Tensile properties of a Fe-32Mn-6Si shape memory alloy
The tensile properties of a Fe-32Mn-6Si shape memory alloy were investigated. It was found that tensile properties depend on temperature, heat treatment and material structure. The relationships of martensitic transformation, tensile properties, and shape memory effect are discussed. Finally,...
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| Опубліковано в: : | Проблемы прочности |
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| Дата: | 2008 |
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Інститут проблем міцності ім. Г.С. Писаренко НАН України
2008
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| Цитувати: | Tensile properties of a Fe-32Mn-6Si shape memory alloy / T. Bouraoui, F. Jemal, T. Ben Zinebc // Проблемы прочности. — 2008. — № 2. — С. 55-65. — Бібліогр.: 11 назв. — англ. |
Репозитарії
Digital Library of Periodicals of National Academy of Sciences of Ukraine| _version_ | 1859847998011342848 |
|---|---|
| author | Bouraoui, T. Jemal, F. Ben Zinebc, T. |
| author_facet | Bouraoui, T. Jemal, F. Ben Zinebc, T. |
| citation_txt | Tensile properties of a Fe-32Mn-6Si shape memory alloy / T. Bouraoui, F. Jemal, T. Ben Zinebc // Проблемы прочности. — 2008. — № 2. — С. 55-65. — Бібліогр.: 11 назв. — англ. |
| collection | DSpace DC |
| container_title | Проблемы прочности |
| description | The tensile properties of a Fe-32Mn-6Si shape
memory alloy were investigated. It was found
that tensile properties depend on temperature,
heat treatment and material structure. The relationships
of martensitic transformation, tensile
properties, and shape memory effect are discussed.
Finally, we propose a macroscopic
one-dimensional constitutive law describing
the thermomechanical behavior in tensile loading.
Numerically obtained results are close to
the experimental ones.
Досліджуються характеристики міцності сплаву Fe-32Mn-6Si з пам’яттю
форми при статичних випробуваннях на розтяг. Показано, що ці характеристики
залежать від температури, термообробки та мікроструктури матеріалу.
Аналізується взаємозв’язок між процесом мартенситного перетворення і
характеристиками міцності та ефектом пам’яті форми матеріалу, в результаті
чого запропоновано одновимірне рівняння стану, яке описує термомеханічну
поведінку матеріалу при статичному розтязі. Отримано хорошу
збіжність між результатами числових розрахунків і експериментальними
даними.
Исследуются характеристики прочности сплава Fe-32Mn-6Si с памятью формы при статических
испытаниях на растяжение. Показано, что эти характеристики зависят от
температуры, термообработки и микроструктуры материала. Анализируется взаимосвязь
процесса мартенситного превращения с характеристиками прочности и эффектом памяти
формы материала, в результате чего предложено одномерное уравнение состояния, описывающее
термомеханическое поведение материала при статическом растяжении. Получено
хорошее соответствие между результатами численных расчетов и экспериментальными
данными.
|
| first_indexed | 2025-12-07T15:39:44Z |
| format | Article |
| fulltext |
UDC 539.4
Tensile Properties of a Fe-32Mn-6Si Shape Memory Alloy
T. Bouraoui,ab F. Jemal,b and T. Ben Zinebc
a Institut Préparatoire aux Études d’Ingénieurs de Monastir, Université de Monastir,
Monastir, Tunisie
b Laboratoire des Systèmes Électromécaniques, Université de Sfax, Sfax, Tunisie
c Laboratoire d’Énergétique et de Mécanique Théorique et Appliquée, Université de
Nancy, Nancy, France
У Д К 539.4
Характеристики прочности сплава Fe-32Mn-6Si с памятью формы
при статических испытаниях на растяжение
Т. Бурауиаб, Ф. Джемал6, Т. Бен Зинебв
а Институт подготовки инженеров, Университет г. Монастир, Тунис
6 Лаборатория электромеханических систем, Университет г. Сфакс, Тунис
в Лаборатория энергетики и теоретической и прикладной механики, Университет
г. Нанси, Франция
Исследуются характеристики прочности сплава Fe-32M n-6Si с памятью формы при ста
тических испытаниях на растяжение. Показано, что эти характеристики зависят от
температуры, термообработки и микроструктуры материала. Анализируется взаимосвязь
процесса мартенситного превращения с характеристиками прочности и эффектом памяти
формы материала, в результате чего предложено одномерное уравнение состояния, описы
вающее термомеханическое поведение материала при статическом растяжении. Получено
хорошее соответствие между результатами численных расчетов и экспериментальными
данными.
К л ю ч е в ы е с л о в а : сплавы с памятью формы на основе железа, характерис
тики прочности при растяжении, термомеханическое поведение, моделиро
вание.
Introduction. It is well known that shape memory alloys (SMA) are a
particular class of materials that can recover a memorized shape by simple
heating. This remarkable property, called the shape memory effect (SME), can be
exploited in the design of original applications able to bring interesting answers to
problems encountered in various industrial fields.
In addition to the classical non ferrous alloys (Ni-Ti- and Cu-based alloys),
iron-based SMA have attracted much attention recently due to their low cost, high
mechanical strength and good formability [1-7].
In Fe-M n-Si-based shape memory alloys system, the parent phase, face
centred cubic austenite (y), transforms to hexagonal (g) martensite by the
formation and overlap of stacking faults. The martensite can be reversed to parent
austenite on annealing, and this imparts the SME [1, 2].
© T. B O U RA O U I, F. JEM A L, T. B EN Z IN EB , 2008
ISSN 0556-171X. Проблемы прочности, 2008, № 2 55
T. Bouraoui, F. Jemal, and T. Ben Zineb
A wide range of experimental works have been carried out in order to
characterize metallurgical properties and thermomechanical behavior of iron-
based shape memory alloys [1-7]. But, works dealing on their behavior modeling,
necessary to the optimization of their performance and application design are still
at an embryonic stage.
Tensile properties are fundamental benchmarks for development of new
materials and essential input material parameters for numerical modeling in order
to design applications. For this reason, we present in this paper a study of
iron-based SMA thermomechanical behavior in tensile. The adopted alloy is the
Fe-32M n-6Si which is considered as a good reference of the iron-based SMA.
The purpose of this paper is to report the effect of heat treatments and temperature
on tensile behavior. The relationship of martensitic transformation, tensile
properties and shape memory effect are also discussed. Finally, we propose a
macroscopic one-dimensional constitutive law able to describe the thermo
mechanical behavior in tensile.
Experim ental Procedure. The studied SMA in this work was obtained from
Aubert & Duval Company [4]. The alloy was supplied as 18 X18 mm swaged bars
and 1373 K water quenched. The chemical composition (in wt.%) of this
polycrystalline alloy is given in Table 1.
T a b l e 1
Chemical Composition of Studied Alloy
Fe Mn Si C
Balanced 31.6 6.45 0.01S
This composition is considered as the reference of iron-based shape memory
alloys. The 6.45% of silicon rate is an optimal value leading to a weak stacking
fault energy favorable to the reversibility of y ( F C C ) ^ £ ( H C P ) martensitic
transformation [5].
Tensile samples were cut by electroerosion machining a long the bar
direction. The shape and dimensions of samples are given in Fig. 1.
135
Fig. 1. Shape and dimensions (in mm) o f tensile samples.
The tensile tests are performed on an MTS machine using a load cell with
maximum capacity of 5 kN and an extensometer with a gauge length of 50 mm.
Strain rate was fixed at 2 - 10 4 s 1.
X-ray diffraction analysis was performed using a Philips diffractometer using
monochromatic Cu radiation (2 = 0.15405 nm).
56 ISSN Ü556-171X. Проблемыг прочности, 2ÜÜ8, N 2
Tensile Properties o f a Fe-32M n-6Si Shape Memory Alloy
1. Influence of Heat Treatment on Tensile Properties. The X-ray diffraction
pattern of the as-received Fe-32M n-6Si shape memory alloy (Fig. 2) shows a
presence of (101 0) e and (1011) e peaks corresponding to martensite e (H C P )
phase in addition to (111)y and (2 0 0 ) y peaks corresponding to austenite
y ( F C C ). The mixed F C C -H C P structure is due to the heat treatment performed
after the material processing.
When the sample is maintained at 873 K during one hour and then water
cooled at room temperature, the alloy presents an austenitic structure as illustrated
by the X-ray diffraction pattern of Fig. 3. After this heat treatment, the trans
formation temperatures determined by electrical resistance measurements are
specified in Table 2 [4].
T a b l e 2
Transformation Temperatures (in K)
Ms M f As Af
270 215 385 395
CPS
500
400
300
200 ■
100 -
(1 ll yi CPS
500 (H1)y
1
400 •
300
<200)r 200 (200)y
/1 (10l1)eJI____________A__I (10l0)e
100 ■ I i
52 51 50 49 48 47 46 45 44 43 42 41 20 52 51 50 49 48 47 46 45 44 43 42 41 20
Fig. 2 Fig. 3
Fig. 2. X-ray diffraction pattern o f as-received Fe-32M n-6Si alloy.
Fig. 3. X-ray diffraction pattern o f Fe-32M n-6Si alloy after reference heat treatment.
Tensile properties depend on the heat treatment and the structure of the
material. Figure 4 presents tensile tests relating to the as-received and after
austenitization heat treatment states.
A detailed analysis of Fig. 4 curves is given in Table 3.
According to the results of the tensile tests of Fig. 4 and the mechanical
properties summarized in Table 3, we can deduce that the presence of thermal
martensite in the initial state is at the origin of yield strength increasing and the
reduction of ductility. Thermal martensite tends to strength the matrix. On the
other hand, the ultimate tensile strength is slightly higher when the initial state is
austenitic. We will further see than even in this case tensile behavior is controlled
by the martensitic transformation. For iron-based shape memory family, one of
the favourable factors to a good shape memory effect is the absence of the thermal
martensite at operating temperature. Pre-existing e martensite suppresses the
ISSN 0556-171X. npoôëeMbi npounocmu, 2008, № 2 57
stress induced martensite transformation to a certain extent due to £-plates
intersections [6 ]. On the basis of this report, the heat treatment which conferred
on alloy an austenitic state at room temperature will be regarded as a reference
heat treatment.
T a b l e 3
T. Bouraoui, F. Jemal, and T. Ben Zineb
Mechanical Characterictics of Fe-32Mn-6Si Alloy
State o f material Yield strength (0.2%),
MPa
Ultimate tensile
strength, MPa
Elongation
to fracture, %
As-received 230 695 20
After heat treatment 190 710 27
Strain [%]
Fig. 4. Stress-strain curves for as-received and after heat treatment Fe-32M n-6Si alloy samples.
2. Stress Induced M artensite and Shape M em ory Effect. The curve of the
Fig. 5 represents tensile behavior of Fe-32M n-6Si alloy after the heat treatment
of austenitization. The general shape of the stress-strain curve is similar to that
observed in traditional metallic materials but inelastic strains are induced by
matrensitic transformation and plastic gliding. During tensile loading, the у ^ £
martensitic transformation occurs starting from a critical stress. According to
X-ray diffraction pattern (Fig. 5b), the sample becomes a mixture of у and £ after
a deformation of 4.5% followed by an unloading. The critical stress inducing
martensite is difficult to determine with precision on the experimental curve.
Conventionally, this stress is given to 0.2%.
The observed non-linear behavior during unloading is related to the pseudo
elasticity phenomenon. This phenomenon cannot be explained solely by the
conventional idea of transformation pseudoelasticity observed in usual SMA
(Ni-Ti- and Cu-based alloys), since the testing temperature is lower than A s and
the martensitic transformation is semi-thermoelastic (or non-thermoelastic). The
pseudoelasticity of Fe-M n-Si-based alloys was reported in other works [7]. The
interpretation of this property was possible in terms of the reversible motion of
the у/£ interfaces and/or of twin positions in the austenite.
58 ISSN 0556-171X. Проблеми прочности, 2008, № 2
ISSN
0556-17IX. IIpoôJieM
bi npouuocm
u, 2008, N
2 2
Stress [MPa]
Strain [%]
a
Fig. 5. Stress-strain-temperature diagram of the Fe-32M n-6Si (a); X-ray diffraction pattern o f initial state (b ); X-ray diffraction pattern after 4.5% o f tensile
!£ deformation (c).
Tensile
Properties
of
a
Fe-32M
n-6Si Shape
M
emory
Alloy
T. Bouraoui, F. Jemal, and T. Ben Zineb
The shape recovery, observed in the temperature-strain diagram (Fig. 5a), is
induced by £ ^ y transformation through the reversion motion of the 1/6< 112>
Shockley partial dislocations in the F C C structure by a heating to a temperature
higher than A j .
The shape recovery rate is defined as
r =
F + F°p e ° r
F + F + F •° pe ° r ° ir
where £ pe, £ r , and £ ir are pseudoelastic, reversible, and irreversible strains,
respectively.
In the case of the test presented in Fig. 5, the shape recovery is equal to 60%.
3. Tensile Properties a t Different Tem peratures. Figure 6 shows the
stress-strain curves of the Fe-32M n-6Si, which were drawn up at different
testing temperatures and with maximum prestrain limited to 3.5%. It can be seen
that the stress curves exhibit remarkably different characters at the testing
temperatures. O f these curves we determine yield stress (0.2%) which corresponds,
according to the test temperature, at the beginning of the martensitic trans
formation or the slip in austenite. The critical stresses relating to the various
temperatures are deferred in the graph of Fig. 7.
Strain [%]
Fig. 6. Stress-strain curves at different temperatures.
On the graph of Fig. 7, we also placed M s, A s, A f , and M d temperatures.
The latter, which corresponds to the limit temperature of strain-induced martensite,
was obtained for experiments at approximately 435 K.
Based on results presented in Fig. 7, two temperature ranges are highlighted.
The first is characterized by a transformation straight line with positive slope
(1 MPa/K), between M s and M as , and where the martensitic transformation
precedes the plastic gliding in austenite. The obtained martensite in this case is
known as stress-induced martensite. The second is characterized by a plastic
60 ISSN 0556-171X. Проблемы прочности, 2008, N2 2
Tensile Properties o f a Fe-32M n-6Si Shape Memory Alloy
strain straight line with negative slope (— 0.9 MPa/K), between M as and M d ,
and where the plastic gliding in austenite precedes a possible martensitic trans
formation. The martensite which could be formed in this case is called strain-
induced martensite. For temperatures lower then M s, we already saw previously
that the presence of thermal martensite tends to strength the matrix and could
inhibit the martensitic transformation.
Critical stress [MPa]
500
400
300
200
100
'
Transform ation lin
\ ^ ^ ■
■ i
1
i
Slip d fo rm a tio n line
•. ■ , !
!
i
1
1
i
i
i
■
|
I
, i
1ii
i
. i.
250 Ms M ? A s
300 350 400
Tem perature [K]
450 500
Fig. 7. Temperature dependence of critical stresses corresponding to martensite formation and slip
deformation.
On the basis of all these observations, we can conclude that in order to
generate stress-induced martensite without introducing slip strain in austenite,
essential condition to have the best possible SME, the operation temperature must
be slightly higher than M s.
In addition, the fact that temperature M as is lower than A f , explains the
absence of superelasticity such as that observed in usual SMA. It is impossible to
be in the configuration where the temperature is higher than A f and the
mechanical loading induces the martensitic without slip in austenite. On the other
hand, it is possible to observe a weak and partial superelasticity if the temperature
of the test is between A f and M d .
Based in these experimental observations, a one-dimensional thermo
mechanical constitutive law is developed. It describes the effect of inelastic strain
induced by martensite transformation on the iron-based SMA behavior for tensile
loading. The next paragraph presents the thermodynamic formulation leading to
this constitutive law.
4. Modeling of Tensile Behavior. The modeling of the thermomechanical
behavior of iron-based shape memory alloys is little treated in bibliography.
Goliboroda et al. [8] presents a study based on a phenomenological approach.
The suggested model in this work is based on a simplified micromechanical
approach in order to lead to macroscopic description [9, 10]. To determine the
behavior of an initial representative volume element (RVE) of austenite, Gibbs
energy, W, was considered.
ISSN 0556-171X. npoôëeMbi npounocmu, 2008, № 2 61
T. Bouraoui, F. Jemal, and T. Ben Zineb
The thermodynamic potential associated to the martensitic transformations is
a function of the control variables (2 , T), and the internal variables related to the
martensitic transformation.
The Helmholtz energy, noted O (2 , T), is defined between two states:
(austenite) and (austenite + martensite). This energy is composed in a chemical
energy (W chemicai X elastic energy due to the elastic strain (W eiastic) and interface
energy QVinterface)
O (2 , T) — Wchemical + W elastic + W interface. (1)
The Gibbs free energy is written as the difference between the potential
energy (Wpotential) and Helmholtz energy
2 , T ) — Wpotential — O (2 , T) — Wpotential — W chemical — Welastic — W interface. (2)
The interface energy can be neglected. This approximation is justified by the
metallographic observations revealing a martensite in the form of fine plates [11].
The chemical energy (Wchemicai ) can be described as a linear function of
temperature and macroscopic volume fraction of martensite, f , without any
stress dependence
Wchemicai — B (T - T o ) f , (3)
where T0 denotes the thermodynamic equilibrium temperature between austenite
and martensite and B is a material constant.
The total strain is decomposed into an elastic strain and a transformation
strain by neglecting the thermal expansion and the plastic gliding in austenite if
the maximum strain is about 2.5% [5]
E = E e + E f = + f , (4 )
where E e, E t , £ t , and E y indicate, respectively, the elastic strain and the
transformation strain, the main strain transformation describing in an averaged
way the martensite orientation, and the Young modulus of the alloy whose elastic
behavior is assumed to be isotropic and linear. By taking into account the Eq. (4),
the potential energy expression is written as
2 2
W po,em a — 2 —2( E ‘ + E ' ) —E Y + 'f . (5)
The expression of elastic energy takes into account, in an averaged way,
interactions between grains (strain incompatibilities between grains) and between
martensite variants (compatibilities inside grains):
1 2 2 1 t 2 1 2
Welastic — 2 E ^ + 2 H (£ f ) + 2 A f , (6 )
62 ISSN 0556-171X. npoôëeubi npounocmu, 2008, N2 2
Tensile Properties o f a Fe-32M n-6Si Shape Memory Alloy
where A and H are material parameters representing respectively the intergranular
and intragranular interactions. This expression is derived from a micromechanical
formulation by considering, in an averaged way, the effect of incompatibilities
between and inside grains [11]. The combination of the different energy
expressions leads to the new expression of Gibbs free energy as a function of
control and state variables and equally material parameters describing elasticity
and martensitic transformation:
1 2 2 1 1
W (2 , T , f , e t ) = 2 e ~y tf - 2 H (* t f ) 2 “ 2 A f 2 _ B {T ~ T0 ■ (7)
In the continuation, we are interested primarily in the transformation stress.
The reorientation stress is neglected because it is assumed that in iron-based SMA
only an oriented martensite is active. The driving transformation stress, F m , is
obtained by deriving energy from Gibbs compared to the martensite volume
fraction f :
Fm = 2 e t - B ( T - To) - H (e t )2 f - A f ■ (8)
Let’s consider F c a nonzero constant which characterizes the critical trans
formation stress. This stress is given from the Eq. (8) for T = M s , a o = 160 MPa
and f = 0 (yield transformation)
F c = a 0e t - B (T - T0). (9)
When F m < F c , the yield transformation is not reached yet and we observe
an elastic behavior obeying to the Hooke law 2 = E y E.
The martensitic transformation starts and progresses until the end of trans
formation when F m = F c , F m = 0, and f ^ f saturation ■
The combination of the Hooke’s law with coherence rule (F m = 0) makes it
possible to lead to the constitutive law of the SMA. The material parameters of
Fe-32M n-6Si alloy at 293K are given in Table 4.
T a b l e 4
Material Parameters for Fe-32Mn-6Si Alloy at 293 K
Ey , MPa r„ ,K B, MPa/K Fc , MPa A, MPa H , MPa e‘
135,000 340 0.016 4.2 -0 .8 8 7760 0.02
The numerical simulation based on the described model is represented on
Fig. 8. The comparison between the experimental curve and the numerical
simulation shows overall a good agreement for 3% prestrain. However, the
observed difference is due to the fact that, even for prestrain lower than 3%, the
martensitic transformation is accompanied, locally, by a slip deformation in
austenite. This behavior, specific to the nonthermoelastic martensitic trans
formation, tends to disappear with thermomechanical cycling.
ISSN 0556-171X. npoÖÄeubi npounocmu, 2008, № 2 63
T. Bouraoui, F. Jemal, and T. Ben Zineb
500
400
<2 3oo
g ,
tn e/i
2 200
</5
100
0
0 1 2 3 4
Strain [%]
Fig. 8. Comparison between experimental and theoretical curves at T = 293 K.
Conclusions. The mechanical tensile behavior o f Fe-32M n-6Si shape
memory alloy is conditioned by y ( F C C ) ^ £ ( H C P ) martensitic transformation
and depends on temperature and microstructure.
In order to generate stress-induced martensite without introducing slip
deformation in austenite, essential condition to have the best possible SME, the
operated temperature must be slightly higher than M s. In addition, for iron-based
shape memory alloys, the fact that temperature M as is lower than A f , explains
the absence of superelasticity.
The tensile behavior is described while following the thermodynamic driving
forces which are obtained by deriving Gibbs energy with respect to the internal
variable martensitic volume fraction.
The comparison between numerical simulation and the experimental results
shows a good agreement when permanent strain is about 3%. However, for more
significant strains, it would be necessary to take into account, in the theoretical
formulation, the plastic slip which occurs in austenite.
A c k n o w le d g m e n ts . Part of this work was realized in the framework of
Cooperation University Joint Committee between France and Tunisia (CMCU
Program No. 04S1117). The authors extend their gratitude to their financial
support.
Р е з ю м е
Досліджуються характеристики міцності сплаву Fe-32M n-6Si з пам’яттю
форми при статичних випробуваннях на розтяг. Показано, що ці характерис
тики залежать від температури, термообробки та мікроструктури матеріалу.
Аналізується взаємозв’язок між процесом мартенситного перетворення і
характеристиками міцності та ефектом пам’яті форми матеріалу, в резуль
таті чого запропоновано одновимірне рівняння стану, яке описує термо
механічну поведінку матеріалу при статичному розтязі. Отримано хорошу
збіжність між результатами числових розрахунків і експериментальними
даними.
64 ISSN 0556-171X. Проблемы прочности, 2008, № 2
Tensile Properties o f a Fe-32M n-6Si Shape Memory Alloy
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transformation in Fe-30M n-Si alloy single crystal,” A c ta M e ta ll., 30, 1177
1183 (1982).
2. A. Sato, E. Chishima, Y. Yamaji, and T. Mori, “Orientation and composition
dependencies of SME in Fe-M n-Si alloys,” A c ta M e ta ll., 32, 539-547
(1984).
3. T. Y. Hsu, “Prediction of martensitic transformation start temperature M s in
Fe-M n-Si shape memory alloys,” M ater. Sci. F orum , 327-328, 199-222
(2000).
4. T. Bouraoui, K. Tamarat et B. Dubois, “Variations de la résistivité électrique
associées aux transformations martensitiques dans l ’acier à mémoire de
forme FM30,” J .P h y s . III, 6, 831-841 (1996).
5. J. H. Yang and C. M. Wayman, “Development of Fe-based shape memory
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Received 26. 08. 2007
ISSN 0556-171X. npo6neMU npouHocmu, 2008, № 2 65
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| id | nasplib_isofts_kiev_ua-123456789-48250 |
| institution | Digital Library of Periodicals of National Academy of Sciences of Ukraine |
| issn | 0556-171X |
| language | English |
| last_indexed | 2025-12-07T15:39:44Z |
| publishDate | 2008 |
| publisher | Інститут проблем міцності ім. Г.С. Писаренко НАН України |
| record_format | dspace |
| spelling | Bouraoui, T. Jemal, F. Ben Zinebc, T. 2013-08-17T12:00:19Z 2013-08-17T12:00:19Z 2008 Tensile properties of a Fe-32Mn-6Si shape memory alloy / T. Bouraoui, F. Jemal, T. Ben Zinebc // Проблемы прочности. — 2008. — № 2. — С. 55-65. — Бібліогр.: 11 назв. — англ. 0556-171X https://nasplib.isofts.kiev.ua/handle/123456789/48250 539.4 The tensile properties of a Fe-32Mn-6Si shape memory alloy were investigated. It was found that tensile properties depend on temperature, heat treatment and material structure. The relationships of martensitic transformation, tensile properties, and shape memory effect are discussed. Finally, we propose a macroscopic one-dimensional constitutive law describing the thermomechanical behavior in tensile loading. Numerically obtained results are close to the experimental ones. Досліджуються характеристики міцності сплаву Fe-32Mn-6Si з пам’яттю форми при статичних випробуваннях на розтяг. Показано, що ці характеристики залежать від температури, термообробки та мікроструктури матеріалу. Аналізується взаємозв’язок між процесом мартенситного перетворення і характеристиками міцності та ефектом пам’яті форми матеріалу, в результаті чого запропоновано одновимірне рівняння стану, яке описує термомеханічну поведінку матеріалу при статичному розтязі. Отримано хорошу збіжність між результатами числових розрахунків і експериментальними даними. Исследуются характеристики прочности сплава Fe-32Mn-6Si с памятью формы при статических испытаниях на растяжение. Показано, что эти характеристики зависят от температуры, термообработки и микроструктуры материала. Анализируется взаимосвязь процесса мартенситного превращения с характеристиками прочности и эффектом памяти формы материала, в результате чего предложено одномерное уравнение состояния, описывающее термомеханическое поведение материала при статическом растяжении. Получено хорошее соответствие между результатами численных расчетов и экспериментальными данными. Part of this work was realized in the framework of Cooperation University Joint Committee between France and Tunisia (CMCU Program No. 04S1117). The authors extend their gratitude to their financial support. en Інститут проблем міцності ім. Г.С. Писаренко НАН України Проблемы прочности Научно-технический раздел Tensile properties of a Fe-32Mn-6Si shape memory alloy Характеристики прочности сплава Fe-32Mn-6Si с памятью формы при статических испытаниях на растяжение Article published earlier |
| spellingShingle | Tensile properties of a Fe-32Mn-6Si shape memory alloy Bouraoui, T. Jemal, F. Ben Zinebc, T. Научно-технический раздел |
| title | Tensile properties of a Fe-32Mn-6Si shape memory alloy |
| title_alt | Характеристики прочности сплава Fe-32Mn-6Si с памятью формы при статических испытаниях на растяжение |
| title_full | Tensile properties of a Fe-32Mn-6Si shape memory alloy |
| title_fullStr | Tensile properties of a Fe-32Mn-6Si shape memory alloy |
| title_full_unstemmed | Tensile properties of a Fe-32Mn-6Si shape memory alloy |
| title_short | Tensile properties of a Fe-32Mn-6Si shape memory alloy |
| title_sort | tensile properties of a fe-32mn-6si shape memory alloy |
| topic | Научно-технический раздел |
| topic_facet | Научно-технический раздел |
| url | https://nasplib.isofts.kiev.ua/handle/123456789/48250 |
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