A pre-strain strategy for suppressing interfacial debonding in carbon fiber structural battery composites

doi:10.1007/s10483-025-3296-7

摘要/Abstract

Abstract:

This study proposes a pre-strain optimization strategy for carbon fiber structural lithium-ion battery (SLIB) composites to inhibit the interfacial debonding between carbon fibers and solid-state electrolytes due to fiber lithiation. Through an analytical shear-lag model and finite element simulations, it is demonstrated that applying tensile pre-strain to carbon fibers before electrode assembly effectively reduces the interfacial shear stress, thereby suppressing debonding. However, the excessive pre-strain can induce the interfacial damage in the unlithiated state, necessitating careful control of the pre-strain within a feasible range. This range is influenced by electrode material properties and geometric parameters. Specifically, the electrodes with the higher solid-state electrolyte elastic modulus and larger electrolyte volume fraction exhibit more significant interfacial damage, making pre-strain application increasingly critical. However, these conditions also impose stricter constraints on the feasible pre-strain range. By elucidating the interplay between pre-strain, material properties, and geometric factors, this study provides valuable insights for optimizing the design of carbon fiber SLIBs.

Key words: pre-strain, carbon fiber, interfacial debonding, structural battery composite, mechanically-based design

中图分类号:

O346

. [J]. Applied Mathematics and Mechanics (English Edition), 2025, 46(9): 1699-1714.

Chuanxi HU, Bo LU, Yinhua BAO, Yicheng SONG, Junqian ZHANG. A pre-strain strategy for suppressing interfacial debonding in carbon fiber structural battery composites[J]. Applied Mathematics and Mechanics (English Edition), 2025, 46(9): 1699-1714.

图/表 10

Parameter	Unit	Value	Reference
Diffusion coefficient of lithium $(D)$	m²/s	$6.8 × 10 − 13$	[22]
Initial lithium concentration $(c ini)$	mol/m³	10	[13]
Maximum lithium concentration $(c max)$	mol/m³	11 596	[13]
Universal gas constant $(R)$	J/(mol·K)	8.314	–
Temperature $(T)$	K	300	–
Fiber radius $(a)$	m	$4.5 × 10 − 6$	–
SBE radius in the analytic model $(b)$	m	$9 × 10 − 6$	–
Representative cell length $(L)$	m	$90 × 10 − 6$	–
Longitudinal modulus of fiber $(E z f)$	GPa	294	[23]
Transverse modulus of fiber $(E r f)$	GPa	22	[23]
Shear modulus of fiber $(G r z f)$	GPa	12.5	[23]
Poisson's ratio of fiber $(v r z f, v r θ f)$	–	0.2, 0.2	[23]
Fiber density $(ρ)$	kg/m³	1 850	[13]
Young's modulus of SBE $(E m)$	GPa	0.535	[24]
Poisson's ratio of SBE $(ν m)$	–	0.38	[13]
Longitudinal expansion coefficient $(α z f)$	m³/mol	$8.63 × 10 − 7$	[13]
Critical shear stress $(τ 0, τ c)$	MPa	5	[25]
Critical interfacial shear displacement $(δ c, δ 1)$	mm	$6.8 × 10 − 5$	[17]–[18]
Slope of the elastic ascending branch in the bilinear traction-separation separation law $(K 0)$	MPa/mm	$7.353 × 105$	[17]–[18]
Slope of the damage descending branch in the bilinear traction-separation law $(K 1)$	MPa/mm	$− 8.170 × 104$	[17]–[18]

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