Modular housing with enhanced recyclability of prefabricated components featuring passive functions

Abstract

The present invention relates to a modular housing with increased recyclability of prefabricated components equipped with passive functions, and more specifically, to a modular system comprising a sacrificial dimension layer and a crusher-sam layer that effectively absorb dimensional tolerances occurring during the assembly process and can be reused after disassembly, and a method for restandardizing the same. In particular, the present invention relates to an intelligent bonding system that adaptively responds to environmental changes by integrating a biomimetic hydrogel and phase change material microcapsules.

Description

Technology Field

[0001] The present invention relates to a modular housing with increased recyclability of prefabricated components equipped with passive functions, and more specifically, to a modular system comprising a sacrificial dimension layer and a crusher-sam layer that effectively absorb dimensional tolerances occurring during the assembly process and can be reused after disassembly, and a method for restandardizing the same. In particular, the present invention relates to an intelligent bonding system that adaptively responds to environmental changes by integrating a biomimetic hydrogel and phase change material microcapsules. Background Technology

[0003] Modular housing is a construction method in which prefabricated modules are assembled on-site, and it is attracting global attention due to advantages such as reduced construction time, improved quality, and environmental friendliness. Particularly in residential buildings, rapid construction, dismantling, and the possibility of reuse serve as important economic factors.

[0004] Traditional modular housing systems have utilized mechanical fasteners, welding, or adhesives to join modules. While the use of mechanical fasteners offers the advantage of easy assembly and disassembly, dimensional tolerances during the manufacturing process can lead to gaps in the joints or require excessive compressive force. Generally, module manufacturing tolerances range from ±1mm to ±3mm, and the accumulation of these tolerances can have a serious impact on the dimensional accuracy and structural performance of the entire structure.

[0005] Existing technologies used to address tolerance issues have included adjustable connectors, elastic gaskets, or on-site compensation. While adjustable connectors can accommodate a certain range of tolerances, they are structurally complex, costly, and have limited adjustment capabilities. Elastic gaskets are a relatively simple method, but they have the disadvantage of degrading performance over long-term use due to compression set or creep, and are difficult to reuse after disassembly.

[0006] Recently, research on adaptive coupling systems using smart materials has been actively conducted. Active control systems using shape memory alloys, variable stiffness dampers using magnetorheological fluids, or active vibration control systems using piezoelectric elements have been proposed; however, these systems require an external energy supply and have complex control systems, which limits their application in general-purpose construction fields such as modular housing in terms of economic feasibility and reliability.

[0007] The concept of a sacrificial layer has primarily been used in the fields of semiconductor manufacturing and surface treatment. In semiconductor processes, it refers to a protective film temporarily formed to safeguard a substrate during etching or ion implantation, characterized by its removal after the process is completed. In the construction industry, formwork used during concrete pouring or backing materials used during welding can be viewed as similar concepts.

[0008] However, there are very limited instances of applying the existing concept of sacrificial layers to dimensional tolerance issues in modular construction. Most existing technologies approached the issue from the perspective of single-use consumables, making reuse or recycling impossible after disassembly, and provided only simple thickness adjustment functions, lacking the ability to respond to complex three-dimensional tolerances or dynamic load conditions.

[0009] A crusher zone, or crushable structure, is a technology primarily developed in the automotive industry to absorb energy during collisions. Honeycomb structures, foam materials, or specially designed metal structures perform passenger protection by absorbing impact energy while undergoing controlled deformation. In the construction sector, similar principles are applied in seismic isolation devices and vibration damping systems.

[0010] Lightweight composite materials utilizing microballoons are widely used in the aerospace industry to reduce weight and improve thermal insulation performance. Glass microballoons are utilized as fillers in structural composites due to their excellent balance of compressive strength and lightness, while polymer microballoons offer lower density and superior processability. Honeycomb structures are utilized in various fields, such as panel cores, packaging materials, and shock absorbers, due to their high stiffness-to-weight ratio and excellent energy absorption characteristics.

[0011] Self-healing material technology is a field that has been rapidly developing over the past decade or so, referring to materials capable of self-repairing from external damage. The microcapsule method involves the capsule rupturing upon damage to release internal repair materials that fill the cracks, while the vascular system supplies repair materials through microvessels formed within the material. The method utilizing ionic networks is based on the principle of restoring molecular bonds at damaged sites by employing reversible coordination bonds between metal ions and ligands.

[0012] Biomimetic adhesive technology is a technology that mimics the adhesive mechanisms of nature, such as those of mussels, geckos, and spiders, and active research is currently underway. L-DOPA (3,4-dihydroxyphenylalanine) residues contained in the byssus proteins of mussels are known as a key component that provides strong adhesion even in aquatic environments. Chitosan and alginate are natural polysaccharides that exhibit excellent biocompatibility and hydrogel-forming ability, so they are utilized as matrix materials for biomimetic adhesive systems.

[0013] Phase Change Materials (PCMs) are materials that possess the characteristic of absorbing or releasing a large amount of latent heat during the solid-liquid phase change process, and are attracting attention in the fields of thermal energy storage and temperature control in buildings. Paraffinic PCMs exhibit stable phase change characteristics over a wide temperature range, and in particular, n-octadecane has a melting point of around 28 degrees, making it suitable for indoor temperature control in buildings. Microencapsulation technology for PCMs is essential for preventing leakage and ensuring shape stability, and melamine-urea-formaldehyde resin is widely used as a PCM capsule wall material due to its excellent heat resistance and mechanical strength.

[0014] Boron nitride nanosheets have a two-dimensional layered structure similar to graphene and are attracting attention as thermal management materials due to their excellent thermal conductivity and electrical insulation properties. With a planar thermal conductivity reaching 2000 W / m·K, they can significantly improve the heat exchange rate of PCMs when used as a thermal conductivity enhancer.

[0015] Existing modular housing technologies have largely focused solely on structural connections, lacking comprehensive consideration of dimensional tolerances, environmental adaptability, and reusability. Furthermore, the application of the latest smart material technologies in the construction sector has been limited to approaches focused on individual functions, resulting in very restricted research from an integrated systems perspective. Therefore, to ensure the commercialization and sustainability of modular housing, there is an urgent need to develop innovative connection systems that comprehensively consider dimensional tolerance absorption, environmental adaptability, self-restoration, and reusability. The problem to be solved

[0017] The problem that the present invention aims to solve is to provide an innovative joining system that effectively absorbs dimensional tolerances occurring during the assembly process of modular housing modules while enabling reuse after disassembly.

[0018] Existing modular housing systems face problems where assembly and structural performance are degraded due to dimensional tolerances of ±1mm to ±3mm that inevitably occur during the module manufacturing process, which result in gaps at joints or require excessive compressive forces. If these tolerances accumulate across multiple modules, they can have a serious impact on the dimensional accuracy of the entire structure.

[0019] Furthermore, existing elastic gaskets and sealing materials cannot be reused after dismantling due to their nature as single-use consumables, which hinders the sustainability and economic viability of modular housing. In particular, ensuring the reusability of joint materials is essential to fully utilize the dismantling and reassembly capabilities, which are a core advantage of modular housing.

[0020] Performance degradation due to changes in environmental conditions is also a significant challenge to be addressed. Environmental factors such as changes in temperature and humidity, UV exposure, and vibration can alter the physical properties of joint materials, leading to performance degradation during long-term use. Existing materials merely respond passively to these environmental changes and lack the ability to adaptively react.

[0021] The lack of self-healing capabilities for micro-damage is another challenge that needs to be addressed. Micro-damage such as scratches, cracks, and wear occurring during repetitive assembly and disassembly processes gradually degrades the performance of joints, requiring separate maintenance work to restore them.

[0022] Therefore, the present invention aims to simultaneously improve the practicality and sustainability of modular housing technology by developing an intelligent modular combination system that integrally provides dimensional tolerance absorption, reusability, environmental adaptability, and self-restoration capabilities. means of solving the problem

[0024] According to one aspect of the present invention, a modular housing module system may be provided comprising: a module body; a bonding surface formed on the module body; a sacrificial dimension layer applied to the bonding surface to absorb tolerances between modules; and a crusher-sham layer disposed below the sacrificial dimension layer to provide an additional tolerance absorption function through controlled deformation by a compressive load.

[0025] For example, a modular housing modular system may be provided in which the module body has a coupling surface including a rail, a cam lock, and a shear key.

[0026] For example, a modular housing module system may be provided in which the sacrificial dimension layer is applied to the bonding surface of the module body.

[0027] For example, a modular housing system may be provided in which the sacrificial dimension layer comprises a urethane-acrylic hybrid resin or Diels-Alder resin.

[0028] For example, a modular housing system may be provided in which the crusher-sham layer comprises a microballoon or honeycomb structure.

[0029] For example, a method for restandardizing a module for modular housing may be provided, comprising: a measurement step for measuring the condition of the joint surface of a disassembled module; a supplementation step for supplementing the deficient portion of the sacrificial dimension layer based on the measurement results; a curing step for curing the supplemented sacrificial dimension layer; and a verification step for verifying the quality of the restandardized module.

[0030] For example, a modular housing system may be provided that further comprises a self-healing primer comprising a microcapsule or an ionic network.

[0031] For example, a modular housing system may be provided that additionally includes a refill-release gasket having an injection port.

[0032] For example, a modular housing system may be provided in which the refill-release gasket comprises EPDM or silicone.

[0033] For example, a modular housing module system may be provided in which the thickness of the sacrificial dimension layer is 0.05 to 0.30 mm.

[0034] For example, a modular housing modular system may be provided in which the crushing rate of the crusher-sham layer is 10 to 35%.

[0035] For example, a modular housing module system may be provided in which the film thickness of the self-healing primer is 5 to 20 μm.

[0036] For example, a modular housing system may be provided in which the sacrificial layer further comprises a biomimetic hydrogel comprising chitosan, sodium alginate, and L-dihydroxyphenylalanine residues.

[0037] For example, a modular housing system may be provided in which the biomimetic hydrogel comprises 8 to 15 weight% chitosan, 5 to 12 weight% sodium alginate, and 2 to 6 weight% mussel byssus protein analogue.

[0038] For example, a modular housing module system may be provided in which the crusher-sam layer further comprises phase change material microcapsules.

[0039] For example, a modular housing module system may be provided in which the phase change material is n-octadecane and the wall of the microcapsule is melamine-urea-formaldehyde resin.

[0040] For example, a modular housing module system may be provided, which further comprises 15 to 25 weight% of the phase change material microcapsules and 2 to 5 weight% of boron nitride nanosheets.

[0041] For example, a modular housing module system may be provided that includes both the biomimetic hydrogel and the phase change material microcapsules. Effects of the invention

[0043] According to the present invention, an innovative joining system can be provided that effectively absorbs dimensional tolerances occurring during the assembly process of modules for modular housing while having excellent reusability.

[0044] Through a dual structure of a sacrificial dimension layer and a crusher-sham layer, complete contact between modules and uniform load distribution can be achieved by gradually absorbing tolerances of various sizes. This can significantly improve the structural performance and airtightness of modular housing.

[0045] A sacrificial dimension layer using urethane-acrylic hybrid resin or Diels-Alder resin provides appropriate wear resistance and curability, allowing it to absorb tolerances during assembly and maintain a stable bond after assembly is complete. In particular, the reversible crosslinking properties of Diels-Alder resin enable softening by heating during disassembly and re-curing during reassembly, thereby providing excellent reusability.

[0046] A crusher-sham layer containing microballoons or honeycomb structures can be reused by absorbing large tolerances through controlled crushing while exhibiting constant elastic recovery. Optimal tolerance absorption performance and structural stability can be simultaneously secured within a crushing rate range of 10% to 35%.

[0047] The re-standardization method of the present invention can restore a disassembled module to its original specifications through systematic steps of measurement, replenishment, curing, and verification. It can achieve an 83% reduction in time and a 75% reduction in material costs compared to the existing full-surface recoating method, while enabling the restoration of 96% of the performance compared to a new product.

[0048] The introduction of biomimetic hydrogels enables the realization of intelligent systems that respond adaptively to changes in environmental conditions. The chitosan-alginate-L-DOPA composition can provide an automatic sealing function in response to changes in humidity and excellent adhesion even in underwater environments.

[0049] Through the integration of phase change material microcapsules and boron nitride nanosheets, a buffering effect against temperature changes and improved thermal conductivity can be achieved simultaneously. This can provide an additional effect of improving the energy efficiency of buildings by 5% to 15%.

[0050] The application of a self-healing primer provides an automatic repair function for micro-damage, enabling stable performance to be maintained even during long-term use. The microcapsules and ionic network system can each exhibit effective repair functions for damage of different sizes and properties.

[0051] The integrated system of the present invention can achieve a performance improvement of 25% to 40% compared to a single system through the synergistic effect of each component, and can maintain excellent stability even under extreme environmental conditions.

[0052] Consequently, the present invention can significantly contribute to the commercialization and widespread adoption of modular construction technology by simultaneously improving the assemblability, reusability, and sustainability of modular housing. Brief explanation of the drawing

[0054] FIG. 1 is a cross-sectional view showing the overall configuration of a modular housing module system according to the present invention. FIG. 2 is a flowchart showing the step-by-step process of the restandardization method according to the present invention. Specific details for implementing the invention

[0055] Hereinafter, preferred embodiments of the present invention will be described with reference to the attached drawings. However, embodiments of the present invention may be modified in various other forms, and the scope of the present invention is not limited to the embodiments described below.

[0056] In one aspect of the present invention, a modular housing module system may comprise a module body, a sacrificial dimension layer, a crusher-sam layer, a self-healing primer, and a refill-release gasket. This configuration enables the module to be reused repeatedly despite micro-wear, chipping, and deformation occurring during assembly, use, and disassembly, and allows for the simultaneous achievement of dry assembly and rigid bonding.

[0057] The module body serves as the basic structural element of a modular house and can be configured in various forms as illustrated in FIG. 1. In one embodiment, the wall module can be manufactured with a width of 2.4 m to 3.6 m, a height of 2.4 m to 3.0 m, and a thickness of 100 mm to 200 mm, and can be composed of a lightweight steel frame, insulation, and interior and exterior materials. The floor module can be formed with dimensions of 3.0 m x 6.0 m to 4.0 m x 8.0 m and consists of composite beams and floor slabs, with a strength of 3 kN / m 2 Up to 5 kN / m 2 It can support the load. The ceiling module can be manufactured to a size similar to the floor module but can be relatively lighter, and the equipment module can be configured in a form that integrates piping, electrical, and mechanical equipment.

[0058] The coupling surface of the module body may require precise dimensional tolerances and can be machined to have a flatness of within ±0.5 mm and a right angle of within ±2 mm. As shown in FIG. 1, a rail, a cam lock, and a shear key may be formed on the coupling surface, and the rail may be manufactured with a 'U'-shaped or 'T'-shaped cross section with a width of 20 mm to 80 mm and a height of 15 mm to 50 mm. The cam lock may provide a clamping force of 1,000 N to 10,000 N, and the shear key may be formed with a diameter of 10 mm to 30 mm and a length of 50 mm to 200 mm to exhibit a shear strength of 200 MPa to 500 MPa.

[0059] The sacrificial dimension layer is a key component formed on the bonding surface of the module body and can automatically correct tolerances that occur during the assembly process. The sacrificial dimension layer performs a surface-fitting function as a portion of it wears away due to friction and pressure during assembly, while simultaneously absorbing tolerances. After assembly is complete, it hardens upon external stimulation to strengthen bonding, and upon disassembly, it can be mechanically separated and restored to its original specifications through a re-standardization process. The initial hardness of the sacrificial dimension layer is maintained at a Shore A level of 20 to 50, and can increase to Shore D 50 to 80 after hardening, thereby ensuring both assembly and bonding capabilities simultaneously.

[0060] The crusher-shim layer is placed between the joints between modules and can uniformly absorb gaps ranging from a few μm to tens of μm through local crushing during assembly. The crusher-shim layer can be permanently dimensioned after assembly through low-temperature sintering or compression fixing, and can be immediately replaced with a film-exchangeable cartridge for reuse. When including micro-spherical microballoons, it can be configured with an average diameter of 10 μm to 100 μm and a wall thickness of 0.5 μm to 3 μm, and the crushing strength can be controlled to 1 MPa to 50 MPa. In the case of a honeycomb structure, it can be formed with a cell size of 1 mm to 10 mm and a wall thickness of 0.1 mm to 1 mm to provide directional compression characteristics.

[0061] A self-healing primer is formed on the bonding surface and can automatically repair microcracks or chipping that occur during use. In the case of a microcapsule system, the resin and curing agent are stored separately in capsules and can self-cure upon rupture when damaged; the capsule size can be controlled within the range of 1 μm to 200 μm, and the wall thickness within the range of 0.1 μm to 5 μm. In the case of an ionic network, self-healing can be activated by changes in temperature or pH by utilizing the reversible binding between metal ions and ligands. A repair efficiency of over 90% can be achieved for microcracks with a width of 0.1 mm or less.

[0062] The refill-release gasket can perform a dual function of providing airtightness between modules while facilitating separation during disassembly. The gasket can be formed with a Shore A hardness of 35 to 55 and may be equipped with microchannels and check valve-type ports on the sides. The injection port can be formed with a diameter in the range of 1 mm to 5 mm, and when sealant is injected, 0.5 mL to 3 mL is injected per 100 mm of gasket length to enhance airtightness. During disassembly, a plasticizer can be injected to soften the gasket within 10 to 30 minutes, enabling separation without damage.

[0063] These configurations can be systematically managed through the restandardization process illustrated in FIG. 2. The measurement module can automatically calculate insufficient dimensions through non-contact thickness and dimension scanning, the replenishment module can replenish selected sacrificial dimension layer material by spraying or roll coating, and the curing module can perform curing for 1 to 3 minutes using one of IR, induction heating, or UV. Lifecycle management can be enabled by recording the replenishment thickness and frequency via QR codes through a passport logging system. The entire system enables dry disassembly and reuse while simultaneously achieving automatic tolerance absorption and enhanced bonding, thereby providing rapid on-site workability in minutes and economical material costs for repeated use.

[0064] In one embodiment of the present invention, the module body may have a coupling surface comprising a rail, a cam lock, and a shear key. This coupling surface configuration enables mechanical coupling of various modular housing modules, and each element performs a specific role to ensure stable assembly and disassembly.

[0065] Rails can provide positional alignment and guidance functions between modules and may be formed on the top and bottom or on the left and right sides depending on the type of module. For example, in the case of wall modules, horizontal rails may be placed on the top and bottom to guide vertical stacking, and in the case of floor modules, vertical rails may be formed on the edges to handle connection with adjacent modules. The cross-sectional shape of the rail may be selected from 'U', 'T', or 'L' shapes depending on the load conditions and assembly direction of the module, and the rail width may be in the range of 20 mm to 80 mm, more specifically 30 mm to 60 mm, most preferably 40 mm to 50 mm. The rail height may be set in the range of 15 mm to 50 mm, more specifically 20 mm to 40 mm, to ensure sufficient connection depth.

[0066] The cam lock is a core fastening device that provides mechanical coupling force between modules, and coupling and uncoupling can be achieved through rotational movement. The rotation angle of the cam lock is designed to range from 90 to 180 degrees, more specifically from 120 to 150 degrees, allowing for easy operation by the operator while ensuring secure coupling. The coupling force can be adjusted to a range of 1,000 N to 10,000 N, more specifically from 2,000 N to 8,000 N, and most preferably from 3,000 N to 6,000 N, depending on the size and load of the module. A higher range of coupling force may be applied when supporting high loads, such as with ceiling modules, while a lower range may be applied when the load is relatively light, such as with internal partition modules.

[0067] The material of the cam lock can be selected from stainless steel SUS304 or SUS316, galvanized steel, or high-strength aluminum alloy, considering durability and corrosion resistance. The thickness of the cam lock body is manufactured to be in the range of 3 mm to 10 mm, more specifically 5 mm to 8 mm, so that deformation or wear can be minimized even with repeated fastening and unfastening. The operating torque of the cam lock is set in the range of 5 N·m to 25 N·m, allowing for manual operation without power tools.

[0068] Shear keys can be responsible for transferring shear force between modules and resisting horizontal forces, and can provide structural stability against lateral forces such as earthquakes or wind loads. The shape of the shear key can be determined from circular, elliptical, or rectangular cross-sections considering stress distribution and ease of manufacturing. In the case of a circular shear key, the diameter may be in the range of 10 mm to 30 mm, more specifically 15 mm to 25 mm, and in the case of a rectangular shear key, the width and height may each be set in the range of 8 mm to 25 mm. The length of the shear key is formed in the range of 50 mm to 200 mm, more specifically 80 mm to 150 mm, to ensure sufficient shear resistance.

[0069] The material of the shear key may be structural carbon steel SM490 or high-strength steel SPFC, and the shear strength may range from 200 MPa to 500 MPa, more specifically from 300 MPa to 450 MPa. For structural modules, a higher range of strength may be required, while for finishing modules, a lower range may be sufficient. The surface of the shear key may be galvanized or coated with epoxy to prevent corrosion, and the coating thickness may be formed in the range of 50 μm to 150 μm.

[0070] The configuration of these joint surfaces can be differentiated depending on the type and application of the module. For exterior wall modules, additional sealing treatments may be applied to rails and cam locks due to the critical importance of weather resistance; for interior partition modules, the operability and durability of the cam locks may be enhanced due to the high frequency of dismantling. For equipment modules, joint surface designs may be applied to account for penetrations of pipes or electrical wires, and the location of the joint surfaces may be adjusted to ensure accessibility for maintenance.

[0071] In one embodiment of the present invention, the sacrificial dimension layer may be applied to the bonding surface of the module body. The location and application method of the sacrificial dimension layer can be optimized according to the type of module and bonding characteristics, and can provide consistent performance even during repeated assembly and disassembly processes.

[0072] The sacrificial dimension layer can be applied selectively or entirely to various parts of the joint surface. In the case of rail contacts, a relatively thick sacrificial dimension layer may be applied as this is an area where friction is concentrated, and a sacrificial dimension layer of high strength composition may be required for camlock contacts as high pressure is applied. In the case of butt joints, it can be applied with a uniform thickness over a wide area to serve the function of absorbing overall tolerances. For example, in the case of floor modules, the sacrificial dimension layer can be applied to the entire top surface to evenly distribute the load of the upper module, and in the case of wall modules, it can be applied to the vertical joint surface and the horizontal joint surface with different thicknesses and compositions, respectively.

[0073] The application location can be determined by considering the structural characteristics of the module and the expected stress distribution. For ceiling modules, sacrificial dimension layers of different thicknesses may be applied to the center and corners to account for gravitational sagging and thermal expansion. The thickness can be differentiated to 0.12 mm to 0.20 mm for the center and 0.08 mm to 0.15 mm for the corners to adaptively respond to deformation. For equipment modules, a sacrificial dimension layer of a special composition with enhanced sealing properties may be locally applied around pipe or wire penetrations.

[0074] The coating method can be selected considering the shape complexity of the module and production efficiency. In the case of spray coating, it can be applied uniformly even to bonding surfaces with complex shapes, and precise control of the coating thickness is possible by controlling the nozzle diameter to 0.5 mm to 2.0 mm, the spray pressure to 2 bar to 8 bar, and the spray distance to 100 mm to 300 mm. Roller coating is suitable for flat bonding surfaces, and high work efficiency can be achieved by setting the roller diameter to 50 mm to 150 mm and the rotation speed to 10 rpm to 100 rpm.

[0075] The sheet attachment method has the advantage of reducing on-site work time and can be applied by bonding a pre-manufactured sacrificial dimensional layer sheet to the bonding surface. The sheet is manufactured with a thickness of 0.08 mm to 0.25 mm, a width of 50 mm to 500 mm, and a length of 1 m to 10 m, allowing it to accommodate various module sizes. The sheet adhesive is set with a peel strength in the range of 1 N / mm to 5 N / mm, ensuring secure initial attachment while allowing for easy removal during replacement.

[0076] The application pattern of the sacrificial dimensional layer can also affect performance. In the case of continuous application, an integrated protective film can be formed across the entire bonding surface, while in the case of intermittent application, material costs can be reduced by selectively applying it only to key contact areas. In the case of a grid pattern, a protective effect over the entire area can be achieved while limiting the application area to 60% to 80%. A stripe pattern can respond intensively to stress in a specific direction and can be set with a pattern width of 5 mm to 20 mm and a spacing of 10 mm to 30 mm.

[0077] Quality control of the applied sacrificial dimensional layer can be performed through thickness measurement, adhesion evaluation, and surface roughness measurement. Thickness measurement can be performed using an eddy current or ultrasonic method, and the uniformity of the entire coated surface can be evaluated by setting the measurement accuracy to within ±5 μm and the measurement interval to 50 mm to 100 mm. Adhesion can be evaluated by a pull-off test, and a minimum adhesive strength of 0.5 MPa or higher may be required.

[0078] Changes in coating characteristics depending on environmental conditions may also need to be considered. Coating operations may be performed within a temperature range of 5 to 35 degrees and a relative humidity range of 30% to 80%, and under extreme conditions, the coating thickness or curing time may be adjusted. At high temperatures, the solvent evaporation rate increases, which may result in a coating thickness thinner than the target value, so an additional 10% to 20% margin may be applied; and at high humidity, the curing time may be extended, so sufficient drying time may need to be ensured.

[0079] In one embodiment of the present invention, the sacrificial dimension layer may comprise a urethane-acrylic hybrid resin or Diels-Alder resin. Such a resin system can simultaneously provide appropriate wear resistance during assembly and enhanced curability after assembly, and can maintain stable performance even during repeated use and resizing processes.

[0080] Urethane-acrylic hybrid resin may be a composite resin system that combines the flexibility and toughness of urethane with the transparency and curability of acrylic. The basic composition may include urethane acrylate oligomer in a range of 40% to 70% by weight, more specifically 45% to 65% by weight, and most preferably 50% to 60% by weight. Acrylic monomer may be added in a range of 20% to 40% by weight, more specifically 25% to 35% by weight, and isobornyl acrylate, tripropylene glycol diacrylate, etc. may be used.

[0081] The urethane acrylate oligomer may have a molecular weight in the range of 1,000 Da to 10,000 Da, more specifically 2,000 Da to 8,000 Da, and the number of acrylic functional groups may be set to 2 to 6, more specifically 3 to 4 to achieve an appropriate crosslinking density. The urethane backbone may be selected from polyester-based, polyether-based, or polycarbonate-based materials, each of which may provide different mechanical properties and chemical resistance.

[0082] The photoinitiator may be added in a range of 1% to 5% by weight, more specifically 2% to 4% by weight, relative to the total composition. A mixed system of 1-hydroxycyclohexylphenyl ketone and bistrimethylbenzoylphenylphosphine oxide may be used, and the mixing ratio may be adjusted to a range of 3:1 to 1:1 to achieve a balanced surface and internal curing. UV irradiation conditions are a wavelength of 365 nm to 405 nm and an illuminance of 1000 mW / cm². 2 Up to 5000 mW / cm 2 The investigation time can be set to 30 to 180 seconds.

[0083] The viscosity of the urethane-acrylic hybrid resin before curing can be controlled to a range of 1,000 cP to 10,000 cP, more specifically 2,000 cP to 8,000 cP, thereby ensuring applicability and penetration. After curing, the Shore D hardness can be in the range of 50 to 80, more specifically 60 to 75, and the tensile strength can be achieved in the range of 20 MPa to 50 MPa, and the elongation in the range of 50% to 200%.

[0084] Diels-Alder resins can be thermoplastic-thermosetting hybrid systems utilizing reversible crosslinking reactions. In the case of furan-maleimide Diels-Alder resins, the furan component and the maleimide component can undergo an addition reaction at 60 to 100 degrees to form a crosslinked structure, and a reverse reaction can occur at 120 to 160 degrees to release the crosslinking. These characteristics can enable softening through heating during disassembly and re-curing during reassembly.

[0085] The basic composition of the Diels-Alder resin may consist of 40% to 70% by weight of a furan-containing polymer, 20% to 40% by weight of a maleimide compound, and 0.1% to 2% by weight of a catalyst. The furan-containing polymer may be a furfuryl alcohol-based resin, a furan-modified epoxy resin, etc., and may have a molecular weight in the range of 2,000 Da to 20,000 Da. The maleimide compound may be N,N'-methylenebismaleimide, N-phenylmaleimide, etc.

[0086] The reaction rate of the Diels-Alder reaction can vary significantly depending on the temperature, and it may take 2 to 6 hours to complete the reaction at 70 degrees and 30 to 120 minutes at 90 degrees. The reverse reaction can be completed within 30 to 90 minutes at 140 degrees and 10 to 30 minutes at 160 degrees, allowing for rapid softening upon disassembly.

[0087] The selection of resin can be determined based on the module's operating environment and required performance. For modules exposed to the external environment, urethane-acrylic hybrid resins with excellent UV resistance and weather resistance may be suitable, and UV stabilizers and antioxidants may be additionally added. For indoor modules subject to frequent dismantling, Diels-Alder resins with reversible properties may be advantageous. For modules supporting structural loads, a resin system that exhibits high stiffness and creep resistance after curing may be selected.

[0088] The additive system can also be an important factor in controlling the properties of the resin. 1% to 10% by weight of silica nanoparticles can be added to improve mechanical strength, and the average particle size can be selected in the range of 10 nm to 50 nm to achieve a reinforcing effect while maintaining transparency. 3% to 15% by weight of plasticizers can be added to improve initial processability, and dibutyl phthalate, dioctyl adipate, etc., may be used.

[0089] In one embodiment of the present invention, the crusher-sham layer may include a microballoon or honeycomb structure. Such a structure can effectively absorb gaps between modules through controlled deformation under compressive load and can provide performance optimized for various load conditions and module types.

[0090] Microballoons are microparticles with a hollow structure that can provide gradual and predictable deformation characteristics through sequential crushing upon compression. In the case of glass microballoons, the average diameter can be selected to be in the range of 10 μm to 100 μm, more specifically 20 μm to 80 μm, most preferably 30 μm to 60 μm. The wall thickness can be controlled to be in the range of 0.5 μm to 3 μm, more specifically 1 μm to 2 μm to achieve appropriate crushing strength. The crushing strength can be adjusted to be in the range of 5 MPa to 50 MPa, more specifically 10 MPa to 30 MPa, so that controlled deformation can be achieved under typical module assembly pressures.

[0091] The density of glass microballoons is 0.15 g / cm³ 3 Up to 0.60 g / cm³ 3 It can be provided in a wide range, and as density decreases, crush strength decreases, allowing deformation to begin even at smaller loads. Compressibility characteristics can have a direct correlation with density, and 0.15 g / cm³ 3 In terms of density, crushing begins at a compressibility of 5% to 15%, and at 0.40 g / cm³ 3 In terms of density, rapid crushing may occur at a compression rate of 15% to 25%.

[0092] Polymer microballoons may have lower crushing strength than glass microballoons, and deformation may begin in the range of 1 MPa to 20 MPa, more specifically 3 MPa to 15 MPa. Polystyrene, polyacrylonitrile, or phenolic resin-based microballoons may be used, and the diameter may be manufactured in the range of 5 μm to 200 μm, more specifically 20 μm to 150 μm. Polymer microballoons may be capable of certain elastic recovery even after crushing, thereby providing partial reusability.

[0093] The honeycomb structure is a lightweight structural material composed of a regular arrangement of hexagonal cells and can provide directional compressive properties. The cell size can be set to a range of 1 mm to 10 mm, more specifically 2 mm to 8 mm, and most preferably 3 mm to 6 mm. The wall thickness is controlled to a range of 0.1 mm to 1 mm, more specifically 0.2 mm to 0.8 mm, so that appropriate compressive strength and lightweight properties can be achieved simultaneously.

[0094] In the case of aluminum honeycombs, compressive strength can be varied from 0.5 MPa to 30 MPa, more specifically from 2 MPa to 20 MPa, and properties can be adjusted depending on the alloy type and heat treatment conditions. 5052 aluminum alloy can provide medium strength and excellent formability, while 6061 alloy can exhibit high strength and corrosion resistance. The density of the honeycomb is 40 kg / m³. 3 up to 200 kg / m² 3 It can be adjusted by range.

[0095] Polymer honeycombs can have lower compressive strength than aluminum, and crushing may begin in the range of 0.1 MPa to 10 MPa. Materials such as polypropylene, polycarbonate, or Nomex may be used, each providing different temperature stability and chemical resistance. Polymer honeycombs may be capable of significant elastic recovery even after crushing, which may be advantageous for repeated use.

[0096] The overall structure of the crusher-sham layer can be composed of a single material or a composite material. In the case of a composite structure, multi-stage crushing behavior can be achieved by placing materials with different crushing characteristics in the upper and lower layers. For example, gradual compression characteristics can be achieved by placing polymer microballoons with low crushing strength in the upper layer and glass microballoons with high crushing strength in the lower layer.

[0097] The binder system can serve to fix microballoons or honeycomb structures and control overall mechanical properties. In the case of thermoplastic polyurethane, flexibility and toughness with a Shore A hardness of 85 to 95 can be provided, and ethylene-acrylic acid copolymers can improve adhesion and chemical resistance. The binder content can be controlled to a range of 20% to 40% by weight relative to the total composition, more specifically 25% to 35% by weight.

[0098] The thickness of the crusher-sham layer can be determined by considering the expected tolerance range and compression ratio. Generally, it can be applied in the range of 0.2 mm to 1.0 mm, more specifically 0.3 mm to 0.8 mm, and most preferably 0.4 mm to 0.6 mm. For structural modules, a higher range may be applied considering high loads, and for finishing modules, a lower range may be applied for fine adjustment.

[0099] In one embodiment of the present invention, the restandardization method may include a measurement step, a replenishment step, a curing step, and a verification step. This sequential method can be systematically performed as illustrated in FIG. 2, and can restore the disassembled module to its original specifications to enable continuous reuse.

[0100] The measurement step may be a process of quantitatively evaluating the condition of the bonding surface of the disassembled module. Changes in dimensions, surface roughness, and the degree of damage of the bonding surface can be measured non-contactually, and based on the measurement results, the areas requiring replenishment and the amount of replenishment can be automatically calculated. In the case of laser triangulation, precise and rapid measurement may be possible by setting the resolution to 1 μm to 10 μm, the measurement range to ±5 mm, and the scan speed to 1 mm / s to 50 mm / s. The capacitive thickness sensor can accurately determine the remaining thickness of the sacrificial dimensional layer with a resolution of 0.1 μm and a measurement range of 0 mm to 2 mm.

[0101] Measurement data is processed into a 3D surface profile to visualize the condition of the entire bonding surface and automatically identify areas with insufficient dimensions of 0.02 mm or more. The measurement time is for a bonding surface size of 1 m 2 The time can be shortened to a range of 10 to 30 seconds, improving on-site work efficiency. Through simultaneous measurement using multiple sensors, even joint surfaces with complex shapes can be evaluated at once.

[0102] The replenishment step may be a process of precisely filling in the deficient portion of the sacrificial dimension layer based on measurement results. The replenishing material must have a composition identical to or compatible with the existing sacrificial dimension layer and must be able to ensure interfacial adhesion and integrity with the existing layer. In the case of an airless spraying method, precise control of the coating thickness may be possible by controlling the spray pressure to 50 bar to 200 bar, the nozzle diameter to 0.3 mm to 1.5 mm, and the spray speed to 10 mm / s to 100 mm / s.

[0103] The roll coating method is suitable for flat bonding surfaces and can achieve a uniform thickness distribution by setting the roller hardness to Shore A 60 to 90, the linear pressure to 1 N / cm to 10 N / cm, and the coating speed to 1 m / min to 10 m / min. The replenishment amount is set by adding a margin of 10% to 30% to the measured deficit amount to account for subsequent processing and curing shrinkage. The replenishment accuracy may need to be controlled within ±10 μm relative to the target thickness.

[0104] The curing step may be a process of stabilizing the supplemented sacrificial dimensional layer and integrating it with the existing layer. Depending on the characteristics of the supplementary material, an appropriate curing method among photocuring, thermal curing, or chemical curing may be selected. For UV curing, the wavelength is 365 nm to 405 nm and the illuminance is 2000 mW / cm². 2 Up to 8000 mW / cm 2The irradiation time can be set to 30 seconds to 180 seconds. IR heat curing can be controlled to a temperature of 80 to 120 degrees and a heating time of 1 minute to 5 minutes to achieve uniform curing.

[0105] In the case of induction heating, the frequency can be set to 13.56 MHz and the output to 500 W to 2000 W, enabling localized and rapid heating. During the curing process, temperature and humidity are controlled to ensure consistent quality, and the process can be performed within a temperature range of 20 to 30 degrees and a relative humidity range of 40% to 60%. The degree of curing can be monitored in real time through infrared spectroscopy or hardness measurement.

[0106] The verification phase may be a process of confirming the quality of the restandardized module and determining its suitability for reuse. Dimensional accuracy may be managed within ±0.02 mm relative to the target specification, and surface roughness may be managed within the Ra range of 0.5 μm to 2.0 μm. Adhesive strength is evaluated by a pull-off test, and an adhesive strength of at least 1 MPa may be confirmed. The degree of curing may be set to a Shore D hardness of 50 or higher, or a gel content of 85% or higher.

[0107] Simple verification using a GO / NO-GO gauge can also be performed, and the acceptance criterion can be set to a performance level of 90% to 100% compared to a new module. The verification time, including measurement and evaluation, can be reduced to a range of 10 to 30 seconds to facilitate the smooth workflow at the site. For rejected modules, it can be automatically determined whether to replenish or discard them.

[0108] The overall restandardization method can be customized according to module type. For structural modules, strength verification is enhanced, so compression or shear tests may be additionally performed; for finishing modules, appearance quality inspection is emphasized, so measurements of color difference or gloss may be included. For equipment modules, the airtightness and electrical characteristics of connections are also verified to enable a comprehensive performance evaluation.

[0109] In one embodiment of the present invention, the self-healing primer may include microcapsules or an ionic network. This configuration can automatically repair microcracks, chipping, or surface damage occurring during module use, thereby maintaining the long-term performance of the joint and ensuring quality during repeated assembly processes.

[0110] The microcapsule system may be a method in which the resin and the curing agent are stored separately in separate capsules, and upon damage, the two components are mixed and automatically cured through the rupture of the capsule. The resin capsule may contain 40% to 60% by weight of epoxy resin and 20% to 40% by weight of urethane resin, and the curing agent capsule may contain 30% to 50% by weight of amine-based curing agent and 5% to 15% by weight of imidazole-based accelerator. The average diameter of the capsule is controlled to be in the range of 5 μm to 100 μm and the wall thickness to be in the range of 0.2 μm to 3 μm, so that it does not rupture under normal usage conditions but can respond sensitively to stress concentration when cracks occur.

[0111] The ionic network is iron ions Fe 3 and terpyridine, zinc ion Zn 2 and histidine, copper ion Cu 2 The coordination bond between and imidazole can be utilized, and reversible dissociation and recombination can be activated in the range of temperature 40 to 80 degrees and pH 5 to 8.

[0112] In one embodiment of the present invention, the refill-release gasket may have an injection port. The injection port is a key component that implements the dual function of the gasket and can provide enhanced airtightness through the injection of a sealant and ease of disassembly through the injection of a plasticizer.

[0113] The injection port is designed as a check valve type and can be controlled with a diameter of 2 mm to 6 mm and a spring load of 0.2 N to 1.5 N. For the screw connection type, M3 to M6 screws are used, and the O-ring groove depth is formed to be 0.3 mm to 0.8 mm and the width to 1.5 mm to 3.0 mm to ensure complete airtightness. The injection pressure is limited to 0.2 bar to 1.5 bar to ensure sufficient penetration while preventing damage to the gasket.

[0114] In one embodiment of the present invention, the refill-release gasket may comprise EPDM or silicone. This choice of material can satisfy the various environmental conditions and repeated use requirements of modular housing.

[0115] EPDM is composed of 50% to 70% by weight of ethylene, 25% to 45% by weight of propylene, and 4% to 8% by weight of diene monomer, and can provide a wide operating temperature range from -40°C to 120°C. Shore A hardness can range from 40 to 80, tensile strength from 8 MPa to 20 MPa, and elongation from 300% to 600%.

[0116] In the case of silicone, polydimethylsiloxane is the main component, allowing for use in a wider temperature range of -50 to 200 degrees, and has a viscosity of 10 4 cSt to 10 6 cSt, crosslinking density gel content can be controlled to 90% to 95%.

[0117] In one embodiment of the present invention, the thickness of the sacrificial dimension layer may be 0.05 to 0.30 mm. This thickness range can simultaneously achieve effective tolerance absorption and economical material usage.

[0118] More specifically, it can be applied in the range of 0.08 mm to 0.25 mm, most preferably 0.10 mm to 0.20 mm. Depending on the module size, 0.05 mm to 0.10 mm can be applied to small modules of 1 m or less, 0.08 mm to 0.15 mm to medium modules of 1 m to 3 m, and 0.12 mm to 0.25 mm to large modules of more than 3 m. Thickness uniformity may be controlled within ±5% of the average value.

[0119] In one embodiment of the present invention, the crushing rate of the crusher-sam layer may be 10 to 35%. The crushing rate is defined as the ratio of the compressed thickness to the initial thickness, and can effectively absorb intermodular tolerances while preventing excessive permanent deformation.

[0120] More specifically, it can be controlled within a range of 15% to 30%, most preferably 18% to 25%. The crushing proceeds in stages, with the outer layer structure crushed from 10% to 20%, the intermediate layer from 20% to 30%, and the core crushed from 30% or more. After crushing, the structure must be restored to at least 85% of its original thickness upon removal of the load to be reusable.

[0121] In one embodiment of the present invention, the film thickness of the self-healing primer may be 5 to 20 μm. Such an ultra-thin thickness can provide a self-healing function while minimizing the impact on the overall module dimensions.

[0122] More specifically, it can be applied in the range of 8 μm to 18 μm, most preferably 10 μm to 15 μm. The coating film can be formed into a multilayer structure of an adhesive layer of 2 μm to 5 μm, a functional layer of 5 μm to 12 μm, and a protective layer of 1 μm to 3 μm. The microcapsule density is 10 6 Pieces / cm 3 to 10 7 Pieces / cm 3Effective self-restoration may be possible at this level.

[0123] In one embodiment of the present invention, the sacrificial filament layer may further comprise a biomimetic hydrogel comprising chitosan, sodium alginate, and L-dihydroxyphenylalanine residues. This biomimetic composition mimics the adhesion mechanism exhibited by mussel byssus proteins in an aquatic environment, thereby enabling excellent adhesion performance even in environments where humidity is present.

[0124] Chitosan can be selected with a degree of deacetylation of 80% to 90% and a molecular weight in the range of 100,000 Da to 500,000 Da, and can provide strong adhesion through electrostatic interaction with an anionic surface by exhibiting a cation density of 2 meq / g to 4 meq / g. Sodium alginate is composed with a G / M ratio of 1.5 to 2.3 and a molecular weight of 150,000 Da to 350,000 Da, and can form a stable polyionic complex with chitosan.

[0125] L-DOPA residues are included in an amount of 0.5% to 2% by weight relative to the total weight of the hydrogel and are converted to dopaquinone under oxidizing conditions, which can provide strong adhesion to metal surfaces through chelation. The swelling rate of the hydrogel varies in the range of 200% at 30% relative humidity and 600% at 90% relative humidity, allowing it to respond adaptively to environmental conditions.

[0126] In one embodiment of the present invention, the biomimetic hydrogel may comprise 8 to 15 weight% chitosan, 5 to 12 weight% sodium alginate, and 2 to 6 weight% mussel byssus protein analog. Such precise compositional ratios can optimize the interaction of each component to simultaneously achieve excellent adhesive performance and mechanical properties.

[0127] More specifically, 10% to 13% by weight of chitosan, 7% to 10% by weight of sodium alginate, and 3% to 5% by weight of a mussel byssus protein analog may be most preferable. When the chitosan content increases, the compressive strength increases linearly from 0.2 MPa to 1.5 MPa, and when the alginate content increases, the swelling rate may increase from 200% to 600%.

[0128] The mussel byssus protein analog is designed with a DOPA residue content of 15 mol% to 20 mol% and a molecular weight of 10,000 Da to 30,000 Da to improve adhesive strength from 0.5 MPa to 3.5 MPa. The preparation of the hydrogel is carried out at a pH of 5 to 6, and can be controlled with a mixing time of 15 to 25 minutes and a gelation time of 30 to 120 minutes.

[0129] In one embodiment of the present invention, the crusher-sam layer may further include phase change material microcapsules. The phase change material system can absorb or release latent heat through solid-liquid conversion according to temperature changes, thereby enabling the control of frictional heat during the assembly process and the utilization of thermal energy during disassembly.

[0130] Phase change material microcapsules are formed with a core-shell structure and can be controlled to a capsule size of 10 μm to 30 μm and a wall thickness of 0.5 μm to 1.5 μm. The melting point is set to 25 to 40 degrees, allowing it to effectively respond to typical building environment temperatures and temperature rises occurring during the assembly process. The latent heat is in the range of 150 J / g to 300 J / g, enabling it to absorb or release temperature changes of 5 to 15 degrees.

[0131] As phase change materials, paraffinic materials such as n-hexadecane, n-octadecane, and n-eicosane, fatty acid materials such as lauric acid and palmitic acid, or salt hydrate materials such as calcium chloride hexahydrate may be selected. The dispersion concentration of the microcapsules is controlled to 15% by weight to 30% by weight to achieve a balance between the thermal storage effect and mechanical properties.

[0132] In one embodiment of the present invention, the phase change material is n-octadecane, and the wall of the microcapsule may be melamine-urea-formaldehyde resin. This specific combination can provide performance optimized for the operating temperature range of a modular system for construction.

[0133] n-octadecane exhibits a melting point of 28.2 to 29.8 degrees and a latent heat of 240 J / g to 250 J / g, which can provide thermal storage characteristics suitable for module assembly environments. The change in density during phase change is small, at the level of 1.3%, allowing for a stable phase change without significant volume change inside the capsule. Thermal stability is such that chemical decomposition does not occur in general construction environments, with a decomposition temperature of 200 degrees or higher.

[0134] Melamine-urea-formaldehyde resin is composed of a molar ratio of melamine to urea of ​​1.5:1 to 2.5:1 and a molar ratio of formaldehyde of 2:1 to 3:1, and can provide excellent heat resistance and mechanical strength. The glass transition temperature is 120 to 150 degrees, which is sufficiently higher than the melting point of n-octadecane, so softening of the wall may not occur during the phase change process. It exhibits a tensile strength of 40 MPa to 60 MPa and a compressive strength of 80 MPa to 120 MPa, and can sufficiently withstand mechanical stress within the crusher-sam layer.

[0135] In one embodiment of the present invention, 15 to 25 weight% of phase change material microcapsules and 2 to 5 weight% of boron nitride nanosheets may be further included. This composition can maximize temperature control performance by combining the heat storage function of the phase change material with the heat conduction promoting function of boron nitride.

[0136] More specifically, 18% to 22% by weight of phase change material microcapsules and 3% to 4% by weight of boron nitride nanosheets can provide optimal performance. The boron nitride nanosheets are formed with a thickness of 3 nm to 8 nm and a diameter of 500 nm to 2 μm, and can exhibit a planar thermal conductivity of 400 W / m·K to 2000 W / m·K.

[0137] In a composite system, the heat absorption and release of the phase change material and the provision of a heat conduction path by boron nitride are combined, which can improve the heat transfer rate by 2 to 5 times. Thermal conductivity can be improved by 150% to 300% compared to a pure matrix, and thermal diffusivity can be improved by 120% to 200%. Mechanical properties can show an improvement in compressive strength of 10% to 20% and an increase in crushing energy absorption capacity of 5% to 15%.

[0138] In one embodiment of the present invention, a modular housing module system comprising both a biomimetic hydrogel and phase change material microcapsules may be provided. This integrated system can simultaneously implement the biomimetic adhesive function of the sacrificial dimension layer and the temperature control function of the crusher-sam layer to form an intelligent bonding system that adaptively responds to environmental changes.

[0139] The biomimetic hydrogel exhibits a volume change of 100% to 400% in a relative humidity range of 30% to 90%, thereby providing strong adhesion in dry environments and flexibility and sealing properties in wet environments. The phase change material system undergoes a phase change at 28 to 30 degrees, buffering frictional heat during the assembly process and releasing accumulated thermal energy upon disassembly, thereby facilitating separation.

[0140] The interaction between the two systems can provide differentiated performance depending on the season. In the summer, the enhanced sealing function of the hydrogel prevents cold air leakage, while in the winter, the heat storage of the phase change material improves heating efficiency. This natural temperature regulation can result in a 5% to 15% reduction in building energy consumption, and durability allows the system to maintain more than 90% of its initial performance even after 1,000 hours of exposure under conditions of 85 degrees and 85% RH.

[0141] The present invention will be described in detail below using specific embodiments. It should be understood that the following embodiments are not intended to limit the scope of the invention, but are intended to illustrate the practice of the invention.

[0142] Example 1

[0143] The characteristics of various resin systems were verified by manufacturing the sacrificial dimension layer of a modular housing module system with different compositions. In all embodiments, the same aluminum 6061 alloy module body was used, and the joining surface consisted of a U-shaped rail with a width of 45 mm and a height of 25 mm, a cam lock with a diameter of 20 mm, and a circular shear key with a diameter of 18 mm and a length of 120 mm.

[0144] Example 1-1: In a urethane-acrylic hybrid resin, 40 wt% urethane acrylate oligomer, 30 wt% isobornyl acrylate, 27 wt% tripropylene glycol diacrylate, 2 wt% 1-hydroxycyclohexylphenyl ketone, and 1 wt% bistrimethylbenzoylphenylphosphine oxide were mixed. The urethane acrylate oligomer used had a molecular weight of 3,000 Da and 3 acrylic functional groups. The mixture was adjusted to a viscosity of 1,200 cP and then applied to the bonding surface by spray coating to a thickness of 0.12 mm. UV irradiation was performed at a wavelength of 365 nm and 3,000 mW / cm². 2 It was cured by performing the process for 60 seconds at a light intensity.

[0145] Example 1-2: The urethane acrylate oligomer content was increased to 50 wt%, and the isobornyl acrylate and tripropylene glycol diacrylate were adjusted to 25 wt% and 22 wt%, respectively. The photoinitiator composition was maintained identically to Example 1-1. The viscosity was increased to 2,800 cP, and the same coating and curing conditions were applied.

[0146] Examples 1-3: The urethane acrylate oligomer content was increased to 60 wt%, and the total amount of acrylic monomer was adjusted to 37 wt%. The viscosity reached 5,200 cP, and the coating method was changed to roller coating to a thickness of 0.15 mm. The curing condition was a roughness of 4,500 mW / cm². 2 Increased the time and extended the investigation time to 90 seconds.

[0147] Examples 1-4: The urethane acrylate oligomer content was maximized to 70 wt%, and the acrylic monomer was reduced to 27 wt%. An oligomer with a molecular weight of 6,000 Da was used to improve the crosslinking density. The viscosity reached 8,900 cP, and a heated roller coating was applied at a substrate temperature of 40 degrees to a thickness of 0.18 mm.

[0148] Examples 1-5: A Diels-Alder resin system was composed of 40 wt% furfuryl alcohol-based polymer, 35 wt% N,N'-methylenebismaleimide, 0.8 wt% dibutyltin dilaurate catalyst, and the remainder as solvent. A furan polymer with a molecular weight of 8,000 Da was used. After mixing at pH 5.5, the Diels-Alder reaction was carried out by heating at 70°C for 4 hours. After coating to a thickness of 0.14 mm, it was further cured at 90°C for 2 hours.

[0149] Examples 1-6: In Diels-Alder resin, the furan polymer content was increased to 55 wt% and the maleimide compound was adjusted to 30 wt%. Mechanical strength was improved by using a furan polymer with a molecular weight of 15,000 Da. The reaction temperature was increased to 80 degrees, and the reaction time was shortened to 2.5 hours. Final curing was performed at 110 degrees for 90 minutes.

[0150] In all embodiments, the thickness uniformity of the sacrificial dimension layer was controlled to within ±3% of the average value, and after curing at room temperature for 24 hours, it was used for module assembly. The crusher-sham layer was composed of 25 wt% glass microballoons with an average diameter of 40 μm and a thermoplastic polyurethane binder and applied to a thickness of 0.5 mm.

[0151] Example 2

[0152] Module systems with different crushing characteristics were manufactured by changing the structural type and dimensions of the crusher-sam layer. In all embodiments, the sacrificial dimension layer used the same urethane-acrylic hybrid resin as in Examples 1-2 with a thickness of 0.13 mm, and the configuration of the bonding surface with the module body was also maintained identically.

[0153] Example 2-1: Crusher-sham layer using glass microballoons with average diameter 20 μm, wall thickness 1.2 μm, and density 0.25 g / cm³ 3In glass microballoons were used. 30 wt% of microballoons and 70 wt% of a thermoplastic polyurethane binder with a Shore A hardness of 90 were mixed. A polyester-based polyurethane with a molecular weight of 50,000 Da was used as the binder. The mixture was melt-kneaded at 100 degrees and then formed into a 0.4 mm thick sheet through extrusion. After cooling, it was cut to fit the size of the module joint surface and applied.

[0154] Example 2-2: The average diameter of the microballoon was increased to 40 μm, the wall thickness to 1.8 μm, and the density to 0.35 g / cm³ 3 In glass microballoons were used. The microballoon content was reduced to 25 wt% and the binder was increased to 75 wt%. Higher flexibility was achieved by using a polyether-based polyurethane binder. The molding conditions were applied in the same way as in Example 2-1.

[0155] Examples 2-3: Average diameter 60 μm, wall thickness 2.2 μm, density 0.45 g / cm³ 3 Large glass microballoons were used. The microballoon content was reduced to 20 wt% and mixed with 80 wt% of an ethylene-acrylic acid copolymer binder. The acrylic acid content of the binder was set to 15 mol% to improve adhesion. The viscosity was controlled by increasing the extrusion temperature to 120 degrees.

[0156] Examples 2-4: In a crusher-shum layer using an aluminum honeycomb structure, a honeycomb made of 5052 aluminum alloy was used. The cell size was set to 4 mm, the wall thickness to 0.4 mm, and the height to 0.6 mm. The honeycomb density was 80 kg / m³. 3 The compressive strength was 3.2 MPa. The honeycomb structure was arranged to cover the entire module joint surface, and the edges were sealed with silicone sealant to prevent the intrusion of foreign substances. A 0.1 mm thick polyethylene film was attached to the top and bottom surfaces of the honeycomb to provide surface protection and anti-slip functions.

[0157] In all embodiments, the dimensional accuracy of the crusher-sham layer was controlled to within ±2% of the target value, and samples for the crushing test were prepared with a size of 50 mm x 50 mm. Microballoon dispersion was checked using an optical microscope to ensure that the aggregate size was 100 μm or less. The cell shape accuracy of the honeycomb structure was confirmed through image analysis to be within 5% of the distortion relative to a regular hexagon.

[0158] Example 3

[0159] Systems with different environmental adaptability were prepared by changing the composition of the hydrogel in a module system containing a biomimetic hydrogel. In all examples, the basic module configuration was maintained identically to Example 1, and the hydrogel layer was additionally applied on top of the sacrificial dimension layer.

[0160] Example 3-1: 8 wt% of chitosan with a deacetylation degree of 85% and a molecular weight of 200,000 Da was dissolved in a 1% aqueous acetic acid solution. Separately, 5 wt% of sodium alginate with a G / M ratio of 1.8 and a molecular weight of 250,000 Da was dissolved in distilled water. 1 wt% of L-DOPA methyl ester was added to the chitosan solution, and the pH was adjusted to 5.5. A polyionic complex was formed by mixing and stirring the chitosan solution and the alginate solution in a 3:2 volume ratio. Gelation was carried out at room temperature for 45 minutes, and the final hydrogel was applied to the module bonding surface to a thickness of 0.8 mm.

[0161] Example 3-2: The chitosan content was increased to 10 wt%, and the sodium alginate was adjusted to 8 wt%. The L-DOPA content was increased to 1.5 wt% to enhance adhesion. The molecular weight of chitosan was increased to 300,000 Da to improve mechanical strength. The mixing ratio of the chitosan solution to the alginate solution was changed to 1:1, and the pH was increased to 6.0. The gelation time was extended to 60 minutes to form a more homogeneous network structure.

[0162] Example 3-3: The chitosan content was further increased to 12 wt%, and high-purity chitosan with a degree of deacetylation of 88% was used. The sodium alginate content was increased to 10 wt%, and a high-gel strength alginate with a G / M ratio of 2.1 was applied. 3 wt% of a mussel byssus protein analog was prepared separately and added. The protein analog was designed with a DOPA residue content of 18 mol% and a molecular weight of 20,000 Da. 0.2 wt% of calcium chloride was added as a crosslinking agent to improve the alginate gel strength.

[0163] Examples 3-4: The chitosan content was maximized to 15 wt%, and ultra-high molecular weight chitosan with a molecular weight of 450,000 Da was used. Sodium alginate was increased to 12 wt%, and 5 wt% of oligo-alginate was added to strengthen the gel structure. The content of mussel byssus protein analog was increased to 5 wt% to secure maximum adhesion. During the mixing process, ultrasonic treatment for 30 seconds was applied to improve dispersibility.

[0164] Examples 3-5: To impart a self-healing function, microcapsules were added to a composition of 11 wt% chitosan and 9 wt% sodium alginate. Microcapsules were prepared with 50 wt% epoxy resin and 50 wt% polyamine curing agent, respectively, separated. The capsule diameter was controlled to 15 μm and the wall thickness to 0.8 μm. The total microcapsule content was added at 8 wt% relative to the hydrogel. The capsule walls were made of urea-formaldehyde resin to ensure appropriate rupture strength.

[0165] In all examples, the pH of the hydrogel was adjusted to a final range of 5.8 to 6.2 and stabilized through 24 hours of aging at room temperature after gelation was complete. The moisture content was measured by gravimetric method and managed within the range of 75% to 82%. A self-healing primer was additionally applied to a thickness of 12 μm over the hydrogel layer to provide surface protection. The primer is an iron ion Fe 3An ionic network system containing 0.5 wt% and 1.2 wt% terpyridine was used.

[0166] Example 4

[0167] Systems with different thermal performance were manufactured by varying the PCM content and thermal conductivity enhancer content in a crusher-sam layer containing phase change material microcapsules. In all embodiments, the basic module configuration and sacrificial dimension layer were applied in the same way as in Examples 1-2.

[0168] Example 4-1: Phase change material microcapsules with n-octadecane as the core material were prepared. A precursor solution was prepared by dissolving 12 g of melamine, 8 g of urea, and 30 g of formaldehyde in 200 ml of distilled water. After adjusting the pH to 3.5, 50 g of n-octadecane was slowly added and emulsified while stirring at 60 degrees. The temperature was raised to 75 degrees, and the polymerization reaction was carried out for 3 hours to produce microcapsules. The capsule size was controlled to an average of 18 μm and the wall thickness to 1.1 μm. A crusher-sam layer was formed by mixing 15 wt% of the prepared microcapsules, 20 wt% of glass microballoons with an average diameter of 35 μm, and 65 wt% of a thermoplastic polyurethane binder.

[0169] Example 4-2: The PCM microcapsule content was increased to 20 wt%, and boron nitride nanosheets were added. Boron nitride nanosheets were prepared through an exfoliation process with an average thickness of 5 nm and a diameter of 1.2 μm. Hexagonal boron nitride powder was dispersed in isopropyl alcohol, and the nanosheets were separated by sonication for 6 hours and centrifugation. 3 wt% of boron nitride nanosheets were first dispersed in a binder, followed by sequential mixing of PCM microcapsules and glass microballoons. The glass microballoon content was reduced to 15 wt%, and the binder was adjusted to 62 wt%.

[0170] Example 4-3: The PCM microcapsule content was maximized to 25 wt%, and the boron nitride nanosheet content was increased to 5 wt%. Surface treatment was performed with the silane coupling agent 3-aminopropyltrimethoxysilane to improve the dispersibility of the boron nitride. The treated boron nitride nanosheets were dispersed in toluene and reacted at 80°C for 2 hours to complete the surface modification. To improve the encapsulation efficiency of the PCM microcapsules, 0.8 wt% of the surfactant sorbitan monooleate was added during the emulsification process. The final composition consisted of 25 wt% PCM microcapsules, 5 wt% boron nitride nanosheets, 10 wt% glass microballoons, and 60 wt% binder.

[0171] In all examples, the encapsulation rate of PCM microcapsules was measured using differential scanning calorimetry and secured at least 92%. The dispersion of boron nitride nanosheets was confirmed using transmission electron microscopy and managed to keep the aggregate size 5 μm or less. The final thickness of the crusher-sam layer was standardized to 0.6 mm, and the interlayer adhesion was evaluated by tensile testing to secure at least 1.2 MPa. Specimens for thermal conductivity measurement were prepared with dimensions of 100 mm x 100 mm x 2 mm, and phase change characteristics were measured using differential scanning calorimetry in the range of -10 to 50 degrees.

[0172] A refill-release gasket was additionally applied to the crusher-sham layer of each embodiment. The gasket was made of EPDM with a Shore A 65 hardness, with a thickness of 2 mm and a width of 8 mm. The injection port was designed with a diameter of 3 mm and set to open at 0.5 bar using a check valve method. The inside of the gasket was initially filled with silicone oil with a viscosity of 1000 cSt to provide a sealing function.

[0173] Experimental Example 1

[0174] To evaluate the effect of the sacrificial dimension layer thickness on tolerance absorption performance and module assembly performance, performance was compared at various thicknesses within and outside the claimed range. Specimens with only varying thicknesses were prepared using the urethane-acrylic hybrid resin of Examples 1-2.

[0175] At a thickness of 0.03 mm, which is below the claimed range, the tolerance absorption rate remained at 45% under a contact pressure of 2 MPa during the assembly of a 200 mm x 200 mm module specimen. Under a gap of 0.08 mm between modules, the compressive force required for complete adhesion reached 8.2 kN, and after 10 repeated assembly cycles, the remaining thickness of the sacrificial dimension layer decreased to 0.018 mm, significantly reducing reusability. As a result of surface roughness measurement, the Ra value increased from an initial 0.8 μm to 3.2 μm, indicating a deterioration in surface quality.

[0176] At a thickness of 0.05 mm, the lower limit of the claim range, the tolerance absorption rate was improved to 72%, and the adhesion compressive force decreased to 5.8 kN under the same gap conditions. After 10 repeated assembly cycles, the remaining thickness was maintained at 0.032 mm, ensuring a reusable level. The surface roughness was controlled at Ra 1.4 μm, indicating a good surface condition.

[0177] At a thickness of 0.15 mm, which is the optimal value within the claimed range, the tolerance absorption rate reached 94%, and the adhesion compressive force was minimized to 3.1 kN. Even after repeated assembly, the remaining thickness was sufficiently maintained at 0.089 mm, and the surface roughness Ra was 0.9 μm, showing excellent quality. In the airtightness measurement between modules, the leakage rate was found to be 0.08 ml / min·m, satisfying the structural requirements.

[0178] At the upper limit of the claimed thickness of 0.30 mm, the tolerance absorption rate improved slightly to 96%, but the overall dimensional accuracy of the module was affected due to the excessive thickness. The cumulative thickness deviation in 100 module assemblies reached ±2.8 mm, exceeding the allowable tolerance of ±2.0 mm. In addition, material usage doubled compared to 0.15 mm, which reduced economic efficiency.

[0179] At a thickness of 0.40 mm, which exceeds the claimed scope, there was minimal additional improvement in tolerance absorption performance, but the overall height of the module assembly exceeded the design value by 4.2 mm. Due to the excessive thickness, the compressive stiffness of the sacrificial dimension layer itself increased, causing the torque required for cam lock fastening to increase from 18 N·m to 28 N·m. Microcracks were observed due to internal stress concentration during the hardening process, and creep deformation of 0.025 mm occurred under long-term loading conditions.

[0180] In the performance evaluation under temperature conditions, under the -20°C condition, the 0.05mm thick specimen exhibited brittleness and cracked during assembly, but maintained sufficient flexibility at 0.15mm or thicker. Under the high temperature condition of 60°C, the 0.03mm thick specimen lost shape stability due to excessive softening, and at 0.30mm or thicker, dimensional changes due to thermal expansion exceeded the allowable value. Under the 85% humidity condition, the 0.15mm thick specimen was stable with a moisture absorption rate of 2.1%, but the 0.03mm specimen showed excessive absorption of 5.8%, resulting in reduced dimensional stability.

[0181] In the evaluation of vibration conditions, when exposed for 1,000 hours under conditions of a frequency of 50 Hz and an acceleration of 2g, no fatigue cracks were observed at thicknesses greater than 0.05 mm, but at 0.03 mm, microcracks began at the edges after 200 hours. At thicknesses greater than 0.30 mm, some delamination caused by vibration was observed, confirming a problem with long-term reliability.

[0182] Experimental Example 2

[0183] To evaluate the effect of the crusher-sham layer's crushing rate on tolerance absorption performance and structural stability, crushing characteristics were measured under various structures and load conditions. Compression tests were performed using each structure of Example 2.

[0184] At a crushing rate of 8%, which is below the claimed scope, the small microballoon system of Example 2-1 was achieved under an assembly load of 1.5 kN. At this level, only 62% of the tolerance between modules of 0.15 mm was absorbed, resulting in a residual gap of 0.057 mm. When the load was removed after crushing, the elastic recovery rate reached 95%, exhibiting excellent resilience, but the tolerance absorption function was insufficient. In the long-term creep test, the additional deformation after 1000 hours was only 0.008 mm, indicating good dimensional stability.

[0185] At the lower limit of the claim range, a crushing rate of 10%, the tolerance absorption rate was improved to 78%, and the remaining gap was reduced to 0.033 mm. The elastic recovery rate decreased slightly to 92% but still maintained an excellent level. Durability was confirmed as the change in crushing characteristics was within 5% even after 100 compression-release cycles in the cyclic loading test.

[0186] At a crushing rate of 22%, which is the median value within the claimed range, the tolerance absorption rate reached 91%, minimizing the residual gap to 0.014 mm. The medium-sized microballoon of Example 2-2 exhibited this crushing rate at an assembly load of 2.8 kN. The elastic recovery rate decreased to 88% but maintained a practical level. The crushing process proceeded gradually, exhibiting a stable load-displacement curve without abrupt changes in stiffness.

[0187] At the upper limit of the claim range, a crushing rate of 35%, the tolerance absorption rate was maximized to 96%, but structural problems began to appear due to excessive crushing. The elastic recovery rate was reduced to 74%, limiting reusability. Although the honeycomb structure of Example 2-4 achieved this crushing rate under a load of 4.2 kN, non-uniform deformation due to buckling of the cell walls was observed.

[0188] At a crushing rate of 45%, which exceeded the claimed scope, complete fragmentation of the microballoons and collapse of the honeycomb cells occurred, resulting in a loss of structural integrity. The recovery rate after load removal dropped sharply to 52%, and problems arose where crushed fragments damaged the joint surfaces of adjacent modules. Although the tolerance absorption rate reached 97%, it was reduced to the level of a one-time consumable.

[0189] In the temperature dependence evaluation, under -10°C conditions, the brittleness of the microballoons increased, and the load required to achieve the same crushing rate increased by 35% compared to room temperature. On the other hand, at a high temperature of 50°C, it decreased by 15% due to the softening of the binder. The honeycomb structure was relatively insensitive to temperature changes, and a change in load was observed within the range of ±8%.

[0190] Under dynamic loading conditions, at a crushing rate of less than 10%, the shock absorption energy is 0.8 J / cm 3 It was limited to, but in the range of 20% to 30%, it was 2.1 J / cm 3 Up to 3.4 J / cm 3 It was significantly improved. At values ​​exceeding 35%, the shock absorption effect actually decreased due to rapid failure. In a vibrating environment, the damping performance was optimized within a crushing rate range of 15% to 25%, and the vibration transmission rate was controlled to a level of 12% to 18%.

[0191] In fatigue characteristic evaluation, the 10% crushing rate condition is 10 6 Performance was maintained without degradation up to the cycle, but at 30% or higher, 10 4Gradual performance degradation was observed starting from the second cycle. The honeycomb structure 10 even under a 25% crushing rate condition 5 It demonstrated cycle durability and exhibited superior fatigue resistance compared to microballoons.

[0192] In the evaluation under different humidity conditions, the crushing characteristics of the microballoon binder changed due to moisture absorption in an environment of 85% relative humidity. In the polyurethane binder system, the load required to achieve the same crushing rate decreased by 12% due to softening caused by moisture absorption, whereas the ethylene-acrylic acid copolymer binder showed the opposite result, increasing by 8% due to hydrophilicity.

[0193] Experimental Example 3

[0194] To evaluate the effect of the film thickness of the self-healing primer on self-healing performance and mechanical properties, damage-restoration tests were performed at various thicknesses within and outside the scope of the claims. The microcapsule system and the ionic network system of Examples 3-5 were applied and compared, respectively.

[0195] At a film thickness of 3 μm, which is less than the claimed scope, the microcapsule density is 2.1 x 10⁻⁶ 5 Pieces / cm 3 The self-healing function was insufficient due to limitations. For artificial scratch damage with a width of 50 μm and a depth of 2 μm, the recovery rate remained at 28%, and the recovery time exceeded 24 hours. Even in ionic network systems, Fe 3 - Re-bonding at the damaged site was limited due to insufficient terpyridine complex concentration. In the measurement of adhesive strength, it decreased significantly from 2.8 MPa before damage to 1.1 MPa after restoration.

[0196] At a thickness of 5 μm, which is the lower limit of the claim, the microcapsule density is 6.8 x 10⁻⁶ 5 Pieces / cm 3Self-healing performance was improved as it increased. For the same scratch damage, the recovery rate reached 68%, and the recovery time was reduced to 8 hours. In the case of the ionic network, the re-bonding speed of the damaged area was improved by increasing the metal ion concentration, achieving 75% recovery within 4 hours. After recovery, the adhesive strength recovered to 89% of the original strength, reaching a practical level.

[0197] At a thickness of 12 μm, which is the optimal value within the claimed scope, the microcapsule density is 1.4 x 10⁻⁶ 6 Pieces / cm 3 It demonstrated excellent self-healing performance. The scratch repair rate reached 91%, and the repair time was significantly reduced to 2 hours. It maintained a repair rate of over 85% even for large damage up to 100 μm in width. The ionic network system achieved 94% repair within 1.5 hours, demonstrating performance superior to the microcapsule system. It also maintained over 92% of its initial performance in 10 repeated damage-repair tests.

[0198] At the upper limit of the claimed thickness of 20 μm, further improvement in self-healing performance was limited, but the mechanical strength of the coating itself increased excessively. Although the recovery rate improved slightly to 93%, the crack resistance of the coating decreased, leading to a problem where new cracks occurred during bending deformation. Due to the excessive density of microcapsules, interference between capsules occurred, resulting in reduced recovery uniformity.

[0199] At a thickness of 30 μm, which exceeds the claimed scope, cumulative errors occurred in the overall dimensions of the module due to the excessive thickness of the coating. Although the self-healing performance reached a saturation state and showed no further improvement, spontaneous cracking was observed due to internal stress within the coating. Due to the excessive concentration of microcapsules, the continuity of the base matrix was compromised, resulting in a decrease in overall adhesive strength.

[0200] In the evaluation of repair performance by damage size, a thickness of 5 μm was effective only for micro-damage with a width of 30 μm or less, while a thickness of 12 μm maintained a repair rate of over 80% for damage up to 150 μm in width. Further improvement in the ability to repair large damage was limited for 20 μm or more.

[0201] In the evaluation under different temperature conditions, at a low temperature of 5°C, the recovery time was extended threefold compared to room temperature due to the increased resin viscosity of the microcapsules, but at a thickness of 12 μm or more, it was limited to within twofold due to the sufficient amount of resin. At a high temperature of 60°C, the recovery time was shortened due to the increased dissociation rate of the ionic network, but permanent crosslinking loss occurred at excessive temperatures.

[0202] Under UV exposure conditions, the self-healing function of a 5 μm thickness decreased to less than 50% after 100 hours of exposure, whereas a thickness of 12 μm or more maintained over 80% of its function even after 300 hours. This indicates that a sufficient film thickness effectively protects the internal capsule and ion complex from UV rays.

[0203] Under mechanical stress conditions, cracks occurred immediately at a tensile strength of 5 MPa with a thickness of 5 μm, but with a thickness of 12 μm or more, it could withstand up to 15 MPa. In the repeated bending test as well, a thickness of 12 μm showed the optimal balance point, ensuring both flexibility and strength simultaneously.

[0204] Experimental Example 4

[0205] To evaluate the effect of the content of each component of the biomimetic hydrogel on adhesive performance and environmental adaptability, performance was compared within and outside the range based on the composition of Example 3. Adhesive strength and swelling characteristics were measured under various humidity conditions.

[0206] At a chitosan content of 6 wt% (less than the claimed range), the adhesive strength remained at 0.8 MPa under 50% relative humidity conditions, and the mechanical strength of the hydrogel was insufficient, resulting in shape collapse upon compression. The swelling rate reached 850% at 90% relative humidity, exhibiting dimensional instability due to excessive volume change. The formation of the polyionic complex with alginate was incomplete, leading to a decrease in the homogeneity of the gel structure.

[0207] At a chitosan content of 8 wt% (lower limit of the claim), the adhesive strength was improved to 1.4 MPa, and the compressive strength of the hydrogel reached 0.15 MPa, ensuring shape stability. The swelling rate decreased to 620% at 90% humidity, exhibiting more stable dimensional changes. The increased cation density of chitosan strengthened electrostatic interactions with the metal surface, thereby improving adhesive performance.

[0208] At a chitosan content of 12 wt% (optimal value within the claimed range), the adhesive strength was maximized to 2.6 MPa, and stable performance was maintained under various humidity conditions. The swelling rate varied within an appropriate range, ranging from 180% at 30% humidity to 450% at 90% humidity, demonstrating excellent environmental adaptability. The compressive strength reached 0.28 MPa, ensuring structural stability.

[0209] At a chitosan content of 18 wt% (exceeding the claimed scope), the excessive cation density led to excessive interaction with alginate, causing the gel structure to become over-cured. The adhesive strength actually decreased to 2.3 MPa, and the swelling rate was limited to 280% at 90% humidity, resulting in reduced adaptability to changes in humidity. The brittleness of the gel increased, causing cracks to occur during repeated deformation.

[0210] At a sodium alginate content of 3 wt% (less than the claimed range), the formation of a complex with chitosan was insufficient, resulting in significantly insufficient gel strength. The adhesive strength was only 0.6 MPa, and long-term stability was problematic due to the dissociation of the gel structure under moist conditions. Even when using alginate with a high G / M ratio, the crosslinking density was limited due to the absolute lack of quantity.

[0211] At a sodium alginate content of 5 wt% (lower limit of the claim), the balance with chitosan was improved, and the adhesive strength was enhanced to 1.2 MPa. The stability of the gel structure was ensured, maintaining structural integrity even during repeated swelling-shrinkage processes. However, excessive swelling was still observed under high humidity conditions.

[0212] At a sodium alginate content of 10 wt% (optimal value within the claimed range), stoichiometric balance with chitosan was achieved, forming an optimal polyionic composite. Adhesion strength reached 2.4 MPa, and swelling behavior was controlled within a predictable range. Interaction with the calcium chloride crosslinking agent was also optimized, resulting in a balance between gel strength and flexibility.

[0213] At a sodium alginate content of 15 wt% (exceeding the claim), the complex with chitosan became excessively dense due to the excessive anion density, which restricted the accessibility of L-DOPA. The adhesive strength decreased to 1.9 MPa, and the brittleness of the gel increased, making it vulnerable to mechanical impact.

[0214] At an L-DOPA content of 0.3 wt% (less than the claimed range), the core adhesion mechanism of the mussel byssus protein was not sufficiently expressed. The chelation effect with the metal surface was limited, so the adhesion strength under wet conditions decreased to 65% compared to dry conditions. The conversion rate to dopaquinone under oxidizing conditions also remained at 28%.

[0215] Excellent adhesive performance was exhibited at an L-DOPA content of 2 wt% (upper limit of the claim), but self-polymerization occurred due to excessive DOPA, forming heterogeneous regions within the gel. Discoloration and performance degradation due to the spontaneous oxidation of DOPA were observed during long-term storage.

[0216] In the evaluation under different temperature conditions, at a low temperature of 5°C, freeze-thaw damage to the gel structure occurred at a chitosan content of less than 8%, but sufficient structural stability was maintained at 12% or more. At a high temperature of 40°C, the decrease in gel strength was accelerated at a content exceeding 15% due to the thermal decomposition of alginate.

[0217] In terms of stability under pH conditions, the complex structure became unstable at pH 4 or lower due to excessive protonation of chitosan, but stable performance was maintained in the pH range of 4.5 to 7.5 at an appropriate composition ratio. At pH 8 or higher, the adhesive strength gradually decreased due to de-protonation of chitosan.

[0218] Experimental Example 5

[0219] To evaluate the effect of phase change material microcapsule content on thermal performance and mechanical properties, performance was measured at various content levels within and outside the claimed range based on Example 4. Thermal properties were quantified through differential scanning calorimetry and thermal conductivity measurements.

[0220] At a PCM microcapsule content of 10 wt% (less than the claimed range), the latent heat storage was only 18 J / g, so the temperature control effect was limited. When the temperature rose from 28 to 30 degrees, the temperature buffering effect remained at 0.8 degrees, and the duration was short at 15 minutes. It did not affect the compression characteristics of the crusher-sham layer, maintaining a crushing rate of 22%, but the thermal function was practically negligible. The thermal conductivity improved by only 5% compared to the pure matrix.

[0221] At a PCM microcapsule content of 15 wt% (lower limit of the claim), the latent heat storage was improved to 32 J / g, and a practical temperature control effect began to appear. Under the same temperature rise conditions, the temperature buffering effect was improved to 1.8 degrees, and the duration was extended to 35 minutes. Compressive strength decreased by 8% compared to the pure matrix but still satisfied structural requirements. Thermal conductivity was improved by 12%, improving heat exchange efficiency.

[0222] At a PCM microcapsule content of 20 wt% (midpoint within the claims), the latent heat storage reached 48 J / g, demonstrating excellent temperature control performance. The temperature buffering effect was optimized to 2.6°C, and the duration was extended to 55 minutes, ensuring practical thermal management capabilities. The reduction in compressive strength was limited to 15%, achieving a balance between structural and thermal functions. Thermal conductivity was improved by 28% due to a synergistic effect with boron nitride nanosheets.

[0223] At a PCM microcapsule content of 25 wt% (upper limit of the claim), the latent heat storage was maximized to 58 J / g, but the deterioration of mechanical properties began to accelerate. Although the temperature buffering effect was further improved to 3.1 degrees, the compressive strength decreased by 28% compared to the original, raising concerns about structural stability. Due to the excessive density of microcapsules, the continuity of the binder matrix was compromised, and the homogeneity of the crusher-sam layer was reduced.

[0224] At a PCM microcapsule content of 35 wt% (exceeding the claimed scope), the latent heat storage reached 68 J / g, but a severe deterioration in mechanical properties was observed. Compressive strength decreased by 45%, posing a risk of loss of structural function, and premature rupture occurred due to contact between microcapsules. Due to insufficient binder content, the fixation of the capsules became unstable, and capsule detachment was observed under vibration conditions.

[0225] At a boron nitride nanosheet content of 1 wt% (less than the claimed range), the improvement in thermal conductivity was only 8%, which limited the improvement in the heat exchange rate of the PCM. The phase transition time was extended to 12 minutes, resulting in a lack of ability to respond to rapid temperature changes. The low dispersion density of the nanosheets resulted in incomplete formation of the heat conduction pathway.

[0226] At a boron nitride nanosheet content of 3 wt% (midpoint within the claims), the thermal conductivity was improved by 25%, significantly improving the heat exchange efficiency of the PCM. The phase transition time was shortened to 6 minutes, enabling a rapid response to temperature changes. A continuous thermal conduction network was formed through the appropriate dispersion of the nanosheets.

[0227] At a boron nitride nanosheet content of 6 wt% (exceeding the claim scope), thermal conductivity improved by 42%, but heterogeneity due to nanosheet aggregation began to appear. Due to the excessive nanosheets, interfacial adhesion with the binder was reduced, affecting mechanical properties. In addition, manufacturing costs increased rapidly, making economic feasibility an issue.

[0228] In the temperature cycle test, excellent durability was observed with a PCM content of less than 15%, with performance degradation within 5% even after 100 cycles; however, at 25% or higher, performance degradation due to capsule rupture accelerated starting from 50 cycles. At a content of 20%, optimal durability was demonstrated by maintaining more than 90% of the initial performance even after 200 cycles.

[0229] In the evaluation under different humidity conditions, the walls of the PCM capsules absorbed moisture in a high-humidity environment (85% RH), which reduced the encapsulation efficiency. At a 15% content, the encapsulation rate remained at 88% even after 1,000 hours of humidity exposure, but at 25% or higher, it decreased to 85% or less.

[0230] In a vibrating environment, the damping effect improved with increasing PCM content, resulting in a decrease in vibration transmission rate. Optimal damping performance was achieved at a content of 20%, reducing the vibration transmission rate to 15%; however, at 25% or higher, excessive damping affected the precision during module assembly.

[0231] In the fire safety evaluation, an increase in PCM content meant an increase in flammability. At a content of 15%, the ignition temperature was maintained at 240 degrees, but at 25% or higher, it dropped to 220 degrees, raising concerns about fire safety. Although improvement was possible through the addition of flame retardants, it had a negative impact on thermal performance.

[0232] Experimental Example 6

[0233] To evaluate the effectiveness of the renormalization method (measurement-replenishment-curing-verification) of the present invention against existing methods, restoration performance was compared using disassembled modules. The modules of Example 1-2 were renormalized using different methods after being assembled and disassembled 20 times.

[0234] In the existing method 1 (full surface recoating), the existing sacrificial dimension layer of the disassembled module was completely removed, and a new layer was applied to the entire surface. The removal process took an average of 25 minutes per module, and mechanical polishing resulted in a roughness of Ra 2.8 μm on the surface of the module body. An additional 15 minutes were required to apply the new sacrificial dimension layer, bringing the total restandardization time to 40 minutes. The dimensional accuracy of the restandardized module was 88% compared to a new one, and the adhesion performance decreased by 12% due to increased surface roughness.

[0235] In the existing method 2 (partial repair), only visually inspectable damaged areas were selectively repaired. Although the work time was reduced to 8 minutes, early performance degradation occurred after reuse due to the omission of micro-damaged areas. After 10 reuses, the tolerance absorption performance decreased by 35% compared to the initial level, and the leakage rate increased to 0.15 ml / min·m, failing to satisfy the airtightness requirements.

[0236] In the renormalization method of the present invention, the entire joint surface was first scanned using laser triangulation during the measurement step. The measurement of a 200mm x 200mm joint surface was completed in 18 seconds, and deficiencies of 0.02mm or more were automatically identified. In the disassembled module, deficiencies were found at an average of 32 points, and the amount of deficiency ranged from 0.025mm to 0.088mm.

[0237] In the replenishment step, sacrificial dimensional layer material was selectively replenished only in the identified areas. Replenishment was performed using an airless spray method with an accuracy of within ±8 μm, and the replenishment time was 4 minutes per module. To ensure interfacial adhesion with the existing layer, partial dissolution using a solvent was applied for 30 seconds, followed by the application of the replenishment material.

[0238] The curing step was completed with 90 seconds of UV irradiation, and over 95% curing was confirmed by monitoring the real-time degree of curing using infrared spectroscopy. During the curing process, the temperature rise was limited to 25 degrees or less to prevent deterioration of the existing layer.

[0239] In the verification phase, quality was confirmed through dimensional measurements and adhesive strength tests. The dimensional accuracy of the restandardized module reached 96% compared to a new product, and the surface roughness maintained excellent quality with Ra 1.2μm. The adhesive strength recovered to 94% of that of a new product, ensuring practical performance.

[0240] The total restandardization time was 6 minutes and 33 seconds, consisting of 18 seconds for measurement, 4 minutes for replenishment, 90 seconds for curing, and 45 seconds for verification. This represented an 83% reduction in time compared to the conventional full-surface recoating method. Material usage was also significantly reduced to approximately 25% of that used for full-surface application.

[0241] In the performance evaluation, the restandardized module maintained stable performance over 50 additional assembly-disassembly cycles. The tolerance absorption rate showed only a decrease of less than 5% compared to the initial level, and the airtightness also maintained an excellent level with a leakage rate of 0.06 ml / min·m. On the other hand, the module restandardized using the conventional method showed accelerated performance degradation starting from the 20th cycle.

[0242] In the precision analysis, the method of the present invention achieved a supplementary position accuracy of ±12μm and a supplementary thickness accuracy of ±6μm, demonstrating significantly improved precision compared to the existing manual-based method's ±50μm and ±25μm, respectively. This was attributed to the effectiveness of the automated measurement and control system.

[0243] Even considering the initial equipment investment costs in the economic analysis, the break-even point was reached at the 100th re-standardization due to improved module reuse rates and material cost savings. Based on 1,000 cycles, a 60% cost reduction effect compared to the existing method was confirmed.

[0244] Unlike conventional manual methods, which have large variations depending on skill level in terms of quality consistency, the method of the present invention maintained consistent quality regardless of the worker. As a result of 10 workers each re-standardizing 10 modules, the quality variation was significantly improved to within ±3% compared to ±15% of the conventional method.

[0245] In terms of performance under various environmental conditions, stable restandardization was possible within a temperature range of 5 to 35 degrees and a relative humidity range of 40% to 70%. Under extreme conditions, quality could be maintained by adjusting the curing time, whereas the existing method showed significant quality variations depending on environmental conditions.

[0246] In a long-term follow-up study, even after one year had passed since restandardization, the module processed by the method of the present invention maintained 92% of its initial performance, whereas the existing method dropped to 78%, confirming its superiority in long-term reliability.

[0247] Experimental Example 7

[0248] The synergistic effect of a module system integrating a biomimetic hydrogel and a PCM system was evaluated compared to the application of each system alone. The integrated system combining Example 3-3 and Example 4-2 was compared with each individual system under the same conditions.

[0249] In the system with a sacrificial dimensional layer alone (Examples 1-2), an adhesive strength of 2.1 MPa and a tolerance absorption rate of 89% were observed under conditions of 50% relative humidity. When the temperature changed from 25°C to 35°C, the adhesive strength decreased by 14% to 1.8 MPa, and further decreased to 1.5 MPa under conditions of 85% relative humidity. The dimensional change due to thermal expansion was 0.12 mm, and an additional compressive force of 1.8 kN was required to absorb it.

[0250] In the biomimetic hydrogel-only system (Example 3-3), humidity adaptability was significantly improved, maintaining an adhesive strength of 2.3 MPa even under conditions of 85% relative humidity. Airtightness was improved due to the self-sealing effect caused by the swelling of the chitosan-alginate complex, reducing the leakage rate to 0.04 ml / min·m. However, the response to temperature changes was limited, and dimensional stability was reduced due to excessive swelling of the hydrogel at 35 degrees.

[0251] In the PCM system alone (Example 4-2), excellent dimensional stability was exhibited in the range of 28 to 30 degrees due to the temperature control function. The temperature rise was buffered by 2.1 degrees due to the absorption of latent heat of phase change, and the dimensional change due to thermal expansion was reduced to 0.05 mm. The time to reach thermal equilibrium was shortened to 8 minutes due to the improved thermal conductivity of the boron nitride nanosheets. However, adaptability to changes in humidity remained at a level equivalent to the basic system.

[0252] In the integrated system, the advantages of each system were combined to produce a synergistic effect. Under combined environmental conditions of 85% relative humidity and 35 degrees Celsius, the adhesive strength reached 2.6 MPa, which is 13% to 25% higher than that of a single system. The combination of the humidity adaptability of the biomimetic hydrogel and the temperature buffering effect of the PCM ensured a comprehensive response capability to environmental changes.

[0253] In terms of airtightness, the integrated system achieved a leakage rate of 0.025 ml / min·m, which is a 40% to 60% improvement compared to a single system. The swelling-based sealing of the hydrogel and the temperature stabilization of the PCM worked complementarily to maintain constant airtightness under various environmental conditions.

[0254] In terms of dimensional stability, dimensional change was limited to within ±0.03 mm in the temperature range of 25 to 40 degrees and relative humidity range of 30% to 90%, which is a significant improvement compared to ±0.08 mm of a single system. The temperature buffering of the PCM and the humidity adaptation of the hydrogel acted simultaneously to effectively relieve stress caused by environmental changes.

[0255] In the durability evaluation, the integrated system maintained 94% of its initial performance even after 100 assembly-disassembly cycles, demonstrating superior durability compared to 82% for the sacrificial dimension layer alone, 87% for the hydrogel alone, and 89% for the PCM alone. It was analyzed that each system performed a mutual protective role, delaying the degradation of individual components.

[0256] In terms of energy efficiency, modular buildings equipped with an integrated system saw a 12% reduction in annual heating and cooling energy consumption compared to the basic system. The combination of the heat storage effect of the PCM and the humidity control effect of the hydrogel improved the stability of the indoor environment, and the resulting reduction in the load of the HVAC system was analyzed as the main cause.

[0257] In terms of self-healing performance, the recovery rate of the integrated system reached 96%, which is a significant improvement compared to 78% of the basic system. It was determined that the moisture supply of the hydrogel and the temperature control of the PCM promoted the rupture of microcapsules and the recombination of the ionic network of the self-healing primer.

[0258] In the analysis of manufacturing complexity and costs, the integrated system increased the manufacturing process by 15% compared to a single system, but the cost-effectiveness was excellent considering the performance improvement. Due to process optimization resulting from the simultaneous application of biomimetic hydrogel and PCM systems, the increase in manufacturing time was more limited than expected.

[0259] In the analysis of synergistic effects by environmental conditions, the synergistic effect was limited to 8% in a general indoor environment (temperature 22°C, relative humidity 45%), but a significant synergistic effect of 25% to 40% was observed in extreme environments (temperature 5°C to 40°C, relative humidity 20% to 95%). This meant that the greater the range of change in the environmental factors handled by each system, the more the complementary effect is maximized.

[0260] In long-term stability tests, the integrated system maintained 88% of its initial performance even after two years of outdoor exposure testing, confirming superior long-term stability compared to 75% to 82% of single systems. Resistance to complex environmental stresses, such as UV radiation, changes in temperature and humidity, and exposure to pollutants, was enhanced due to the mutual protective effects of each system.

[0261] Experimental Example 8

[0262] To evaluate the performance stability of a modular housing module system under various environmental conditions, long-term performance changes were measured under complex environmental conditions such as temperature, humidity, ultraviolet rays, and vibration for an integrated system combining Example 3-3 and Example 4-2.

[0263] In the evaluation under different temperature conditions, at a cryogenic temperature of -20°C, the adhesive strength decreased by 35% during the first 24 hours due to freezing of the biomimetic hydrogel, but recovered to 95% after thawing. The thermal storage function of the PCM system was temporarily suspended due to the solidification of n-octadecane, but no structural damage occurred. The crushing characteristics of the crusher-sam layer required a 20% increased load at low temperatures, but the crushing rate remained the same.

[0264] Under high temperature conditions of 60°C, the thermal storage effect was saturated due to the complete liquefaction of the PCM; however, no capsule rupture was observed due to the excellent heat resistance of the melamine-urea-formaldehyde capsule wall. Although the thickness of the biomimetic hydrogel increased by 130% due to excessive swelling, no shape collapse occurred due to the structural stability of the polyionic composite. The ionic network of the self-healing primer showed an increased dissociation rate at high temperatures, reducing the recovery time from 30 minutes to 8 minutes.

[0265] In the temperature cycle test (-10°C <-> 40°C, 24-hour cycle), the adhesive strength of the sacrificial dimension layer decreased by only 8% compared to the initial value after 200 cycles. Due to the flexibility of the urethane-acrylic hybrid resin, thermal expansion and contraction stresses were effectively absorbed. The PCM microcapsules demonstrated excellent durability by maintaining an encapsulation rate of 92% even with repeated phase changes.

[0266] In the evaluation under different humidity conditions, the biomimetic hydrogel reached a swelling rate of 580% in an environment of 95% relative humidity, demonstrating maximum performance. Due to the self-sealing effect caused by the moisture absorption of the chitosan-alginate complex, airtightness was improved to a leakage rate of 0.018 ml / min·m. On the other hand, under extremely dry conditions of 15% relative humidity, the hydrogel shrank excessively, causing surface cracks in some areas, but these were restored within 6 hours by a self-healing primer.

[0267] In the humidity cycle test (30% <-> 85% RH, 12-hour cycle), there was no change in the swelling-shrinkage characteristics of the hydrogel even after 100 cycles, and the adhesive performance also maintained the initial level. The wet adhesive characteristics of the L-DOPA-containing mussel byssus protein analog were stably expressed even under repeated changes in humidity.

[0268] UV exposure test (UV-A 340nm, illuminance 0.89 W / m² 2 After 1,000 hours of exposure to (·nm), the color change △E value of the sacrificial layer was 2.1, which was a level that was almost imperceptible to the eye. Due to the effect of the UV stabilizer added to the urethane-acrylic resin, the degradation of mechanical properties was limited to within 5%. Although the L-DOPA component of the biomimetic hydrogel was accelerated by UV oxidation, the performance degradation remained at 12% due to the protective effect of chitosan and alginate.

[0269] In a salt environment test (3.5% NaCl spray, 35°C), all components exhibited excellent salt resistance after 720 hours of exposure. No corrosion was observed in the aluminum module body due to the protection of the anodic oxide film, and the sacrificial layer also showed no change in performance due to salt penetration. The biomimetic hydrogel's adhesive strength actually improved by 8% as the polyionic composite became more stabilized due to the increase in ionic strength caused by salt.

[0270] The damping performance of the crusher-sham layer was confirmed in vibration environment tests (frequency 5 Hz to 200 Hz, acceleration 1 g). Due to the combined effect of PCM microcapsules and boron nitride nanosheets, the vibration transmission rate was reduced by 32% compared to the basic system. In the area where the honeycomb structure was applied, resonance was observed at specific frequencies (45 Hz, 120 Hz), but no structural damage occurred.

[0271] In the evaluation under different loading conditions, the permanent deformation of the crusher-sham layer was only 8% even after being held for 24 hours under a compressive load of 5 MPa (2.5 times the design load). Stress relief was effectively achieved due to the progressive crushing of the microballoons, and the elastic recovery rate after load removal was 87%. Under a shear load of 2 MPa, the interlayer adhesion between the sacrificial dimension layer and the hydrogel was excellent, so no delamination was observed.

[0272] In a combined environmental stress test (simultaneous application of temperature 40°C, humidity 85%, UV irradiation, and vibration of 50Hz), the overall performance degradation after 500 hours of exposure was found to be 18%. This is lower than the expected value of 28%, which is the sum of the individual effects of each environmental factor, confirming that the complementary effects of the integrated system are effective even under combined stress conditions.

[0273] In a regional climate condition simulation test, an accelerated test (1 year -> 2 months) was conducted using annual climate data based on Seoul, Korea. As a result of repeatedly applying low-temperature, dry winter and high-temperature, high-humidity summer conditions, the system performance remained at a 7% decrease compared to the initial level, confirming excellent climate adaptability.

[0274] In the fire safety evaluation, the ignition temperature measurement results showed that the PCM-containing system was 235 degrees and the non-PCM-containing system was 250 degrees; however, in the actual fire spread test, the temperature rise was delayed due to the absorption of the latent heat of phase change by the PCM, which was found to be advantageous for securing evacuation time.

[0275] As a result of measuring the impact of all constituent materials on indoor air quality in the eco-friendliness assessment, the formaldehyde emission was 0.02 mg / m³ 3 ,Total volatile organic compounds 0.08 mg / m² 3 It satisfied the eco-friendly building material standards.

[0276] In the economic analysis, the total cost of ownership over a 20-year usage period was analyzed. Although the initial investment cost increased by 15% compared to the existing system, the break-even point was reached at the 8-year mark due to energy savings and reduced maintenance costs.

[0277] Although embodiments of the present invention have been described in detail above, the scope of the present invention is not limited thereto, and it will be obvious to those skilled in the art that various modifications and variations are possible within the scope of the technical concept of the present invention as described in the claims.

Claims

Claim 1 A modular housing modular system comprising a module body; a sacrificial dimension layer; a crusher-sam layer; a self-healing primer; and a refill-release gasket, wherein the module body has a bonding surface including a rail, a cam lock, and a shear key. Claim 2 delete Claim 3 A modular housing module system according to claim 1, wherein the sacrificial dimension layer is applied to the bonding surface of the module body. Claim 4 In paragraph 3, the sacrificial dimension layer comprises a urethane-acrylic hybrid resin or Diels-Alder resin, for a modular housing module system. Claim 5 delete Claim 6 delete

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