Submitted Successfully!
To reward your contribution, here is a gift for you: A free trial for our video production service.
Thank you for your contribution! You can also upload a video entry or images related to this topic.
Version Summary Created by Modification Content Size Created at Operation
1
Xuhong Qiang
 -- 2498 2023-06-09 05:28:15 |
2 update references and layout
Rita Xu
 Meta information modification 2498 2023-06-09 05:45:57 |

Video Upload Options

We provide professional Video Production Services to translate complex research into visually appealing presentations. Would you like to try it?
No, upload directly Yes

Confirm

Are you sure to Delete?
Yes No
Cite
If you have any further questions, please contact Encyclopedia Editorial Office.
Qiang, X.; Wu, Y.; Wang, Y.; Jiang, X. Fe-Mn-Si-Based Shape Memory Alloys. Encyclopedia. Available online: https://encyclopedia.pub/entry/45372 (accessed on 16 November 2024).
Qiang X, Wu Y, Wang Y, Jiang X. Fe-Mn-Si-Based Shape Memory Alloys. Encyclopedia. Available at: https://encyclopedia.pub/entry/45372. Accessed November 16, 2024.
Qiang, Xuhong, Yapeng Wu, Yuhan Wang, Xu Jiang. "Fe-Mn-Si-Based Shape Memory Alloys" Encyclopedia, https://encyclopedia.pub/entry/45372 (accessed November 16, 2024).
Qiang, X., Wu, Y., Wang, Y., & Jiang, X. (2023, June 09). Fe-Mn-Si-Based Shape Memory Alloys. In Encyclopedia. https://encyclopedia.pub/entry/45372
Qiang, Xuhong, et al. "Fe-Mn-Si-Based Shape Memory Alloys." Encyclopedia. Web. 09 June, 2023.
Fe-Mn-Si-Based Shape Memory Alloys
Edit
This entry is adapted from the peer-reviewed paper 10.3390/app13063404

In civil engineering, beam structures such as bridges require reinforcement to increase load-bearing capacity and extend service life due to damage, aging, and capacity degradation under long-time services and disasters. The utilization of Fe-based shape memory alloys (Fe-SMA) to reinforce structures has been proven efficient and reliable, and the recovery stress of activated Fe-SMA can satisfy the reinforcement requirements.

Fe-based shape memory alloys shape memory effect activation recovery characteristics

1. Introduction

Civil engineering structures, such as bridges, buildings, and high-rise structures, may suffer various defects in the design, production, and construction processes. Under long-term service conditions, they are faced with cracking, rustiness, and aging problems due to overload, corrosion, fatigue, etc. [1][2][3]. Under the action of fire, earthquake, wind, and other disasters, existing structures may also sustain damage and deformation [4][5][6][7]. In the United States and Europe, where the infrastructures were constructed earlier, a large number of engineering structures have been suffering aging problems and require reinforcement and maintenance. Although the prosperous infrastructure construction in China started late, increasing demands for structural reinforcement are emerging, which contains great scientific research value and economic prospects. The beam, an essential and fundamental component of structures, plays a crucial role in achieving the spanning, bearing, and linking functions. Therefore, it is of considerable value to strengthen and repair the deteriorated beams in existing structures to ensure their bearing capacity and prolong their service life.
Shape memory alloys (SMAs), as a new intelligent material, have been widely used in aerospace, robotics, medicine, and other fields, possessing two typical characteristics: shape memory effect (SME) and superelasticity (SE) [8][9][10][11]. SMAs contain two different composition phases: austenite and martensite. The phase transformation between austenite and martensite, which is induced by changes in temperatures or stresses, is referred to as the martensite transformation [12][13][14]. The martensite transformation is a diffusionless and solid-state phase transition, in which the atoms move cooperatively. It differs from the plastic deformation of normal metal materials, which is due to the dislocations of crystals slip [15]. Thus, the martensite transformation is a reversible process, and the characteristics of SME and SE benefit from this peculiarity. In civil engineering, SE is mainly used in structural seismic resistance and energy dissipation. SMA can be manufactured into basic components (wire, bar, spring, etc.) and key components (dampers, supports, isolation devices, etc.) [16][17][18][19]. SME can be used for structural reinforcement and enhancement. The recovery stress generated by activating SMA can introduce prestress based on increasing the stiffness of structures [20][21][22].
Retrospectively, the shape memory materials were first discovered in the gold–cadmium (Au-Cd) alloys by Arne Ölander in 1932 [23]. Decades later, the reversible phase transformation of SME, governed by the thermoelastic martensite phase of Au-Cd alloys, was reported by Kurdjumov and Khandros in 1949, and by Chang and Read in 1951 [24][25]. In the 1960s, Buehler et al. found the SME of nickel–titanium (Ni-Ti) alloys in shock absorption tests [26]. In the 1970s, Otsuka et al. found that the shape memory effect of Cu-Al-Ni alloys was closely related to the thermoelastic martensite transformation [27]. In the early 1980s, Sato et al. first studied the SME of Fe-Mn-Si alloys [28][29].
NiTi-SMA and Fe-SMA are the two SMAs appropriately employed in civil engineering. The shape recovery ability of Fe-SMA is weaker than that of NiTi-SMA, but it also possesses high strength, excellent plasticity, and good forming properties [30][31]. Furthermore, its lower production costs compared to NiTi-SMA make it more economical for large-scale application in the field of structural reinforcement [32]. After thermal activation, Fe-SMA can realize the active control of structural stiffness and deformation, as well as repair local damage and cracks of structures [33][34]. Due to SME, no complex tension devices are required to achieve pretension, which eliminates the restriction on operating spaces and improves the convenience of construction [35].

2. Material Properties of Fe-SMA

2.1. Introduction of Fe-Mn-Si Alloys

Overall, Fe-SMA contains three types of crystal structures, as shown in Figure 1, which are the face-centered cubic lattice of austenite phase (fcc, γ-austenite), the body-centered tetragonal lattice of martensite phase (bct, α′-martensite), and the hexagonal close-packed lattice of martensite phase (hcp, ε-martensite).
Applsci 13 03404 g001
Figure 1. Crystal phase of Fe-SMA: (a) γ-austenite (fcc), (b) α′-martensite (bct), (c) ε-martensite (hcp).
Fe-SMA is divided into two different groups based on material properties [36]. The first group of Fe-SMA is thermoelastic martensite alloys, including Fe-Pt [37], Fe-Pd [38][39], and Fe-Ni-Co [40][41], whose typical characteristics are similar to NiTi-SMA. The martensite transformation is the crystal lattice changes between fcc (γ-austenite) and bct (α′-martensite). The first group alloys possess the ability of SE (or pseudoelasticity), but with a narrow thermal hysteresis, its SME is limited by temperature when used for structural reinforcement. The second group of Fe-SMA contains alloys such as Fe-Ni-C [42] and Fe-Mn-Si [43][44]. This group of alloys carries a large thermal hysteresis in the transformation and expresses SME in an acceptable temperature range. For the Fe-Ni-C alloys, the crystal changes are fcc ⇌ bct (γ-austenite ⇌ α′-martensite) in the martensite transformation. The crystal changes in Fe-Mn-Si alloys are fcc ⇌ hcp (γ-austenite ⇌ ε-martensite) in the martensite transformation.
The Fe-Mn-Si alloys show considerable SME, and its phase transformation temperature is easy to realize, so it has been widely researched and applied [45][46]. Therefore, this research mainly focuses on the Fe-Mn-Si alloys in Fe-SMA.
The original Fe-Mn-Si based SMA only contains the elements Fe, Mn, and Si. The optimization of corrosion prevention, training improvement, and cyclic strengthening of materials mainly experiences two stages [47]. The optimization of alloy elements is the first improvement stage [48]. The SME and corrosion resistance of SMA are improved by changing the percentage of elements and adding new elements. The element contents of Mn and Si have an obvious influence on SME [49][50], and the corrosion resistance can be greatly improved by adding elements of Cr, Ni, N, etc. [51][52][53]. At the same time, the alloys possess an excellent recovery capacity with the cyclic thermo-mechanical process of “training” [54]. The second optimization stage is introducing fine precipitates, such as NbC, VC, and VN, into the alloy microstructure to improve the SME of Fe-SMA without “training” [55][56][57]. The most significant alloys for the development process of Fe-SMA are presented in Table 1.
Table 1. The most significant Fe-Mn-Si alloys in the development history.
Stage Alloys (Composition in Mass %) Year References
First stage:
optimization of alloy elements		 Fe-30Mn-1Si 1982 [28]
Fe-30Mn-6Si 1984 [29]
Fe-32Mn-6Si 1986 [58]
Fe-28Mn-6Si-5Cr 1990 [48]
Fe-20Mn-5Si-8Cr-5Ni
Fe-16Mn-5Si-12Cr-5Ni
Fe-30Mn-6Si 1995 [54]
Fe-28Mn-6Si-5Cr 2001 [46]
Fe-18Mn-8Cr-4Si-2Ni-0.36Nb-0.36N
Fe-30Mn-6Si 2002 [51]
Fe-30Mn-6Si-5Cr
Fe-13Mn-5Si-12Cr-5Ni
Fe-25Mn-6Si-5Cr-0.14N 2006 [53]
Second stage:
introduction of fine precipitates		 Fe-28Mn-6Si-5Cr-0.5(Nb,C) 2001 [55]
Fe-28Mn-6Si-5Cr-1(V,N) 2004 [56]
Fe-15Mn-5Si-9Cr-5Ni-(0.5-1.5)NbC 2005 [59]
Fe-28Mn-6Si-5Cr-0.53Nb-0.06C 2006 [60]
Fe-14Mn-5Si-8Cr-4Ni-0.16C 2007 [61]
Fe-17Mn-5Si-10Cr-4Ni-1(V,C) 2009 [57]
Fe-16Mn-5Si-10Cr-4Ni-1(V,N) 2013 [44]
Fe-19Mn-4Si-8Cr-4Ni-0.01C 2021 [35]

2.2. SME and Activation Recovery Performance

The SME is the result of the reversible martensite transformation [12]. The corresponding relationship between the temperature and martensite fractions is depicted in Figure 2. There are four characteristic temperatures in the transformation process from low to high: martensite finish temperature (Mf), martensite start temperature (Ms), austenite start temperature (As), and austenite finish temperature (Af). The martensite transformation from fcc (γ-austenite) to hcp (ε-martensite) is induced when the temperature decreases lower than Ms. The martensite fraction increases with the decreasing temperature, and the martensite transformation is completed until the temperature is below Mf. Adversely, the reverse transformation from hcp (ε-martensite) to fcc (γ-austenite) is induced when the temperature increases beyond As and the martensite fraction decreases until the reverse transformation is completed with the temperature higher than Af [62][63]. In Table 2, the characteristic temperatures in the phase transformation of several typical Fe-SMA are compared. Notably, in the absence of external force, the martensite transformation induced only by temperature change will not cause macroscopic deformation.
Applsci 13 03404 g002
Figure 2. Schematic definition of characteristic temperatures in martensite transformation.
Table 2. Martensite transformation temperatures of Fe-SMA.
Alloys Mf (°C) Ms (°C) As (°C) Af (°C) Refs.
Fe-30Mn-1Si — 27 127 — [28]
Fe-28Mn-6Si-5Cr — 20 120 180 [64]
Fe-14Mn-6Si-9Cr-5Ni — 20 70 300 [65]
Fe-17Mn-5Si-10Cr-4Ni-1(V,C) −90 −75 85 110 [57]
Fe-17Mn-5Si-10Cr-4Ni-1(V,C) −64 −60 103 162 [66]
Fe-19Mn-4Si-8Cr-4Ni-0.01C −100 −38 138 218 [35]
The SME of Fe-SMA is illustrated in Figure 3a [67][68]. Pre-stretching the alloy at ambient temperature (T < As), it deforms macroscopically (Path 1). The macroscopic deformation includes four parts: elastic deformation, recoverable deformation, pseudoelastic deformation, and plastic deformation. After unloading, the elastic and pseudoelastic deformations can be recovered (Path 2). Then, with raising the temperature higher than As, the reverse martensitic transformation is induced, in which the recoverable deformation gradually diminishes until the temperature is beyond Af (Path 3). The residual deformation is only the plastic deformation. Without external force, the cooling stage does not experience macroscopic deformation (Path 4).
Applsci 13 03404 g003a
Applsci 13 03404 g003b
Figure 3. SME and activation performance of Fe-SMA: (a) SME, (b) activation performance.
As shown in Figure 3b, after stretching the alloy to the predetermined strain and stress (εpre and σpre) and unloading to residual strain (εr) (Paths 1 and 2), restricting the free shrinkage of Fe-SMA will produce recovery stress (σr) inside the alloy in the activation process (Paths 3 and 4) [67]. The activation contains two processes: heating and cooling. The stress in Fe-SMA initially decreases for thermal expansion in the heating process (Curve a). With the temperature raising higher than As, the reverse martensite transformation is induced, and the tensile stress in Fe-SMA gradually increases (Curve b). After stopping heating, the tensile stress increases continuously and finally reaches the recovery stress (σr) (Curve c). Notably, the higher stress in Fe-SMA may occasionally cause a slight degree of martensite transformation and stress relaxation at the later stage of cooling [69]. Finally, the Fe-SMA will work under the service load based on the recovery stress (Green dotted line in Figure 3b).

3. Mechanical Performance of Fe-SMA

3.1. Basic Mechanical Properties

When applied in practice, Fe-SMA materials can be manufactured into various shapes and sizes, such as rods, bars, and strips [70][71][72], as shown in Figure 4. As an alloy, the basic properties of Fe-SMA are similar to those of steel. The physical properties of Fe-SMA, steel, and concrete are summarized in Table 3. Their thermal expansion coefficients are numerically close, and the three materials can deform collaboratively when the temperature changes; hence, Fe-SMA has prominent advantages in strengthening steel and concrete structures [73][74][75].
Applsci 13 03404 g004
Figure 4. Schematic diagram of Fe-SMA: (a) Fe-SMA bars, (b) Fe-SMA strips.
Table 3. Physical parameters of Fe-SMA, steel, and concrete.
Materials Density
(kg/m3)		 Elastic Modulus
(GPa)		 Thermal Expansion
(K−1)		 Poisson Ratio Elongation
(%)		 Ultimate Strength
(MPa)
Fe-SMA 7200~7500 170 16.5 × 10−6 0.359 16~30 680~1000
Steel–Q235 7860 208 11~13 × 10−6 0.294 25 467
Steel–Q355 206 25 533
Steel–Q690 218 7 990
Concrete 1950~2500 32.5 12 × 10−6 0.18~0.21 — —
Note: The steel grades is defined by the Chinese standards of carbon structural steels (GB/T 700-2006) and high-strength low-alloy structural steels (GB/T 1591-2018).
Fe-SMA is a typical elasto-plastic material without a yield platform, as shown in Figure 5. Therefore, the stress of σy,0.2, corresponding to its residual strain of 0.2%, is used to describe the yield strength. The mechanical properties of Fe-SMA tested by different researchers are summarized in Table 4. Due to the various factors such as elemental composition, processing technology, and fine precipitates the mechanical characteristics of Fe-SMA studied by scholars are different. The elastic modulus of Fe-SMA is distributed in the range of 125–200 GPa, the ultimate strength is in the range of 676–1140 MPa, the yield strength is in the range of 260–600 MPa, and the ultimate strain of Fe-SMA can exceed 50%, demonstrating excellent ductility and deformability.
Applsci 13 03404 g005
Figure 5. Stress–strain curves of Fe-SMA.
Table 4. Mechanical properties of Fe-SMA.
Alloys Elastic Modulus
(Gpa)		 σy,0.2
(MPa)		 Ultimate Strength
(MPa)		 Ultimate Strain
(%)		 References
Fe-17Mn-5Si-10Cr-4Ni-1(V,C) 194 476 950 45 [15]
184 450 950 54 [31]
160 535 ≈1000 47 [67]
173 546 1015 54.9 [76]
200 310 993 15.4 [77]
Fe-Mn-Si alloys 133 463 863 12.4 [78]
Fe-Mn-Si alloys 186 490 894 35.5 [79]
Fe-17Mn-5Si-5Cr-0.3C-1T 125 599 1140 22.56 [80]
Fe-17Mn-5Si-5Cr-4Ni-0.1C 123 410 1080 39.51 [80]
Fe-15Mn-4Si-10Cr-8Ni 184 260 676 74 [81]
Fe-Mn-Si alloys 172 298 774 48.05 [82]

3.2. Cyclic Mechanical Properties

When reinforcing structures, the mechanical properties of Fe-SMA under cyclic load, such as pseudo-static and fatigue load, are noteworthy and crucial. In this regard, the Empa Institute has carried out some relevant studies, in which the alloy elements are Fe-17Mn-5Si-10Cr-4Ni-1(V,C).
Ghafoori et al. [76] studied the pseudo-static performance of Fe-SMA with a 1% strain increment, and the loading curves are presented in Figure 6a. The hardening of Fe-SMA occurs under cyclic load, due to the corresponding stress in the pseudo-static process being higher than that in the static tensile process. According to the study by Koster et al. [77], the stress corresponding to the pseudo-static tensile strain of 9% is about 60 MPa higher than that in the static tensile test. Additionally, owing to the pseudo-elasticity of Fe-SMA, the unloading process of hysteresis curves does not follow Hooke’s law, and this discovery is of great significance for the energy dissipation capacity of Fe-SMA.
Applsci 13 03404 g006
Figure 6. Loading curves of Fe-SMA: (a) under pseudo-static load, (b) under fatigue load after activation.
The fatigue properties of Fe-SMA were investigated by Koster et al. [77]. When a fatigue stress of ±230 MPa was applied based on 300 MPa pretension stress, the Fe-SMA members could withstand a fairly high number of loading cycles without fatigue fracture. The fatigue limit of Fe-SMA under 2 × 106 loading cycles is 450 MPa, much higher than its yield strength (σy,0.2 = 371 MPa), and the transition stress between high-cycle and low-cycle fatigue is about 500 MPa. Ghafoori et al. [76] studied the fatigue performance of Fe-SMA after activation. Based on the recovery stresses of 359–372 MPa, fatigue load with strain amplitudes (Δε) of 0.035% and 0.07% was applied to the Fe-SMA members (as shown in Figure 6b), and the alloy did not undergo fatigue fracture after 2 × 106 loading cycles. The above fatigue properties of Fe-SMA shall be considered in the design of structural reinforcements.

3.3. Stress Relaxation and Creep

Previous studies have found that stress relaxation and creep are notable characteristics of Fe-SMA. Michels et al. [83] obtained a recovery stress of 316 MPa of Fe-SMA, but the recovery stress decreased 19 MPa (accounting for 6% of the total recovery stress) after maintaining the displacement for 10 h. Schranz et al. [84] discovered that stress relaxation is slightly dependent on recovery stress, but further investigation is necessary to thoroughly understand their relationship. In the fatigue loading process, Ghafoori et al. [76] found that the stress relaxation mostly took place in the early stage, and the recovery stress decreased by roughly 10–20% under different strain amplitudes after 2 × 106 loading cycles. Therefore, the stress loss caused by stress relaxation should be considered when using Fe-SMA to reinforce structures, and stress compensation shall be performed by secondary activation under special conditions.
Except for normal room temperature, the relaxation and creep of Fe-SMA are also affected by different ambient temperatures. Weber et al. [85] investigated the stress relaxation and creep of Fe-SMA in the temperature range of −45 °C–50 °C, and found that both the two increased with the decrease in temperatures. Keeping the temperature at 45 °C, the alloy experienced a 0.6% creep with the constant stress of 600 MPa in 30 min, or incurred a stress relaxation of 10% when the strain remained constant. Ghafoori et al. [69] carried out a series of transient total deformation tests under high temperatures. The initial creep and failure temperatures decreased with the increase in load level, while all the initial creep temperatures were above 500 °C. This research is very significant for the potential fire hazards faced by Fe-SMA in engineering reinforcement.

References

  1. Woo, S.K.; Nam, J.W.; Kim, J.H.J.; Han, S.H.; Byun, K.J. Suggestion of Flexural Capacity Evaluation and Prediction of Prestressed CFRP Strengthened Design. Eng. Struct. 2008, 30, 3751–3763.
  2. Ghafoori, E.; Motavalli, M.; Botsis, J. Fatigue Strengthening of Damaged Metallic Beams Using Prestressed Unbonded and Bonded CFRP Plates. Int. J. Fatigue 2012, 44, 303–315.
  3. Ghafoori, E.; Motavalli, M.; Nussbaumer, A. Design Criterion for Fatigue Strengthening of Riveted Beams in a 120-year-old Railway Metallic Bridge Using Pre-stressed CFRP Plates. Compos. Part B Eng. 2015, 68, 1–13.
  4. Qiang, X.H.; Bijlaard, F.S.K.; Kolstein, H.; Jiang, X. Behaviour of Beam-to-column High Strength Steel Endplate Connections Under Fire Conditions-Part 1: Experimental Study. Eng. Struct. 2014, 64, 23–38.
  5. Qiang, X.H.; Shu, Y.; Jiang, X. Mechanical Behaviour of High Strength Steel T-stubs at Elevated Temperatures: Experimental Study. Thin-Walled Struct. 2023, 182, 110314.
  6. Araujo, M.; Castro, J.M. A Critical Review of European and American Provisions for the Seismic Assessment of Existing Steel Moment-Resisting Frame Buildings. J. Earthq. Eng. 2017, 22, 1336–1364.
  7. Huo, T.; Tong, L.W. An Approach to Wind-induced Fatigue Analysis of Wind Turbine Tubular Towers. J. Constr. Steel Res. 2020, 166, 105917.
  8. Janke, L.; Czaderski, C.; Motavalli, M.; Ruth, J. Applications of Shape Memory Alloys in Civil Engineering Structures-Overview, Limits and New Idea. Mater. Struct. 2005, 38, 578–592.
  9. Hariri, N.G.; Almadani, I.K.; Osman, I.S. A State-of-the-Art Self-Cleaning System Using Thermomechanical Effect in Shape Memory Alloy for Smart Photovoltaic Applications. Materials 2022, 15, 5704.
  10. Cao, S.S.; Ozbulut, O.E. Long-stroke Shape Memory Alloy Restrainers for Seismic Protection of Bridges. Smart Mater. Struct. 2020, 29, 115005.
  11. Wang, B.; Zhu, S.Y. Superelastic SMA U-shaped Dampers with Self-centering Functions. Smart Mater. Struct. 2018, 27, 055003.
  12. Sergio, D.A.O.; Vanderson, M.D.; Marcelo, A.S.; Pedro, M.C.L.P.; Alberto, P. A Phenomenological Description of Shpae Memory Alloy Transformation Induced Plasticity. Mecc. J. Ital. Assoc. Theor. Appl. Mech. 2018, 53, 2503–2523.
  13. Zou, Q.; Dang, G.; Li, Y.G.; Wang, M.Z.; Xiong, J.C. Research Progress of Iron-based Shape Memory Alloys: A Review. Mater. Rep. 2019, 23, 3955–3962. (In Chinese)
  14. Cao, S.S.; Ozbulut, O.E.; Shi, F.; Deng, J. Experimental and Numerical Investigations on Hysteretic Response of a Multi-level SMA/lead Rubber Bearing Seismic Isolation System. Smart Mater. Struct. 2022, 31, 035024.
  15. Montoya-Coronado, L.A.; Ruiz-Pinilla, J.G.; Ribas, C.; Cladera, A. Experimental Study on Shear Strengthening of Shear Critical Rc Beams Using Iron-based Shape Memory Alloy Strips. Eng. Struct. 2019, 200, 109680.
  16. Seo, J.W.; Kim, Y.C.; Hu, J.W. Pilot Study for Investigating the Cyclic Behavior of Slit Damper Systems with Recentering Shape Memory Alloy (SMA) Bending Bars Used for Seismic Restrainers. Appl. Sci. 2015, 5, 187–208.
  17. Mas, B.; Biggs, D.; Vieito, I.; Shaw, J.; Vieito, I.; Martínez-Abella, F. Superelastic Shape Memory Alloy Cables for Reinforced Concrete Applications. Constr. Build. Mater. 2017, 148, 307–320.
  18. Tabrizikahou1, A.; Kuczma, M.; Łasecka-Plura, M.; Farsangi, E.N.; Noori, M.; Gardoni, P.; Li, S.F. Application and modelling of Shape-Memory Alloys for structural vibration control: State-of-the-art review. Constr. Build. Mater. 2022, 342, 127975.
  19. Deng, J.; Hu, F.; Ozbulut, O.E.; Cao, S.S. Verification of Multi-level SMA/lead Rubber Bearing Isolation System for Seismic Protection of Bridges. Soil Dyn. Earthq. Eng. 2022, 161, 107380.
  20. Maji, A.K.; Negret, I. Smart Prestressing with Shape-Memory Alloy. J. Eng. Mech. 1998, 124, 1121–1128.
  21. Czaderski, C.; Hahnebach, B.; Motavallia, M. RC Beam with Variable Stiffness and Strength. Constr. Build. Mater. 2006, 20, 824–833.
  22. Rogowski, J.; Kotynia, R. Comparison of Prestressing Methods with CFRP and SMA Materials in Flexurally Strengthened RC Members. Materials 2022, 15, 1231.
  23. Ölander, A. An Electrochemical Investigation of Solid Cadmium-Gold Alloys. J. Am. Chem. Soc. 1932, 54, 3819–3833.
  24. Kurdjumov, G.V.; Khandros, L.G. First Reports of The Thermoelastic Behaviour of The Martensitic Phase of Au-Cd Alloys. Dokl. Akad. Nauk. SSSR 1949, 66, 211–221.
  25. Chang, L.C.; Read, T.A. Behavior of The Elastic Properties of AuCd. Trans. Met. Soc. AIME 1951, 191, 47–52.
  26. Buehler, W.J.; Gilfrich, J.V.; Wiley, R.C. Effect of Low-Temperature Phase Changes on the Mechanical Properties of Alloys near Composition TiNi. J. Appl. Phys. 1963, 34, 1475–1477.
  27. Otsuka, K. Origin of Memory Effect in Cu-Al-Ni Alloy. Jpn. J. Appl. Phys. 1971, 10, 571–579.
  28. Sato, A.; Chishima, E.; Soma, K.; Mori, T. Shape Memory Effect in γ⇄ε Transformation in Fe-30Mn-1Si Alloy Single Crystals. Acta Metall. 1982, 30, 1177–1183.
  29. Sato, A.; Chishima, E.; Yamaji, Y. Orientation and Composition Dependencies of Shape Memory Effect in Fe-Mn-Si Alloys. Acta Metall. 1984, 32, 539–547.
  30. Mohd, J.J.; Leary, M.; Subic, A.; Gibson, M.A. A Review of Shape Memory Alloy Research, Applications and Opportunities. Mater. Des. 2014, 56, 1078–1113.
  31. Rosa, D.I.H.; Hartloper, A.; Sousa, A.D.C.E.; Lignos, D.G.; Motavalli, M.; Ghafoori, E. Experimental Behavior of Iron-based Shape Memory Alloys under Cyclic Loading Histories. Constr. Build. Mater. 2021, 272, 121712.
  32. Cladera, A.; Weber, B.; Leinenbach, C. Iron-based Shape Memory Alloys for Civil Engineering Structures: An Overview. Constr. Build. Mater. 2014, 63, 281–293.
  33. Czaderski, C.; Shahverdi, M.; Michels, J. Iron Based Shape Memory Alloys as Shear Reinforcement for Bridge Girders. Constr. Build. Mater. 2021, 274, 121793.
  34. Yeon, Y.M.; Hong, K.N.; Ji, S.W. Flexural Behavior of Self-Prestressed RC Slabs with Fe-Based Shape Memory Alloy Rebar. Appl. Sci. 2022, 12, 1640.
  35. Choi, E.; Ostadrahimi, A.; Kim, W.J.; Seo, J. Prestressing Effect of Embedded Fe-Based SMA Wire on the Flexural Behavior of Mortar Beams. Eng. Struct. 2021, 227, 111472.
  36. Yamauchi, K.; Ohkata, I.; Tsuchiya, K.; Miyazaki, S. Shape Memory and Superelastic Alloys: Technologies and Applications; Woodhead Publishing Limited: Cambridge, UK, 2011; Chapter 12; pp. 141–159.
  37. Wayman, C.M. On Memory Effects Related to Martensitic Transformations and Observations in β-Brass and Fe3Pt. Scr. Metall. 1971, 5, 489–492.
  38. Sohmura, T.; Oshima, R.; Fujita, F.E. Thermoelastic FCC-FCT Martensitic Transformation in Fe-Pd Alloy. Scr. Metall. 1980, 14, 855–856.
  39. Xiao, F.; Fukuda, T.; Kakeshita, T.; Takahashi, K. Concentration Dependence of FCC to FCT Martensitic Transformation in Fe-Pd Alloys. J. Alloys Compd. 2013, 577, S323–S326.
  40. Maki, T.; Kobayashi, K.; Minato, M.; Tamura, I. Thermoelastic Martensite in an Ausaged Fe-Ni-Ti-Co Alloy. Scr. Metall. 1984, 18, 1105–1109.
  41. Cesari, E.; Chernenko, V.A.; Kokorin, V.V.; Pons, J.; Seguí, C. Physical Properties of Fe-Co-Ni-Ti Alloy in the Vicinity of Martensitic Transformation. Scr. Mater. 1999, 40, 341–345.
  42. Guimarães, J.R.C.; Rios, P.R. The Mechanical-induced Martensite Transformation in Fe-Ni-C Alloys. Acta Mater. 2015, 84, 436–442.
  43. Xu, Z.Y.; Jiang, B.H. Shape Memory Materials; Shanhai Jiaotong University Press: Shanghai, China, 2000; pp. 204–220. (In Chinese)
  44. Li, K.; Dong, Z.Z.; Liu, Y.C. A Newly Developed Fe-based Shape Memory Alloy Suitable for Smart Civil Engineering. Smart Mater. Struct. 2013, 22, 045002.
  45. Sawaguchi, T.; Maruyama, T.; Otsuka, H.; Kushibe, A.; Inoue, Y.; Tsuzaki, K. Design Concept and Applications of Fe-Mn-Si-Based Alloys-from Shape-Memory to Seismic Response Control. Mater. Trans. 2016, 57, 283–293.
  46. Soroushian, P.; Ostowari, K.; Nossoni, A.; Chowdhury, H. Repair and Strengthening of Concrete Structures through Application of Corrective Posttensioning Forces with Shape Memory Alloys. Transp. Res. Board 2001, 1770, 20–26.
  47. Sato, A.; Kubo, H.; Maruyama, T. Mechanical Properties of Fe-Mn-Si Based SMA and The Application. Mater. Trans. 2006, 47, 571–579.
  48. Otsuka, H.; Yamada, H.; Maruyama, T.; Tanahashi, H.; Matsuda, S.; Murakami, M. Effects of Alloying Additions on Fe-Mn-Si Shape Memory Alloys. Trans. Iron Steel Inst. Jpn. 1990, 30, 674–679.
  49. Koyama, M.; Sawaguchi, T.; Tsuzaki, K. Si Content Dependence on Shape Memory and Tensile Properties in Fe–Mn–Si–C Alloys. Mater. Sci. Eng. A 2011, 528, 2882–2888.
  50. Sawaguchi, T.; Nikulin, I.; Ogawa, K.; Sekido, K.; Takamori, S.; Maruyama, T.; Chiba, Y.; Kushibe, A.; Inoue, Y.; Tsuzaki, K. Designing Fe–Mn–Si Alloys with Improved Low-cycle Fatigue Lives. Scr. Mater. 2015, 99, 49–52.
  51. Lin, H.C.; Lin, K.M.; Lin, C.S.; Chen, F.H. The Corrosion Behavior of Fe-Based Shape Memory Alloys. Corros. Sci. 2002, 14, 439–442.
  52. Maji, B.C.; Das, C.M.; Krishnan, M.; Ray, R.K. The Corrosion Behaviour of Fe-15Mn-7Si-9Cr-5Ni Shape Memory Alloy. Corros. Sci. 2006, 48, 937–949.
  53. Wan, J.F.; Chen, S.P.; Hsu, T.Y.; Huang, Y.N. Modulus Softening During The γ→ɛ Martensitic Transformation in Fe-25Mn-6Si-5Cr-0.14N Alloys. Mater. Sci. Eng. A 2006, 438, 887–890.
  54. Wang, D.F.; Chen, Y.R.; Gong, F.Y.; Liu, D.Z.; Liu, W.X. The Effect of Thermomechanical Training on the Microstructures of Fe-Mn-Si Shape Memory Alloy. J. Phys. IV (Proc.) 1995, 5, 527–530.
  55. Kajiwara, S.; Liu, D.Z.; Kikuchi, T.; Shinya, N. Remarkable Improvement of Shape Memory Effect in Fe-Mn-Si Based Shape Memory Alloys by Producing NbC Precipitate. Scr. Mater. 2001, 44, 2809–2814.
  56. Farjami, S.; Hiraga, K.; Kubo, H. Shape Memory Effect and Crystallographic Investigation in VN Containing Fe-Mn-Si-Cr Alloys. Mater. Trans. 2004, 45, 930–935.
  57. Dong, Z.Z.; Klotz, U.E.; Leinenbach, C.; Bergamini, A.; Czaderski, C.; Motavalli, M. A Novel Fe-Mn-Si Shape Memory Alloy with Improved Shape Recovery Properties by VC Precipitation. Adv. Eng. Mater. 2009, 11, 40–44.
  58. Murakami, M.; Otsuka, H.; Suzuki, H.; Matsuda, S. Complete Shape Memory Effect in Polycrystalline Fe-Mn-Si Alloys. In Proceedings of the International Conference on Martensitic Transformations, Nara, Japan, 26–30 August 1986; pp. 985–990.
  59. Dong, Z.Z.; Kajiwara, S.; Kikuchi, T.; Sawaguchi, T. Effect of Pre-deformation at Room Temperature on Shape Memory Properties of Stainless Type Fe–15Mn–5Si–9Cr–5Ni–(0.5–1.5)NbC Alloys. Acta Mater. 2005, 53, 4009–4018.
  60. Dong, Z.Z.; Sawaguchi, T.; Kajiwara, S.; Kikuchi, T.; Kim, S.H.; Lee, G.C. Microstructure Change and Shape Memory Characteristics in Welded Fe-28Mn-6Si-5Cr-0.53Nb-0.06C Alloy. Mater. Sci. Eng. A 2006, 438, 800–803.
  61. Zhang, W.; Wen, Y.H.; Li, N.; Xie, W.L.; Wang, S.H. Directional Precipitation of Carbides Induced by c/e Interfaces in an FeMnSiCrNiC Alloy Aged after Deformation at Different Temperature. Mater. Sci. Eng. A 2007, 459, 324–329.
  62. Otsuka, K.; Wayman, C.M. Shape Memory Materials; Cambridge University Press: Cambridge, UK, 1998.
  63. Qiang, X.H.; Chen, L.L.; Jiang, X. Achievements and Perspectives on Fe-Based Shape Memory Alloys for Rehabilitation of Reinforced Concrete Bridges: An Overview. Materials 2021, 22, 8089.
  64. Lei, Z. Fe-based Shape-memory Alloy and its Applications. Dev. Appl. Mater. 2000, 15, 40–45. (In Chinese)
  65. Jin, X.; Jin, M.; Geng, Y. Recent Development of Martensitic Transformation in Ferrous Shape Memory Alloys. Mater. China 2011, 56, 32–41. (In Chinese)
  66. Lee, W.J.; Weber, B.; Feltrin, G.; Czaderski, C.; Motavalli, M.; Leinenbach, C. Phase Transformation Behavior under Uniaxial Deformation of An Fe-Mn-Si-Cr-Ni-VC Shape Memory Alloy. Mater. Sci. Eng. A 2013, 581, 1–7.
  67. Shahverdi, M.; Michels, J.; Czaderski, C.; Motavalli, M. Iron-based Shape Memory Alloy Strips for Strengthening RC Members: Material Behavior and Characterization. Constr. Build. Mater. 2018, 173, 586–599.
  68. Sun, L.; Hhang, W.M. Nature of The Multistage Transformation in Shape Memory Alloys Upon Heating. Met. Sci. Heat Treat. 2009, 51, 573–578.
  69. Ghafoori, E.; Neuenschwander, M.; Shahverdi, M.; Czaderski, C.; Fontana, M. Elevated Temperature Behavior of an Iron-based Shape Memory Alloy Used for Prestressed Strengthening of Civil Structures. Constr. Build. Mater. 2019, 211, 437–452.
  70. Maruyama, T.; Kurita, T.; Kozaki, S.; Andou, K.; Farjami, S.; Kubo, H. Innovation in Producing Crane Rail Fish Plate Using Fe-Mn-Si-Cr Based Shape Memory Alloy. Mater. Sci. Technol. 2008, 24, 908–912.
  71. Shahverdi, M.; Czaderski, C.; Annen, P.; Motavalli, M. Strengthening of RC Beams by Iron-based Shape Memory Alloy Bars Embedded in a Shotcrete Layer. Eng. Struct. 2016, 117, 263–273.
  72. Czaderski, C.; Shahverdi, M.; Brönnimann, R.; Leinenbach, C.; Motavalli, M. Feasibility of Iron-Based Shape Memory Alloy Strips for Prestressed Strengthening of Concrete Structures. Constr. Build. Mater. 2014, 56, 94–105.
  73. Hosseini, A.; Ghafoori, E.; Al-Mahaidi, R.; Zhao, X.L.; Motavalli, M. Strengthening of A 19th-century Roadway Metallic Bridge Using Nonprestressed Bonded and Prestressed Unbonded CFRP Plates. Constr. Build. Mater. 2019, 209, 240–259.
  74. Ghafoori, E.; Hosseini, A.; Al-Mahaidi, R.; Zhao, X.L.; Motavalli, M. Prestressed CFRP-Strengthening and Long-Term Wireless Monitoring of an Old Roadway Metallic Bridge. Eng. Struct. 2018, 176, 585–605.
  75. Hosseini, E.; Ghafoori, E.; Leinenbach, C.; Motavalli, M.; Holdsworth, S. Stress Recovery and Cyclic Behaviour of An Fe-Mn-Si Shape Memory Alloy after Multiple Thermal Activation. Smart Mater. Struct. 2018, 27, 025009.
  76. Ghafoori, E.; Hosseini, E.; Leinenbach, C. Fatigue Behavior of a Fe-Mn-Si Shape Memory Alloy Used for Prestressed Strengthening. Mater. Des. 2017, 133, 349–362.
  77. Koster, M.; Lee, W.J.; Schwarzenberger, M.; Leinenbach, C. Cyclic Deformation and Structural Fatigue Behavior of an FE-Mn-Si Shape Memory Alloy. Mater. Sci. Eng. A 2015, 637, 29–39.
  78. Hong, K.; Lee, S.; Yeon, Y.M.; Jung, K. Flexural Response of Reinforced Concrete Beams Strengthened with Near-Surface-Mounted Fe-Based Shape-Memory Alloy Strips. Int. J. Concr. Struct. Mater. 2018, 12, 45.
  79. Qiang, X.H.; Wu, Y.P.; Jiang, X. Experimental Investigation on Mechanical Properties and Activation-recovery Performance of Fe-based Shape memory alloys. J. Tongji Univ. (Nat. Sci.), 2022; in press.
  80. Hong, K.N.; Yeon, Y.M.; Shim, W.B.; Kim, D.H. Recovery Behavior of Fe-Based Shape Memory Alloys under Different Restraints. Appl. Sci. 2020, 10, 3441.
  81. Inoue, Y.; Kushibe, A.; Umemura, K.; Mizushima, Y.; Sawaguchi, T.; Nakamura, T.; Otsuka, H.; Chiba, Y. Fatigue-resistant Fe-Mn-Si-based Alloy Seismic Dampers to Counteract Long-period Ground Motion. Jpn. Archit. Rev. 2020, 4, 76–87.
  82. Fang, C.; Wang, W.; Ji, Y.; Yam, M.C. Superior Low-cycle Fatigue Performance of Iron-based SMA for Seismic Damping Application. J. Constr. Steel Res. 2021, 184, 106817.
  83. El-Hacha, R.; Michels, J.; Shahverdi, M.; Czaderski, C. Mechanical Performance of Iron-Based Shape-Memory Alloy Ribbed Bars for Concrete Prestressing. ACI Mater. J. 2018, 115, 877–886.
  84. Schranz, B.; Czaderski, C.; Shahverdi, M.; Michels, J.; Motavalli, M. Ribbed Iron-based Shape Memory Alloy Bars for Pre-stressed Strengthening Applications. In Proceedings of the International Association for Bridge and Structural Engineering Symposium, Guimaraes, Portugal, 27–29 March 2019.
  85. Leinenbach, C.; Lee, W.J.; Lis, A.; Arabi-Hashemi, A.; Cayron, C.; Weber, B. Creep and Stress Relaxation of a FeMnSi-based Shape Memory Alloy at Low Temperatures. Mater. Sci. Eng. A 2016, 677, 106–115.
More
© Text is available under the terms and conditions of the Creative Commons Attribution (CC BY) license; additional terms may apply. By using this site, you agree to the Terms and Conditions and Privacy Policy.
Upload a video for this entry
Information
Subjects: Engineering, Civil
Contributors MDPI registered users' name will be linked to their SciProfiles pages. To register with us, please refer to https://encyclopedia.pub/register :
Xuhong Qiang
,
Yapeng Wu
,
Yuhan Wang
,
Xu Jiang
View Times: 703
Revisions: 2 times (View History)
Update Date: 09 Jun 2023
Table of Contents
    1000/1000
    Hot Most Recent
    ScholarVision Creations
    Feedback