The WLC model envisions a continuously flexible isotropic rod.^[1][2][3] This is in contrast to the freely-jointed chain model, which is only flexible between discrete freely hinged segments. The model is particularly suited for describing stiffer polymers, with successive segments displaying a sort of cooperativity: nearby segments are roughly aligned. At room temperature, the polymer adopts a smoothly curved conformation; at ${\displaystyle T=0}$  K, the polymer adopts a rigid rod conformation.^[1]

For a polymer of maximum length ${\displaystyle L_{0}}$ , parametrize the path of the polymer as ${\displaystyle s\in (0,L_{0})}$ . Allow ${\displaystyle {\hat {t}}(s)}$  to be the unit tangent vector to the chain at point ${\displaystyle s}$ , and ${\displaystyle {\vec {r}}(s)}$  to be the position vector along the chain, as shown to the right. Then:

${\displaystyle {\hat {t}}(s)\equiv {\frac {\partial {\vec {r}}(s)}{\partial s}}}$  and the end-to-end distance ${\displaystyle {\vec {R}}=\int _{0}^{L_{0}}{\hat {t}}(s)ds}$  .^[1]

The energy associated with the bending of the polymer can be written as:

${\displaystyle E={\frac {1}{2}}k_{B}T\int _{0}^{L_{0}}P\cdot \left({\frac {\partial ^{2}{\vec {r}}(s)}{\partial s^{2}}}\right)^{2}ds}$ 

where ${\displaystyle P}$  is the polymer's characteristic persistence length, ${\displaystyle k_{B}}$  is the Boltzmann constant, and ${\displaystyle T}$  is the absolute temperature. At finite temperatures, the end-to end distance of the polymer will be significantly shorter than the maximum length ${\displaystyle L_{0}}$ . This is caused by thermal fluctuations, which result in a coiled, random configuration of the undisturbed polymer.

The polymer's orientation correlation function can then be solved for, and it follows an exponential decay with decay constant 1/P:^[1][3]

${\displaystyle \langle {\hat {t}}(s)\cdot {\hat {t}}(0)\rangle =\langle \cos \;\theta (s)\rangle =e^{-s/P}\,}$ 

A useful value is the mean square end-to-end distance of the polymer:^[1][3]

${\displaystyle \langle R^{2}\rangle =\langle {\vec {R}}\cdot {\vec {R}}\rangle =\left\langle \int _{0}^{L_{0}}{\hat {t}}(s)ds\cdot \int _{0}^{L_{0}}{\hat {t}}(s')ds'\right\rangle =\int _{0}^{L_{0}}ds\int _{0}^{L_{0}}\langle {\hat {t}}(s)\cdot {\hat {t}}(s')\rangle ds'=\int _{0}^{L_{0}}ds\int _{0}^{L_{0}}e^{-\left|s-s'\right|/P}ds'}$ 

${\displaystyle \langle R^{2}\rangle =2PL_{0}\left[1-{\frac {P}{L_{0}}}\left(1-e^{-L_{0}/P}\right)\right]}$ 

Note that in the limit of ${\displaystyle L_{0}\gg P}$ , then ${\displaystyle \langle R^{2}\rangle =2PL_{0}}$ . This can be used to show that a Kuhn segment is equal to twice the persistence length of a worm-like chain. In the limit of ${\displaystyle L_{0}\ll P}$ , then ${\displaystyle \langle R^{2}\rangle =L_{0}^{2}}$ , and the polymer displays rigid rod behavior.^[2] The figure to the right shows the crossover from flexible to stiff behavior as the persistence length increases.

Experimental data from the stretching of Lambda phage DNA is shown to the right, with force measurements determined by analysis of Brownian fluctuations of a bead attached to the DNA. A persistence length of 51.35 nm and a contour length of 1560.9 nm were used for the model, which is depicted by the solid line.^[4]

Other biologically important polymers that can be effectively modeled as worm-like chains include:

• double-stranded DNA (persistence length 40-50 nm) and RNA (persistence length 64 nm)^[3][5]
• single-stranded DNA (persistence length 4 nm) ^[6]
• unstructured RNA (persistence length 2 nm) ^[7]
• unstructured proteins (persistence length 0.6-0.7 nm)^[8]
• microtubules (persistence length 0.52 cm) ^[9]
• filamentous bacteriophage^[10]

Upon stretching, the accessible spectrum of thermal fluctuations reduces, which causes an entropic force acting against the external elongation. This entropic force can be estimated from considering the total energy of the polymer:

${\displaystyle H=H_{\rm {elastic}}+H_{\rm {external}}={\frac {1}{2}}k_{B}T\int _{0}^{L_{0}}P\cdot \left({\frac {\partial ^{2}{\vec {r}}(s)}{\partial s^{2}}}\right)^{2}ds-xF}$ .

Here, the contour length is represented by ${\displaystyle L_{0}}$ , the persistence length by ${\displaystyle P}$ , the extension is represented by ${\displaystyle x}$ , and external force is represented by ${\displaystyle F}$ .

Laboratory tools such as atomic force microscopy (AFM) and optical tweezers have been used to characterize the force-dependent stretching behavior of biological polymers. An interpolation formula that approximates the force-extension behavior with about 15% relative error is:^[11]

${\displaystyle {\frac {FP}{k_{B}T}}={\frac {1}{4}}\left(1-{\frac {x}{L_{0}}}\right)^{-2}-{\frac {1}{4}}+{\frac {x}{L_{0}}}}$ 

A more accurate approximation for the force-extension behavior with about 0.01% relative error is:^[4]

${\displaystyle {\frac {FP}{k_{B}T}}={\frac {1}{4}}\left(1-{\frac {x}{L_{0}}}\right)^{-2}-{\frac {1}{4}}+{\frac {x}{L_{0}}}+\sum _{i=2}^{i=7}\alpha _{i}\left({\frac {x}{L_{0}}}\right)^{i}}$ ,

with ${\displaystyle \alpha _{2}=-0.5164228}$ , ${\displaystyle \alpha _{3}=-2.737418}$ , ${\displaystyle \alpha _{4}=16.07497}$ , ${\displaystyle \alpha _{5}=-38.87607}$ , ${\displaystyle \alpha _{6}=39.49944}$ , ${\displaystyle \alpha _{7}=-14.17718}$ .

A simple and accurate approximation for the force-extension behavior with about 1% relative error is:^[12]

${\displaystyle {\frac {FP}{k_{B}T}}={\frac {1}{4}}\left(1-{\frac {x}{L_{0}}}\right)^{-2}-{\frac {1}{4}}+{\frac {x}{L_{0}}}-0.8\left({\frac {x}{L_{0}}}\right)^{2.15}}$ 

Approximation for the extension-force behavior with about 1% relative error was also reported:^[12]

${\displaystyle {\frac {x}{L_{0}}}={\frac {4}{3}}-{\frac {4}{3{\sqrt {{\frac {FP}{k_{B}T}}+1}}}}-{\frac {10e^{\sqrt[{4}]{900{\frac {k_{B}T}{FP}}}}}{{\sqrt {\frac {FP}{k_{B}T}}}\left(e^{\sqrt[{4}]{900{\frac {k_{B}T}{FP}}}}-1\right)^{2}}}+{\frac {\left({\frac {FP}{k_{B}T}}\right)^{1.62}}{3.55+3.8\left({\frac {FP}{k_{B}T}}\right)^{2.2}}}}$ 

The elastic response from extension cannot be neglected: polymers elongate due to external forces. This enthalpic compliance is accounted for the material parameter ${\displaystyle K_{0}}$ , and the system yields the following Hamiltonian for significantly extended polymers:

${\displaystyle H=H_{\rm {elastic}}+H_{\rm {enthalpic}}+H_{\rm {external}}={\frac {1}{2}}k_{B}T\int _{0}^{L_{0}}P\cdot \left({\frac {\partial ^{2}{\vec {r}}(s)}{\partial s^{2}}}\right)^{2}ds+{\frac {1}{2}}{\frac {K_{0}}{L_{0}}}x^{2}-xF}$ ,

This expression contains both the entropic term, which describes changes in the polymer conformation, and the enthalpic term, which describes the stretching of the polymer due to the external force. Several approximations for the force-extension behavior have been put forward, depending on the applied external force. These approximations are made for stretching DNA in physiological conditions (near neutral pH, ionic strength approximately 100 mM, room temperature), with stretch modulus around 1000 pN.^[13][14]

For the low-force regime (F < about 10 pN), the following interpolation formula was derived:^[15]

${\displaystyle {\frac {FP}{k_{B}T}}={\frac {1}{4}}\left(1-{\frac {x}{L_{0}}}+{\frac {F}{K_{0}}}\right)^{-2}-{\frac {1}{4}}+{\frac {x}{L_{0}}}-{\frac {F}{K_{0}}}}$ .

For the higher-force regime, where the polymer is significantly extended, the following approximation is valid:^[16]

${\displaystyle x=L_{0}\left(1-{\frac {1}{2}}\left({\frac {k_{B}T}{FP}}\right)^{1/2}+{\frac {F}{K_{0}}}\right)}$ .

As for the case without extension, a more accurate formula was derived:^[4]

${\displaystyle {\frac {FP}{k_{B}T}}={\frac {1}{4}}\left(1-l\right)^{-2}-{\frac {1}{4}}+l+\sum _{i=2}^{i=7}\alpha _{i}\left(l\right)^{i}}$ ,

with ${\displaystyle l={\frac {x}{L_{0}}}-{\frac {F}{K_{0}}}}$ . The ${\displaystyle \alpha _{i}}$  coefficients are the same as the one of the above described formula for the WLC model without elasticity.

Accurate and simple interpolation formulas for the force-extension and extension-force behaviors for the extensible worm-like chain model are:^[12]

${\displaystyle {\frac {FP}{k_{B}T}}={\frac {1}{4}}\left(1-{\frac {x}{L_{0}}}+{\frac {F}{K_{0}}}\right)^{-2}-{\frac {1}{4}}+{\frac {x}{L_{0}}}-{\frac {F}{K_{0}}}-0.8\left({\frac {x}{L_{0}}}-{\frac {F}{K_{0}}}\right)^{2.15}}$ 

${\displaystyle {\frac {x}{L_{0}}}={\frac {4}{3}}-{\frac {4}{3{\sqrt {{\frac {FP}{k_{B}T}}+1}}}}-{\frac {10e^{\sqrt[{4}]{900{\frac {k_{B}T}{FP}}}}}{{\sqrt {\frac {FP}{k_{B}T}}}\left(e^{\sqrt[{4}]{900{\frac {k_{B}T}{FP}}}}-1\right)^{2}}}+{\frac {\left({\frac {FP}{k_{B}T}}\right)^{1.62}}{3.55+3.8\left({\frac {FP}{k_{B}T}}\right)^{2.2}}}+{\frac {F}{K_{0}}}}$ 

• Ideal chain
• Polymer
• Polymer physics

• Kratky, O.; Porod, G. (1949). "Röntgenuntersuchung gelöster Fadenmoleküle". Recueil des Travaux Chimiques des Pays-Bas. 68 (12): 1106–1123. doi:10.1002/recl.19490681203.
• Marko, J. F.; Siggia, E. D. (1995). "Stretching DNA". Macromolecules. 28 (26): 8759–8770. Bibcode:1995MaMol..28.8759M. doi:10.1021/ma00130a008.
• Bustamante, C.; Marko, J. F.; Siggia, E. D.; Smith, S. (1994). "Entropic elasticity of lambda-phage DNA". Science. 265 (5178): 1599–1600. Bibcode:1994Sci...265.1599B. doi:10.1126/science.8079175. PMID 8079175.
• Wang, M. D.; Yin, H.; Landick, R.; Gelles, J.; Block, S. M. (1997). "Stretching DNA with optical tweezers". Biophysical Journal. 72 (3): 1335–1346. Bibcode:1997BpJ....72.1335W. doi:10.1016/S0006-3495(97)78780-0. PMC 1184516. PMID 9138579.
• C. Bouchiat et al., "Estimating the Persistence Length of a Worm-Like Chain Molecule from Force-Extension Measurements", Biophysical Journal, January 1999, p. 409-413, Vol. 76, No. 1