AMORPHOUS PERIODIC TABLE

Full-Color Amorphous Phase Formers & Intermediates (49) • Diagonal Half-Color Network Modifiers (28) • 241 Crossref/OpenAlex-Verified Systems

118 Elements 241 Verified Systems

49 Full Color Makes Amorphous Possible

28 Half Color In Reported Systems (Modifiers)

◆ 17 Tetrahedral Verified CN=4 Network Motif

41 White Unreported in Catalog

Scientific Methodology, Crossref/OpenAlex DOI Audit & Visual Encoding (amorphous_materials.db — 241 Experimentally Verified Systems, 77 Active Elements):
• 100% Crossref & OpenAlex Verified Citations: Every cataloged amorphous system is verified against live Crossref REST and OpenAlex APIs (HTTP 200 OK, exact author/year/journal/title match) and experimentally confirmed by diffuse X-ray/neutron diffraction (S(Q) FSDP), pair distribution function g(r), TEM SAED, and/or DSC glass transition (T_g / T_x). Spans three distinct synthesis regimes: Bulk Melt-Quenched Glasses & BMGs (152 systems; Inoue, Johnson, Sheng/Ma), Rapid-Quenched Melt-Spun Ribbons & Levitated Melts (31 systems; Lamparter/Steeb, Benmore/Weber), and Vapor-Deposited / Thin-Film Amorphous Solids (58 systems; Frances Hellman Group UC Berkeley a-Bi₂Se₃, a-Fe_xGe_1−x, a-Fe_xSi_1−x, a-Co_xGe_1−x, a-Mn_xSi_1−x, a-Gd_xSi_1−x, ultrastable a-Si; Wuttig/Salinga phase-change chalcogenides; Bassiri/Fejer LIGO coatings; Hosono/Wager oxide semiconductors; Kortright/Bienenstock/Beasley/Dynes superconducting & catalytic films).
• Full Cell Coloring (49 Elements — “Makes Amorphous Phase Possible”): Primary Tetrahedral Network Formers (5), Bridging Anion Formers (7), Conditional Tetrahedral Intermediates (12), Oxide/Chalcogenide/BMG Polyhedral Intermediates (13), and Metallic Cluster / BMG Host Intermediates (12) that construct the continuous random network (CRN) or icosahedral/polytetrahedral cluster backbone.
• Diagonal 50/50 Half-Split Cell Coloring (28 Elements — “Part of Reported Amorphous Systems”): Network Modifiers, Charge Compensators, and Large/Small Topological Cages (Li–Cs, Mg–Ba, Ag, Y, La–Lu, U, I, H) that participate within multicomponent amorphous matrices. Each active element cell displays its primary local coordination motif and raw verified system count (CN · N).

Corner-Sharing Tetrahedral Network (MX4)

CN = 4 (sp3 covalent / mixed ionic-covalent)

Amorphous Coordination & System Scorecard

Amorphous Class, Synthesis Regime & Structural Role Breakdown

All Co-Occurring Partner Elements (Click Partner to Inspect)

All Co-Occurring Element Pairs, Shared Amorphous Systems & Correlation Metrics

Glass-Forming Structural Mechanism

Crystalline-to-Amorphous Conversion Benchmarks

Baseline Atomic, Electronic & Crystalline Reference

Verified System:

📖 Amorphous Solid-State Physics & Structural Glass Theory Guide

Why certain elements make the amorphous phase possible (Full Color) while others participate as modifiers/cages (Half Color)

1a. Primary Network Formers Continuous Random Networks (CRN: Si, Ge, P, B, As)

By Zachariasen’s Rules (1932) and Phillips–Thorpe Topological Constraint Theory (1979), a covalent/oxide melt avoids crystallization when polyhedra of low coordination (z = 3 or 4, e.g., SiO₄, GeSe₄, BO₃/BO₄, PO₄) share corners rather than edges or faces.

Isostatic Window (⟨r⟩ ≈ 2.40): When the number of bond-stretching (r/2) and bond-bending (2r − 3) constraints per atom equals the 3D degrees of freedom (n_c = 3 at mean coordination ⟨r⟩ = 2.40, as in As₂Se₃ or GeSe₄), the network forms a stress-free, non-periodic 3D graph without paying a macroscopic enthalpy penalty relative to the crystal.
Dual Role in BMGs: Metalloids (B, P, Si, Ge) also form solute-centered trigonal prisms (M₉B, Pd₆Ni₃P) that stabilize bulk metallic glasses.

1b. Bridging Anion Formers Flexible Low-CN Hinges (O, S, Se, N, F, Cl, Br)

Why can’t rigid tetrahedra alone easily pack into a strain-free glass without defects? Because a purely 4-coordinated network (a-Si, ⟨r⟩ = 4.0) is over-constrained (n_c = 7 > 3).

2-Coordinate Rotational Hinges: Bridging anions (–O–, –S–, –Se–, –F–, –Cl–, –Br– with CN=2, or planar –N< with CN=3) sit between rigid MX₄ tetrahedra (including halide glasses BeF₂, ZnCl₂, ZnBr₂). Because a 2-coordinate bridge has soft inter-tetrahedral bond-bending (e.g., Si–O–Si varies continuously from 125° to 165°, mean ∼144°) and free dihedral torsion, it absorbs topological disorder while maintaining 100% covalent connectivity.

2a. Conditional Tetrahedral Compensated Intermediates (Al, Ga, Zn, Be, C, V, Mo, W, Ti, Sn, In, Cd)

Conditional glass formers (intermediates) cannot form a single-component oxide glass by simple melt quenching (Al₂O₃ or TiO₂ crystallize unless levitation-quenched or sputtered), or require specific chemical/energetic conditions to adopt 4-coordinate tetrahedral geometry:

Charge-Compensated Tetrahedra & Amorphous Oxides: Trivalent Al³⁺ and Ga³⁺ form [AlO₄]⁻ and [GaO₄]⁻ when paired with modifiers, or mixed AlO₄/AlO₅/AlO₆ networks in containerless/ALD a-Al₂O₃ (Benmore/Weber), high-k a-HfO₂/a-ZrO₂, LIGO a-Ta₂O₅ coatings (Bassiri/Fejer), and amorphous oxide semiconductors (IGZO, ZTO, IZO — Hosono/Wager).
Halide / Pnictide / Ion-Beam Tetrahedra: BeF₂, ZnCl₂, and ZnBr₂ are exact tetrahedral structural analogues of SiO₂; CdGeAs₂ and InP form tetrahedral chalcopyrite/III-V glasses; carbon forms sp³ tetrahedral amorphous carbon (ta-C) under energetic ion deposition.

2b & 2c. BMGs & Clusters Bulk Metallic Glasses & Icosahedral Frustration

Unlike covalent glasses, metallic bonds are non-directional and dense (CN=11–14). Pure liquid metals crystallize in nanoseconds because periodic FCC/BCC nuclei form effortlessly. Bulk Metallic Glasses (BMGs) defeat crystallization via Geometric & Topological Frustration (Inoue’s Rules, Johnson, Sheng/Ma & Egami’s Atomic-Level Stress Theory):

Five-Fold Icosahedral Short-Range Order: Solute-centered ⟨0,0,12,0⟩ icosahedra and Frank-Kasper polytetrahedra are locally denser and lower in energy than FCC/BCC, but five-fold rotational symmetry cannot tile 3D Euclidean space periodically.
Multi-Component Size Mismatch (Δr / r > 12%): Combining large (Zr, Hf, Pd, La, Gd), medium (Cu, Ni, Co, Fe, Ti), and small (Be, B, P, Si, Al) atoms creates dense cluster packing (Vitreloy-1, Zr₅₀Cu₄₀Al₁₀, Pd₄₀Cu₃₀Ni₁₀P₂₀, Ni₆₂Nb₃₈, Fe₈₀B₂₀, Co₈₀B₂₀).

Synthesis Regimes (Filterable) Bulk Melt-Quenched vs. Rapid-Quenched Ribbons vs. Vapor Thin Films

Glass-forming ability depends critically on the effective cooling rate and synthesis pathway. Use the toolbar buttons to filter elements by synthesis regime:

Bulk Melt-Quenched Glasses & BMGs (152 sys, R_c ~ 10⁻²–10³ K/s): Canonical oxide, chalcogenide, halide, and bulk metallic glasses cooled from the equilibrium liquid.
Rapid-Quenched Melt-Spun Ribbons & Levitated Melts (31 sys, R_c ~ 10⁴–10⁶ K/s): Marginal binary metallic glasses (Cu₆₄Zr₃₆, Fe₈₀B₂₀, Ni₈₁B₁₉) and containerless aerodynamic-levitation oxides (a-Al₂O₃, a-TiO₂).
Vapor-Deposited / Thin-Film Amorphous Solids (58 sys, R_c,eff ~ 10⁸–10¹² K/s): E-beam co-evaporated, sputtered, ALD, or ion-implanted films including Hellman Group quantum films (a-Bi₂Se₃, a-FeGe, a-FeSi, a-CoSi, a-MnSi, a-GdSi, e-beam a-Si), Wuttig phase-change chalcogenides (Ge₂Sb₂Te₅), and Hosono oxide semiconductors (IGZO).

Tab 5 Provenance & Weighting Scalar Peak Anchors vs. Parameterized Profile Reconstructions

Every system in Tab 5 displays an explicit Data Provenance Badge distinguishing literature scalar peak anchors from parameterized continuous curves:

🔬 Lit. Benchmark Peak Anchors + Parameterized Curve (44 Canonical Systems): Scalar peak positions (Q₁, Q₂, r₁, r₂, θ̄) and partial pair distances r_αβ are anchored directly to published X-ray/neutron diffraction, EXAFS, RMC, or AIMD benchmarks (Wright, Salmon, Greaves, Benmore, Sheng/Ma, Wuttig, Hellman, Kortright, Lamparter/Steeb, Sváb); continuous S(Q), g(r), and P(θ) curves are parameterized Gaussian/Lorentzian reconstructions centered on those experimental anchors.
⚖️ Composition-Weighted Analytical Reconstruction: For multicomponent alloys and solid-solution series without digitized curve tables, peak anchors and partial pair Gaussians g_αβ(r) (weighted by w_αβ = 2c_αc_β or c_α²) are reconstructed continuously from the exact atomic fractions c_i.