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each stage of the shape- memory cycle (Fig. 3a). Once heated to the deformation temperature Treset, an external force is applied, resulting in a corresponding increase in stress. Upon reaching a strain εm, the sample is equilibrated for a specific holding time at constant strain, leading to initial stress relaxation. This position- controlled process is then switched to a stress- controlled process, in which the stress at the total deformation σm is maintained during cooling to Tlow. Finally, strain decreases as the external force is removed, providing a value for the fixed strain εu of the sample. After pro- gramming, the sample is heated from Tlow to Treset, which causes recovery to the recovery strain εp. Ensuring the resistance of shape- memory materials to degradation during performance is vital for their application as functional devices. Plotting strain against time for multi- ple cycles enables the assessment of the robustness of motion and gives information about the time depend- ency of the change in shape of shape- memory materials (Fig. 3b), because any cycle- to-cycle strain shift would be clearly recognizable in this graph52. The recovery process can take place under stress-free or constant- strain conditions (Fig. 3c,d). In a stress-free recovery process, the strain of the material is allowed to change during the shape recovery. By contrast, in a constant- strain condition, movement of the mate- rial is limited to specific shape changes caused by the geometry of the specimen. The force exerted through macromolecular reorientation of the chain segments generates a recovery stress against the apparatus. A stress- free recovery enables the determination of the temperature at the highest recovery rate, that is, the inflexion point on the stress–temperature curve (Fig. 3c), called switching temperature TSW. Characteristic values, such as the recovery temperature range ΔTrec and the recovery rate νrec, can also be obtained from stress- free recovery testing. A constant- strain recovery process enables the determination of the maximum recovery- stress temperature Tσ,max and the inflexion point of the stress–temperature curve Tσ,inf (Fig. 3d). These two recovery regimes provide complementary data. When comparing different types of polymeric shape- memory materials, only slight differences are observed between a physically crosslinked thermo- plastic material and a covalently crosslinked polymer network during a stress- free recovery; however, in the constant- strain regime, the materials display substan- tially different behaviour. At Tσ,max, the entropic elas- ticity of the thermoplastic sample exactly balances the decrease in Young’s modulus of the softening material. In contrast to the covalently crosslinked polymer network, the increasing chain mobility of the physical netpoints becomes dominant beyond Tσ,max, driving a substantial decrease in stress. Reversible shape- memory actuator. Similar to the one- way shape- memory effect, the programming pro- cedure for a reversible shape- memory actuator contains deformation and fixation steps before the release of external stress (Fig. 4a). The deformation is performed at a temperature Treset above the melting transitions of the two crystalline domains. The fixation is performed by cooling to a temperature Tlow below the melting transi- tions of the two crystalline domains. Heating and cool- ing between a temperature Tsep, which bisects the two melting transitions, and Tlow causes a reversible change in shape of the sample. Multicyclic measurements are a b d c e Reversible shape-memory effect Time (min) T (° C ) ε ( % ) 60 40 20 0 100 600500400300200 Time (min) 40 20 30 100 600500400300200 Shape A Shape A T sep T act,cool T act,heat T low Shape B Shape B Programming T low T reset T→ 12 3 ε↑ σ ↑ σ ↑ T↑ Temperature (°C) ε ( % ) ε → 40 ε m 20 30 0 20 40 σ = 0 T act,cool T act,heat T low T reset T sep 60 1 2 3 T low T reset T low T sep T low T low T sep T sep From program m ing Fig. 4 | Quantification of a reversible shape- memory effect. a | The stress (σ)–temperature (T )–strain (ε) graph is shown for the programming of a reversible shape- memory effect. The stages are the following: (1) deformation, (2) cooling and (3) release of external stress. Tlow is chosen to be beneath the melt transitions of the two crystalline domains; by cooling to this temperature under external stress, the shape- shifting pathway is defined. Treset is chosen to be above the melt transitions of the two crystalline domains; heating to this temperature allows the material to be deformed by the application of external stress. b | The reliability of actuation after programming is tested by performing repetitive heating to Tsep (separation temperature) and cooling to Tlow with ε = 0 MPa. Tsep is chosen to bisect the two crystalline domains; heating to this temperature before cooling generates reversible actuation. c | Schematic illustration of programming with subsequent actuation. A sample is first deformed at Treset (1) before undergoing cooling to Tlow while under external stress (2); the external stress is removed (3) before the temperature is cycled, and the corresponding change in strain is measured under an external stress- free condition. d | Schematic curve showing the actuation of a sample under stress- free conditions. This curve can be used to determine the highest actuation rate during heating Tact,heat and cooling Tact,cool. e | Recovery under different applied stresses is illustrated. Panels b and d are adapted with permission from reF.22, Wiley- VCH. www.nature.com/natrevmats R e v i e w s Reprogrammable recovery and actuation behaviour of shape-memory polymers Characterization Reversible shape-memory actuator. Fig. 4 Quantification of a reversible shape-memory effect.
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