during the transformation are the
major factors influencing the hardness of the investigated
steel.
Heterogeneities in the plastic deformation in the form
of shear bands were found mainly in the case of larger,
cold plastic working and tensile tests at reduced tempe-
ratures up to –196 °C. Thin foils in the TEM revealed in
steel X5CrNi18-10, cold rolled with a degree of defor-
mation of 50 %, a cellular structure of dislocations of an
austenitic matrix with a considerable density of disloca-
tions with local twins (Figure 2). Also, single reflexes of
the type (112)’ and (123)’ were observed, resulting
from the martensitic phase ’ (Figure 3d). Based on
electron diffraction and the dark-field method, the
localisation of the deformation twins could be identified
and the direction of twinning (TD) <111> o was deter-
mined (Figures 2b and 3d). In the microstructure of the
investigated steel, highly elongated subgrain  and
shearing bands dominate, and also an ultra-fine lath of
martensite ’ with a characteristic dislocation forest
(Figures 4 and 5). After cold rolling, observed in high-
resolution microscopy (HREM), the structure of the
investigated steel reveals significant morphological
details – on the nanometer scale – microbands of mecha-
nical twinning as well as in the range of periodicity of
the structure and its modulated character (Figure 6). The
disclosed structural periodicity is reflected in the
A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
Materiali in tehnologije / Materials and technology 50 (2016) 6, 837–843 841
Figure 8: TEM micrograph structure of the X5CrNi18-10 steel: a)
mechanical twins after 70 % of deformation and tensile test at tem-
perature of –196 °C with  =10–5 s–1, b) dark field in (002), c), d)
diffraction pattern
Slika 8: TEM-posnetek strukture jekla X5CrNi18-10: a) mehanski
dvoj~ki po 70 % deformaciji in nateznem preizkusu pri –196 °C, z
 =10–5 s–1, b) temno polje pri (002) , c), d) uklonska slika
Figure 7: TEM micrograph structure of X5CrNi18-10 steel after
cold-rolling with 70 % and tensile test at temperature of -196 °C with
a strain rate of 10–5 s–1: a) microstructure of elongated subgrain  with
shear bands and heavily deformed lath of martensite ’, b) diffraction
pattern from a, c) detail in Figure a, d) diffraction pattern from c
Slika 7: TEM-posnetek strukture jekla X5CrNi18-10 po hladnem
valjanju, 70 % in nateznem preizkusu pri –196 °C, s hitrostjo obre-
menjevanja 10–5 s–1: a) mikrostruktura razpotegnjenih podzrn , s
stri`nimi pasovi in mo~no deformiranimi latami martenzita-’, b)
uklonska slika iz a, c) detajl iz slike a, d) uklonska slika iz c
distribution of the atomic cores in the inverse Fourier
transform (IFFT) (Figure 6c). High-resolution analysis
of the sequence of microtwin bands (Figure 6a) and the
corresponding Fourier transforms (FFT), comprising the
entire area of HREM (Figure 6b) and the marked area of
the microstructure (Figure 6c) justify the statement that
the visible and most intense reflections result mainly
from the matrix  oriented as a zone axis of orientation
[011] (Figure 6b). The additional weak reflections
between the reflections of the planes (002) and (111) 
can be attributed to the deformation twins (Figure 6b).
However, the presence of two weak reflections between
the beam passing (000) and the planes (111) and
(111), dividing these distances into three equal parts
with a length of 1/3 (111), require an explanation. The
presence of these reflections is not justified, however, in
the case of twin orientations.12 In the transform (FFT)
concerning the area of the band of microtwins (Figure
6c) there is a twin orientation with strong defocusing
reflections in the planes (111). The inverse Fourier
transform resulting from a transform (FFT) (Figure 6c)
after filtering out the noise reveals that in the matrix 
(M-matrix) a microtwin (T-twin) is located with a width
of about 5 nm, inside which the modulation effects are
visible. Modulations are caused by periodic sequences of
stacking faults occurring on the following planes (111)
(Figure 6d).
The investigated cold-rolled steel with the degree of
deformation of 70 % and then subjected to a tensile test
at strain rate () of about 10–5 s–1 at cryogenic tem-
peratures –196 °C displayed – similar to the cold-rolling
– a subgrain structure elongated in the rolling direction
with a high density of dislocations (Figure 7) and a
considerably higher density of microtwinning (Figure
8). The hardness in these areas reaches about 460 HV5
(Table 2). The subgrain boundaries and the microtwins
constitute potential locations for the phase ’, in the
form of elongated lamellar areas with a width of
approximately 0.1 μm (Figure 7b). It can be assumed
that the nucleation of the phase ’ occurs preferentially
in microtwins areas, mainly at their borders. It is sig-
nificantly associated with the accumulation of the stress
in a dislocation field, as suggested in11. Electron-diffrac-
tion analysis of the investigated steel not only provides
evidence for the presence in its structure of martensitic
phase ’ (Figures 3d, 4b, 5b, 7a, 7b and 8d) and M23C6
type carbides (Figure 8d), but also the occurrence of a
crystallographic relationship between the matrix  and
phase ’ type K-S, namely: (111)  II (011)’ and
<011>  II <111> ’ (Figure 4b), also quoted with res-
pect to similar grades of Cr-Ni steel.11,13
4 CONCLUDING REMARKS
The structural investigations of the steel
X5CrNi18-10 conducted in a TEM and the analysis of
the obtained results allows us to draw the following
conclusions:
The plastic deformation of the investigated steel
X5CrNi18-10 induces the direct transformation of
metastable austenite to the deformation martensite ’ of
the (bcc) lattice during both the cold-rolling process, as
well as the tensile test at temperatures lowered to –196
°C.
The microstructure of the investigated steel after cold
rolling with a degree of deformation in the range from
50 % to 70 % observed in the TEM, displays a high dis-
location density in the matrix  and the presence of
mechanical twins, as well as shearing bands in the area
where the lamellar formations of the martensite ’ phase
nucleate.
The cold rolling and stretching at low temperature of
the austenitic stainless-steel sheets resulted in the occur-
rence of the strain-induced   ’ phase transformation.
During plastic deformation the volume fraction of mar-
tensite ’ phase increases, which causes the hardening of
the investigated steel. The hardness of the cold-rolled
steel within the draft from 20–70 % is from the range
323–418 HV5, whereas in the case of samples after 70 %
degree of cold rolling and stretching at –196 °C it is
about 460 HV5.
High-resolution electron microscopy (HREM) of the
microstructure revealed essential morphological details
of the resulting microbands of twins on the nanometer
scale. The application of Fourier’s reverse transform
(IFFT) indicated a periodicity of the analyzed structure
and its modulated character in the range of appearing
sequentially, the local disorder of the crystalline lattice.
The transformations   ’ of the investigated steel
induced by plastic deformation indicate a typical crystal-
lographic relationship between austenite and martensite
’ given by Kurdjumov-Sachs, in the form:
(111)II(011)’ and <011>II<111>’.
Acknowledgements
The authors gratefully acknowledge financial support
from the research project: Innovative sanitary sewage
system DEMONSTRATOR + NCBR under the contract
No. UOD-DEM-1-591/001.
5 REFERENCES
1 K. H. Lo, C. H. Shek, J. K. L. Lai, Morphologies and characteristics
of deformation induced martensite during tensile deformation of 304
LN stainless steel, Materials Science and Engineering, 65R (2009)
4–6, 39–104, doi:10.1016/j.msea.2007.09.005
2 A. Das, S. Sivaprasad, M. Ghosh, P. C. Chakraborti, S. Tarafder,
Morphologies and characteristics of deformation induced martensite
during tensile deformation of 304 LN stainless steel, Materials
Science and Engineering, 486A (2008), 283–286, doi:10.1016/
j.msea.2007.09.005
3 J. Huang, X. Ye, Z. Xu, Effect of Cold Rolling on Microstructure and
Mechanical Properties of AISI 301LN Metastable Austenitic Stain-
A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
842 Materiali in tehnologije / Materials and technology 50 (2016) 6, 837–843
less Steels, Journal of Iron and Steel Research International, 19
(2012) 10, 59–63, doi:10.1016/S1006-706X(12)60153-8
4 C. J. Gunter, R. P. Reed, Transaction of American Society for Metals,
55 (1962) 3, 399–419
5 S. Rajasekhara, L. P. Karjalainen, A. Kyröläinen, P. J. Ferreira,
Microstructure evolution in nano/submicron grained AISI 301LN
stainless steel, Materials Science and Engineering, 527A (2010),
1986–1996, doi:10.1016/j.msea.2009.11.037
6 T. Angel, Journal of the Iron and Steel Institute, 177 (1954), 165–174
7 European Standard, Stainless Steels - Part 1: List of stainless steels,
Polish version PN-EN 10088:1-2007
8 European Standard, Metals. Hardness measurements made by
Vickers’s method, Polish version PN-EN ISO 6507-1:2007
9 ASTM E407, Standard Practice for Microetching Metals and Alloys
10 W. S. Lee, C. F. Lin, The morphologies and characteristics of
impact-induced martensite in 304L stainless steel, Scripta Materialia,
43 (2000) 8, 777–782, doi:10.1016/S1359-6462(00)00487-5
11 J. A. Venables, The martensite transformation in stainless steel, Phi-
losophical Magazine, 73 (1962) 7, 35–44, doi:10.1080/
14786436208201856
12 W. Maziarz, Structure changes of Co–Ni–Al ferromagnetic shape
memory alloys after vacuum annealing and hot rolling, Journal of
Alloys and Compounds, 448 (2008) 1–2, 223–226, doi:10.1016/
j.jallcom.2006.12.044
13 M. Blicharski, S. Gorczyca, Structural inhomogeneity of deformed
austenitic stainless steel, Metal Science, 12 (1978) 7, 303–312,
doi:10.1179/msc.1978.12.7.303
A. KURC-LISIECKA et al.: THE MICROSTRUCTURE OF METASTABLE AUSTENITE IN X5CrNi18-10 STEEL ...
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