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A dense uniform polymer brush with $\varphi \simeq 1$ must have height $H\simeq N{v}_{0}s$ by polymer-brush volume fraction. The contour bound $H\le Na$ therefore requires $s\le a/v_0$. If $v_0=a^3$, the limit is $s{a}^2\le 1$; beyond it the putative incompressible branch demands chains longer than their polymer contour length. This is a failure of that microscopic packing model. A Kuhn length does not alone determine $v_0$.

The end-to-end vector joins the two ends of a polymer chain. In an isotropic unforced polymer solution, its vector expected value is zero; a useful measure of chain size is its root-mean-square length. For an ideal chain with $N$ independent isotropic steps of length $b$, the cross terms in the square of the step sum have zero expected value, so $R_{\mathrm{rms}}^2=N{b}^2$. For a long Gaussian chain, its radius of gyration obeys $R_g^2=R_{\mathrm{rms}}^2/6$. If $N$ counts chemical repeat units instead of independent Kuhn length segments, the statistical length used in $R_{\mathrm{rms}}^2=N{b}^2$ must be calibrated to that choice of $N$; it is not automatically the physical bond length or the Kuhn length itself.

For a free three-dimensional worm-like chain with contour length $L$ and persistence length ${\ell }_p$, the unit-tangent correlation is $⟨\mathbf{t}(s)\cdot \mathbf{t}(s^{\prime })⟩=e^{-|s-s^{\prime }|/{\ell }_p}$. Since $\mathbf{R}={\int }_0^L\mathbf{t}(s)ds$, integrating this correlation givesFor $L\gg {\ell }_p$, the leading term is $2{\ell }_{p}L$, the ideal chain law with Kuhn length $2{\ell }_p$. For $L\ll {\ell }_p$, a Taylor series gives $⟨R^2⟩=L^2-L^3/(3{\ell }_p)+O(L^4/{\ell }_p^2)$, approaching a rigid rod. This ideal semiflexible-chain model omits long-range excluded volume; sufficiently long dilute chains in a good solvent can cross over to swollen-chain statistics.

Entropic elasticity is a restoring response arising from the reduction of accessible molecular configurations under deformation. For an ideal freely jointed chain, weak extension has free energy $\Delta \mathcal{F}=3k_{B}T{R}^2/(2N{b}^2)$ and spring constant $k=3k_{B}T/(N{b}^2)$. The proportionality to temperature assumes fixed segment geometry; temperature-dependent Kuhn length modifies it.

Let an adsorbed Gaussian chain gain free energy $\mu >0$ per bound monomer. A pulled segment of $n$ Kuhn length steps spanning height $z$ has elastic free energy $3k_{B}T{z}^2/(2n{b}^2)$, giving $F=-(N-n)\mu +3k_{B}T{z}^2/(2n{b}^2)$. Minimizing over $n$ yields $n=(z/b)\sqrt{3k_{B}T/(2\mu )}$ and $F_{\min }=-N\mu +z\sqrt{6k_{B}T\mu }/b$. Its height derivative is the constant peeling force displayed above. The plateau lasts while $0<n<N$ and the Gaussian chain approximation remains valid. In the slab model $F_{\mathrm{ads}}=N{k}_{B}T[(b/\xi {)}^2-ϵb/\xi ]$, optimization gives $\mu =k_{B}T{ϵ}^2/4$ and $f=\sqrt{3/2}ϵk_{B}T/b$.

The Kuhn length is the link length of an equivalent long ideal chain with the same contour length and mean squared end-to-end distance. A three-dimensional worm-like chain satisfies $⟨R^2⟩\sim 2l_{p}L$ for $L\gg l_p$, hence $b_K=2l_p$.

For fixed bond length $b$, fixed forward bond angle $\alpha$, and independently uniform torsion angles, the bond correlations are $⟨{\mathbf{b}}_i\cdot {\mathbf{b}}_{i+s}⟩=b^2{c}^s$. Thus for $N$ bondsFor fixed $|c|<1$ and a sufficiently long chain, divide by contour length $Nb$ and sum the geometric series to obtain the title formula. Positive forward persistence raises the Kuhn length, and negative correlation lowers it relative to $b$. A chemical internal angle is supplementary to the forward-vector angle. The long-chain formula cannot be used uniformly as $c\to 1$ at fixed $N$: the exact chain obeys $R\le Nb$ and hence $l_K\le Nb$, with equality in the rigid-rod limit.

A monomer is a chemical substance whose molecules can undergo polymerization and contribute units to the essential structure of a polymer. A monomer molecule is the individual reactant; its incorporated monomeric unit is the portion identifiable as derived from that reactant. Incorporation can change chemical bonds and release small byproducts, so the unit in the chain need not have the complete molecular formula of the feed molecule. See IUPAC: monomer molecule and IUPAC, A brief guide to polymer terminology: monomeric units.

Three different counts answer three different questions. Monomer molecules describe the feed; monomeric units trace that feed's contributions to the product; a constitutional repeating unit describes the smallest chemical pattern repeating along a regular chain. In Nylon 6,10, two different monomers supply one interior constitutional repeating unit,Its molecular formula is ${\mathrm{C}}_{16}{\mathrm{H}}_{30}{\mathrm{N}}_2{\mathrm{O}}_2$. The diamine feed is ${\mathrm{C}}_6{\mathrm{H}}_{16}{\mathrm{N}}_2$, and the diacid-chloride feed is ${\mathrm{C}}_{10}{\mathrm{H}}_{16}\mathrm{C}{\mathrm{l}}_2{\mathrm{O}}_2$; subtracting two $\mathrm{HCl}$ gives the interior-repeat budget. For a finite linear chain made from $n$ of each reactant, there are $2n-1$ joining connections, hence $2n-1$ formal $\mathrm{HCl}$ eliminations, rather than $2n$. One amine end and one acid-chloride end remain in that ideal unmodified chain. This is a stoichiometry check on the depicted reaction, not a claim that the washed experimental thread retains those ends. The reacting end-group chemistry is documented in Hammond, lecture 5, p. 4; the specified Nylon 6,10 reactant pair is reported in Polymer Day, nylon demonstration.

Ethene shows the reverse counting mismatch. One $\mathrm{C}{\mathrm{H}}_2=\mathrm{C}{\mathrm{H}}_2$ monomer molecule contributes a two-carbon $-\mathrm{C}{\mathrm{H}}_2-\mathrm{C}{\mathrm{H}}_2-$ monomeric unit to ideal linear polyethylene, without a small byproduct in that growth step. But the smallest constitutional repeating unit of its uniform backbone is just $-\mathrm{C}{\mathrm{H}}_2-$: a chain containing $m$ incorporated ethene monomeric units contains $2m$ such interior one-carbon repeats. End groups are additional bookkeeping. The frequently drawn $[-\mathrm{C}{\mathrm{H}}_2-\mathrm{C}{\mathrm{H}}_2-{]}_m$ is useful for tracing the feed, although it is not the smallest constitutional repeat. The minimum-pattern definition is given in IUPAC: constitutional repeating unit; the ethene growth chemistry is described by ^[ref].

A segment of a freely jointed chain or Gaussian chain instead belongs to a statistical model. It can represent many chemical bonds and several constitutional repeating units; its length and the segment count are chosen to describe chain conformation at the intended scale. The three-repeats-per-segment drawing in Figure "From two liquid layers to a Nylon 6,10 thread: monomers, a constitutional repeating unit, and statistical segments" is a deliberately arbitrary coarse-graining example, not a measured Kuhn length. Always state the counting convention before substituting a segment count for a degree of polymerization. This separation lets chemistry track which chemical atoms entered the material while statistical models track how the material bends and extends.

With independently uniform torsion, consecutive forward tangent correlations multiply by $\cos \vartheta$. After $n$ bonds the correlation is $(\cos \vartheta {)}^n$. Matching it to $e^{-nb/{\ell }_p}$ gives the displayed decay length for positive correlation. This discrete orientational definition need not equal half the equivalent Kuhn length exactly.

An inextensible freely jointed chain of $N$ links of Kuhn length $b$ has contour length $L_c=Nb$ and cannot be extended beyond it at any finite force. There is an explicit numerical contradiction in the printed parameters:The discrepancy is present in the original page, not introduced by digitization. To obtain $26\mu \mathrm{m}$ with $186$ links requires $b\simeq 140\mathrm{nm}$; to obtain it with $b=7\mathrm{nm}$ requires $N\simeq 3714$. No single inextensible FJC can satisfy all three stated numbers. The graph's much larger extension is an immediate counterexample to treating the literal $N,b$ as an accurate global fit.

Separately, accepting the graph's nominal $26\mu \mathrm{m}$ contour as an effective low-force model, its continuation to $32.7\mu \mathrm{m}$ is about $26\%$ beyond that contour. An inextensible ideal chain contains orientational entropy only; it excludes stretching of segments, energetic compliance of bonds, changes in helix structure or base pairing, and heterogeneous attachments. An extensible freely jointed chain or a semiflexible-chain model with appropriate energetic terms can describe some departures. Calibration or contour-length assignment can also be wrong. The graph alone does not identify which mechanism contributes, and its displayed moderate forces do not justify assigning a specific high-force DNA structural transition. Arithmetic inconsistency in $Nb$ is not explained away by these physical mechanisms.

At fixed $N$ and $b$, the entropic spring constant is proportional to absolute temperature, because the free-energy penalty for a given loss of conformational entropy is $-T\Delta S$. ThereforeFor the literal printed chain this is $\boxed{1.287\times 10^{-6}\mathrm{N}{\mathrm{m}}^{-1}}$. The same factor multiplies either alternative contour-consistent spring constant from part (d), provided its Kuhn length is held fixed. Real DNA's persistence length, base pairing and solvent interactions can themselves vary with temperature and salt; then $b(T)$ contributes through $k\propto T/b(T{)}^2$ at fixed segment count, or $k\propto T/[L_{c}b(T)]$ if the physical contour is instead held fixed. The simple linear temperature result belongs to the specified ideal-chain model.

Let $b\simeq 2l_p$ be the Kuhn length, $N=L/b$ the number of statistical segments, and $v$ their effective excluded volume. We first assume a good-solvent, strongly confined self-avoiding walk, rather than an ideal chain. A confinement blob contains $g$ links and has diameter $D\sim b{g}^{3/5}$ in the simple $v\sim b^3$ scaling model. Therefore $g\sim (D/b{)}^{5/3}$. Distant blobs cannot freely pass through one another in a narrow tube, so the $N/g$ blobs form an axial string. The de Gennes confinement scaling is consequentlyThe free energy is of order $k_{B}T$ per blob, not the energy of stretching a straight elastic rod.

The role of solvent and chain thickness can be made explicit by a Flory approximation: an axial extension $X$ costs an entropic term $k_{B}T{X}^2/(N{b}^2)$, while the confined number density gives an interaction term $k_{B}Tv{N}^2/(X{D}^2)$. Minimizing their sum gives $X^3\sim v{N}^3{b}^2/D^2$, henceFor a thin statistical segment of effective diameter $d$, $v\sim b^{2}d$ instead gives $X\sim L(bd/D^2{)}^{1/3}$. Thus the simpler answer implicitly fixes the excluded volume; the DNA thickness and ionic environment can matter quantitatively.

Both blob arguments require $b\ll D\ll R_{\mathrm{free}}$ and $N/g\gg 1$, where $R_{\mathrm{free}}\sim b{N}^{3/5}$ in the simple good-solvent model. The printed comparison with $L$ alone does not ensure confinement relative to the unconfined coil. If $D\gg R_{\mathrm{free}}$, the tube barely perturbs the coil. An ideal chain without excluded volume has axial spread of order $\sqrt{Lb}$ and does not acquire the extensive extension of a nonoverlapping blob string. These are distinct physical regimes, not changes to a numerical prefactor.

For a three-dimensional worm-like chain, the tangent correlation length is $l_p=B/(k_{B}T)$, where $B$ is the filament bending modulus. The measured persistence length therefore givesRepresent the actin filament as an isotropic solid circular cylinder with diameter $d=10^{-9}\mathrm{m}$. Its second moment of area is $I=\pi d^4/64=4.909\times 10^{-38}{\mathrm{m}}^4$. Since $B=EI$,This is an effective Young's modulus within the given continuum cross-sectional model; the numerical diameter and persistence length must not be replaced by unrelated typical biological values.

The same measurement corrects the independent-link approximation: the Kuhn length is $b_K=2l_p=40\mathrm{nm}$, with $N_K=L/b_K=2.5\times 10^9$. Thus the long-chain entropic stiffness is $3k_{B}T/(2l_{p}L)=3.105\times 10^{-15}\mathrm{N}{\mathrm{m}}^{-1}$, and the root-mean-square end-to-end distance is $2\mathrm{mm}$. For comparison, the material axial stiffness is $EA/L=1.325\times 10^{-11}\mathrm{N}{\mathrm{m}}^{-1}$, using $A=\pi d^2/4$. The corrected coil response remains much softer than axial backbone stretching.

At the theta condition, effective excluded volume approximately cancel and a freely jointed ideal chain has $⟨R^2⟩=N{b}^2$. With the stipulated segment length $b=2a$,In a good solvent repulsive excluded volume swells the coil, giving $R\sim b{N}^{\nu }$ with $\nu \simeq 0.588$ in three dimensions, or the Flory approximation $\nu =3/5$. In a poor solvent effective segment attraction favours a compact globule, whose linear size scales as $b{N}^{1/3}$ at roughly fixed internal density. The latter are scaling laws with model-dependent prefactors. A real chemical monomer need not be a statistical Kuhn length; using $2a$ as the independent segment length is part of this question's idealized model.

The Kuhn length $l_K$ is the segment length of an equivalent freely jointed chain chosen to match contour length $L$ and the unperturbed mean-square end-to-end distance: $⟨R^2⟩=L{l}_K$. Since $R\le L$, its maximum finite-chain value is $l_K=L$, attained by a straight rigid rod. Independent steps of length $b$ have $L=Nb$ and $⟨R^2⟩=N{b}^2$, soFor a long freely rotating chain with fixed angle $\alpha$ between successive forward bond vectors, orientational correlations decay as $c^s$ with $c=\cos \alpha$. Summing them gives the Kuhn length of a freely rotating chain:Positive persistence increases the statistical segment length, while negative bond correlations can reduce it. A chemical internal bond angle is supplementary to this forward-vector angle, so the cosine convention matters. Near the perfectly aligned limit the finite-chain bound $l_K\le L$ replaces the long-chain asymptotic formula.

Write $s$ for the number of grafted chains per unit area and $\Sigma =s{a}^2$ for its dimensionless form; this separates the physical grafting density from a dimensionless coverage. A free dilute chain has size $R_0\sim a{N}^{\nu }$, with $\nu =1/2$ in a theta solvent and approximately $3/5$ in a good solvent. An isolated end-grafted chain loses translations and configurations that cross the substrate, but retains the same leading size exponent if the surface is nonadsorbing. When the lateral graft spacing $D\sim s^{-1/2}$ exceeds $R_0$, the layer consists of polymer mushrooms. When coils overlap, crowding stretches the chains away from the surface into a polymer brush.

The polymer mushroom-to-brush crossover isFor the stipulated statistical-segment interpretation of $N$ and $a$, the scaling estimates areThus ${\Sigma }_{\ast }\simeq 2.50\times 10^{-3}$ and $7.54\times 10^{-4}$ respectively. The numerical constants are scaling conventions: using a radius of gyration rather than an end-to-end size changes order-one amplitudes, not the powers of $N$.

In the Alexander-de Gennes brush model, take blobs of lateral size $D$. Within a blob, $D\sim a{g}^{\nu }$; beyond it, the $N/g$ blobs are aligned away from the wall. ThusWith coarse-grained segment volume $a^3$, conservation gives the polymer-brush volume fraction through $\varphi H\sim N{a}^{3}s$, henceThe theta-solvent brush height includes three-segment repulsion even though the effective two-segment interaction vanishes. These are scaling estimates for a roughly uniform brush, not an assertion that every chain end lies at the same height in an actual brush.

The many-segment-blob requirement $g\gg 1$ gives $D\gg a$, or $\Sigma \ll 1$. Together with overlap, the regime is $N^{-2\nu }\ll \Sigma \ll 1$. At the dense-brush packing limit, $\varphi \sim 1$, $g\sim 1$ and $H\sim Na$. Here $s\sim a^{-2}=2.04\mathrm{n}{\mathrm{m}}^{-2}$ and $H\sim 280\mathrm{nm}$. If one formally continues a dense incompressible layer above this boundary, conservation would instead giveThis is the requested formal dense-layer expression, but for $\Sigma >1$ it gives $H>Na$, which violates finite extensibility of a polymer chain. There is no physically admissible continuation above this limit in the stated segment-volume model. A Kuhn length segment is not necessarily a cube of material: with an independently specified material volume $v_0$ per counted segment, the dense-layer law is $H=N{v}_{0}s$, and the packing bound is $s\le a/v_0$. The data do not determine $v_0$ separately. The simple model therefore establishes its own breakdown, rather than a universal microscopic maximum grafting density.

grafting-to uses preformed chains whose lengths and dispersities can be characterized before attachment. As coverage rises, each incoming coil must penetrate a crowded brush and lose conformational entropy to bring its end to the surface; the growing insertion barrier limits achievable coverage. grafting-from supplies small monomers to surface-bound growing chains and avoids insertion of a whole coil. Choose grafting-from for high grafting density. Initiator coverage and reaction control still matter, and inaccessible active sites, termination and unequal growth can broaden the resulting chain-length distribution. Neither route removes the elastic and packing costs of the final brush.

A generic application is steric stabilization of synthetic colloids in a good solvent. Bringing coated particles together compresses and interpenetrates their brushes, increasing osmotic pressure and conformational free-energy cost. This repulsion can oppose aggregation. The chains must remain attached and sufficiently cover the surface; poor-solvent collapse, sparse coverage or interparticle bridging can defeat stabilization.

Use a freely rotating chain: fixed bond length $b$, fixed angle $\vartheta$ between forward bond vectors, and independently random torsion angles. Then $⟨{\hat{t}}_0\cdot {\hat{t}}_n⟩=(\cos \vartheta {)}^n=e^{-nb/{\ell }_p}$, giving the orientational persistence length of a freely rotating chainThe equivalent long-chain Kuhn length divided by two, $b(1+\cos \vartheta )/[2(1-\cos \vartheta )]\simeq 3.48\mathrm{nm}$, is nearly equal here but is a distinct discrete-chain convention. A chemical internal bond angle is supplementary to the forward-vector angle used above.

Synthetic examples are relatively stiff poly(p-phenylene terephthalamide) and flexible polydimethylsiloxane. Light scattering and viscometry established rodlike solution conformations for the former; single-chain mechanical measurements support the latter's flexibility. Persistence is solvent- and model-dependent, so no universal numerical value is inferred for either example.^[ref][ref]

Polydispersity means that a sample contains chains of different molar masses or lengths. Let $n_i$ count chains with molar mass $M_i$. The number-average molar mass gives every chain equal weight, while the weight-average molar mass weights a chain population by its contribution to total mass:Writing $w_i=n_i{M}_i/{\sum }_j{n}_j{M}_j$ makes the latter interpretation explicit: $M_w={\sum }_i{w}_i{M}_i$. Large chains therefore influence $M_w$ more strongly. If brackets denote an average over chain number,The ratio is molar-mass dispersity, conventionally written Đ. It equals one only when every chain has the same molar mass. Different distributions can share the same ratio, so it does not specify the full distribution.

For a freely jointed chain, write the end-to-end vector as the sum of $N$ independently oriented steps ${\mathbf{b}}_i$, each of fixed length $a$. Isotropy gives $⟨{\mathbf{b}}_i⟩=0$, and independence gives $⟨{\mathbf{b}}_i\cdot {\mathbf{b}}_j⟩=0$ for $i\ne j$. HenceThe root-mean-square end-to-end distance of a polymer chain is $a\sqrt{N}$, although the mean vector is zero. Its polymer contour length is $L=Na$, an upper bound on extension; it is not the typical unforced end-to-end length.

Stiffness correlates neighboring bond directions, so the discarded cross terms need not vanish. A freely rotating chain fixes the angle $\theta$ between successive forward bond vectors but leaves torsion uniformly distributed. Set $q=\cos \theta$, so $⟨{\mathbf{b}}_i\cdot {\mathbf{b}}_{i+s}⟩=a^2{q}^s$. ThenFor a chain long compared with its orientational correlation range, the characteristic ratio of a freely rotating chain approaches $C_{\infty }=(1+q)/(1-q)$. Positive forward persistence increases the mean-square size and gives the Kuhn length of a freely rotating chain $b_K=a{C}_{\infty }$. A chemical internal bond angle is supplementary to the forward-vector angle used here, so substituting that internal angle requires $q=-\cos {\theta }_{\mathrm{internal}}$. For $q\to 1$ at fixed $N$, the finite sum tends to $N^2{a}^2$, the rigid-rod result; taking the long-chain limit first would incorrectly predict an unbounded size. Real torsional energy preferences can be represented by a rotational isomeric state model, with weighted torsional states and correlations beyond independent free rotations.

A worm-like chain describes continuously varying local orientation. For unit tangent $\mathbf{t}(s)$ and bending stiffness $\kappa$, its elastic energy is $E_b=(\kappa /2){\int }_0^L|d\mathbf{t}/ds{|}^{2}ds$. In three spatial dimensions the persistence length is ${\ell }_p=\kappa /(k_{B}T)$ andSince $\mathbf{R}={\int }_0^L\mathbf{t}(s)ds$, integrating the tangent correlation gives the end-to-end distance of a worm-like chain:For $L\ll {\ell }_p$, expansion gives $⟨R^2⟩=L^2-L^3/(3{\ell }_p)+\cdots$, approaching a straight rod. For $L\gg {\ell }_p$, it gives $⟨R^2⟩\simeq 2{\ell }_{p}L$, the long-chain ideal chain result with Kuhn length $2{\ell }_p$. These models isolate stiffness; long-range excluded volume can additionally swell an isolated chain in a good solvent. When coarse-graining, a chemical repeat count and a count of independent statistical steps must not be silently interchanged.

The first panel shows the exact worm-like chain crossover between a rod and a long flexible coil. The second compares original normalized scaling curves for a uniform polymer brush; their prefactors have been chosen for illustration and do not fit the exam's experimental points.

For a good solvent, consider long flexible grafted polymer chains with grafting density $\sigma$ and lateral spacing $D\sim {\sigma }^{-1/2}$. At high coverage, $D$ is smaller than the isolated coil size, and adjacent chains cannot retain their unperturbed conformations. A scaling model divides each chain into concentration blobs of diameter $D$. Inside one blob the chain retains good-solvent statistics,using the Flory approximation exponent $3/5$. The $N/g$ blobs per chain form a stretched sequence approximately normal to the surface. The good-solvent brush height therefore obeysHere $a$ and $N$ refer to consistently chosen effective segments, whose microscopic properties are held fixed as chain length changes. The result is a scaling law with an undetermined order-one prefactor, not a fully specified height in nanometres.

A complementary free-energy balance per chain iswhere $v>0$ is effective segment excluded volume. The first term is the chain entropy cost of stretching and the second is the cost of crowding segments into a layer of volume $h/\sigma$ per chain. Minimization gives $h^3\sim v{N}^3{a}^2\sigma$; with $v\sim a^3$ it recovers the same height. The blob argument incorporates good-solvent correlations more directly. Both descriptions require overlapping chains, many segments per chain, and heights below the polymer contour length; the power law cannot be extrapolated to infinite grafting density.

In the printed experimental graph, the vertical axis is $h{D}^2/(10^6{\mathring{\mathrm{A}}}^3)$ and the horizontal axis is $M/10^5$. The approximately straight trend through the origin therefore means $h{D}^2\propto M$. Since $D^{-2}\sim \sigma$ and $M$ is proportional to chain length for a fixed repeat chemistry,The dashed guide rises by roughly $1.8$–$1.9$ vertical units over six horizontal units, corresponding to $h{D}^2/M$ of order $3{\mathring{\mathrm{A}}}^3$ per unit of the plotted $M$. This is an approximate graphical slope, not a fitted material constant; the graph does not specify a numerical monomer count or a repeat-unit volume from which an absolute brush height could independently be calculated.

The poor-solvent brush height has a simple volume argument. Let $v_0$ be the volume per repeat and $\varphi$ the roughly fixed polymer volume fraction within a dense uniform layer. There are $N\sigma$ repeats per substrate area, soFor fixed poor-solvent conditions, $\varphi$ is approximately independent of $N$ and $\sigma$, giving the observed linear grafting-density dependence. Polymer–polymer contacts are favored and the layer becomes relatively compact; in a good solvent, favorable solvent contact and segment repulsion instead produce a swollen layer whose stretching and osmotic costs balance at the weaker ${\sigma }^{1/3}$ dependence. Sparse isolated polymer globules or lateral segregation fall outside the uniform-brush model.

The cited experimental paper's abstract independently reports these two scaling laws, but identifies polydimethylsiloxane chains on porous silicon dioxide, rather than the polystyrene system named in the exam. The solution uses the printed axes to infer the exponents and does not treat that material identification as verified experimental provenance.^[ref]

Ideal and self-avoiding walks. An ideal chain has independent isotropic coarse-grained steps and permits self-intersections in its mathematical model. For $N$ steps of length $b$, the cross terms average to zero, so its root-mean-square end-to-end distance of a polymer chain obeysA self-avoiding walk excludes repeated occupancy or intersection at the segment scale. This represents positive excluded volume in a dilute good solvent. The nonlocal constraint correlates otherwise distant portions of the chain and swells it:The Flory approximation replaces this exponent by $3/5$, by balancing stretching free energy $R^2/(N{b}^2)$ with an interaction contribution $v{N}^2/R^3$. The result is a more extended and less internally dense coil than the ideal walk; self-avoidance changes the statistics, not merely the local step length.

Two ideal-chain regimes. At the theta temperature for a dilute polymer–solvent pair, leading effective segment attractions and repulsions cancel. Large-scale chain statistics are approximately ideal, even though microscopic atoms still have finite size. In a homogeneous polymer melt, surrounding chains screen long-range excluded volume interactions of a chosen chain, again making its equilibrium large-scale size approximately ideal. Local bond-angle correlations must be included in an effective statistical length such as the Kuhn length. Polymer entanglements can slow the dynamics without invalidating this leading equilibrium size law.

Semiflexible DNA. The nucleic acid double helix gives double-stranded DNA a bending stiffness and substantial local orientational persistence. Independent step orientations are therefore a poor description on short scales, while self-avoidance alone does not specify the energy cost of bending. The worm-like chain describes the molecule as a continuously bendable, locally inextensible curve $\mathbf{r}(s)$ parameterized by arc length $s$, with unit tangent $\mathbf{t}(s)=d\mathbf{r}/ds$. Its bending energy iswhere $A$ is bending stiffness. In the free three-dimensional model, the persistence length is ${\ell }_p=A/(k_{B}T)$ andThus ${\ell }_p$ is the contour separation over which tangent alignment falls by the factor $e^{-1}$; it quantifies stiffness relative to thermal bending. The model bridges locally rod-like and globally coil-like conformations. It omits long-range self-avoidance in its simplest form, so sufficiently long dilute DNA can require excluded-volume corrections.

Flexible and rigid limits. Integrating the tangent correlation over the two contour positions gives the end-to-end distance of a worm-like chain:For a very flexible chain on the scale of its total length, $L/{\ell }_p\gg 1$, the exponential is negligible andThis is the ideal chain result with Kuhn length $b_K=2{\ell }_p$ and effective step count $N_K=L/(2{\ell }_p)$. Many persistent sections have decorrelated orientations. The flexible limit means a large ratio $L/{\ell }_p$ within the continuum model's range, not an extrapolation of the persistence length below all molecular length scales.

For a nearly rigid chain, $L/{\ell }_p\ll 1$, the constant and linear terms in the exponential cancel those outside it. The Taylor series givessoThis is the expected rod limit: all tangents are nearly aligned, and the end-to-end distance approaches the arc length.

Helix–coil curves. A helix-coil transition model allows ordered helical runs and disordered coil regions. Use $s$ and $\sigma$ with exactly the free-energy conventions defined in the paper. A negative $\Delta F_{\mathrm{hc}}$ gives $s>1$ and favors the helical state; a positive junction cost gives $0<\sigma <1$ and penalizes starting new domains. The supplied helical fraction is the long-chain form associated with the Zimm-Bragg model.

Its main features follow directly without assuming a sharp transition. Put $Q=(s-1{)}^2+4s\sigma$. For every $\sigma >0$,and differentiating givesThus all curves rise monotonically and cross at $(1,1/2)$. Increasing the boundary free-energy cost reduces $\sigma$, suppresses frequent coil–helix boundaries and makes longer runs favorable. The transition region becomes narrower and steeper: balancing $(s-1{)}^2$ against $4s\sigma$ gives a width of order $\sqrt{\sigma }$ near $s=1$.

For $\sigma =1$, the fraction simplifies to $\boxed{f_h=s/(1+s)}$, the noncooperative two-state result. For $0<\sigma \ll 1$, the steep curve describes cooperative helix formation. In the singular limit $\sigma \downarrow 0$, it approaches zero for $s<1$ and one for $s>1$; its midpoint remains $1/2$ when approached through positive $\sigma$. Setting $\sigma =0$ directly makes the formula indeterminate at $s=1$. For any fixed positive $\sigma$, the given long-chain curve is smooth: it is a cooperative crossover, not a true discontinuity. The plot varies $s$ at fixed $\sigma$; in an actual temperature scan both parameters may change, and a finite chain can further round the crossover.

For an ideal chain, independent Kuhn length steps give the random walk relationwhere $R_{\mathrm{sub}}$ denotes the end-to-end displacement of a subchain. Equivalently the mass-size fractal exponent is $2$. Numerical factors depend on the chosen definition of blob diameter.

A subchain smaller than the adsorption height explores three dimensions much as a free ideal chain does. At scales exceeding $\xi$, adsorption restricts its perpendicular extent to order $\xi$, so the coil is anisotropic. Its in-plane projection may still have a random walk law for an ideal chain, but the isotropic three-dimensional blob construction cannot be extrapolated to $\sigma >\xi$. This is the reason to use adsorption blobs of size $\xi$.