Introduction

Mechanochromic polymers are able to change their color of absorption or emission as a response to mechanical force. This visualization of molecular deformation1,2,3,4 and covalent bond cleavage5,6,7,8,9 sheds light on the force transduction at the single polymer chain level and offers ample possibility for applications, such as force sensor design, tamper-proof packing, and safety of materials10. Likewise, mechanochromic materials are in high demand for the investigation of fundamental physical and biological questions, including visualization of force distributions in Gecko-type adhesives11 or cell hydrogel interactions relevant to tissue engineering and cell differentiation12. Mechanochromic materials are known for some time1,3, but activity in this area is increasing since the last decade after seminal works on force-induced C–O bond cleavage of spiropyran (SP) furnishing colored merocyanines (MC), which has been demonstrated in solution13 and in bulk materials14. Such two-state systems represent a mechanically triggered optical switch with “on” (MC) and “off” (SP) states. Other mechanophores such as Diels-Alder adducts15, various spiro compounds7,16,17, or precursors for stable radicals5,18,19 are based on this general principle as well. Mechanistically different is mechanically induced cleavage of dioxetane-containing polymers leading to excited states, which undergo energy transfer to chromophores and light emission in the visible region20. Next to covalent systems, supramolecular interactions enable the design of mechanoresponsive materials, using processes that rely on distinct optical properties of differently stacked chromophores1,2,21.

Depending on application and mode of detection, reversibility of mechanophores may or may not be required. Most of the mentioned mechanophores make use of a mechanically triggered chemical reaction and thus involve a two-state system in the most simple case. Here, one advantage lies in the tunable but typically long lifetime of the mechanically induced “on state” after stress release, which is critical for signaling damage in e.g., glass fiber composites22 once exposed to a critical overload. After stress release, a fast back reaction to the initial, active state often demands external energy like heat21 or UV-light6,17. In the case of SP, the barrier of the back reaction depends sensitively on the substitution pattern and can be lowered to obtain a transient mechanochromic response that is only stable under-maintained stress23. Yet, in order to allow for the investigation of dynamic mechanical processes or online monitoring of stress distributions, two-state systems are rather inappropriate. Another drawback of two-state systems is their lack of differentiation between different forces, as soon as the activation energy is reached, i.e., the restriction to a switch between “on” and “off”. An interesting but sophisticated remedy to this restriction is the usage of multiple mechanophores in polymer blends24 or composites25.

Another principle of mechanochromism in polymers that has received far less attention relies on conformational changes in conjugated π-systems such as polydiacetylenes3,4 or poly(3-alkylthiophene)26,27. Reported examples of force-induced conformational changes in conjugated polymers include polyfluorenes28,29 and polythiophenes30,31 where coplanarity is possible due to rather shallow torsion potentials. In most cases28,29,31, blending approaches were used to attenuate absorption of specimens under scrutiny, which is associated with morphological and processing issues, and eventually limits the scope of applications.

Here, we report a donor (D)-acceptor (A) mechanochromic torsional spring that exhibits a large dihedral angle in the equilibrium geometry. The mechanochromic response originates from the force-induced planarization of D and A, which leads to increased electronic communication and hence marked changes in the optical properties. Our system is based on differently substituted diphenyldiketopyrrolopyrroles (PhDPP) that are covalently incorporated into the backbone of an amorphous, rigid yet tough polyphenylene. As the mechanically induced planarization corresponds to a deflection from equilibrium geometry, stress release gives rise to fast recovery of the initial optical properties, despite the rigid polyphenylene matrix. Consequently, the bathochromic shift of both absorption and emission bands is directly related to the tensile stress acting on the polymer chain. These results are corroborated by detailed theoretical calculations, including tensile testing, which confirms force-induced planarization and the associated optical changes. The calculations furthermore reveal qualitative forces acting on the PhDPP units.

Results

Design of a DA torsional spring

The principle of the herein presented mechanochromic torsional spring is based on a pair of an electron-rich donor (D) and an electron-deficient acceptor (A) brought into conjugation. Sterical hindrance between D and A results in a significant deviation from coplanarity at equilibrium geometry that only allows for partial conjugation of the π-systems (Fig. 1a). This situation causes both, a hypsochromic shift (a shift to smaller wavelengths) of the charge-transfer (CT) absorption band in the UV-vis spectrum and a decrease in the oscillator strength compared to the fully coplanar DA-system. If the position of polymer chain attachment at the DA spring is appropriately chosen, elongating the end-to-end distance of the chain by macroscopic force may lead to planarization of the DA spring (Fig. 1b). The resulting increase in conjugation leads to a bathochromically shifted CT band and an increase in oscillator strength (Fig. 1c). Consequently, a release of the external force restores the initial conditions with respect to the geometry and optical properties of the DA spring.

Fig. 1: Principle of a mechanochromic torsional spring.
figure 1

a A donor-acceptor (DA) unit with a large torsional angle φ is covalently incorporated into a polymer chain. b Stretching of the polymer backbone causes a decrease of φ. c Schematic reversible shift of the UV-vis-absorption band as a response to elongational stress. d Structure of the DA-system reported here based on diphenyldiketopyrrolopyrrole (PhDPP).

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As a DA system, a DPP core (A) with two ortho-substituted phenyl rings (D) as flanking units was chosen. N-methylation of the lactam rings impedes intermolecular H-bonding and strong aggregation between DPP chromophores (Fig. 1d)32. To evaluate the suitability of the ortho-substituted PhDPP (o-DPP) as DA spring, we start from bromine-substituted diphenyl DPP. Ortho-substitution of the phenyl ring with bromine (o-BrPhDPP) increases the torsional angle compared to more often used para-Br functionalization including ortho-hydrogens (p-BrPhDPP). While our DFT calculations reveal a dihedral angle of 30° for p-BrPhDPP similar to other p-PhDPPs33,34, sterical hindrance enforces a more than doubled dihedral angle of 67° for o-BrPhDPP (Supplementary Fig. 1, Fig. 2a).

Fig. 2: Theoretical evaluation of ortho-substitution in PhDPP.
figure 2

a Molecular structures of o-BrPhDPP (red) and p-BrPhDPP (blue). b Computed torsion potentials for the rotation of the BrPh group. c Simulated UV-vis spectra for the relaxed structures in the gas phase and experimental UV-vis spectra in DMF (0.035 mmol L−1). d Variation of the simulated CT-peak position with the dihedral angle. Dashed lines indicate equilibrium geometries (minima in the torsion potentials in b), and the arrow the direction if an external force is applied.

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To further evaluate the suitability of the ortho-substituted PhDPP as DA spring, we calculated how the rotation of the BrPh-group with respect to the DPP core changes the energy and optical properties of BrPhDPP (Fig. 2b–d). The corresponding torsion potentials for the simultaneous rotation of both flanking BrPh groups in p-BrPhDPP and o-BrPhDPP are depicted in Fig. 2b (very similar potentials are obtained when rotating single BrPh groups in hypothetically asymmetric DPP molecules, see Supplementary Fig. 2). Moderate sterical hindrance drives the equilibrium configuration of p-BrPhDPP away from the electronically preferred coplanar conformation. This effect is much stronger for o-BrPhDPP, where the equilibrium dihedral angle is much larger, as well as the maximum energy of up to 200 kJ mol−1 required to reach full coplanarity. The observed asymmetry in the torsion potentials is caused by the different interactions of the BrPh ring with the methyl and carbonyl groups of the DPP core. Full rotation, therefore, shows a hysteresis that effectively stabilizes the orientation to one side (Fig. 2b).

Figure 2c shows the experimental and calculated UV-vis spectra of o-BrPhDPP and p-BrPhDPP. The spectra are in good qualitative agreement, in particular for the relative shift of the low energy bands of o-BrPhDPP and p-BrPhDPP. In theory and experiment, these bands differ by 0.31 eV and 0.30 eV, respectively. The possibility to detect geometric changes by optical changes (or vice versa) can now be inferred from Fig. 2d, which displays the change of the absorption wavelength of the CT band with varying dihedral angles. Deviations of 15° and 30° from the equilibrium geometry shift the CT band by 30 nm and 55 nm, respectively. This estimation confirms the diphenyl DPP system as a promising candidate for an experimental realization of a DA spring.

Theoretical investigation of the DA spring under force

We now turn to the question of the effect of force acting on the DPP spring once covalently incorporated into a polymer matrix. We simulated an external force pulling on o-MeOBuDPP or m-MeOBuDPP, which are alkylated PhDPP versions used later experimentally, as depicted in Fig. 3a. Our model structures show similar effects of sterical hindrance in their equilibrium structures at zero force compared to BrPhDPP, whereby the methoxybutyl substituent in o-MeOBuDPP provides slightly less repulsion with the DPP core than the Br atom in o-BrPhDPP.

Fig. 3: Theoretical elongation of the DA spring.
figure 3

a Structures of the ortho-4-methoxybutyl and meta-4-methoxybutyl functionalized DA spring (MeOBuDPP) for theoretical investigations. b Calculated relation between external elongational force (F) and the dihedral angles α, β between Ph and DPP core. c Analysis of the contributions from changes in the dihedral angles and deformation of the structure on the optical properties. d Calculated relation between F and both wavelength and energy of the charge-transfer absorption band of o-/m-MeOBuDPP.

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As the external force increases, the distance between pulling points and the central part of the molecule increases too. This leads to a deformation of the molecule, which reduces sterical hindrance caused by the interaction of ortho-substituents at the phenyl ring and the DPP core (Fig. 3b, Supplementary Figs. 3 and 4). This effect is significantly stronger for o-DPP due to its larger ortho-substituent and larger initial dihedral angle. In both isomers, the dihedral angle decreases until the molecule eventually reaches a nearly coplanar structure (Fig. 3b). Thus, the primary cause for planarization is not the direct force acting on the DA spring, rather the tendency of the DA system to increase π orbital overlap and thereby reduce its energy, which becomes increasingly possible as a sterical hindrance is relieved. Therefore, the independent rocking of the central DPP core is restricted (cf. Fig. 2b). The two weakest Me-O bonds break spontaneously at larger forces of around 6 nN.

The force-induced planarization has a clear effect on the optical properties as revealed by time-dependent DFT (TDDFT) calculations in Fig. 3c and d. The absorption maximum λmax,abs shows a clear bathochromic shift with increasing external force. This effect is strongest in o-MeOBuDPP which displays a large total absorption shift Δλmax,abs of 115 nm at 6 nN, whereas for the analogous meta-derivative Δλmax,abs = 50 nm at 5.9 nN is obtained. Figure 3c reveals that the shift is caused both by the rotation of the phenyl rings, as well as by the deformation of PhDPP. There is a striking similarity in the CT peak positions between ortho-springs and meta-springs for pure rotation (without action of an external force). The deviation of these two modes at small dihedral angles is caused by steric repulsion between the Ph rings and DPP cores, which leads to an additional deformation and a stronger shift in o-PhDPP. In particular, for m-MeOBuDPP, deformation is the main source of the shift due to the initially smaller rotation. Accordingly, the possibility for relaxation in this mode under the action of the external force is decreased. Further analysis of the effect of deformation is presented in Supplementary Information (Supplementary Figs. 5–11), indicating that the elongation of C-C bonds in the DPP core has the strongest influence on the wavelength of the CT peak.

With a linear fit up to ~1 nN, which is expected to be a reasonable range for the forces present in this experiment23, we predict shifts Δλmax,abs depending on the force F acting on the DA system of Δλmax,abs/F = 7 ± 1 nm nN−1 and 21 ± 1 nm nN−1 for m-MeOBuDPP and o-MeOBuDPP, respectively. These numbers are obtained from the rotamer with trans-up-down conformation. Other rotamers of m/o-MeOBuDPP (Supplementary Table 1 and Supplementary Fig. 12) are very similar in energy but show different behavior under external force. Assuming all four rotamers to be present with equal probability gives a slightly lower averaged response of Δλmax,abs/F = 5 ± 1 nm nN−1 and 17 ± 2 nm nN−1 for m-MeOBuDPP and o-MeOBuDPP, respectively. An exchange of the methoxybutyl substituents by methyl groups (Supplementary Table 2 and Supplementary Figs. 13–17) and additionally considering all rotamers leads to enhanced shifts in the range of small forces: Δλmax,abs/F is about 12 ± 1 nm nN−1 and 45 ± 3 nm nN−1 for m-MeDPP and o-MeDPP, respectively. This result hints at the rigidity of the linker being important for force transduction. We will use these force-dependent shifts to estimate the molecular forces acting in the experiment below.

Synthesis of a DPP based DA torsional spring

In order to verify these predictions experimentally, we synthesized ortho-functionalized and meta-functionalized diphenyl DPPs and covalently incorporated them into a rigid, yet ductile, polymer matrix. Prior investigations with DA spring functionalized polydimethylsiloxane (PDMS) showed only very little mechanochromic response, which we ascribed to its soft nature (Supplementary Fig. 18). Despite the growing interest in DPP-based materials during the last two decades32,35, ortho-substituted diphenyl DPPs have been rarely reported so far. One reason is certainly that coplanarity of DPP-containing conjugated materials is a common target33. Another factor may be related to the chemistry involved in ortho-substitution, which is significantly more challenging due to the increased sterical hindrance. The few reported syntheses of o-substituted diphenyl DPP chromophores state poor yields of 2–7%36,37. Using the direct and efficient succinate synthesis route, the preparation of bis(o-bromophenyl)diketopyrrolopyrrole (o-BrPhDPPH) 2a is displayed in Fig. 4a.

Fig. 4: Synthesis route of the DA torsional springs.
figure 4

a, b Synthesis of o-LBrPhDPP (5a) and m-LBrPhDPP (5b) with L = phenoxybutyl. c, d Incorporation of 5a and 5b into the polyphenylene matrix to o-DPP-PmmpP (6a) and m-DPP-PmmpP (6b). Reaction conditions: (i) diisopropylsuccinate, NaOt-Am, FeCl3, t-AmOH, 100 °C, 15 h; (ii) Me-p-Tos, K2CO3, DMF, 120 °C, 3 h; (iii) 4-bromobutylzinc bromide (in situ), Pd2(dba)3, SPhos, DMAc, 80 °C, 2 h; (iv) 4-bromophenol, K2CO3, DMF, 50 °C, 16 h; (v) Pd2(dba)3, SPhos, Aliquat 336, toluene/2 M K2CO3 (aq), 70 °C, 24 h.

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For the herein achieved, comparably high yield of 10% of 2a (Supplementary Fig. 19), very slow addition of the succinate is crucial. However, with increasing reaction time debromination occurs, therefore the reaction was stopped after 15 h. The first evidence for the increased torsional angle of o-BrPhDPPH is its relatively high solubility. The lower ability of o-BrPhDPPH to aggregate compared to the meta-analog m-BrPhDPPH 2b even allowed acquiring 13C NMR spectra in good quality in the absence of solubilizing alkyl groups. After N-methylation of 2a, most of the debrominated species could be removed by repeated recrystallization to obtain 3a in 60% yield and with a purity of 97%.

In light of the results from theory highlighting beneficial rigid linkers (Supplementary Figs. 13–17), direct incorporation of 3a into the polyphenylene PmmpP23 via Suzuki polycondensation (SPC) appeared most straightforward. However, this synthetic approach failed (Fig. 4). Apparently, the sterically hindered 2-bromo group of 3a reacts much slower compared to 5,5′-dibromo-2,2′-bis(hexyloxy)-1,1′-biphenyl (M2). For this reason, a butylene linker was introduced via Negishi coupling while maintaining the general o-substitution pattern, leading to 4a in 14% yield38. To introduce the 4-bromophenyl unit required for SPC, ether synthesis with 4-bromophenol was straightforward and led to the monomer bis(o-(4-(4-bromophenoxy)butyl)phenyl)DPP (o-LBrPhDPP) 5a in 38% yield.

Terpolymerization of 1 mol% of 5a with 1,4-benzenediboronic acid bis(pinacol)ester (M1) and M2 resulted in the statistically functionalized o-DPP-PmmpP (6a) with the number and weight average molecular weights from size exclusion chromatography (SEC) Mn,SEC = 34 kg mol−1 and Mw,SEC = 130 kg mol−1 after Soxhlet extraction (Fig. 4c). To provide reference material, the entire synthesis route was repeated with the same DPP chromophore (m-LBrPhDPP) 5b having the point of attachment in meta position (Fig. 4b, d). The resulting m-DPP-PmmpP (6b) had Mn = 33 kg mol−1 and Mw = 84 kg mol−1. Differential scanning calorimetry (DSC) and thermogravimetric analysis of 6a and 6b furnished onset temperatures of 411 °C and glass transition temperatures of 115 °C and 112 °C, respectively (Supplementary Figs. 20 and 21).

Experimental investigation of the DA spring

Experimental investigations of the mechano-optical properties were carried out on dumbbell-shaped films of the DPP-functionalized PmmpPs 6a and 6b. The good agreement of UV-vis absorption spectra of monomers 5a, b and polymers 6a, b in solution (Supplementary Fig. 22) excludes significant interference between DA spring and polymer matrix and DA aggregation. During tensile testing, the UV-vis absorption band of 6a shown in Fig. 5a flattens significantly with increasing elongation. The strong broadening at high strain suggests a force-induced broadening of the distribution of torsional angles.

Fig. 5: Combination of tensile testing and in-situ optical characterization of thin films.
figure 5

Left column: o-DPP 6a; right column: m-DPP 6b. a, b UV-vis absorption spectra measured during/after stress-strain experiments and (c, d) the corresponding emission spectra. e, f Stress-strain curves (black) together with the detected emission maxima λmax,em (blue) and the changes in Full Width at Half Maximum of the emission bands (ΔFWHM, red). Strain values as percentage elongation with respect to initial specimen length.

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A comparison of the stress-strain curve with the corresponding values of absorption maxima λmax,abs (Supplementary Fig. 23b) illustrates the relationship between tensile stress and absorption behavior. It can clearly be seen that for strains larger than 60%, the bathochromic shift Δλmax,abs is strongly linked to the stress-strain behavior and can therefore be described as mechanochromic response with a maximum Δλmax,abs ~8 nm. The delay of the mechanochromic response below 50% strain is due to the combination of the experimental setup and specimen shape (see Supplementary Figs. 23 and 24), which does not guarantee maximum force localization centered at the optical path. A similar analysis of m-DPP-PmmpP 6b was not possible, because the shape of absorption spectra indicates several contributions (Fig. 5b). The higher resolution of the vibronic bands with increasing planarity of the π-system is already known from other DPP derivatives39,40.

The rather moderate changes in absorption under stress motivated us to investigate photoluminescence (PL), which is generally more sensitive for the detection of a mechanochromic response1,41. Photoluminescence recorded from 6a during tensile testing is depicted in Fig. 5c, which displays clearly stress-induced red-shifted spectra. The second advantage of photoluminescence compared to UV-vis absorption is the further reduced contribution of the polyphenylene matrix due to the high PL intensity of the DPP chromophore (Supplementary Fig. 25). The stress-dependent PL spectra illustrate the continuous bathochromic shift of the emission band Δλmax,em of up to 19 nm with increasing stress (Fig. 5e). We assume that the retardation of mechanochromic response, i.e., between the onsets of necking and rise of Δλmax,em, is an artifact, produced by the migration of the necking region into the optical path of PL detection and thus caused by the DIN norm of the specimen used (see Supplementary Figs. 23 and 24). Strikingly, a qualitative correlation between Δλmax,em, and stress is observed, i.e., a stronger increase in stress produces a stronger Δλmax,em. On the other hand, the rather constant stress during the continuous yielding between 20 and 150% strain results in a plateau of Δλmax,em. Together with a negative control experiment using low molecular weight o-DPP-PmmpP (Supplementary Fig. 26), this confirms that the torsion potential of the DPP chromophore and the mechanochromic response of the DA spring can indeed be modulated by macroscopic force. Such a mechanism is clearly different from two-state systems, in which an increasing force commonly increases intensity but does not alter the wavelength of emission2. Upon rupture of the specimen, force is released and the o-DPP spring quickly returns to equilibrium seen by the PL spectrum perfectly matching the original spectrum of the non-strained state (Fig. 5c). While it is expected that a torsional profile enables such reversibility upon deviation from equilibrium geometry, the fast reversibility is still remarkable as the plastically deformed, tough PmmpP matrix with its high Tg of 115 °C has undergone strains up to 300% at that time. Furthermore, Fig. 5c shows that the low energy onset of emission increases while the high-energy onset does not change much. This strain-induced broadening of the emission band is reflected by the increasing full width at half maximum (FWHM) in Fig. 5e. In addition to the overall increasing planarization, the distribution of DA torsional angles within the polymer becomes broader as not all springs are deformed in the same way.

Figure 5d reports the corresponding emission spectra of m-DPP 6b also featuring a clear maximum. However, as for the absorption spectra, the more planar m-DPP derivative shows stronger vibronic features in the form of shoulders compared to ortho-DPP. The pronounced shoulder around 570 nm is also present in dilute solution (Supplementary Fig. 27), but its intensity is increased in solid-state of 6b. The good agreement of the PL spectra of m-DPP monomer 5b and polymer 6b (Supplementary Fig. 27) excludes an influence of PmmpP on the PL properties of the chromophore. Furthermore, different solvent polarities do not show a noteworthy effect on the emission behavior of the m-DPP unit (Supplementary Fig. 27). Under elongational force, the normalized spectra of 6b in Fig. 5d show a bathochromic shift of λmax,em, and growth of the low-energy band. Due to superposition, the increased intensity of the shoulder influences the position of λmax,em. Interestingly, the FWHM changes only marginally (Fig. 5f, red dashed line). At strain at break (229%), m-DPP exhibits Δλmax,em = 7 nm, which depicts a weaker mechanochromic response compared to o-DPP as expected from theory. Thus, the m-DPP spring clearly displays an overall weaker response. Due to different intensities of vibronic shoulders, the quantitative comparison of the mechanochromism between o-DPP and m-DPP on the basis of Δλmax,em values is not straightforward.

It is now interesting to compare the computed Δλmax,abs range with the much smaller experimentally observed values of Δλmax,em, assuming a stress-independent Stokes shift. Usage of the theoretical fits from m/o-MeOBuDPP and the measured Δλmax,em = 7 and 19 nm for m-DPP and o-DPP, respectively (Fig. 5c, f), results in estimated forces of 1.4 ± 0.6 and 1.1 ± 0.1 nN to act on the m-DPP and o-DPP springs, respectively (Fig. 3c). Thus, by combining theory and experiment it is possible to read out forces that act on single chains, which is not possible from experimental investigations alone.

Reversibility of the mechanochromic response

The reversibility of the o-DPP–based DA spring was further investigated in a back-and-forth stress-strain experiment, in which the stress was released three times by negative elongation (Fig. 6a). PL spectroscopy was measured during tensile testing and the time-dependent stress and Δλmax,em values were recorded. The images displayed in Fig. 6b show 6a under UV-light (365 nm) at different times. At position 2 (50% strain), with the necking region of the sample having reached the light path of PL detection, 6a showed a mechanochromic response Δλmax,em of 6 nm. The shift of λmax,em reversed immediately upon stress release (Fig. 6, pos. 3) and remained constant until further stretching of the sample. Similar behavior was observed during the following stress and release steps. Considering that tensile testing was performed 90 °C below the polymer’s Tg, the quick reversibility of the DA spring is remarkable. Furthermore, despite the increasing deformation of the polymer matrix, the mechanochromic response Δλmax,em remains strongly dependent on the applied tensile stress until rupture of the specimen. At 263% strain (Fig. 6b, pos. 4), the mechanically induced shift of 16 nm is clearly visible by the naked eye.

Fig. 6: Reversibility of the mechanochromic response.
figure 6

a Stress vs. time curve (black) of o-DPP 6a during a stress-strain experiment with three relaxation breaks via negative elongation (5 mm min−1 for both directions). The corresponding shifts Δλmax,em (blue) from PL-spectroscopy were correlated to the stress values by the time. b Images of the specimen under UV-light (365 nm) at the four indicated positions in the stress-time curve.

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Discussion

We have designed, simulated, and synthesized a mechanochromic donor-acceptor (DA) torsional spring based on ortho-substituted diphenyldiketopyrrolopyrrole (o-DPP), in which a stress-induced decrease of the dihedral angle between D and A caused a bathochromic shift of absorption and emission wavelength during tensile testing. Incorporation of the DA spring into an amorphous, high Tg, and tough polyphenylene matrix was key to experimentally observe spectral shifts. The theoretical calculations were crucial to minimize synthetic efforts and enable a deep understanding of the molecular properties and mechanistic details of the DA spring. The combination of simulations and experimentally determined spectral shifts allowed us to extract the effective microscopic forces that experimentally acted on a single DA spring in a quantitative manner. The maximum average force acting on the chains was estimated to be ~1.1 nN based on theoretical calibration. Thus, the tough polyphenylene matrix did not only enable deformation at room temperature but also provided high rigidity for transduction of sufficiently large forces. These estimated forces for a single chain are difficult to reconcile with macroscopically measured stress values of ~50 MPa. Establishing quantitative correlations between forces on single chains and macroscopic stress remains an open question and is the subject of ongoing investigations. As the mechanochromic response relies on a deflection of the equilibrium geometry of the DA spring, conformational and color changes were fully reversible on a short timescale even within the rigid polyphenylene matrix. The herein presented mechanochromic DA spring has several advantages over existing mechanophores, such as (i) fast response due to the missing barrier as present in two-state systems, (ii) reversibility for the same reason and (iii) continuous variation of wavelength with stress. These properties render the DA spring concept qualitatively different from other mechanochromic systems. In future studies, we will address the correlation of single-chain and bulk properties required for applications that involve real-time stress-sensing and mapping of force distributions.

Methods

Syntheses

All details regarding the synthesis and characterization of small molecules and polymers are given in the Supplementary Information.

Preparation of films

60 mg of DPP-PmmpP (6a or 6b) were mixed with 120 mg pristine PmmpP and dissolved in 3 mL dichloromethane (DCM) followed by stirring for 30 min. The clear solution was filtered and cast into a petri dish (ø = 35 mm). The sample was covered with an inverted beaker and the solvent evaporated overnight in a fume hood at room temperature. The dumbbell-shaped specimens for mechanical testing were die-cut from the film using a standard punching tool (DIN 53504 type 3) having a width of 2 mm and an initial testing length between 18 and 20 mm. Typical thicknesses were between 100–130 µm. In order to observe full reversibility of the m-DPP spring, complete removal of DCM either by prolonged room temperature storage or the application of vacuum following film casting is necessary.

Combination of tensile testing and optical characterization

Tensile Testing was carried out on a Linkam TST-350 without closing the stress-strain chamber and by using a displacement ramp of 5 mm min−1. The shown values of stress were calculated by considering the constant cross-section area of the specimen’s mid-point at 0% strain. Absorption spectra were measured in transmission with a Flame-S UV-vis spectrometer from Ocean Optics. The spectra were smoothed via Savitzky-Golay filter considering 51 pts (6a) and 21 pts (6b). Excitation for photoluminescence (PL) spectra was carried out using a UV LED (Nichia NVSU233A UV SMD-LED, 365 nm, max. 1030 mW, operated with 900 mA) at a distance of 10 cm. The angle between exciting and detected light was 60 degrees. PL spectra were measured on the same spectrometer used for UV-vis spectroscopy and smoothed via Savitzky-Golay filter considering 21 pts. The data of optical properties and mechanical analysis was correlated via measuring time and include a maximum error in the strain of ±2%.

Computational settings

The electronic structure of the molecules was calculated using DFT as implemented in the GPAW package42,43 where the exchange-correlation potential is modeled as devised by Perdew, Burke, and Ernzerhof44. Wave functions and electron density were described within the projector augmented wave method, where their smooth parts are represented on real-space grids with grid spacing 0.15 Å for the wave functions and 0.075 Å for the electron density. The grid was ensured to cover at least 4 Å around each atom. Optical properties were calculated by time-dependent DFT (TDDFT) in Casidas linear response formalism45,46. All transitions between Kohn-Sham orbitals within an energy range of 8 eV were considered in the linear response calculations, which were checked for convergence for excitations in the optical range (<3 eV) of interest here.

In order to explore the action and effects of external forces on the molecules, we used the method of constrained geometries to simulated external force (COGEF)47,48,49. This method restricts the distance d between the two atoms where the external force is thought to act. Relaxation of all other degrees of freedom defines a potential U(d) and the necessary external force F(d) to satisfy the constraint. In the calculation, the force can be determined either from the derivative δU⁄δd or equivalently from the forces acting on the constrained atoms.