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Thermoresponsive Micropatterned Substrates for Single Cell Studies

Thermoresponsive Micropatterned Substrates for Single Cell Studies

  • Kalpana Mandal, 
  • Martial Balland, 
  • Lionel Bureau


We describe the design of micropatterned surfaces for single cell studies, based on thermoresponsive polymer brushes. We show that brushes made of poly(N-isopropylacrylamide) grafted at high surface density display excellent protein and cell anti-adhesive properties. Such brushes are readily patterned at the micron scale via deep UV photolithography. A proper choice of the adhesive pattern shapes, combined with the temperature-dependent swelling properties of PNIPAM, allow us to use the polymer brush as a microactuator which induces cell detachment when the temperature is reduced below C.


Surface patterning is a powerful tool for the design of cell-based assays and sensors, or for fundamental studies of cellular response to environmental cues [1][3]. The combination of surface chemistry and microfabrication or self-assembly techniques allows to create substrates onto which adhesion can be tuned so as to obtain regular 2D arrays of immobilized cells, with adhesive features controlled at the cellular or even sub-cellular scales [4], [5]. Such patterns have proven to be highly valuable for statistical analysis of the response of cells cultured in a well-controlled microenvironement, in studies related to cell polarity [6], critical adhesion [7], or stem cell differentiation [8].

Many different strategies have been developed to fabricate surfaces presenting cell-adhesive patterns, among which the most popular are based on microcontact printing or photolithography [2], [3]. These widespread techniques may yet exhibit drawbacks in terms of ease of use ( needed equipments or large number of steps), reproducibility, large scale homogeneity of the patterns, or stability of the produced surfaces. A key point in designing such surfaces is to obtain a high contrast between the regions onto which cells attach and the surrounding non-adhesive background. The use of background polymer coatings, and in particular polymer brushes, have become a favorite choice, for they exhibit excellent protein-repellency, hence efficient cell non-adhesiveness [9][12].

On the one hand, patterned brushes of “passive” water soluble polymers have been elaborated via two main routes:

  1. uniform coating of the substrate by a “grafted-onto” brush, i.e. by adsorption of a block-copolymer containing a protein-repellent part (often poly(ethylene-glycol)) stretching away from the underlying surface. Such a uniform brush is subsequently patterned by selective UV irradiation to create adhesive zones [11], [12].
  2. polymer brushes grafted from the substrate, i.e. grown from a layer of polymerization initiators first grafted on the substrate. Patterning is achieved by micro-contact printing of the initiator, which ensures a growth of polymer chains restricted to the intiator-printed regions [9], [10].

These two techniques have already proven to yield patterned substrates suitable, in terms of length scale and adhesive contrast, for single cell studies. However, long term use or storage stability is a limitation of coatings using physisorbed copolymers, while spatial resolution might be an issue with methods employing microcontact printing, because surface diffusion of the printed molecules may blur the initial pattern.

On the other hand, the use of thermosensitive polymer coatings (as opposed to the above “passive” ones) attracts an ever-growing interest in the field of cell adhesion control. Since the pioneer work of Okano et al. [13], it has been shown that poly(N-isopropylacrylamide) (PNIPAM) brushes could switch from a cell-adhesive to a cell-repellent state when the temperature was decreased from 37C to below 32C, the temperature at which water goes from poor to good solvent of PNIPAM chains [14], [15]. Such a temperature-controlled cell adhesion has been observed to be favored by brushes of low enough thicknesses, while thicker and/or more dense brushes behaved essentially as non-adhesive coatings irrespective of the temperature [16], [17]. Coatings based on PNIPAM or its copolymers have been employed in several previous studies in order to create patterned thermoresponsive substrates [18][21]. However, these studies have focused on patterns of large dimensions (tens or hundreds of microns up to several millimeters), for they aimed at harvesting macroscopic cell sheets for tissue reconstruction applications.

In the present article, we report a method to fabricate thermoresponsive patterned substrates which combines many of the advantages of the above-mentioned techniques and allows for single cell studies.

We show that the use of high density polymer brushes of PNIPAM, bound to glass substrates via the so-called “grafting-from” method, and patterned by direct photo-ablation, represents a reliable, fast and cost-effective technique to design thermosensitive micropatterned platforms. Compared to the existing well-established templating techniques, the method we report presents the following important features, and comes as an interesting alternative to elaboration of coatings based on adsorbed ethylene-glycol copolymers [12]:

  1. PNIPAM brushes are elaborated from common and inexpensive chemicals, and their molecular structure can be tuned at will. Furthermore, micron-scale patterning is achieved in one single step, without requiring access to clean room facilities.
  2. Polymer chains being covalently bound to the substrate, such coatings show excellent usage and storage long-term stability.
  3. High grafting density brushes display superior protein and cell repellency, obtained in an extremely reliable and reproducible way.
  4. Although such high density brushes are cell-repellent at 37C, PNIPAM chains still shift from a collapsed to a swollen state as the temperature is decreased below the polymer LCST (Lower Critical Solution Temperature) of 32C. This temperature-controlled conformation change of PNIPAM, combined with a proper choice of the pattern shapes, make the polymer coating act as a thermoactuator which allows us to detach the studied cells by lowering the surface temperature. This adds a very attractive feature to the usual “passive” micropatterned platforms.

In contrast to previous works describing structured PNIPAM substrates exhibiting pattern dimensions suitable for multicellular organizations [18][21], we show here for the first time that PNIPAM coatings are easily and accurately patterned at the single cell level via a photoablation technique that is easier to implement than e.g. laser-ablation [22] or photolithography methods previously reported [19]. The substrates described here thus combine in a unique way the sharp definition of single cell patterns obtained with “passive” polymer brushes [10] and the thermal detachment facility provided by PNIPAM. Furthermore, we describe an original process for temperature-induced cell detachment, that relies only on the repulsive forces generated due to swelling of the PNIPAM brushes.

Materials and Methods

The various steps required to produce micropatterned PNIPAM brushes are summarized on the scheme Fig. 1.

Figure 1. Elaboration steps: grafting of an ATRP (Atom Transfer Radical Polymerization) initiator on a glass surface (2) is followed by NIPAM polymerization (3), yielding a polymer brush which is selectively removed by UV irradiation (4).

APTES: 3-aminopropyl-triethoxysilane, BMPB: 2-bromo-2-methylpropionyl bromide, PNIPAM: poly(N-isopropylacrylamide).

Polymer brush synthesis

PNIPAM brushes were grafted from glass coverslips and oxidized silicon wafers by surface-initiated Atom Transfer Radical Polymerization (ATRP), according to a protocole akin to that described in details in [23].

N-isopropylacrylamide (NIPAM) was purified by recrystallization in n-hexane. 3-aminopropyl-triethoxysilane (APTES), triethylamine (TEA), copper chloride (CuCl), 1,1,7,7-Pentamethyldiethylenetriamine (PMDETA) and 2-bromo-2-methylpropionyl bromide (BMPB) were used as received. All aqueous solutions were prepared in ultra-pure water. (i) Glass and silicon substrates were cleaned in a 1 M sodium hydroxide aqueous solution for 15 minutes and rinsed with water. (ii) Samples were immersed, for 1 minute, in an aqueous solution of APTES of concentration chosen in the range 10 M. After rinsing with water and drying in a nitrogen stream samples were immersed, for 1 minute, in a solution of dichloromethane (25 mL) containing TEA (1.2 mL) and BMPB (260 L), followed by rinsing with dichloromethane, ethanol and water. This leads to surface immobilization, on the amino-terminated sites, of the ATRP initiator. (iii) A solution of NIPAM (1 g), PMDETA (150 L) and water (20 mL) was prepared in a flask and bubbled with argon gas for 30 minutes before adding CuCl (25 mg). Initiator-grafted samples were immersed in this solution for a prescribed amount of time during which polymerization occurred, and finally rinsed with pure water.

Brush characterization

Brushes were characterized by ellipsometry and Surface Forces Apparatus (SFA) mesurements.

We have used a custom-built ellipsometer in the rotating compensator configuration, at a wavelength of 632 nm and an angle of incidence of 70. The dry thickness of the brushes grown on oxidized silicon wafers was determined assuming a Si/SiO/PNIPAM multilayer, with a thickness of 2 nm and a refractive index of 1.46 for silicon oxide, and a refractive index of 1.47 for the PNIPAM layer [24].

Surface Forces experiments were performed on a home-built instrument, according to a protocol described in details in [23]. Briefly, a pair of freshly cleaved mica sheets (m in thickness) were glued onto cylindrical lenses of 1 cm radius of curvature. A PNIPAM brush was grown on one mica sample after plasma activation of its surface. The brush-bearing mica sheet was then mounted into the SFA, facing the bare mica sample, and the gap between the two surfaces was filled with ultra-pure water. The surfaces were then approached at low velocity (1 nm.s), while recording the force and the distance between the mica substrates by means of multiple beam interferometry, as described in [23]. Force/distance curves during quasi-static compression have been measured at temperatures of 25 and 37C.


Dry PNIPAM-bearing coverslips were placed in direct contact with a chromium quartz photomask (Toppan Photomasks inc., Texas USA). UV irradiation of the surfaces through the photomask was done in a custom-built device housing a set of 4 low-pressure mercury lamps (Heraeus Noblelight GmbH, NIQ 60/35 XL longlife lamp, 185 and 254 nm, quartz tube, 60 W). Samples were placed at a fixed distance of 9 cm from the UV tubes and irradiated for a prescribed duration between 5 and 10 minutes.

Protein coating

PNIPAM treated glass coverslips were first extensively washed with phosphate-buffered saline (PBS), pH 7.4. Before cell seeding, a 100 L drop (this volume was used for a 20×20 mm glass coverslip and must be adapted to the coverslip size) of protein solution composed of 20 g/ml fibronectin (Sigma)/fibrinogen-Alexa fluor 546 nm (Invitrogen) in 10 mM Hepes (pH 8.5) was deposited on a flat piece of parafilm. The patterned substrates were then directly placed on top of the protein solution drop and incubated for one hour at room temperature, protected from external light. They were washed twice with PBS.

Cells seeding, fixing and staining

Mouse Embryonic Fibroblasts (MEF) were the generous gift of Dr Olivier Destaing (Institut Albert Bonniot, la Tronche, France) [25]. MEF were maintained at 37C in a humidified atmosphere of 5% CO2 and 95% air in Dulbecco's modified Eagle medium (DMEM) containing 10% bovine fetal serum, 0.2% peni-streptomycin. Cells were deposited on micropatterned surfaces at a density of 50 000 cells/cm. Micropattern area was adapted to ensure full spreading of MEF cells on each pattern (900 m).

After 30 minutes non adherent cells localized in between the patterns were removed by gentle flushing with fresh media. After 2 hours of culture, spread cells were either observed at room temperature during thermodetachment experiments, or fixed in order to preserve their shapes. For image averaging, cells were fixed in paraformaldehyde 4% for 30 min at room temperature. After two washes in PBS, fixed cells were permeabilised 10 mins with Triton X-100 0.2% in PBS. Then cells were stained as described below. After a last wash in PBS, preparations were mounted in fluoroshield mounting medium.

Actin cytoskeleton assembly is regulated at multiple levels, including the organization of actin monomers (G-actin) into actin polymers and the super-organization of actin polymers into a filamentous network (F-actin) F-actin filaments were stained using fluorescent-labeled Phalloidin (FITC-conjugated Phalloidin, 2 M, Sigma Aldrich) to map the local orientation of actin filaments within the cells.


Microscopy experiments were performed using a Nikon Ti-E microscope equipped with an incubator maintaining the temperature at 37C. Stained cells were imaged with a Nikon 63× oil objective lens (NA 1.4). For the thermoresponsive experiments, time-lapse sequences were acquired while regulating the temperature of the room between 21 and 30C. Phase contrast images of the detaching cells were taken using an Olympus CKX41 microscope equipped with a 10× air objective(NA 0.25) and a 12-bit monochrome camera.

Results and Discussion

Brush characterization

PNIPAM brushes grown on silicon wafers were characterized by measuring their dry thickness, by ellipsometry. The dry thickness of a brush is given by , where is the number of monomer per chain, is the monomer size, and is the distance between anchoring sites. is determined by the polymerization time, and is fixed by the surface density of ATRP initiator, which depends on the concentration . Fig. 2a and b show that indeed increases with increasing or polymerization time. No difference in was noticed between measurements immediately after grafting and after several days of immersion in water, showing that polymer layers are stable and covalently grafted to the underlying substrate. We have checked that all the grafted brushes displayed the previously reported hydrophilic/hydrophobic transition when measuring the water contact angle at temperatures below and above the Lower Critical Solution Temperature (LCST) of PNIPAM. Dry thickness measurements performed at 5–6 different locations over a surface of about 1 cm yielded the same results to within nm, showing that brush growth was very homogeneous over large scales.

Figure 2. Brush growth characterization:

(a) Brush dry thickness polymerization time, for M. (b) for 1 min polymerization. Error bars are of the symbols size and correspond to a typical nm variation in thickness observed between samples elaborated under the same nominal conditions.

Swelling of the brushes immersed in water was estimated from the Force/Distance curves measured with the SFA. First, the dry thickness of brushes grown on plasma-activated mica were measured in the SFA and checked to be the same as those obtained under the same grafting conditions on silicon wafers. This allowed us to control that PNIPAM brushes grown on mica had the same density as those grafted on silicon oxide. Fig. 3 illustrates two typical compression curves obtained for a brush in water below and above the LCST: it can be seen that the range of repulsive forces is clearly narrower at 37 than at 25C. Since interactions in such a situation are attributable to steric repulsion due to confinement and compression of the macromolecules grafted on one of the surfaces [23], the observed decrease in repulsive range at 37C directly indicates chain collapse above the polymer LCST (i.e. the brush thickness is reduced above the LCST).

Figure 3. Force-distance curves measured on a water immersed PNIPAM brush ( nm), at two temperatures below and above the polymer LCST (see labels on main panel).

It can be seen that the range of steric, repulsive forces due to the presence of the brush is markedly reduced at 37C, and that the hard-wall repulsion at high temperature occurs at a distance close to the dry thickness of the brush, indicating almost full expulsion of the solvent from the PNIPAM layer above its LCST. Inset: scheme of the SFA experimental configuration.

The data shown on Fig. 3 have been obtained with a brush of nm, grafted from an initial solution of M. All the results shown in the following have been obtained with brushes of the same grafting density, which we can roughly estimate as follows: as described in Malham and Bureau [23], the grafting density is expected to be, within the Alexander-de Gennes model of polymer brushes [26], , with the monomer size and the swelling ratio. corresponds to , with the equilibrium thickness of the brush in its swollen state. In the present case, as it was done in [23], we take for the distance measured at the onset of repulsion in SFA experiments performed at room temperature (i.e. the distance at which the bare mica surface just touches the outer surface of the opposing brush). For the data presented on Fig. 3, nm at 25C, hence . Such a swelling ratio is fully consistent with those measured for high density brushes in [23]. We then deduce, taking Å, a grafting density chain.Å for the brushes used in the present study. This value of has been estimated from data reported in reference [27]. We have used the values of the grafting density, dry thickness and molecular weight reported in [27] and computed from .


Exposure of the dry PNIPAM brushes to deep UV light in air results in ablation of the polymer from the surface (PNIPAM brushes are stable under soft UV irradiation: we have checked that a 15 min exposure at 2 cm from a 75 W UV lamp ( = 365 nm) resulted in no dry thickness decrease of the grafted layers). We have characterized the ablation rate under such conditions, by monitoring as a function of UV irradiation time () on grafted silicon wafers. Results are presented on Fig. 4. It is seen that, starting from initial brush thicknesses of a few tens of nm, a complete removal of the polymer is achieved for s.

Figure 4. UV irradiation time for brushes of initial thickness 82 nm (blue), 65 nm (green), and 54 nm (red).

Patterns elaborated on PNIPAM-bearing coverslips using s can be observed by phase contrast microscopy. Fig. 5 provides an illustration of different pattern shapes thus observed. Contrast on such images arises from both the height and the refractive index difference between the PNIPAM background layer and the bare glass which has been exposed in the UV-irradiated regions. Best spatial resolution of the patterns was obtained by placing the dry PNIPAM-bearing coverslips in direct contact with the photomask. This resulted in patterns obtained on PNIPAM being m broader than the original shapes of the photomask.

Figure 5. Phase contrast image of annular and triangular patterns obtained by UV photoablation of PNIPAM.

The light grey regions have been irradiated by deep UV, where the polymer have been removed. Image size is 473355 m.

Under culture conditions (at 37C), the maximum height variation experienced by the cells corresponds to the difference between the bare and polymer-covered regions. This height difference is the collapsed thickness of the PNIPAM brushes (approximately the dry thickness, as suggested by Fig. 3), at most 70–80 nm in the present study.

Protein and Cell Adhesion

The results shown below have been obtained with high density brushes ( M) of varying between 15 and 80 nm, and between 5 and 10 min. No significant influence of these two parameters on the observed behavior has been noticed. We have used phototomasks displaying various pattern shapes having the same projected area of 900 m. Similar results regarding protein adsorption and cell adhesion have been obtained with freshly elaborated substrates and with samples stored under ambient conditions for three months before use.

Images of stained fibronectin adsorbed on the surfaces reveal a high contrast between the UV-irradiated patterns, where the protein adheres, and the brush-covered background which is free of fibronectin. This is illustrated on Fig. 6: the signal to noise ratio along the intensity profile drawn on Fig. 6a is about 10∶1. This shows that high density PNIPAM brushes are excellent protein-repellent layers at room temperature.

Figure 6. Protein adsorption on micropatterns:

(a) Fibronectin adsorption into V-shaped patterns (V arms of length 40 m and width 10 m). Inset: fluorescence intensity profile along the blue line drawn in main panel. (b) Wide field image of stained fibronectin adsorbed on V-shaped patterns, showing large scale homogeneity. Image size: 22001664 m (taken with a 4× objective on an Olympus IX70 microscope. Reduced contrast quality is due to the low NA of the objective).

Moreover, the quality of cell patterns obtained at T = 37C (Fig. 7) shows that good protein resistance is also maintained above the polymer LCST, since no cells are seen to adhere outside the defined adhesive zones. Besides, we have checked that, in contrast to the behavior exhibited on dense brushes, cells do adhere, at 37C, on low-density brushes ( M) having the same chain length. Such an effect of brush density on cell adhesion agrees with a recent report [15]. It is consistent with recent theoretical works concluding that the protein resistance of brushes is mainly controlled by the osmotic penalty associated with protein insertion within the brush, such a penalty being lower or negligible at low grafting densities [28].

Figure 7. Phase contrast images of cells adhered on square (up), triangular (middle), and rectangular-shaped patterns (down).

Scale bar is 80 m.

The photo-ablation technique yields a good pattern resolution: features of typically 10 m in size (Fig. 6a) and down to 5 m (Fig. 8A) were routinely obtained. This ensures cell shape reproducibility, as shown on Fig. 7, and makes the present substrates well suited for statistical analysis of cellular response based on image overlay, as exemplified on Fig. 8. Previous studies have shown that micropattern allow to control cell cytoskeletal architecture. In particular, cells are known to form actin bundles in response to the geometry of the pattern itself [6], [10]. We have used our PNIPAM patterned substrates to generate averaged actin orientation maps using a home-made software written in Matlab: after normalization of the individual fluorescent images to the same integrated total signal value, averaged fluorescent staining images were automatically aligned, using the protein-stained micropattern images as position references. As can be seen on Fig. 8, the heat map generated from the overlay of several actin images unambiguously confirms the ability of our micropatterns to orient actin network organisation: cells form preferentially contractile F-actin bundles, or stress fibers, along the adhesive regions of the micropatterns.

Figure 8. Cell adhesion on PNIPAM micropatterns:

A/ Fibronectin and fibrinogen-A546 coating on micropatterned PNIPAM glass surface (red). Scale bar is 15 m. B/ individual MEF cells plated on pentagon, annulus, triangle or square-shaped fibronectin micropatterns. Cells were fixed and stained with phalloidin to reveal F-actin filaments (green). Scale bar represents 15 m. C/ Average distributions of actin (fire), built from the overlay of 10 images for each shape. The average distribution highlights the reproducibility of the distributions shown in B/ and enhances the spatial distribution of F-actin bundles along micropattern border regions. Scale is 15 m.

Our PNIPAM micropatterns therefore allow for cell confinement within a given geometry as well as for the analysis of cell cytoarchitecture in response to external adhesive conditions such as changes in the pattern geometry, as previously described by other groups using different patterning techniques [6], [10], [29].

Next, we have checked for the possibility of long term cultures on the substrates. We have maintained cells in culture up to 5 days, during which cell division occurred, indicating good biocompatibility of the patterned surfaces. Furthermore, we have observed that cell adhesion is also achieved without fibronectin pre-coating. Such a non protein-specific cell patterning method, along with the ability to reach long culture time, make the present surfaces a potentially powerful tool for stem cells culture. It also shows that our technique is a versatile one, for e. g. different protein coatings can be used on our surfaces, thus allowing to address more specific biological questions.

Thermally induced cell detachment

Finally, we show that, although dense PNIPAM brushes are protein repellent irrespective of the temperature, their thermosensitive property can still be used for local cell manipulation. Fig. 9 shows a proof of concept for such a thermoresponsive actuation. It can be seen that cells which were spread and adhered on patterns change their shape to round up and finally detach from the surface within a few minutes after the temperature has been lowered below the LCST. The kinetics depends on the temperature imposed below the LCST, the lower the temperature the faster the detachment (from a few minutes at 20C to about 1 hour at 30C). We have checked that such a thermo-actuated detachment does not depend on the pattern shape, provided that the shape is chosen as follows. The pattern has to be such that cells spread over a non adhesive PNIPAM region, while bridging two adhesion zones, as sketched on Fig. 9C. Under such conditions, we have observed systematic cell detachment when the temperature was lowered below the polymer LCST, without the need for the trypsin treatment classically employed for cell harvesting. Cells thus detached from the patterned substrates were subsequently recultured in a polystyrene petri dish and were observed to spread and divide on the surface. This shows that detachment achieved by the method we report here does not affect cells' viability.

Figure 9. Thermally-induced cell detachment:

(A) and (B): Sequences of cells detaching as temperature is lowered (images 6767 m, dry brush thickness nm). The time stamp gives the time elapsed since the surfaces were taken out of the incubator. The rightmost image in each line shows the free pattern after full cell detachment. (A) cell initially adhered on a circular pattern. Imposed temperature is 21C. (B) cell initially adhered on a hexagonal pattern. Imposed temperature is 26C. (C): sketch of the polymer chains swelling inducing cell detachment.

A commonly invoked qualitative argument to explain cell adhesion switching on temperature-responsive polymer layers is the change in polymer hydrophobicity as the temperature is varied across the LCST [15]. However, as already discussed in the literature [30], the change in surface energy of the polymer layer alone cannot account for the observed change of adhesion. It has been recently proposed that cell adhesion on PNIPAM brushes is rather controlled by the hydration state of the polymer chains, which affects the insertion of adhesion proteins into the brush, through the change in osmotic pressure that occurs when the PNIPAM chains go from their collapsed, dehydrated state to their swollen state as the temperature is lowered.

However, this mechanism, involving variations in the amount of adsorbed proteins, cannot be at the origin of the observed cell detachment in the present study. Indeed, we have shown above that the grafting density used here is such that our PNIPAM brushes are protein repellent irrespective of the temperature. Still, we interpret our observations as a result of the change in chain hydration, through the following mechanism. Starting from a situation, at 37C, where cells are adhered on the patterns that comprise a non-adhesive polymer zone (fig. 9C), lowering the temperature below the LCST induces swelling of the PNIPAM chains (as characterized by the SFA measurements presented above). In the polymer-bearing region that is confined between the cell and the underlying glass substrate, chain swelling is expected to result, due to confinement, in the build-up of a net repulsive force applied over the cell membrane, which eventually induces cell detachment.

The cell detachment mechanism reported here is therefore quite different from what has been described previously [13][18], since it does not involve a temperature-induced change in the cell/substrate affinity, but rather takes advantage of polymer swelling to generate forces. The originality of the present work stems in particular from this simple cell detachment mechanism, which, to the best of our knowledge, has never been reported.


We have shown that dense PNIPAM brushes exhibit excellent protein resistance and are readily patterned at the micron scale via a single photo-ablation step. The reported fabrication method presents the following advantages: (i) robust and stable anti-adhesive brushes are covalently grafted at high density on common glass coverslips by surface-initiated ATRP, (ii) photolithography yields sharp patterns, in contrast to microcontact-printing techniques which may be limited in resolution by surface diffusion of the printed species [10], (iii) the method is easy to implement and requires only basic laboratory equipment, (iv) patterned substrates can thus be produced within 2–3 hours only, in a highly reproducible way. Moreover, we have shown that a proper choice of the pattern shapes allows us to combine the cell non-adhesiveness of dense PNIPAM brushes with their thermoresponsiveness, which permits gentle cell detachment. These features make such PNIPAM-based substrates a choice tool for single cell patterning and thermally-induced on-chip cell manipulation.


We are grateful to P. Ballet for assistance with ellipsometry.

Author Contributions

Conceived and designed the experiments: MB LB. Performed the experiments: MB LB KM. Analyzed the data: MB LB KM. Wrote the paper: MB LB KM.


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