Metallic photonic crystals, metal-based structures with periodicities on the scale of the wavelength of light, have attracted considerable attention due to the potential for new properties, including the possibility of a complete photonic bandgap with reduced structural constraints compared to purely dielectric photonic crystals, [1] unique optical absorption, thermally stimulated emission behavior, [2,3] and interesting plasmonic physics.[4]Photonic applications may include high-efficiency light sources, [5] chemical detection, [6] and photovoltaic energy conversion. [3] Other applications for 3D porous metals, so-called "metal foams", include acoustic damping, high strength to weight structures, catalytic materials, and battery electrodes.[7]The photonic properties of metallic inverse opal structures have been of significant interest because of the simplicity of fabrication and potential for large-area structures. However, in practice, experiments on metal inverse opals have been inconclusive, [8][9][10] presumably because of structural inhomogeneities due to synthetic limitations. In this work, we demonstrate an electrochemical approach for fabricating high-quality metal inverse opals with complete control over sample thickness, surface topography, and, for the first time, the structural openness (metal filling fraction (FF)). Optical measurements conclusively demonstrate that metal inverse opals modulate the absorption and thermal emission of the metal and that these effects only become 3D in nature at high degrees of structural openness. Various metals, for example, Au, Ag, W, Pt, Pd, Co, Ni, and Zn, [10][11][12][13][14] have been formed into inverse opals. Here, Ni is selected because of its high reflectivity in the IR, temperature stability, and ease of electrochemical processing. Ni inverse opals are fabricated by using electrodeposition through a polystyrene (PS) opal template that was first deposited on a surface-treated Au film evaporated on a Si wafer. PS opals formed from microspheres ranging in diameter from 460 nm to 2.2 lm were used as templates; this paper focuses on metal inverse opals formed using 2.2 lm microspheres. Templated electrodeposition is observed in all systems; this range of microsphere diameters is not an upper or lower limit. The final thickness of the sample is regulated by controlling the total charge. After electrodeposition, the PS microspheres are removed with tetrahydrofuran, resulting in a Ni inverse opal. Although the electrodeposition is quite homogeneous, gradual thickness variations do occur over the sample surface. These variations turn out to be useful, as they generate regions of different number of layers and surface terminations over the same sample (Fig. 1)