14 March 2014 Glass optical waveguides: a review of fabrication techniques
Author Affiliations +
Optical Engineering, 53(7), 071819 (2014). doi:10.1117/1.OE.53.7.071819
Glasses, either pure or suitably doped, constitute an excellent material for the development of integrated optical circuits. A brief review is presented of the most widely used processes for the fabrication of passive and active glass waveguides. Brilliant prospects of glass-based platforms for the development of photonic integrated circuits are outlined.
Righini and Chiappini: Glass optical waveguides: a review of fabrication techniques



The success of optical fibers for lightwave communications, employing silica (i.e., amorphous SiO2) as base material, has paved the way to a large use of optical glasses in photonic applications and, in particular, integrated optics (IO). The field of IO had been conceived in 19691 to complement the passive transmissive medium (i.e., the optical fibers) with integrated chips, where all the active (signal generation or amplification) and passive (signal addressing and processing) functions could be performed via the guided propagation of light.

Since then, much activity has been carried out to develop what we can also refer to as photonic integrated circuits (PICs); an interesting overview was published some years a ago by Kaminow, who had been member of the Bell Labs’ group which was pioneering in this area.2 Many optical materials are currently employed in the fabrication of PICs, but glass remains a fundamental one. Novel glasses and/or fabrication processes have obviously been developed to respond to the growing new requirements, and glass IO now constitutes a branch of photonics capable of offering sophisticated and innovative solutions to many problems—yet involving rather simple technologies.

Integration was the keyword in the seminal paper by Miller;1 even today, however, the goal of a full monolithic integration, possible in semiconductor materials, does not always represent the best solution, while hybrid integration often permits to take advantage of the complementary characteristics of the different classes of materials needed in IO (namely, semiconductors, ferroelectrics, glasses, and polymers). Thus, glassy materials keep offering many useful characteristics such as relatively low cost, excellent transparency, high threshold to optical damage, a relatively wide interval of refractive indices to choose from, and, last but not least, the easiness of doping with active and functional atoms and oxides. Glass is also a fundamental component of the main technological platforms for PICs, namely silica-on-silicon (SOS) and silicon-on-insulator (SOI).

Optical waveguides (WGs) are the building block over which PICs are designed and fabricated; this paper presents a brief overview of a number of different processes suitable for the fabrication of glass WGs. As to the material itself, pure glasses are the most popular material for the fabrication of passive components, but extended the functionality can be easily achieved by doping the glass matrix with proper ions, elements, or compounds. This aspect is also briefly considered in the following.


Thin Film Fabrication Processes

Glass WGs exhibit very good properties, owing to the relatively simple technology, the low propagation losses, and the easy matching to glass fibers. The availability of low-loss glasses and cheap and reliable WG fabrication techniques has been of major importance. A general requirement is that the fabrication technologies must—first of all—be capable of high yield, with assured reproducibility within the specified tolerances, and of intrinsic low operation cost. In the case of glass IO, the most usual WG fabrication techniques can be classified according to the scheme in Fig. 1. Since the most basic requirement for confining the light is that the guiding layer has a refractive index (RI) higher than the surrounding media, two major approaches can be followed: (a) deposition of a thin film and (b) local modification of the bulk material. The former approach includes processes such as radio frequency (RF) and magnetron sputtering, chemical vapor deposition (CVD, and in particular plasma-enhanced chemical vapor deposition—PECVD), flame hydrolysis deposition (FHD), spray pyrolysis (SP) deposition, pulsed laser deposition (PLD), sol–gel coating; the latter approach, which is also suitable to the direct definition of a channel WG, includes ion exchange, ion implantation, UV irradiation, and femtosecond laser writing. All the above processes may then be followed or complemented by other ones such as annealing, photolithography, and etching.

Fig. 1

Fabrication techniques of glass optical waveguides (WGs) can be classified in two major categories: one refers to thin film deposition techniques, either physical or chemical, and the other concerns process for local modification of the refractive index of the glass, either in bulk or thin film format.


It has to be remarked that none of the fabrication techniques indicated in Fig. 1 is peculiar to glass IO only: they are largely used in a wide range of application areas, from thin-film coatings to microelectronics, material processing, and glass strengthening. Indeed, some of these techniques, like resistive evaporation, are rarely used for the fabrication of WGs, being, on the contrary, a standard method of producing thin metal films and, as such, largely used to produce the metal layers needed in the patterning processes of IO circuits and for electrical contacts. Electron-gun evaporation would be more effective, but it too has not been frequently used for optical WGs. Another technique cited in Fig. 1 but not so common in IO is SP: it is a process in which a thin film is deposited by spraying a solution on a heated surface, where the constituents react to form a chemical compound.3 It involves three main steps: atomization of the precursor solution, transportation of the resultant aerosol, and decomposition of the precursor on the substrate, with final sintering of the solid particles. SP is suitable to prepare dense and porous oxide films, ceramic coatings, and powders. An advantage of SP is that it does not require high quality substrates or chemicals. Films prepared by the SP have been used in various devices, such as solar cells, sensors, antireflection coatings, thermal coatings, solid oxide fuel cells, and many others; as an example, rare-earth-doped Al2O3 films prepared by the SP have shown efficient blue-green luminescence and white light emission.4 Let us now briefly consider the most common deposition techniques for glass optical WGs.


Pulsed Laser Deposition

PLD, namely thin film deposition by laser ablation from a target material, is a technique in use since the end of the 1980s, which proved to be effective for depositing high-quality optical films.5 PLD has a high potential to produce complex high-quality glassy films for integrated optical applications. Its main advantages over other deposition methods are the capability of producing glassy films in an extended compositional range with respect to bulk materials, the possibility of avoiding oxygen deficiencies in the glass network by using an oxygen pressure during deposition, the capability of producing complex oxide hosts and the possibility of incorporating controlled structure nanoparticles. PLD has also been used to produce thin films with high erbium ion concentration from bulk phosphate,6 tellurite, phospho-tellurite, and chalcogenide glasses.7,8 As an example, high-quality phospho-tellurite thin films up to 2-μm thickness with <0.05dB/cm propagation losses were deposited using a 193 nm ArF excimer PLD system in a low pressure oxygen atmosphere.8


Sputtering Deposition

Sputtering is one of the most popular techniques, in the category of physical deposition processes, for producing low loss and even complex glass WGs. Some of the earliest glass WGs, made of Corning 7059 glass, were fabricated by sputtering.9 Sputtering is based on the use of positively charged highly accelerated ions to eject particles—usually atomic clusters or neutral atoms—from a target made of the material to be deposited. Most of the ejected particles then strike the substrate and adhere to it, so that a high-quality film is gradually built up. The sputtered films are generally more dense than evaporated films,10 but less dense than pulsed-laser-deposited films.11 The accelerated particles may be created in a glow discharge plasma of an inert gas (usually argon) or by an ion beam. The physics of sputtering is quite complex, and the interested reader is referred to some of the many review articles and textbooks on this topic.12 The sputtering yield is defined as the ratio, in a given time, of the number of particles sputtered to the number of incident particles. The sputtering yield increases with the angle of incidence of the accelerated ions, and it is dependent upon the energy of the incident particle and on the nature of the particle and of the target to be sputtered. The simplest sputtering system is a planar “diode” system, where a potential difference is maintained between a cathode (the electrode with which the target to be deposited is in contact) and an anode (usually electrically grounded), on which the substrate is placed. Although a metal target can be easily sputtered by applying a direct current (dc) voltage, for the sputtering of an insulating material (such as silica), an RF discharge (usually at 13.56 MHz frequency) is adopted to avoid the accumulation of negative electrical charges onto the target. More recently, the magnetron configuration has often been used with permanent magnets placed below the cathode: when a magnetic field is coupled with the sputtering source, it traps electrons close to the target surface and hence decreases their mean free path in the plasma. More ions are thus created by impact with electrons close to the target and this lead to higher sputtering rates.

Sputtering is a relatively slow process, with deposition rates of the order of a few nanometers per hour per Watt of RF electric power applied to the electrodes. In typical working conditions, the pressure of the sputtering gas is of the order of 102mbar, and the electric power is in the range of 200 to 300 W. The quality of films is generally quite good, with propagation losses repeatedly <0.5dB/cm. Composition and RI of sputtered films vary as a function of the power level and/or the gas pressure at which the deposition is made. Neither compounds nor alloys are removed from the target in their combined or associated state: the material is often sputtered as a range of atoms and fragments of the original molecule, so that the compound must reform on the substrate. Thus, when sputtering oxide glasses, there is a good likelihood of loss of oxygen caused by the dissociation of glass during the collisions of ions onto the target.13 In order to reduce these effects, a percentage of oxygen can be introduced in the plasma (reactive sputtering) and a little potential can be applied to the anode (bias sputtering). In order to reduce optical losses, a thermal annealing process is often necessary; annealing, in fact, reduces losses by oxidizing the sputtered material and homogenizing the deposited thin film by enhancing the diffusion process.14

Magnetron sputtering, in particular, appears to be a valuable alternative to other WG fabrication processes; high-quality films have been produced, for instance, for light amplification, due to doping with rare-earth1516.17 and biosensing.18 It is worth of notice the fact that the two latter devices use chalcogenide glasses, so showing a viable approach to the development of glass IO for mid-IR.



The CVD method19 was originally developed for the production of preforms of optical fibers, but it can be advantageously applied to planar WGs as well. In the latter case, CVD is employed to create thin films of a material on a substrate via the use of chemical reactions. Reactive gases are fed into a vacuum chamber and these gases react on a substrate and form a thin film or a powder. In classical CVD equipment, the silica (or silicon) substrate is placed in a reaction chamber, where accurately controlled flows of oxygen (carrier gas) and reactant gases (such as SiCl4, BBr3, and GeCl4) are introduced. Depending on the process and operating conditions, the reactant gases may undergo homogeneous chemical reactions in the vapor phase before striking the surface. The gaseous by-products of the reaction are transported out of the reaction chamber. Referring to the above gases, the reaction with oxygen at a temperature >1200°C causes the reagents’ oxidation and the deposition of a thin oxide layer (with SiO2B2O3GeO2 composition) onto the substrate. The WG is then obtained by vitrification of the soot at a temperature around 1700°C; a lower-index cladding layer can also be deposited on the WG by reducing the flowing rate of GeCl4. The resulting CVD-deposited glass films usually show absorption loss <0.1dB/cm at 632.8-nm wavelength. Low-loss rib or channel WGs can also be formed by this technique, through the use of suitable etching processes. The CVD process lends itself to many modifications, which have been developed in different laboratories with the aim of optimizing both the quality and the yield of the process. The most common types of CVD-derived fabrication techniques used to make IO devices include FHD,20,21 low pressure CVD (LPCVD),22 PECVD,23,24 and atmospheric pressure CVD (APCVD)25,26 processes.

FHD likely is the most economical technique for the deposition of SiO2 films, exploiting the hydrolysis of SiCl4 in a high temperature H2O2 flame. Even if the precise control of deposition and stoichiometry is quite difficult, and an additional process of densification of the porous soot into dense SiO2 film is necessary, FHD is extensively employed to deposit thick amorphous silica films due to the high deposition rate and high material quality.21 The flexibility of this technology, however, has allowed to successfully adopt it for various applications, like optical biochemical sensor arrays, integrating optical, and microfluidic circuitry.27

LPCVD can only be performed at high temperatures, and its low rate of the reaction allows us a greater control over film thickness and uniformity, also improving films purity. In the case of composite glasses, like borophosphosilicates, the choice of the source materials may also be important for a better control of the film properties.22 The simplicity of the process permits the processing of large wafer batch sizes.

PECVD permits energetic reactions at low temperatures (even 100°C in some cases), due to the formation of cold plasma by electrical ionization rather than thermal ionization.23 The process is more complicated than LPCVD and therefore is less suitable to large batches. It is, however, very frequently used for the deposition of low-loss silica and silica-germanate WGs.28 Further developments have made possible to effectively avoid problems which can occur when fabricating dense WG arrays, like the creation of voids during the deposition of the upper cladding. An improved process, for instance, that uses boron–germanium codoped upper-cladding and high-temperature annealing has produced a low-loss cross-order arrayed-waveguide-grating (AWG) triplexer used as test device.29

APCVD is attractive for both economic and technological reasons, particularly due to the online-processing capability, which substantially reduces substrate handling cost.26 It is often applied to the deposition of passivation layers in the semiconductor manufacturing process, but can also be employed in IO, due to the advantage of low temperature treatment, which is effective for minimizing film stress and therefore producing low-birefringence WGs. As an example, APCVD was applied to the fabrication of a frequency division multiplexer and of a Mach–Zehnder interferometer; the latter one was used to test the photosensitivity of guiding structures based on phosphorous-doped silica glass cladding and codoped germanium and phosphorous silica core.25


Sol–Gel Deposition

A low cost and versatile approach for the realization of glass and glass ceramic (GC) WGs is based on sol–gel route. This method exploits chemical reactions of a main precursor, generally an organometallic compound in alcoholic solutions.30 From an historical point of view, even if the synthesis of the first silica gel dates back to 1846,31 sol–gel chemistry has been investigated extensively only since the mid-1970s, when sol–gel reactions were shown to produce a variety of inorganic networks that can be formed from metal alkoxide solution. Here, we will focus on the metal–organic route with metal alkoxides in organic solvent,32 which offers unique opportunities for the synthesis of optical materials in different forms such as fine powders, monosize nanoparticles, aerogels, xerogels, and WGs, as represented in the simple diagram of Fig. 2. Another possible approach is to follow the inorganic route with metal salts in aqueous solution:30 it has the advantage of being much cheaper than using metal alkoxides, but the control of the reactions is more difficult.

Fig. 2

Sketch of the sol–gel synthesis processes of optical glassy materials in different forms, such as monosize nanoparticles, aerogels, and xerogels, in thin film or bulk format.


As shown in Fig. 2, the sol–gel chemical process is self-described in the definition of a sol, a gel, and a summary of the processes in which the sol evolves into a gel. The main reactions involved in the sol–gel chemistry are based on the hydrolysis and condensation of metal alkoxides, which can be outlined as shown in Fig. 3.

Fig. 3

Summary of the main reactions involved in the sol–gel chemistry based on hydrolysis and condensation of metal (M) alkoxides (OR). OH indicates the hydroxyl group.


In the first step, the hydrolysis reaction, due to a nucleophilic attack of water to the metalloid atom, allows the substitution of the alkoxide groups (OR) with the hydroxyl groups (OH). In the second step, the condensation reaction brings to the constitution of the amorphous network M–O–M with the elimination of water and alcohol. Due to the fact that the hydrolysis kinetic in a neutral environment is very slow, generally it is preferable to make the reaction happen in acid or basic catalysis. Because of the presence of a lot of chemical reactions and several involved compounds, the thermodynamic and kinetic description of the process result to be very complex; the main parameters that affect the reactions are the water-to-alkoxide ratio, the type and amount of catalyst, the type of organic groups attached on M (metallic) atom, and the solvent. All these conditions should be considered in order to create a stable suspension necessary for the realization of efficient optical devices.

Other aspects concern the form of the final material: the precursor sol, in fact, can be either deposited on a planar substrate to form a film (WG), e.g., by dip-coating or spin-coating, or can be cast into a suitable container with the desired shape (xerogel), or it can be used to coat substrates with nonplanar shape. A limitation to the film deposition is the time length of the process: due to the risk of stress cracking, that is, a result of the reduction of volume of the deposited layer during the drying process, generally it is impossible to deposit films with thickness >200nm in a single step. Several deposition/heating cycles are, therefore, necessary to achieve films with a thickness suitable for an optical WG. Viscosity of the solutions, deposition parameters (dipping rate for dip-coating process and rotation speed for spin-coating one), and postdeposition heat treatment (HT) conditions are crucial aspects that have to be calibrated for each material.

Silica-based WGs are mostly produced by using alkoxysilanes, such as tetramethoxysilane and tetraethoxysilane; the acid nature of the catalyst permits to obtain a material with high uniformity, low porous volume, and high density, fundamental properties for the development of photonic devices. A complementary approach uses organic–inorganic hybrid materials (e.g., hydrogen silsesquioxane, 3-glycidoxypropyl-trimethoxysilane) as starting reagents; in this case, the removal of the organic part occurs using HT process at high temperature. In all materials obtained by sol–gel route, the HT process is critical for the densification of the structures: HT, in fact, permits not only the stiffening of the network, but also the removal of hydroxyl groups (OH) that are one of the main causes of absorption in the near-infrared and of the luminescence quenching for rare-earth ions, especially erbium ions. Finally, playing with HT, it is possible to pass from an amorphous matrix to a GC system, usually exhibiting better characteristics (see Sec. 3).

Literature is rich of papers where the sol–gel route has been used for the realization of planar WGs with low propagation losses (better than 0.3dB/cm at 1.5 μm)33 and for the fabrication of integrated optical devices such as monolithic lasers34 and optical sensors.35 The choice of a suitable precursor is also fundamental for achieving WGs with low losses. Many precursors can be used, typical reagents being salts,36 alkoxides,37 and oxysalts.38 Another aspect that must be considered concerns the total molar concentration of the sol, which also plays an important role in the formation of a matrix with very low defects and good intermingling of the network. In particular, it has been demonstrated that a high total molar concentration yields a more viscous sol, but the final film presents a lower intermingling of the network, thus being less suitable for good WGs. A typical value of total molar ratio that permits one to obtain high optical quality films is about 0.5mol/L.39

As previously mentioned, the fabrication of an optical WG requires a sequence of deposition/heating cycles; if we consider a guiding film with a RI of about 1.57 at 1.5 μm, the minimum thickness needed to support one mode at this wavelength is around 1 μm. Referring to the dip-coating approach, a reasonable withdrawing rate is about 40mm/min: this value permits to deposit a layer thick some 30 nm for each cycle, so that 35 dips are necessary to obtain the required 1 μm film. Typical HT condition after each deposition cycle is 900°C for about 1 min, but the temperature and duration of HT strongly depend on the nature and molar composition of the binary system; for instance, in silica–tin oxide or silica–titanium oxide layers an HT of 900°C for 50 s may induce phase separation in the system and create nanocrystals (of SnO2 or TiO2, respectively) with the size around 4 to 5 nm, while in silica–hafnia or silica–zirconia, the same HT does not produce any phase separation.40 The final HT has also to be optimized according to the molar ratio of the binary systems. As an example, in silica–hafnia or silica–zirconia films with different molar ratios (i.e., 70%SiO230%XO2, 80%SiO220%XO2, 90%SiO210%XO2, where X=Hf or Zr) the HT time has to be decreased when the molar content of X is increasing. Typical duration of HT at 900°C in order to achieve full densification is around 5 min for the 70:30 composition, 3.5 h for 80∶20 and 30 h for 90∶10.41 On the other hand, increasing the temperature above 900°C (e.g., 1000°C) produces phase separation with the formation of nanocrystals, thus creating a GC matrix.


Glass Ceramic Waveguides

GCs may be defined as polycrystalline materials produced through controlled crystallization of base glass; they share many properties with both glasses and ceramics and can be considered as a class of nanocomposite materials, that is of those materials whose structural elements (clusters, crystallites, or molecules) have dimensions in the 1 to 100 nm range.42 Applications of GC in optics date back to 1968, with the development by Schott of Zerodur®, which has been largely used as low-thermal-expansion substrate of telescope mirrors.43 More recently, huge advances have been made both in the synthesis of size-tunable, monodisperse nanoclusters of various chemical compositions and in the development of techniques for their assembly into well-ordered nanostructured solids facilitating the synthesis of what are often termed designer materials. The importance of GC for the development of photonic devices appeared clear in the nineties, when one of the pioneering works was published by Wang and Ohwaki.44 Another important step was made in 1998 when it was demonstrated that subdecibel per kilometer loss could be achieved in Tm-doped fluoride optical GC fibers.45

GC WGs are produced by a suitable thermal treatment; laser annealing too may be quite effective.46 They are characterized by high transparency in the cerammed state and by the fact that rare-earth dopants are preferentially incorporated into the crystals, so that the emitting ions experience a lower phonon energy environment than in the glass matrix. The propagation losses of GCs depend, as usual, on absorption and scattering: absorption can generally be reduced to acceptable levels by purification of the starting materials and by careful melting practices; scattering, on the contrary, is not easily eliminated in glasses, and a general theory describing the relationship between structure and transparency in GCs is still under investigation.45,47 From an experimental point of view, four criteria must be fulfilled for a GC material in order to be suitable for optical waveguiding: particle size must be smaller than 15 nm (for visible light); interparticle spacing must be comparable with the crystal size; particle-size distribution must be narrow; no clustering of the crystals should occur. As an example, high-quality GC WGs may be easily produced by suitably processing the SiO2HfO2 matrix; for a molar concentration of HfO2 below 30%, the matrix remains amorphous if treated at 900°C, but an annealing at 1000°C for 30 min is sufficient to produce the formation of nanocrystals.48 In these conditions, it is possible to obtain a nanostructured system fulfilling the three conditions to achieve low-losses WGs: (i) nanocrystals (NCs) that present low size (4 to 6 nm), (ii) NCs with narrow particle-size distribution, and (iii) NCs homogeneously dispersed in the amorphous matrix.

GCs have thus proved to be one kind of the most promising materials for the fabrication of photonic devices like optical amplifiers, tunable solid-state lasers, luminescent solar concentrators and up-conversion luminescence devices.49,50 A number of papers, in particular, deals with planar and channel WGs; some examples refer to: (i) optical WGs produced by ion exchange in electro-optical GCs, demonstrating a high Kerr coefficient51 and (ii) WGs realized using sol–gel route, presenting low attenuation coefficient at 1.5 μm and suitable for single band amplification in the C band of telecommunications.5253.54.55


Local Modification of Optical Properties

Optical WGs can also be produced by varying the RI of the bulk material, either by diffusion processes (at low energies: ion exchange; at high energies: ion implantation) or by selective irradiation by a light beam (UV or fs-laser writing). In this section, the main characteristics of these processes will be summarized.


Ion Exchange

Ion exchange is a very old process that is based on the substitution of an ion already present in the glass (usually Na+) with another ion (e.g., Ag+, K+, and Li+) supplied from an external source (usually a salt melt).56 As a technique to color glasses, it dates back to the first millennium: it appears that Egyptians already used it in the sixth century to decorate dishes and pots in brownish yellow. A few centuries later, the Moors used this technique to stain the window glass of their palaces in Spain. The strengthening of glass surface by ion exchange (IE) became a standard industrial process in the 1960s. The suitability of IE technology to produce optical WGs in glass has been recognized since the early 1970s, when the pioneering works of Izawa and Nakagome57 and Giallorenzi et al.58 demonstrated the way to take advantage of the RI increase in IO, which is produced by the substitution of the sodium ion with another ion having higher electronic polarizability, such as silver. Different ion exchanges, e.g., with Ag, K, Cs, Rb, and Tl ions, have been investigated, and these processes have been extensively used for the fabrication of graded-index optical planar and channel WGs and IO components. Both ion diffusion from molten salt baths and the electro-migration of a metal film deposited onto the sample surface have been exploited. Some excellent review papers are available, and the reader is referred to them for an overview of the different processes and models.5960.61

Ion exchange produces graded-index WGs, and one of the critical issues in this area concerns the accurate determination of their RI profile. The most common method in IO is to reconstruct the RI profile starting from the experimental measurement of the synchronous coupling angles (i.e., the angles at which the light from a laser source is coupled into the WG modes). In fact, that knowledge is fundamental to proper designing of IO components and to minimize the insertion loss of any graded-index planar IO device. Different numerical methods and computational algorithms have been thus developed and tested for the index profile modeling; commercial software is now available for index profiling and simulation of the optical guided propagation. It is interesting to note that the analysis of the same ion-exchanged WGs in different laboratories did not give completely uniform results.62

On the fabrication side, it is quite obvious that one of the greatest advantages of the IE technique stays in the simplicity of the process, with its low cost and convenience for large-batch production. The simplest laboratory equipment for IE only requires an oven where the vessel (usually in stainless steel or fused quartz) containing the salt can be placed and then the sample is dipped in the molten salt. The only critical issue may be the accurate control of the temperature of the salt melt during long exchange processes. Planar and channel WGs are easily and consistently fabricated.60 A systematic study of thermal Ag+ IE used for the fabrication of optical channel WGs in a single-alkali glass was published by Li et al.63

The burial of channel WGs is of particular interest in order to achieve a more symmetrical modal field, and therefore an efficient matching to modal field of input/output fibers. Simple thermal annealing after IE may be useful, but the best results are obtained through field-assisted processes.64,65 In the latter case, the experimental apparatus is a bit more complex because of the problems related to electrical contacts on the sample and the need for electrical insulation between cathode and anode (which are often the molten salts themselves).

Moreover, since IE in glass allows manufacturing either surface or buried WGs, this technology is well adapted for three-dimensional (3-D) integration of passive and/or active devices provided that any parasitic light transfer between the two layers is avoided. The feasibility of this approach has been demonstrated by using thermal IE for the surface WG and thermal plus field-assisted IE for the deeply buried one.66

So many IO devices have been fabricated so far by using IE that it would be impossible to enlist them; let us just make the reference to a few of them, starting from pioneering works on WG lasers,67 arrayed waveguide gratings (AWG),68 add-drop filters,69 lossless or amplified splitters/combiners,70,71 up to WG laser arrays.7273.74


Ion Implantation

Ion implantation is a high-energy process that is often used in the semiconductor industry and is becoming more and more common in IO as well. In this process, a beam of atoms is ionized, accelerated to kinetic energies up to several MeV, and aimed at a suitable material target. A great advantage of ion implantation is that virtually any element can be inserted in the near-surface region of any solid substrate. When an energetic ion is implanted into a material, it looses its energy by electronic and nuclear damage. The nature of the process is quite complex and the interested reader is referred to one of the many books on the subject.75,76 Implantation in dielectric materials, however, is always producing a change in RI; depending on the process and the material, the change can be positive or negative. Often most of the damage occurs at the end of the ion track inside the substrate, which results in a volume expansion with consequent decrease of the physical density and decrease of the RI. An optical barrier is thus created that permits the confinement of light in a narrow layer between the substrate’s surface and the barrier. This confinement can be rather weak and a so-called tunneling effect may take place, with leakage of energy of the propagating beam. In some cases, however, the RI might first experience a positive change in the main region of the ion range, forming an enhanced index well, which provides better confinement. Accordingly, the confinement structure of ion implanted WGs can be divided in two types: “barrier” and “well+barrier.” The penetration depth profile of the vacancies produced by the ion beam is generally calculated with the Stopping and Range of Ions in Matter (SRIM) code.77

Optical WGs have been fabricated by ion implantation in more than hundred optical materials, including crystals, glasses, and polymers,78,79 and also materials where other techniques failed, as tellurite glasses.80,81 Early attempts to use ion implantation for glass WGs had been made by bombarding silica substrates with H+ ions accelerated at 1.5 MeV82 and with Li+ ions accelerated at 32 to 200 keV.83 Figure 4 shows a graphical comparison of 3.5 MeV implanted N+ distribution in an Er3+-doped tungsten tellurite glass as obtained by SRIM with the barrier layer boundaries obtained by spectroscopic ellipsometry (SE).81 In the plot, two fluences are considered, equal to 1×1016 and 8×1016ions/cm2, respectively. A three-layer optical model was applied in the evaluation of the SE data. The first layer, adjacent to the substrate, represents the stopping region. The second layer is the region that the implanted ions traverse before they stop. The third layer is a surface roughness film taken into account on the basis of effective medium approximation. RI difference between guiding and barrier layers varies in the range 3×102 to 9×102, depending on the fluence. The blue and red line pairs in Fig. 4 represent the two boundaries of the barrier layer (layer 1) of the irradiated WGs, obtained from the SE simulations.

Fig. 4

Graphical comparison of implanted N+ distributions in an Er-doped tellurite glass, obtained by SRIM (curve with squares), and WG barrier layer boundaries obtained by spectroscopic ellipsometry. Data refer to energy irradiation E=3.5MeV, with fluence of 1×1016 and 8×1016ions/cm2 (Ref. 81).


The well (layer 2) is delimited by the sample surface (z=0μm) and the upper (left) boundary of the barrier. Centre of the calculated barrier layer is shifted downwards with respect to the center of the N+ distribution. This may be attributed to the fact that SRIM slightly overestimates stopping power, and consequently predicts lower ranges than the experimental ones.

Ion implantation, moreover, may be very effective in introducing a suitable dopant into a glass substrate or a glass WG, with the aim of increasing the functionality of the glass. Particular attention has been directed to the implantation of erbium84,85 or Neodymium86 to achieve the capability of optical amplification. A device fabricated by implanting erbium ions with the concentration of 2.7×1020cm3 in alumina films was claimed to be then (1996) the world’s smallest erbium-doped optical amplifier.85 The formation of metal nanoparticles in glass by ion implantation has also been attracting the large interest for the fabrication of nonlinear optical devices; a comprehensive review of nonlinear optical properties of implanted metal nanoparticles in various transparent materials was recently published.87


UV Laser Writing

The fabrication of PICs by all the methods considered so far also requires the use of cleanroom technologies such as lithography and chemical or plasma-based etching, in order to define the channel WGs and the other optical components. Since the lithography and etching approach is costly, cumbersome, and slow for development; in recent years, the search for fast direct writing techniques has been growing up.88 Electron-beam writing is not effective in oxide glasses; chalcogenide glass thin films, however, have been investigated as e-beam resists for nanoscale and ultrathin applications in MEMS/NEMS technology,89 and recent results have proved that ridge optical WGs can be obtained by e-beam writing in GexSe1x chalcogenide films.90 Laser writing, however, exhibits many more advantages and has eventually emerged as a viable rapid-prototyping and small-batch-production technique.

Direct UV laser writing is one of the available effective techniques; it exploits the absorption of a specific laser wavelength (generally at around 240 nm) by a photosensitive material to produce a permanent modification of the RI. Despite the disadvantage of requiring photosensitive/photorefractive properties, in practice, this technique can be used on a wide range of materials, obviously including polymers91,92 and crystalline materials such as lithium niobate,93 but also ion exchanged pyrex glasses94 and, more important here, Ge-doped silica glasses.

Historically, the way to UV writing in IO was opened by Chandross et al.,95 who used a photochemical reaction produced by a 364 nm laser to fabricate 4-μm wide optical WGs in doped polymer films. As to glassy materials, direct UV writing in a SOS structure was first reported by Svalgaard et al., who demonstrated buried single-mode channel WGs in Ge-doped silica films with a RI increase of 103.96 Shortly, later the same group and others demonstrated low-loss (0.2dB/cm) WGs 97,98 and components such as directional couplers and power splitters.99 Since then, numerous works have been performed regarding the fabrication of planar lightwave circuits (PLCs), using different photosensitive materials and producing fundamental photonic structures such as optical WGs,100101.102.103.104 diffractive gratings,105106.107 and photonic crystals.108

Although the complete understanding of the microscopic origins of the index variation remains an issue, complementary models have been proposed in order to explain the phenomenon. The three main mechanisms that can be responsible of the modification of the RI can be summarized as follows: (i) color centers, (ii) stress relaxation, and (iii) volume changes; the contribution ratio of each mechanism to the RI change, however, is still under investigation. In the color center model, strong UV absorption due to localized electronic transitions of laser-induced defects gives rise to RI changes in the visible/infrared spectral region according to the Kramers–Kronig relationship.109,110 A typical example is represented by the SiO2GeO2 glass that presents an intense absorption band around 240 nm, originated from Ge related oxygen deficient defects (GODC). The underlying premise of this model is the excitation of localized precursor defects or dopants below the bandgap such as GODC at 240 nm,111 Eu2+ at 250 nm and Ce3+ at 260 nm.112 Moreover, an improvement of the effects can be achieved by loading the material with suitable elements such as boron,113 deuterium,114 and hydrogen.115

A second mechanism is related to the so-called stress relaxation through the photoelastic effect;109 this theory is based on the hypothesis that the RI changes originate from residual stress in materials due to a difference in thermal expansion coefficients between film and substrate. Finally, the last contribution to photosensitivity arises from volume changes such as densification and expansion, which are observed in the form of valley or bumps along the writing path. According to Lorenz–Lorentz relationship,116 compaction increases the RI while the expansion decreases it. The type of volume change depends on the glass structure, which in turn is determined by its composition and the fabrication technique used for its synthesis. For example, typical glasses that show a compaction behavior after irradiation are (i) Ge-doped silicates106 and (ii) gallium–lanthanumsulphides,117 while As2S3 and Zr–Ba–fluoride glasses exhibit a photoexpansion behavior due to a widening of interlayer distances.118

From a fabrication point of view, the most important parameters of the writing process are: (i) wavelength of the laser, (ii) operation regime, and (iii) composition and geometry of the glass samples. The correct parameters have to be chosen having in mind that focusing high energy into a small volume of material can have detrimental effects if the energy dissipation from the exposed region is not rapid enough. Thermalization of a small volume due to large amounts of energy being coupled into a material with low thermal conductivity may result in local melting and even in vaporization of the material; both these effects are undesirable since they surely lead to an increase of propagation losses, if not to a stop of waveguiding. One direct writing approach uses a cw laser, normally with a wavelength of 244 nm, focused on the photosensitive material; the actual writing occurs translating the structure beneath a tightly focused laser beam by a computer-controlled high-precision translation stage. The typical scanning speeds range from 1 to 5000mm/min, resulting in very short exposure times of 0.1 to 400 ms.100,101,119 Another approach makes use of a pulsed laser (usually, a KrF excimer laser source operating at 248 nm) and the definition of the photonic components (WG, grating, etc.) occurs using a single step UV exposure through an amplitude mask. Generally, the mask is constituted by a suitably patterned Ti film, with the thickness of 200 nm, deposited on the photorefractive material. Typical parameters are pulse fluence lower than 36mJ/cm2 to prevent damaging of the mask, repetition rate (RR) of 10 Hz, and cumulative exposure dose up to 20kJ/cm2.103,106 Finally, an alternative approach is based on the interference of two UV beams producing a tightly focused writing spot, near circular, that presents micron-order dimension at the intersection point.120 A typical experimental setup is based on cw frequency-doubled Ar-ion laser (λ=244nm) with the beam power controlled via an acoustic optical modulator; typical writing values for germanosilicate glasses are: (i) laser power of 100 mW at 244 nm, (ii) translation speed from 10 to 120mm/min, and (iii) fluence of the order of few kJ/cm2. Indeed, a significant advantage of the direct writing system with an UV laser is the small spot size of the focused laser beam, which can be used to inscribe both WGs and gratings.121 In the direct grating writing (DGW), rather than using the wide area exposure such as that from a phase mask, the dimensions of the UV induced structure are determined by the focal spot size. A DGW experimental setup is sketched in Fig. 5, together with a photo of the actual system.121

Fig. 5

Illustration of (a) direct grating writing (DGW) setup; (b) crossed beams focused on the core layer of the silica-on-silicon substrate; (c) photo of DGW system (Ref. 107).


Nowadays, the direct UV writing technique can be considered a consolidated method for the realization of photonic devices; as an example, Stratophase (an UK Company) has recently acquired UV writing technology in order to develop lab-on-chip systems, ranging from individual disposable sensors for biotechnology to multiplexed sensor networks in pharmaceutical manufacturing.122 Even complex integrated optical circuits, useful for the realization of quantum optical states and information networks, have been very recently implemented by UV writing technique.123,124


Femtosecond-Laser Writing

Femtosecond-laser writing (fs-writing) is now one of the most efficient techniques for direct 3-D microfabrication of optical WGs and micromachining of transparent optical materials.125 The seminal paper in this field was published by Hirao, who is demonstrating the possibility to modify the RI of pure and Ge-doped silica glasses as a function of the radiation dose.126 Then, a number of works have been performed concerning not only the fabrication of optical WGs, photonic crystals, diffractive gratings, etc. in various transparent materials, but also micromachining (namely, drilling, etching, and milling). The most important features of fs-writing are the following ones: (i) it is a single-step and mask-less process, so that cost and time consuming are reduced; (ii) it can be applied to different materials (i.e., glasses, crystals, and polymers), just modifying the irradiation parameters (repetition rate, fluence, etc.); (iii) it is an intrinsically 3-D technology because it is possible to induce material variation and to realize optical devices at any arbitrary depth in the substrate. Moreover, by exploiting its micromachining capability, fs-writing makes possible the integration on the same substrate of the IO circuits with microfluidic channels,127,128 as depicted in Fig. 6.129

Fig. 6

Illustration of femtosecond-laser direct writing used to add optical WGs to a lab-on-a-chip device designed for capillary electrophoresis. The optical WGs, coupled to optical fibers, excite fluorescence in a highly localized region in the microchannel, and guide emissions to a detector (Ref. 129).


Even in the case of fs-writing, the analysis of the process mechanisms is quite complex and of course also depends on the linear and nonlinear optical properties of the material. The physical origin can concurrently involve several processes, such as ionic rearrangement, lattice stress, heat accumulation, defect creation, changes in local stoichiometry, thermal diffusion, and changes in the electronic polarizability.125,130,131 It is generally agreed, however, that the laser energy is rapidly absorbed through a combination of multiphoton absorption and avalanche photoionization. Mechanisms leading to the formation of WGs and optical components have been investigated in crystalline materials, too.132,133

For low laser intensities, the glass is heated by each pulse and rapidly cools through thermal conduction between pulses. The resulting RI change is determined by the relationship between the density of the glass and the cooling rate, and by the residual stresses caused by this density gradient. For high laser intensities, a plasma forms within the glass, creating a large charge separation that leads to a Coulomb explosion. This results in a shockwave: the pressure induces RI changes with an inhomogeneous redistribution of the material within the modified region, and the stress induces RI changes in the surrounding material. A model that describes the theory of femtosecond laser modification mechanisms is summarized in Fig. 7.130

Fig. 7

Illustration of the physical mechanisms of the femtosecond laser writing method. [adapted from Reichman (Ref. 130)].


From a fabrication point of view, the most important parameters that have to be taken into account during the writing step concern writing geometry, pulse energy, and RR.

Depending on the direction of translation of the sample under the laser beam, longitudinal or transverse writing can be adopted for the fabrication of optical devices. Longitudinal writing permits to obtain WGs with a cylindrical symmetry; their length, however, is limited by the working distance of the lens which, for a typical focusing objective with NA=0.4, is approximately 5 mm.

In the transverse writing scheme, the sample is scanned orthogonally relative to the incoming laser; in this case, the working distance no longer restricts the WGs length and many devices at different depths can be written into the sample, providing 3-D optical circuits. The disadvantage of this approach is that the WG cross section is asymmetric, due to the ratio between depth of focus and spot size. The asymmetry produces elliptical WG cross sections with elliptical guided modes, which cause a poor coupling with external to optical fibers. Suitably shaping the writing laser beam, however, can help to overcome the focal volume’s asymmetry problem; several solutions have been proposed, including astigmatic focusing,134 slit focusing,135 deformable mirror beam reshaping,136 and multiscan writing.137

The laser pulse energy is typically the most influential experimental variable for all the writing configurations. Adjusting the laser fluence by an order of magnitude can cause dramatically different results: from no modification to the controlled modification used for producing optical devices to uncontrolled damage.138 Considering glassy materials, such as fused silica, phosphate glass, and heavy-metal oxide glasses,139 typical energy pulse values for the realization of WGs with low losses are around few μJ in the case of low RR (1÷250kHz) or of the order of hundreds of nJ in high repetition regime (MHz). For slightly higher pulsed energies, the formation of birefringent nanostructures can be observed, which can lead to photonic devices with polarization dependent characteristic.140 For even higher pulse energies, fs-writing can induce microexplosions, which results in the formation of microvoids; an interesting application for this type of systems can be represented by high density 3-D data storage.141,142

The RR is also a crucial parameter for the realization of optical devices; traditionally, kHz RR amplified fs lasers have been used for fs device fabrication, but the recent development of high power oscillators and other high-RR fs sources has opened up the possibility of writing WGs with RR>1MHz. The main differences reported when using high-RR lasers are an increase in the perceived line diameter, and a potentially greater RI modification.143 These features are related to the fact that with high-RR lasers there is insufficient time between pulses for the heat to diffuse out of the focal region, and as a result, heat accumulation occurs.144,145 Additionally, it has been observed that MHz systems provide better quality WGs in some transparent glasses, while kHz systems are preferable for other materials. Currently, it is still unclear why some materials respond better with one laser respect to the other. In a recent study, the thermal stability of femtosecond laser modification inside fused silica has been investigated, and the results have been related to different types of bond rearrangements in the glass network.146

Undoubtedly, fs-laser writing technique permits to obtain low-loss WGs in different types of glasses, as proved by a number of reports: Nasu et al.137 have demonstrated that it is possible, using a multiscan writing scheme, to induce in fused silica a RI change of 4×103, suitable for WGs with propagation loss of 0.12dB/cm at 1550 nm and for low loss coupling to single-mode fibers; in phosphate glasses, using a scan of 20μm/s with a 1 kHz, 150-fs Ti:Sapphire laser with 0.3 NA microscope objective, and 5 μJ pulse energy, devices were produced with damping loss of about 0.25dB/cm at 1550 nm;134 in heavy metal oxide, using a 1 kHz, 100-fs Ti:Sapphire laser with 0.42 NA objective, and 1.8 μJ pulse energy, WGs with loss below 0.7dB/cm at 633 nm were realized.139 It is also worth pointing out that fs-laser micromachining has been successfully applied in a number of more exotic glasses, such as tellurite glasses,147 where other fabrication techniques do not easily apply; oxyfluoride silicate systems,148 that are considered a promising host for RE because they combine the attractive spectroscopic properties of the fluoride glass with the structural compatibility and stability of silica; Bi-doped silica glasses,149 which exhibit broadband emission around 1.3 μm; high quantum efficiency Er-doped Baccarat glasses;150 phospho-tellurite glasses,151 that can exhibit ultra-broadband amplification in S-C-L telecom bands (1460 to 1625 nm); Er–Yb-doped tellurium zinc glasses;152 Tm:ZBLAN glass,153 where in a 9-mm long planar chip, an 1.89 μm free-running cw laser has been fabricated, which produces 205 mW and achieves a 67% internal slope efficiency, corresponding to a quantum efficiency of 161%. With reference to this last result, as a proof of the enormous advance in technology in the last 12 years, let us just recall that in the first active device obtained by fs-laser writing in a commercial Nd-doped (2×20ions/cm3) silica glass rod a signal enhancement of 1.5 dB/cm at 1054 nm was achieved with an incident pump power of 350 mW.154

Finally, the direct-write approach has proved to be suitable for the rapid development of sophisticated quantum optical circuits and their scaling into 3-D.155,156


Conclusions and Perspectives

The advance of modern technology is still largely driven by miniaturization, and PICs are expected to play an even more important role in optical communications, imaging, computing, and sensing. Recent developments in materials and technologies have expanded the number of optical functions to be implemented in a single integrated optical chip. Two major platforms for PICs are constituted by SOI hybrid technology and InP monolithic technology. SOI WG structures are defined on a Si wafer (e.g., 200 mm or 8 in.) in a CMOS pilot line. A typical SOI wafer consists of a 220 nm Si core layer on top of a 2 μm buried SiO2 cladding layer fabricated on the silicon wafer. Direct band gap III–V layer (InP/InGaAsP) heterostructures can then be integrated on top of the SOI WG substrate; one approach makes use of a polymer bonding layer to bond III–V dies onto the SOI, so that, after removal of the original InP growth substrate, only a thin epitaxial InP/InGaAsP film remains attached to the SOI WG circuit: laser diodes and photodetectors can finally be fabricated in it on a wafer scale and lithographically aligned to the underlying SOI WG circuit.157 An alternative approach, followed among others by Infinera,158 uses a single material—indium phosphide (InP)—with which it is possible to fabricate all the necessary optical functions on a single semiconductor chip. Infinera’s DTN-X platform supports 500Gb/s superchannels based on next generation coherent 500Gb/s PICs, which integrate over 600 optical functions into just two optical chips, one for transmit and one for receive.

Despite these challenging competitors, glass remains one of the most important materials even in the era of photonics; perspectives of a large functional integration based on SOS and novel glass platforms are becoming quite real, due to the advanced development of fabrication technologies of glass WGs.

One should not forget some pioneering works in this area, especially by groups at AT&T Bell Labs and at NTT Photonics Laboratories, such as the fabrication by Adar et al.159 of strong Bragg reflectors, nearly polarization independent, embedded into fiber-matched silica-on-silicon WGs; or the development of optical switches and WDM modules at NTT using silica-based PLC technology since the 1980s.160,161

Ion exchange in glass, PECVD, and FHD are mature technologies, which have already led to the production of high-quality, low-loss, low-cost passive components for optical communication systems and optical interconnections. It is worth recalling that record low losses below 1dB/m have been achieved in different glass systems and by different processes: for instance, Adar et al. reported single-mode propagation loss of 0.85dB/m in phosphorus-doped cores deposited through plasma-enhanced CVD,162 while Kominato et al., using a larger, multimode core design, reported 0.3dB/m propagation loss for germanium-doped cores deposited by flame hydrolysis.163

Integrated optical devices made by other processes, like sol–gel deposition, ion implantation, and fs-laser writing, are perhaps still not fully ready for the market, but these technologies keep having a great potential: in its many variations, the sol–gel process offers a viable route to the preparation of virtually every kind of glasses and composites, in any desired shape, while ion implantation and fs-laser writing permit to define even 3-D guided structures in a large variety of materials, amorphous, and crystalline. Femtosecond laser written WGs exhibit low losses, and photonic lattices with one or two transverse dimensions fabricated by this technique in fused silica have emerged as a versatile system for the experimental investigation of light propagation in discrete optical systems with Kerr nonlinearity, with possible application in photonic circuitry based on switching with blocker solitons.164

Among the emerging deposition technologies in photonics one should also include atomic layer deposition (ALD), which is a CVD-type process based on sequential, self-limiting surface reactions and typically performed at low temperature, capable of thickness control at the Ångstrom or monolayer level.165 ALD films remain extremely smooth, pinhole-free, and conformal to the original substrate: all qualities that are extremely important in the case of waveguiding dielectric films and integrated optical components. As a matter of fact, the basic technology dates back to 1974, with the pioneering work of Suntola.166 Atomic Layer Evaporation (ALE—as it was named in that first paper) epitaxy soon became the elective method of depositing thin semiconducting films on a substrate for thin film electroluminescent devices’ production. The term ALE switched to ALD in the 2000s, due to the fact that amorphous dielectric films were becoming more and more important and that therefore epitaxy was no more a peculiarity. The excellent characteristics of ALD films have recently increased the interest toward photonic applications, with the demonstration, among others, of low-loss Al2O3 WGs167 and of amorphous and crystallization-controlled TiO2 WGs.168,169 Moreover, the ability to conformally coat nanostructured surface results in unique possibilities,170 and the development of ALD processes for novel materials has a strong potential for significant breakthroughs in the fabrication of monolithically integrated devices.

Nanostructured and nanocomposite glasses (e.g., GCs) are also assuming larger importance, due to the enhancement of their optical, spectroscopic, and thermal properties with respect to the corresponding amorphous matrices.

New horizons have also been opened by the development of another versatile platform, based on chalcogenide glasses, which exhibit high RI, high mid-IR (λ=3 to 20 μm) transmittance, and high nonlinearity. Chalcogenide glasses can be formed with a variety of compositions and doped with additional elements to provide further functionality (e.g., with rare-earth elements). 3-D photonic circuits can be written by femtosecond laser.171 Hybrid integration of chalcogenide glass WGs and quantum cascade lasers has also been demonstrated.172 Demonstrated or envisioned applications include light amplification and generation,173174.175 all-optical signal processing,176 spectroscopic chemical sensing,177,178 astrophotonics, and biochemical sensing.170,179

Finally, the quest for high-performance platforms for integrated nonlinear optics has led to two new material structures, which also offer CMOS compatibility and have already achieved considerable success, based on silicon nitride (Si3N4) and high-index doped silica, trade named Hydex.180 An integrated silicon and ultra-low-loss Si3N4 WG platform has also been demonstrated, with minimum propagation loss measured in the silicon nitride core equal to 1.2dB/m in the 1590-nm wavelength regime.181 As to Hydex™, it was developed as a high-Δn system for low-loss WGs;182 it is a robust material that is deposited through conventional CVD processes, with RI contrast adjustable from 0% to over 20%, and propagation losses estimated to be as small as 0.06dB/cm.183 Using the dispersion characteristics of this glass, supercontinuum (SC) generation was achieved in a 45-cm long spiral WG, obtaining an SC spectral width of >300nm at both 1290 and 1550 nm.184

We can therefore conclude that the prospects of integrated optical devices in glass are still very good, with continuously growing applications in the area of on-chip devices and biosensors. Optimization of the synthesis processes of glasses tailored for the specific application and of the WG fabrication technologies may guarantee that new record performances of glass PICs will be achieved.


The authors are grateful to Maurizio Ferrari for his valuable comments and to Alessandro Carpentiero for his technical assistance and figure drawing; both are at IFN-CNR in Trento.


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Giancarlo C. Righini is director of research at Enrico Fermi Center in Rome, Italy. He was the director of the DMD Department (CNR, Rome) and research director at IFAC CNR (Florence), where he is now associate scientist. His research interests have included holography, geodesic optics, fiber, and integrated optics. He is author of over 200 papers in JCR Journals and of over 150 papers in SPIE Proceedings. He is fellow of SPIE, OSA, EOS, and SIOF.

Andrea Chiappini received MS and PhD degrees in physics from the University of Trento in 2003 and 2006, respectively. Since August 2007 he has been a postdoctoral researcher at the CNR–IFN section of Trento. Since 2003, his principal activity concerns the investigation of the properties and processing of confined structures for photonics. He is a coauthor of 33 papers in JCR Journals. He is member of the Italian Society of Optics and Photonics (SIOF).

© The Authors. Published by SPIE under a Creative Commons Attribution 3.0 Unported License. Distribution or reproduction of this work in whole or in part requires full attribution of the original publication, including its DOI.
Giancarlo C. Righini, Andrea Chiappini, "Glass optical waveguides: a review of fabrication techniques," Optical Engineering 53(7), 071819 (14 March 2014). https://doi.org/10.1117/1.OE.53.7.071819






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