Water-Assisted Lift-Off Mechanisms

• Water-assisted lift-off is a water-mediated detachment process employing mechanisms such as sacrificial dissolution, interfacial wedging, capillary lifting, and hydrodynamic exit.
• It leverages engineered interfaces and controlled aqueous conditions to precisely transfer delicate films and nanostructures while preserving their structural integrity.
• Applications range from crystalline oxide membranes and 2D materials to droplet removal, highlighting trade-offs in process speed, mechanical support, and material performance restoration.

Water-assisted lift-off denotes a class of water-mediated release, transfer, and removal processes in which water acts not as a passive rinse but as the enabling medium for detachment. In the literature covered here, the term encompasses at least four distinct mechanisms: dissolution of a water-soluble sacrificial layer beneath an epitaxial or van der Waals film, interfacial water intercalation that wedges a hydrophobic support film away from a hydrophilic donor substrate, quasi-static capillary lifting of a resident droplet by an immiscible working liquid, and rapid withdrawal of a solid from a water surface where fluid inertia produces hydrodynamic suction. These usages share a common outcome—release from an initial interface—but differ fundamentally in their driving physics, process windows, and performance metrics (Takeda et al., 8 Feb 2026).

1. Conceptual scope and governing mechanisms

Across materials-transfer and fluid-mechanical contexts, water-assisted lift-off is best understood as a mechanistic umbrella rather than a single protocol. In complex-oxide and 2D-material processing, lift-off is achieved by dissolving an engineered interfacial layer in water or an aqueous solution, thereby reducing the interfacial energy release rate at the donor substrate and allowing a supported thin film to separate and be transferred (Takeda et al., 8 Feb 2026). In wedging transfer, water invades the interface between a hydrophilic substrate and a hydrophobic polymer/nanostructure film, and capillary forces peel the film away so that it floats at the air–water interface (Schneider et al., 2010). In droplet-removal studies, a rising immiscible working liquid forms a capillary bridge and induces dewetting of a resident droplet from a solid; full, partial, or no dewetting follows from the wetting geometry and interfacial tensions rather than from sacrificial-layer dissolution (Sun et al., 4 Aug 2025). In the hydrodynamic water-exit problem, by contrast, the relevant “lift-off” concerns a plate or disc withdrawn rapidly from the water surface, where early-time motion is controlled by added mass and hydroelastic coupling rather than wet chemistry (Vega-Martínez et al., 2018).

The underlying thermodynamic and mechanical descriptions are correspondingly different. Wetting-driven and wedging processes are rationalized through Young’s equation,

$$\cos \theta = \frac{\gamma_{SV}-\gamma_{SL}}{\gamma_{LV}},$$

and the Young–Dupré work of adhesion,

$W_A = \gamma_{LV}(1+\cos\theta),$

which determine whether water preferentially invades a buried interface or weakens adhesion at a substrate (Schneider et al., 2010). Capillary-lifting of droplets additionally requires a ternary interfacial description at a top Neumann junction and a bottom Young-law contact line, with the dewetting criterion

$\cos \theta_t < \cos \theta_{dl}$

separating dewetting from non-dewetting configurations under quasi-static bridge formation (Sun et al., 4 Aug 2025). Dissolution-mediated membrane release depends instead on the chemistry and kinetics of the sacrificial layer, such as

$\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$

or dissolution of Na$_2$S/Na$_2$SO$_4$ in aqueous NaOH (Takeda et al., 8 Feb 2026). In rapid water exit, the leading-order hydrodynamic load is written as

$$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$

so that water resists detachment through inertia rather than facilitating it chemically (Vega-Martínez et al., 2018).

2. Dissolution-mediated lift-off of crystalline membranes and thin films

A prominent contemporary usage of water-assisted lift-off is the release of crystalline thin films by dissolving an intentionally inserted water-soluble interlayer. In ultrathin La$_{2/3}$Sr$_{1/3}$MnO$W_A = \gamma_{LV}(1+\cos\theta),$0 (LSMO) membranes, BaO was used as a sacrificial layer on SrTiO$W_A = \gamma_{LV}(1+\cos\theta),$1 (STO)(001), enabling epitaxial lift-off and transfer of approximately $W_A = \gamma_{LV}(1+\cos\theta),$2 nm-thick LSMO membranes onto SiO$W_A = \gamma_{LV}(1+\cos\theta),$3/Si (Takeda et al., 8 Feb 2026). The reported heterostructure consisted of STO with a TiO$W_A = \gamma_{LV}(1+\cos\theta),$4-terminated surface prepared by HF cleaning and $W_A = \gamma_{LV}(1+\cos\theta),$5 anneal, BaO of approximately $W_A = \gamma_{LV}(1+\cos\theta),$6 u.c. and approximately $W_A = \gamma_{LV}(1+\cos\theta),$7 nm, and LSMO of $W_A = \gamma_{LV}(1+\cos\theta),$8 u.c. and approximately $W_A = \gamma_{LV}(1+\cos\theta),$9 nm. BaO was grown by molecular beam epitaxy at $\cos \theta_t < \cos \theta_{dl}$0 without oxygen or ozone flux to avoid BaO$\cos \theta_t < \cos \theta_{dl}$1 formation; owing to a $\cos \theta_t < \cos \theta_{dl}$2 in-plane rotation relative to STO, BaO’s pseudocubic constant is $\cos \theta_t < \cos \theta_{dl}$3 Å, giving a lattice mismatch of $\cos \theta_t < \cos \theta_{dl}$4 to STO. LSMO was then deposited at $\cos \theta_t < \cos \theta_{dl}$5 under a mixed O$\cos \theta_t < \cos \theta_{dl}$6/O$\cos \theta_t < \cos \theta_{dl}$7 atmosphere at a total pressure of $\cos \theta_t < \cos \theta_{dl}$8 Pa (Takeda et al., 8 Feb 2026).

The lift-off sequence used a thermal release tape mechanically supporting the ultrathin oxide. After lamination of the tape onto the LSMO surface, immersion in pure water for $\cos \theta_t < \cos \theta_{dl}$9 hour dissolved the approximately $\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$0 nm BaO and released the membrane onto the tape; the stack was placed onto SiO$\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$1/Si, heated at $\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$2 for $\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$3 minutes to bond the membrane, and then heated to $\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$4 to remove the tape (Takeda et al., 8 Feb 2026). Dissolution was substantially faster than for Sr$\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$5Al$\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$6O$\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$7 layers of comparable thickness, which typically require $\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$8 hours. The authors attributed the speed advantage to BaO’s simpler binary composition and lower lattice robustness, invoking Madelung-energy considerations. HAADF-STEM showed that transferred LSMO retained high crystallinity, while EDX indicated slight Ba diffusion confined within approximately $\mathrm{BaO + H_2O \rightarrow Ba(OH)_2},$9 nm, approximately $_2$0 u.c., near the original LSMO/BaO interface (Takeda et al., 8 Feb 2026).

This dissolution-driven route is not restricted to perovskite membranes. In centimeter-scale transfer of 2D transition-metal dichalcogenides, an Na$_2$1S/Na$_2$2SO$_2$3 interfacial layer formed during NaCl-assisted APCVD served as the water-soluble release layer beneath $_2$4L MoS$_2$5 and $_2$6L WS$_2$7 (Sharma et al., 2021). The protocol used PMMA spin-coated at $_2$8 rpm for $_2$9 s, an edge scratch to create an initiation site, and immersion in $_2$0 M NaOH at room temperature. Within approximately $_2$1 min, the aqueous NaOH penetrated the hydrophobic TMDC interface and dissolved the underlying Na$_2$2S/Na$_2$3SO$_2$4, causing the PMMA/TMDC stack to float. After DI-water rinsing, scooping onto sapphire, SiO$_2$5/Si, mica, or polyimide, N$_2$6 blow-drying, overnight adhesion, hot-acetone PMMA removal, and Ar annealing at $_2$7 for $_2$8 h at $_2$9 sccm, centimeter-scale transferred films remained wrinkle-free and residue-free by SEM, preserved trilayer thickness of approximately $_4$0 nm by AFM, and showed disappearance of the Na $_4$1 XPS peak after transfer (Sharma et al., 2021).

An allied but structurally different embodiment is etching-free dual-lift-off for direct patterning of epitaxial oxide thin films using amorphous Sr$_4$2Al$_4$3O$_4$4 or Sr$_4$5Al$_4$6O$_4$7 as a “high-temperature photoresist” (Qin et al., 1 Sep 2025). In that sequence, photoresist on TiO$_4$8-terminated STO was overcoated with room-temperature-deposited amorphous SAO, the resist was stripped in IPA to leave patterned SAO openings, the functional oxide was grown at $_4$9–$$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$0, and a second lift-off was performed by soaking in DI water for $$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$1 min followed by $$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$2 min ultrasonic agitation at $$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$3. Functional oxide grown on SAO was removed with the dissolving sacrificial layer, whereas oxide grown directly on bare STO remained, yielding lithographically defined LSMO Hall bars and patterned BiFeO$$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$4 (Qin et al., 1 Sep 2025). Minimum feature size was approximately $$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$5, a designed linewidth of $$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$6 was preserved in patterned LSMO, and the patterned LSMO retained $$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$7 K with transport and magnetization nearly identical to unpatterned films (Qin et al., 1 Sep 2025).

3. Wedging transfer and interfacial water intercalation

A second major lineage of water-assisted lift-off is wedging transfer, where water intercalation at a buried interface performs the detachment. The method reported for nanostructures uses a hydrophobic polymer film, cellulose acetate butyrate (CAB), to entrap graphene flakes, metallic nanostructures, or other objects on a hydrophilic donor substrate such as glass, quartz, mica, or Si/SiO$$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$8 (Schneider et al., 2010). Water spontaneously wets the hydrophilic solid but avoids the hydrophobic CAB film. When the polymer-coated substrate is immersed in water, water enters at exposed edges, forms a meniscus at the hydrophilic/hydrophobic interface, and wedges the CAB/nanostructure film away from the donor. The released film floats at the air–water interface, can be aligned optically, and is finally redeposited onto a target substrate by lowering the water level and dissolving CAB in ethyl acetate (Schneider et al., 2010).

The method is explicitly capillarity-driven. At the exposed edges, the pressure in a cylindrical meniscus scales as

$$F_h(t)=m_a(t)\,\ddot{w}(t)+\dot{m}_a(t)\,\dot{w}(t), \qquad m_a(t)=\frac{4}{3}\rho c(t)^3,$$9

so a small meniscus radius generates a peeling force that advances the wetting front. The process is reversible: the film detaches when the water meniscus invades the interface and can re-adhere if the substrate is retracted from water. Successful wedging was shown at immersion geometries of approximately $_{2/3}$0 and $_{2/3}$1, indicating robustness to incidence angle, provided immersion is slow and clean edges are available for intercalation (Schneider et al., 2010).

The reported protocol used CAB at approximately $_{2/3}$2 mg/mL in ethyl acetate, applied by dipping for approximately $_{2/3}$3 s and dried at room temperature. After solvent evaporation, the edges had to be cleared with an ethyl acetate–wet cotton swab or scratched with a razor blade; otherwise water could not nucleate the meniscus at the interface (Schneider et al., 2010). For graphene, additional handling included plasma oxidation of the surrounding substrate and, when needed, a protective CAB droplet of approximately $_{2/3}$4 over the flake during brief air plasma. During placement, a standard sewing needle mounted on three orthogonal micrometric screws translated the floating film with sub-micrometer precision under a low-magnification optical microscope (Schneider et al., 2010).

Quantitatively, the method achieved $_{2/3}$5 successful graphene transfers onto SiN and SiO$_{2/3}$6 receiver substrates, with flake shape preserved after CAB dissolution (Schneider et al., 2010). For gold microelectrodes, CAB alone adhered poorly to Au, yielding transfer yields $_{2/3}$7; adding $_{2/3}$8 v% 1-dodecanethiol to the CAB solution formed a hydrophobic self-assembled monolayer on Au and increased transfer success to $_{2/3}$9 for gold microelectrodes (Schneider et al., 2010). Transfer of gold letters with $_{1/3}$0 nm line width and $_{1/3}$1 nm thickness onto $_{1/3}$2 polystyrene microspheres was also demonstrated, though some features, approximately $_{1/3}$3, were not transferred fully, a limitation attributed to CAB elasticity (Schneider et al., 2010).

Wedging transfer differs from sacrificial-layer dissolution in that water need not chemically dissolve the buried layer. Instead, selective wetting and capillary invasion generate a thermodynamic preference for replacing polymer/substrate contact with water/substrate contact. This suggests that the decisive material requirement is not water solubility per se but a sufficiently strong contrast between a hydrophilic donor and a hydrophobic, water-avoiding carrier film.

4. Capillary lifting of droplets by an immiscible working liquid

In soft-matter and surface-science usage, water-assisted lift-off can refer to removal of a resident droplet from a substrate by capillary lifting. Here the object being lifted is liquid rather than solid, and the driving force is a quasi-static capillary bridge formed by a rising immiscible working liquid (Sun et al., 4 Aug 2025). A droplet initially resting on a substrate in air is contacted from below by a slowly rising working liquid, typically at approximately $_{1/3}$4 m/s. Once contact occurs, the system becomes ternary: droplet, working liquid, and air. As the working liquid continues to rise, the droplet touches the liquid–air interface above it, producing a liquid lens at that interface and a capillary bridge connecting the interface to the solid (Sun et al., 4 Aug 2025).

The theoretical description is energy-based: $_{1/3}$5 with bottom wetting constrained by Young’s law, the top tri-junction by Neumann balance, and capillary pressure given by

$_{1/3}$6

Two angles govern the stability of the bridge: the bottom receding contact angle in the presence of the working liquid, $_{1/3}$7, and the top apparent liquid-lens angle, $_{1/3}$8. Dewetting is favored when

$_{1/3}$9

because the bottom contact radius then shrinks faster than the top (Sun et al., 4 Aug 2025). The process is quasi-static, with $W_A = \gamma_{LV}(1+\cos\theta),$00; using $W_A = \gamma_{LV}(1+\cos\theta),$01 Pa·s, $W_A = \gamma_{LV}(1+\cos\theta),$02 m/s, and $W_A = \gamma_{LV}(1+\cos\theta),$03 N/m gives $W_A = \gamma_{LV}(1+\cos\theta),$04 (Sun et al., 4 Aug 2025).

Systematic simulations and experiments defined six regimes: film at the air interface, anti-bubble, always attached, full dewetting, partial dewetting, and no dewetting despite bridge (Sun et al., 4 Aug 2025). Two trends were identified. Increasing $W_A = \gamma_{LV}(1+\cos\theta),$05 strongly favors full or partial dewetting, and lower $W_A = \gamma_{LV}(1+\cos\theta),$06 together with higher $W_A = \gamma_{LV}(1+\cos\theta),$07 decreases $W_A = \gamma_{LV}(1+\cos\theta),$08 and favors lens formation and dewetting (Sun et al., 4 Aug 2025). The latter is noteworthy because it reverses the intuition of conventional surfactant-based cleaning: high interfacial tension in the working liquid enhances lift-off. Experimentally, water with $W_A = \gamma_{LV}(1+\cos\theta),$09 mN/m removed $W_A = \gamma_{LV}(1+\cos\theta),$10 of tetradecane droplets from PMMA, while tetradecane with $W_A = \gamma_{LV}(1+\cos\theta),$11 mN/m could not lift water droplets (Sun et al., 4 Aug 2025). Water lifted tetradecane on PMMA and glass with approximately $W_A = \gamma_{LV}(1+\cos\theta),$12–$W_A = \gamma_{LV}(1+\cos\theta),$13 removal, decane with $W_A = \gamma_{LV}(1+\cos\theta),$14–$W_A = \gamma_{LV}(1+\cos\theta),$15 removal across PC, PMMA, and stainless steel but only approximately $W_A = \gamma_{LV}(1+\cos\theta),$16 on PTFE, squalane on PMMA with approximately $W_A = \gamma_{LV}(1+\cos\theta),$17 removal, and olive oil with approximately $W_A = \gamma_{LV}(1+\cos\theta),$18 removal; used engine oil showed approximately $W_A = \gamma_{LV}(1+\cos\theta),$19, with solid residues hindering lift-off (Sun et al., 4 Aug 2025).

The same study emphasized that interfacial tensions must be measured under ternary conditions when amphiphiles are present. In glycol-ether water formulations, binary measurements gave $W_A = \gamma_{LV}(1+\cos\theta),$20 and $W_A = \gamma_{LV}(1+\cos\theta),$21, whereas Neumann-triangle analysis under ternary exposure shifted these to approximately $W_A = \gamma_{LV}(1+\cos\theta),$22 and $W_A = \gamma_{LV}(1+\cos\theta),$23, restoring agreement with observed lift-off behavior (Sun et al., 4 Aug 2025). A plausible implication is that “water-assisted” in this context names a capillary-thermodynamic architecture rather than a specific water chemistry: dewetting efficiency depends on bridge geometry, $W_A = \gamma_{LV}(1+\cos\theta),$24, and the working liquid’s high $W_A = \gamma_{LV}(1+\cos\theta),$25, not simply on whether water wets the substrate in air.

5. Process windows, performance restoration, and materials constraints

Although water-assisted lift-off is often framed as gentle, the reported processes are conditional on narrow chemical and mechanical windows. In BaO-enabled release of LSMO membranes, the speed of BaO dissolution came with a specific materials penalty: because BaO was grown without O$W_A = \gamma_{LV}(1+\cos\theta),$26/O$W_A = \gamma_{LV}(1+\cos\theta),$27, it likely extracted oxygen from the adjacent LSMO during growth, forming La$W_A = \gamma_{LV}(1+\cos\theta),$28Sr$W_A = \gamma_{LV}(1+\cos\theta),$29MnO$W_A = \gamma_{LV}(1+\cos\theta),$30 with reduced Mn valence (Takeda et al., 8 Feb 2026). X-ray absorption spectroscopy at the Mn $W_A = \gamma_{LV}(1+\cos\theta),$31 edges showed Mn$W_A = \gamma_{LV}(1+\cos\theta),$32 states in the as-transferred membrane, and post-transfer annealing at $W_A = \gamma_{LV}(1+\cos\theta),$33, $W_A = \gamma_{LV}(1+\cos\theta),$34 atm pure O$W_A = \gamma_{LV}(1+\cos\theta),$35, for $W_A = \gamma_{LV}(1+\cos\theta),$36 hours eliminated Mn$W_A = \gamma_{LV}(1+\cos\theta),$37 and increased the Curie temperature from $W_A = \gamma_{LV}(1+\cos\theta),$38 K to $W_A = \gamma_{LV}(1+\cos\theta),$39 K, while magnetic hysteresis at $W_A = \gamma_{LV}(1+\cos\theta),$40 K was essentially unchanged (Takeda et al., 8 Feb 2026). The method therefore achieved rapid release, but intrinsic magnetic performance required oxygen restoration after transfer.

Water-soluble-layer transfer of TMDCs exhibited a different constraint set. Lift-off in $W_A = \gamma_{LV}(1+\cos\theta),$41 M NaOH at room temperature started within approximately $W_A = \gamma_{LV}(1+\cos\theta),$42 min, but $W_A = \gamma_{LV}(1+\cos\theta),$43 M NaOH caused film damage, while hot DI water above $W_A = \gamma_{LV}(1+\cos\theta),$44 generated bubbles, cracks, wrinkles, and slow delamination exceeding $W_A = \gamma_{LV}(1+\cos\theta),$45 min (Sharma et al., 2021). The protocol therefore relied on moderate base, room temperature, immediate DI rinsing, and short exposure. XPS evidence of disappearance of the Na $W_A = \gamma_{LV}(1+\cos\theta),$46 peak after transfer indicated removal of the interfacial salts, and PL of transferred WS$W_A = \gamma_{LV}(1+\cos\theta),$47 showed recovery of the neutral exciton $W_A = \gamma_{LV}(1+\cos\theta),$48 at $W_A = \gamma_{LV}(1+\cos\theta),$49 eV together with a Raman $W_A = \gamma_{LV}(1+\cos\theta),$50 blueshift of approximately $W_A = \gamma_{LV}(1+\cos\theta),$51 cm$W_A = \gamma_{LV}(1+\cos\theta),$52, consistent with tensile strain release without added doping (Sharma et al., 2021).

In dual-lift-off patterning of oxides, solvent selectivity was central. Amorphous SAO is stable in IPA, allowing the first lift-off during photoresist stripping, but dissolves in water and in acetone; acetone was therefore explicitly avoided during the first lift-off because it would compromise the SAO mask (Qin et al., 1 Sep 2025). The authors recommended keeping the photoresist thicker than the SAO to prevent bridging across resist and substrate, which improves edge quality, and standardized on a $W_A = \gamma_{LV}(1+\cos\theta),$53-min DI-water soak followed by $W_A = \gamma_{LV}(1+\cos\theta),$54-min ultrasonication at $W_A = \gamma_{LV}(1+\cos\theta),$55 for $W_A = \gamma_{LV}(1+\cos\theta),$56–$W_A = \gamma_{LV}(1+\cos\theta),$57 nm SAO layers (Qin et al., 1 Sep 2025).

Wedging transfer has its own failure modes. Water intercalation requires exposed, clean edges; if edges remain covered by polymer, wedging does not initiate (Schneider et al., 2010). Bare Au adheres poorly to CAB, causing transfer yields below $W_A = \gamma_{LV}(1+\cos\theta),$58 unless $W_A = \gamma_{LV}(1+\cos\theta),$59 v% 1-dodecanethiol is added to form a hydrophobic SAM. Highly curved targets can induce partial feature loss because of limited polymer-film elasticity (Schneider et al., 2010). In capillary lifting of droplets, roughness, chemical heterogeneity, and contact-line pinning cause partial dewetting and residue, while viscous or particulate-laden soils such as used engine oil resist full lift-off (Sun et al., 4 Aug 2025). The notion that “water-assisted” automatically implies residue-free or chemically benign processing is therefore inaccurate; successful lift-off depends on correctly matched dissolution chemistry, interfacial wetting, support mechanics, and post-transfer restoration.

6. Hydrodynamic lift-off and hydroelastic water exit

A physically distinct usage of lift-off concerns rapid withdrawal of a solid from a water surface, where water resists rather than assists separation through inertia. Experiments on a circular acrylic disc of radius $W_A = \gamma_{LV}(1+\cos\theta),$60 cm showed that at very early times the hydrodynamic suction force can be estimated by a simple extension to linear exit theory with added mass (Vega-Martínez et al., 2018). For the main series, the plate thickness was $W_A = \gamma_{LV}(1+\cos\theta),$61 cm, plate mass $W_A = \gamma_{LV}(1+\cos\theta),$62 kg, connector and instrumentation mass $W_A = \gamma_{LV}(1+\cos\theta),$63 kg, and total instrumented mass $W_A = \gamma_{LV}(1+\cos\theta),$64 kg. The added mass of a wetted disc at early time was

$W_A = \gamma_{LV}(1+\cos\theta),$65

so $W_A = \gamma_{LV}(1+\cos\theta),$66, indicating hydrodynamic dominance (Vega-Martínez et al., 2018).

The measured force and acceleration satisfy

$W_A = \gamma_{LV}(1+\cos\theta),$67

and while the wetted radius remains approximately $W_A = \gamma_{LV}(1+\cos\theta),$68, the early-stage relation reduces to

$W_A = \gamma_{LV}(1+\cos\theta),$69

Experiments showed peak center acceleration $W_A = \gamma_{LV}(1+\cos\theta),$70 within approximately $W_A = \gamma_{LV}(1+\cos\theta),$71–$W_A = \gamma_{LV}(1+\cos\theta),$72 ms, with $W_A = \gamma_{LV}(1+\cos\theta),$73 (Vega-Martínez et al., 2018). High-speed imaging revealed that the wetted radius remained nearly constant for the first approximately $W_A = \gamma_{LV}(1+\cos\theta),$74 ms and that the contact line did not recede until the edge had lifted by order millimeters. Once detachment began, the experiments recovered the self-similar law

$W_A = \gamma_{LV}(1+\cos\theta),$75

The central result of the study is that elasticity modifies this apparent lift-off substantially. A linear hydroelastic model coupled axisymmetric potential flow to Kirchhoff–Love plate dynamics,

$W_A = \gamma_{LV}(1+\cos\theta),$76

and showed that the measured center acceleration can decay even while the applied force continues to increase, because elastic mode excitation redistributes acceleration across the plate (Vega-Martínez et al., 2018). For the $W_A = \gamma_{LV}(1+\cos\theta),$77 cm plate, the first wet-mode frequency was $W_A = \gamma_{LV}(1+\cos\theta),$78, corresponding to a period of approximately $W_A = \gamma_{LV}(1+\cos\theta),$79 ms. Computations indicated that the edge acceleration was negative for $W_A = \gamma_{LV}(1+\cos\theta),$80 ms and the edge vertical velocity changed sign only at $W_A = \gamma_{LV}(1+\cos\theta),$81 ms, explaining the delay in contact-line motion (Vega-Martínez et al., 2018).

This hydrodynamic problem is conceptually opposite to dissolution- or wetting-assisted membrane transfer: water here provides a virtual mass that must be accelerated. Yet it belongs in the broader encyclopedic scope of “water-assisted lift-off” because the detachment event is again controlled by how water mediates interface separation. A plausible implication is that the phrase acquires domain-specific meaning: in microfabrication and soft matter, water usually enables release; in fast water exit, it determines the suction load that delays release.

7. Comparative interpretation and recurring design principles

Despite their diversity, the reported forms of water-assisted lift-off exhibit recurring design principles. First, the buried interface is engineered so that water either lowers adhesion, invades a favorable wetting path, or dissolves a compositionally vulnerable interlayer. BaO beneath LSMO, Na$W_A = \gamma_{LV}(1+\cos\theta),$82S/Na$W_A = \gamma_{LV}(1+\cos\theta),$83SO$W_A = \gamma_{LV}(1+\cos\theta),$84 beneath TMDCs, and amorphous SAO beneath epitaxial oxides all exemplify deliberate interfacial engineering for selective aqueous removal (Takeda et al., 8 Feb 2026). CAB wedging instead uses hydrophilic/hydrophobic contrast, while droplet capillary lifting uses a ternary topological transition from sessile droplet to liquid lens and capillary bridge (Schneider et al., 2010).

Second, time-in-water is treated as a control variable rather than an incidental detail. BaO was favored because approximately $W_A = \gamma_{LV}(1+\cos\theta),$85 nm dissolved in approximately $W_A = \gamma_{LV}(1+\cos\theta),$86 hour rather than the $W_A = \gamma_{LV}(1+\cos\theta),$87 hours typical for comparable Sr$W_A = \gamma_{LV}(1+\cos\theta),$88Al$W_A = \gamma_{LV}(1+\cos\theta),$89O$W_A = \gamma_{LV}(1+\cos\theta),$90 layers; the authors explicitly connected faster dissolution to higher throughput and lower risk of time-dependent aqueous damage (Takeda et al., 8 Feb 2026). TMDC transfer limited immersion to approximately $W_A = \gamma_{LV}(1+\cos\theta),$91 min in $W_A = \gamma_{LV}(1+\cos\theta),$92 M NaOH to avoid pH-driven damage (Sharma et al., 2021). Capillary lifting of droplets unfolded over seconds under quasi-static bridge evolution, whereas wedging transfer took a few seconds when performed slowly enough (Sun et al., 4 Aug 2025). Hydrodynamic water exit, by contrast, is governed by milliseconds, added mass, and wet-mode periods rather than chemical dwell time (Vega-Martínez et al., 2018).

Third, most implementations require a mechanical or geometric auxiliary to stabilize the detached object. Thermal release tape supported ultrathin oxide membranes during BaO dissolution and transfer to SiO$W_A = \gamma_{LV}(1+\cos\theta),$93/Si (Takeda et al., 8 Feb 2026). PMMA supported TMDC monolayers and trilayers through alkaline lift-off and lamination (Sharma et al., 2021). CAB served simultaneously as scaffold and hydrophobic layer in wedging transfer (Schneider et al., 2010). In capillary lifting, the bridge geometry itself is the temporary support that converts a sessile droplet into a liquid lens (Sun et al., 4 Aug 2025).

Finally, lift-off success does not by itself guarantee functional recovery. LSMO required oxygen annealing to restore the optimal Mn$W_A = \gamma_{LV}(1+\cos\theta),$94/Mn$W_A = \gamma_{LV}(1+\cos\theta),$95 balance and increase $W_A = \gamma_{LV}(1+\cos\theta),$96 from $W_A = \gamma_{LV}(1+\cos\theta),$97 K to $W_A = \gamma_{LV}(1+\cos\theta),$98 K (Takeda et al., 8 Feb 2026). TMDC transfer used hot acetone and Ar annealing to minimize PMMA residue (Sharma et al., 2021). Dual-lift-off was valued because patterned LSMO and BiFeO$W_A = \gamma_{LV}(1+\cos\theta),$99 retained ferromagnetic and ferroelectric functionality, respectively, with LSMO showing $\cos \theta_t < \cos \theta_{dl}$00 K and BFO showing $\cos \theta_t < \cos \theta_{dl}$01 polarization reversal, butterfly amplitude loops of approximately $\cos \theta_t < \cos \theta_{dl}$02 pm, and coercive voltage of approximately $\cos \theta_t < \cos \theta_{dl}$03–$\cos \theta_t < \cos \theta_{dl}$04 V (Qin et al., 1 Sep 2025). Water-assisted lift-off is therefore not merely a detachment step; it is an interfacial engineering strategy whose practical value is determined by how completely structural, chemical, and functional integrity are preserved after release.