Insight into the structure and chemical durability of Cr-bearing lead crystal glass

Insight into the structure and chemical durability of Cr-bearing lead crystal glass | Research Square window.SnipcartSettings = { analytics: { enabled: false } }; (function() { var accessVector = localStorage.getItem('access_vector') || ''; window.dataLayer = window.dataLayer || []; if (accessVector) { window.dataLayer.push({ user: { profile: { profileInfo: { snid: accessVector } } } }); } })(); (function(w,d,s,l,i){w[l]=w[l]||[];w[l].push({'gtm.start':new Date().getTime(),event:'gtm.js'});var f=d.getElementsByTagName(s)[0],j=d.createElement(s),dl=l!='dataLayer'?'&l='+l:'';j.async=true;j.src='https://www.googletagmanager.com/gtm.js?id='+i+dl;f.parentNode.insertBefore(j,f);})(window,document,'script','dataLayer','GTM-K279D39R'); Browse Preprints In Review Journals COVID-19 Preprints AJE Video Bytes Research Tools Research Promotion AJE Professional Editing AJE Rubriq About Preprint Platform In Review Editorial Policies Our Team Advisory Board Help Center Sign In Submit a Preprint Cite Share Download PDF Article Insight into the structure and chemical durability of Cr-bearing lead crystal glass Lea Brunswic, Frederic Angeli, Thibault Charpentier, Stephane Gin, and 7 more This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-5284279/v1 This work is licensed under a CC BY 4.0 License Status: Published Journal Publication published 02 May, 2025 Read the published version in npj Materials Degradation → Version 1 posted 9 You are reading this latest preprint version Abstract The scientific understanding and demonstration of the immobilization of heavy metals (notably lead and chromium) in food contact materials is crucial for the safety of environment and humans. To tackle this issue lead crystal glasses doped between 50 and 2000 ppm of chromium oxide were carried out under severe aqueous alteration conditions (acetic acid 4% (v/v), pH 2.4, 70°C, 330 days). The increase in Cr leads to a decrease in the Pb release into the solution. The leached Cr content was lower than Pb, itself much lower than alkali ones. Structural characterization before and after alteration points out the presence of Cr(III) exclusively, with no redox changes in the course of alteration. Cr and Pb are partially retained during alteration near cationic domains, less accessible to protonated species. Cr favors the Si recondensation in the rich non-bridging oxygen (NBO) mixing sites, leading in an increase of glass polymerization within the altered layer. Physical sciences/Materials science Physical sciences/Materials science/Condensed matter physics Physical sciences/Chemistry Physical sciences/Chemistry/Materials chemistry Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 Figure 7 Figure 8 Figure 9 INTRODUCTION Chromium is used as a colorant in the glass industry rendering different colours in function of its oxidation degree, notably blue for Cr(II), green for Cr(III) and yellow for Cr(VI). The latter was introduced in the 1970s as a replacement for uranium in tinting wine bottles, after uranium was banned due to well-documented human health risks. But in 2001, after working on Pb, Cd and Hg, a group of international experts gained interest for hexavalent chromium following a report by the World Health Organization 1 about the toxicity of Cr(VI) towards environment and human health. These experts highlighted the scientific challenge of accurately distinguishing between Cr(III), considered harmless, and Cr(VI) in various media, including solids and liquids, as well as inhibiting the oxidation of Cr(III) to Cr(VI).The latter must be carefully controlled and immobilized, particularly in the case of glass containers intended for food consumption or packaging, where prolonged contact between the glass and the edible contents occurs. A method was then proposed for the detection of Cr(VI) in daily glass containers with a claimed sensibility of 2 mg per kg of glass. The method consists in total dissolution of the glass through strong acidic attack and analysis of Cr(VI) by spectrophotometry 2 . About 20 years later, the European commission has lowered the authorized Cr(VI) content to 0.005 mg/kg for liquid or sticky toy material 3 . Another comparison can be made with plastic materials, since the European Regulation on articles intended to come into contact with food was amended in 2020 4 taking into account the great difficulty to differentiate Cr(III) from Cr(VI). Therefore two different regimes were promulgated, i) if it can be proved that the presence of hexavalent chromium in the plastic material can be excluded because it is not used or formed during the entire production process, a migrating limit of 3.6 mg/kg is applied but, ii) if it is not the case, then the second regime is enforced: a migration limit of 0.01 mg/kg corresponding to the detection limit for total chromium according to current tests performed by the National Reference Laboratories. The urge for lowering the authorized thresholds raises the question of the scientific limits for Cr(VI) detection routinely and draws attention to the fundamental understanding of the structural role and behavior of chromium in glass. Addressing these challenges from a materials science perspective, using advanced analytical techniques, could prevent the complete banning of chromium in all oxidation states from industrial use, provided it cannot be definitively demonstrated that Cr(III) cannot transform into Cr(VI). Currently, Cr(VI) is subject to authorization in Europe under Appendix XIV of the Registration, Evaluation, Authorization, and Restriction of Chemicals (REACh) regulation, which lists substances of very high concern (SVHC) 5 . This regulation compels industrial manufacturers to reconsider their use of chromium, which remains essential in its Cr(III) form, particularly in the long-standing process of producing green-colored lead crystal glass. The main goal of our study is to understand the effects of chromium on the structure and durability of lead crystal glass. The alteration of lead crystal glass has already been studied through various works in the literature, especially with acetic acid solution 6,7 and at the same leaching temperature, 70°C 6,8 . These works have already evidenced the rapid initial leaching of alkalis at the first stage of alteration which is then inhibited over time by the increase of the diffusion distance and the repolymerization of the silicate network with the formation of a diffusive barrier of a few hundreds of nanometers. The release of lead is significantly lower than that of alkalis, and its leaching rate becomes nearly negligible after the reorganization of the silicate network, indicating effective retention of lead in the altered layer over the course of several years 8 . But to date, the impact of the leaching of chromium on the other constitutive elements of lead crystal glass (Si, Pb, Na and K) and on the solution chemistry have not been reported. The structure of Cr-free lead crystal glass of the same composition has already been examined extensively by solid-state high resolution Nuclear Magnetic Resonance (NMR) 6,8,9 . Building on from this knowledge, further structural characterizations would allow to determine the structural role of chromium and its interactions with the constitutive elements in a lead crystal glass matrix. To answer all these questions, 4 ingots of lead crystal glasses with roughly 50, 250, 500, 2000 ppm of chromium oxide (Cr 2 O 3 ) were prepared by adding the coloring oxide to the plain crystal glass creating a palette of green hues from light tender green to deep forest green. These glasses were then leached in acetic acid 4 % (v/v), considered as the reference medium for food contact studies 10 , at 70 °C to accelerate alteration mechanisms, under the form of powder and slabs up to 330 days. Slabs were analyzed by micrometric X-Ray Fluorescence (µXRF) and X-Ray Absorption Near Edge Spectroscopy (XANES) at the Cr K-edge. These techniques allowed us to determine the oxidation degree of chromium in the pristine and altered glass, tracking potential dismutation mechanisms of this element induced by the alteration process. These results were supported by Optical Absorption Spectroscopy performed on the pristine glass slabs. Finally the structural changes of the pristine glass structure brought by the addition of chromium were uncovered by solid-state 29 Si and 207 Pb NMR spectroscopy. RESULTS Glass composition The glasses shown on Figure 1 were found to be homogeneous and fully vitreous under scanning electron microscopy (SEM) that is a micrometric scale. They were analyzed by electron micro probe analyzer (EMPA) and the results are available in Table 1 displaying Cr concentrations ranging from 0.002 mol% (BAC_Cr50) to 0.028 mol% (BAC_Cr2000) and minimal composition differences besides the Cr content. Table 1 Composition of the studied glass analysed by electron micro probe analyzer (EMPA) expressed in mol% of elements. Cr 50 Cr 250 Cr 500 Cr 2000 Si 26.8 26.8 26.9 26.8 Na 0.6 0.6 0.6 0.6 K 7.2 7.2 7.3 7.3 Pb 3.6 3.6 3.5 3.6 Sb 0.1 0.1 0.1 0.1 Cr 0.002 0.006 0.013 0.028 Leaching of chromium colored lead crystal glasses During 330 days, glass powders of BAC_Cr50, BAC_Cr250, BAC_Cr500, BAC_Cr2000 were altered with a high SA/V geo ratio (500 m − 1 calculated from equation 1 giving access to the Equivalent Thickness (ETh) of glass altered per element from equations 2 and 3 over time. The ETh for Si, Pb, Na and K, the main glass constituents, are represented for 112 days in Figures 2a, 2b, 2c and 2d, respectively. The alkalis are released through an ion-exchange mechanism (linear release as function of the square root of time), as expected from the literature 6–8 . Silicon showed the lowest alteration rate of all measured elements, about 100 times smaller than for alkalis, indicative of a slow hydrolysis reaction of the silicate network compared to the fast ion-exchange mechanism. This results in a linear release of Si as a function of time. There is no relation between Cr content in the glass and the alteration rates of Na, K, and Si. The increasing concentration of dissolved silica reduces the rate of Si‒O‒Si hydrolysis and favors the re-organization of the alteration layer 11 . Polymerization may contribute to the formation of a diffusive barrier, along with other phenomena, which could explain the sharp decrease in alkali alteration observed after 14 days 12 . Unlike the other constitutive elements studied (Na, K and Si), the leaching of Pb showed a different behavior. A final sampling at 330 days confirmed the consistent long-term behavior of Pb and Cr. (Figure 3). Additionally, the Eth(Pb) showed a clear correlation with the Cr content in the glass, demonstrating a decrease in Pb leaching as the Cr content increased. Moreover, the behavior of Cr followed the linear release of Si (Figure 3). At 330 days, the Cr and Pb leached layer is about 200 nm and 500 nm, respectively. The evolution of Eth(Na, K, Pb) have been represented as a function of the square root of time, as displayed in Supplementary Figure 1a for Na, 1b for K and Figure 4a for Pb. The trend for Na and K are fully linear confirming the diffusion controlled mechanism of alteration. For Pb, a domain of linearity between 0 and 14 days of alteration can be noticed in figure 4a, from which diffusion coefficients were calculated using equation 5 for each of the Cr-bearing glasses. These coefficients D(Pb) are presented in function of the logarithm of the molar content in Cr of the glasses in Figure 4b, exposing a linear correlation between the decrease of the diffusion coefficient of Pb and the logarithm of the molar Cr content in these glasses. Pristine glass structure and properties For many decades, various relationships between alteration behavior and glass structure have been highlighted and investigated by the glass community across a wide range of glass compositions, including lead crystal glass 6 . Since the results of the present work revealed differential leaching kinetics that depended on a single compositional variable, namely the Cr content, investigations into the redox state and structure of the pristine glasses were conducted. The oxidation degree of Cr was first determined by optical absorption spectroscopy to gain information on the configuration of Cr in the bulk pristine glasses. Then, the structure of glasses was addressed through 29 Si and 207 Pb solid-state NMR. Optical absorption spectroscopy For Cr, the most common oxidation states found in silicate glasses are Cr(III) and Cr(VI) which have close but distinct absorption bands in the visible and near ultraviolet regions of the light spectrum 13 . The presence of both species in the Cr-bearing pristine glasses has been investigated by optical absorption spectroscopy and the results are shown in Figure 5. The spectra obtained on pure crystalline reference compounds of Cr(III) and Cr(VI) (extracted from Bamford, 1977 14 ) are displayed on Figure 5. The spectrum of Cr(III) is characterized by two large Gaussian shaped bands of absorption centered at 15 000 and 22 000 cm − 1 which are responsible for the green color of Cr(III)-bearing materials. They account for the spin-allowed, parity forbidden d–d transitions of octahedral Cr 3 + : 4 A 2 g → 4 T 2 g and 4 A 2 g → 4 T 1 g . The most oxidized specie of Cr, Cr(VI), is identified by an unique Gaussian shaped band of absorption, centered at 27 500 cm − 1 and yields yellowish colored glasses, especially when unmixed with other Cr species. The spectra obtained on pristine Cr-bearing glasses were collected on large portions of the glasses (about 7 mm 2 ) and are presented above the reference spectra clearly showing the presence of Cr(III). The raising intensity of the bands located at 15 000 and 22 000 cm − 1 went along with the increase of the total Cr-content in the glasses. From the Beer-Lambert law, the absorbance of a glass depends on the molar extinction coefficient of its compounds, the length of the light path and the concentration of the optically active species, in our case Cr(III) and Cr(VI). It has been calculated that for Cr(III) in silicate alkali glasses, the molar extinction coefficient ε Cr ( III ) is around 18-20 L.mol − 1 .cm − 1 14–16 whereas for Cr(VI) the molar extinction coefficient associated with the absorption band at 27 500 cm − 1 is around 4200 L.mol − 1 .cm − 1 in the same glass matrices 13,17,18 . Hence an absorbance more than 200 times greater for Cr(VI) compared to Cr(III) at equal concentrations and light path length. Considering our least concentrated sample, with a given light path and a given total Cr concentration of 0.002 mol%, the absorbance of equal concentrations of Cr(III) and Cr(VI), which depend directly on their respective molar extinction coefficients, is then 200 times more intense for Cr(VI) than Cr(III). Consequently, a 200 times lower concentration of Cr(VI) than Cr(III) can be detected. Since only two absorption bands are detected at 15 000 and 22 000 cm − 1 , corresponding to Cr(III) signal only, it can be assumed that the detection limit for Cr(VI) is at least 200 times lower than the total Cr amount which has been attributed to Cr(III), that is 1 × 10 − 5 mol%. Thus, the optical absorption spectroscopy demonstrated that the Cr-bearing pristine glasses contained Cr(III) only with a detection limit for Cr(VI) of 1 × 10 − 5 mol%. 29 Si and 207 Pb NMR spectroscopy The distribution of Q n species in the glass is accessed via 29 Si MAS NMR, which was performed on Cr-bearing glasses. The results are presented in Figure 9 for the two extrema of Cr-bearing glasses showing a distribution centered on Q 3 and Q 4 species. Tetracoordinated silicate units Q 4 have four bridging oxygens (i.e. oxygen bonding two silicate units at a corner). A slight variation in the distribution of Q 3 and Q 4 species can be observed, with a slight decrease in Q 3 and a corresponding increase in Q 4 species as the Cr content increases. Surprisingly the addition of a paramagnetic compound like chromium oxide to the glass batch did not affect the intensity of the 29 Si MAS NMR spectra obtained for Cr-bearing glasses, but significant effect is observed on 207 Pb signal intensity than that observed on 29 Si as displayed in Figure 6. The spectra were normalized to the same sample mass, with identical experimental conditions allowing direct quantitative comparison of the obtained results. Additionally, for the glass with the highest Cr content, the lineshape of the 29 Si MAS NMR spectrum did not vary with the recycle delay as shown in Supplementary Figure 2. Considering the paramagnetic nature of Cr(III), and according to previous studies using contrast in the NMR signal induced by differential spin-lattice relaxation rates, (see 19 for example), this suggests that no phase segregation occurs, which would have led to a preferential relaxation of specific Si sites. The growing intensity of the 207 Pb NMR spectra observed in Figure 6 can only be related to the increase of the Cr content in the glass samples. This could be explained by the shortening of 207 Pb relaxation time T 1 by paramagnetic Cr, leading to higher intensity signals. No detailed investigation of 207 Pb T 1 were carried out, mainly because of the very long time required to collect the data (several days). The NMR lineshape, acquired under static, i.e. non-spinning conditions, is close to that of an environment dominated by a large CSA tensor, as already measured in lead silicate glasses 20,21 . Then, NMR pointed out the proximity between Pb and Cr atoms suggested by the increase 207 Pb spectra intensity upon to the addition of Cr. Structure of altered glasses XANES on bulk glasses The behavior of Cr in lead crystal glass exposed to harsh alteration conditions was investigated using X-ray Absorption Near Edge Spectroscopy (XANES) at the Cr K-edge on both pristine and altered glasses at the ID21 beamline of the European Synchrotron Radiation Facility (ESRF, France) 22 . While optical absorption spectroscopy established the absence of Cr(VI) at the pristine state, the potential changes in oxidation state caused by the local restructuring of the altered layer required to investigate Cr speciation specifically in the surface region. Two approaches were followed. First, XANES was performed with a large, unfocused beam (100-350 µm) directly at the surface of pristine and altered glass slabs. Then, µXANES analyses were obtained with a focused beam (0.26 × 0.8 µm 2 , v × h.), on cross-section of altered glass, both in the most external area and in a deeper region. In the first approach, photons are spread over a large area, decreasing the dose and consequently the risk of beam damage. However, it should be taken into account that at the Cr K-edge, the attenuation length of X-ray is 7 µm, larger than the alteration layer (6 µm). Therefore, a small contribution from deep, unaltered glass should not be neglected. In the second approach, the photons are laterally concentrated in a very small probe. Radiation tests were carried out by repeating XANES acquisitions at the same positions and revealed the formation of chromate, Cr(VI), under the beam. To slow down this oxidation reaction, different adaptations to the standard set-up were done. The beam intensity was reduced with a 50 µm Al attenuator; the energy step was increased from 0.4 eV (as used in unfocused mode) to 0.6 eV; the starting energy was increased from 5.95 keV to 5.985 keV, to avoid unnecessary exposure of the samples to photons. Finally, the beam fast shutter was opened only during data collection. Besides, spectra were collected as single scans, over different points, from the surface to the depth of the glass. A first µXRF map was systematically collected prior to µXANES spectra to locate this alteration layer. The first method yielded good quality spectra as shown in Figure 7, however with merged signals of the pristine and altered glass. The second approach allowed to target alteration layers only but with a low X-ray dose to preserve the samples producing noisier spectra as exposed in Figure 8b. Figure 7a displays the superposition of the mean spectrum acquired on bulk pristine and 330 days altered glass for each of the Cr-bearing glass. The same shape of spectrum was observed for all the glasses although the least concentrated glasses in Cr (BAC_Cr50 and BAC_Cr250) yield, evidently, noisier spectra. Perfect good overlap of the pristine (solid lines) and altered (dashed lines) XANES spectra of each glass was observed with a slightly lower intensity of the main peak for the spectra collected on altered samples revealing small modification of Cr environment between the pristine and altered glasses. The same acquisitions were carried out on all the samples. To confirm the oxidation state of Cr in our glasses, the experimental pristine and altered spectra of BAC_Cr2000 were compared to mineral references of Cr(III): stichtite (a magnesium and chromium carbonate), and Cr(VI): crocoite (PbCrO4) and fornacite (Pb2Cu(CrO4)(AsO4)(OH)), both containing Pb, as our samples. The results are shown in figures 7b and 7c, respectively. A good agreement can be noticed between the experimental spectra and the Cr(III) reference highlighting a key feature in the pre-edge region with a peak common to all spectra at 5.9913 keV. The features of this region of the spectrum, before the edge, are indicative of electronic transitions from orbital 1 s to orbital 3 d of transition metal cations like Cr. The intensity of the peak at 5.9913 keV is notably low for all spectra which is expected from the inversion of symmetry of p and d orbitals in the octahedral configuration imposed by Cr(III) valence. Regarding Cr(VI) which exhibits tetrahedral configuration, the geometry of orbitals p and d is favorable to their mixing resulting in an intense pre-edge at 5.9935 keV (Figure 7c). The post-edge region echoes the Cr local environment which varies a lot among references compounds as awaited. Regarding the edge region in figure 7b, an offset of 3 eV between the white-line position of our samples and the stichtite Cr(III) reference is discerned. Variation in the edge position is usually significant of different oxidation state. In this case the shift towards lower energies could have been interpreted as the presence of Cr(II) mixed with Cr(III) as described by Berry et al. 23 but the presence of Cr(II), characterized by a large absorption band spreading from 10 000 to 20 000 cm − 1 24 was not detected by optical absorption spectroscopy on the pristine glass (Figure 5). Most likely, these differences are significant of the different ligands of Cr between the references and the glasses of interest. Then, XANES spectra on the bulk pristine and altered Cr-bearing lead crystal glasses evidenced the presence of Cr(III), reinforcing the conclusions obtained by optical absorption spectroscopy in the pristine glasses. µXRF and µXANES on cross-sections XRF mapping of polished cross sections of the altered slabs enabled the identification and localization of an alkali depleted layer outlining the pristine glass and corresponding to the alteration layer. An example of XRF mapping for potassium (K-K-α) obtained on BAC_Cr2000 cross-section after 330 days of alteration is given in Figure 8a. The layer appeared of constant thickness and perfectly parallel to the edge of the sample despite the rugosity which arose from the sample preparation. The measured thickness of the potassium depleted altered layer was of 6.00 ± 0.25 µm, corresponding to the green area at the top in Figure 8a. The dark blue area represents the epoxy resin that embedded the sample and the yellow region designates the pristine glass with hues variations reflecting the local topographic rugosity created by the sample preparation and not actual gradients of concentration in potassium. By focusing the incident X-ray beam a resolution of 0.8 × 0.26 µm 2 ( h × v ) was obtained allowing µXANES analyses in the pristine glass and in the altered layer distinctively. Three points of interest were selected, their location is indicated in Figure 8a and the corresponding XANES spectra are presented in Figure 8b alongside the spectra obtained on bulk slabs of BAC_Cr2000 with a defocused beam. As anticipated due to the attenuated intensity of the beam used for focused XANES analyses on the cross-section, the spectra obtained display more background noise than those collected on the bulk glass using a defocused beam. Nonetheless, the comparison of spectra from the pristine glass, cross-section and bulk showed very similar shape and intensity, validating the presence of Cr(III) only in both cases. For the spectra obtained from the alteration layer of the cross-section (spectra 'altered_50' and 'altered_55'), the edge position remained consistent with that observed in the bulk glass analyses (spectrum 'BAC_Cr2000 (5) altered') and in the pristine glass, located at 6.0075 keV. The pre-edge region (5.9800 - 5.9950 keV) of the cross-section spectra is not very well defined because of the low dose of X-ray used in the focused mode to avoid photoinduced oxidation. The presence of Cr(VI), indicated by a pre-edge at 5.9935 keV with greater intensity than that expected for Cr(III) 13 , should be distinguishable from the background noise. The absence of distinct features in this region can be interpreted as evidence for the lack of Cr(VI). Consequently, µXANES allowed the identification of Cr(III) only in pristine and altered Cr-bearing lead crystal glass samples with a Cr intake up to 0.028 %mol. 29 Si NMR spectroscopy After alteration, glass powder was sampled from each reactor. These powders were dried and analyzed by 29 Si MAS NMR. Figure 9 displays the structural changes in the silicate network induced during the leaching time. These changes are characterized by a shift towards lower chemical shifts after alteration meaning a higher amount of Q 4 species to the detriment of Q 2 and Q 3 species, all indicative of the increase of polymerization of the silicate network in the course of alteration. It corresponds to the strengthening of the most superficial part of the altered layer participating in the diffusive barrier effect responsible for the drop of the rate of alteration noticed in Figure 2 for Na, K and Pb after 14 days. The extent of polymerization can be inferred from the increase of the area of the Q 4 line. After alteration, Cr-rich glass BAC_Cr2000 had the largest proportion of Q 4 species compared to BAC_Cr50. Consequently, it can be assumed that the presence of Cr in the glassy matrix favored the polymerization of the glass in the course of alteration. Besides the slightly more polymerized network noticed for Cr-bearing glasses at the pristine state, this trend is then confirmed and amplified after alteration by the leaching mechanisms calling attention to the strong effect of Cr, even at low concentrations, on the structure of Cr lead crystal glasses. Discussion The presence of Cr(III) only in the investigated glasses has been established using XANES and optical absorption spectroscopy. Moreover, extensive studies of Cr(III) in various other Cr-containing glasses using the same analytical techniques arrived at the following conclusions. On the one hand, XANES showed that Cr(III) was always found hexacoordinated with an octahedral geometry and low variations in its local environment 15,23,25,26 . On the other hand, optical absorption spectroscopy revealed the preferential localization of Cr atoms in cationic domains of the glass 27 with a preference for alkalis over earth-alkalis 15 . Overall, Cr(III) was not uniformly distributed within the glass networks but was located in specific, somewhat disordered sites 15 . Previous structural studies on lead crystal glass without Cr highlighted the presence of sites mixing Pb and K, written: Si–O–(Pb, K), near Non-Bridging Oxygens (NBOs) by 17 O multi-quantum magic-angle spinning (MQMAS) NMR 6 . These sites exhibit the previously described characteristics for hosting Cr(III), namely a higher degree of chemical disorder in the cationic domains. 207 Pb static NMR spectroscopy successfully demonstrated the proximity of Pb and Cr within the glass network. In lead crystal glasses, the 10.6 mol% of PbO is too low to form a subnetwork of Pb units. Consequently, Pb is not considered as a network former, and glass network is composed of silicate units, within whose interstices Pb and alkali metals are localized 28,29 . Thus, Cr cations could be positioned near these NBO domains. 29 Si MAS NMR spectroscopy points out a slight increase in polymerization as the Cr content increases. These findings support the description of Cr(III) as a network hardener, reinforcing the network polymerization of the pristine glass. From the structural and alteration data, the specific role of Cr can be highlighted. Cr is partially retained near the cationic domains during alteration, also improving Pb retention though the role of network hardener. Pb and Cr entities are less accessible to protonated species, which reduces their mobility compared to alkali metals that are distributed throughout the entire glassy matrix. Consequently, their exchange and transport kinetics are slower compared to Na and K. The part of leached Cr and Pb favors the Si recondensation in the rich NBO mixing sites, leading in an increase of the glass polymerization within the altered layer, as observed by 29 Si MAS NMR after leaching. The polymerization is clearly amplified when the Cr content in the glass increases. The fact that the release kinetics of Pb is lower than a purely diffusional behavior proportional to the square root of time may be linked to the increased polymerization in the alteration layer, which serves as an additional barrier. On the other hand, the behavior of Cr is released similarly to Si, in agreement with the role of a network hardener in the silicate network. The high sensitivity of lead crystal glass structure to very low contents of Cr can be outlined. In 2016, Liao et al. 30 reported a double barrier effect leading to the immobilization of Cr under the form of Cr(III) in glass-ceramic material where Cr(III) was retained in crystallized spinel structure and in the glassy matrix. In this study, we extend this conclusion to a fully amorphous material, demonstrating how Cr used as a colorant is well retained while 50 % of the alkalis are leached out of the glass developing micron-sized alteration layers. The results are favorable from a toxicological and environmental standpoint, supporting the absence of Cr(VI) in both the pristine and altered glasses. Additionally, only a small amount of Cr was measured in the leachate after 330 days of alteration under extremely harsh conditions (70 °C, pH = 2.4, SA/V geo = 500 m − 1 ). Furthermore, the origin of the retention mechanism was clarified thanks to structural analysis tools like XANES at Cr K-edge and NMR of 29 Si and 207 Pb nuclei, overcoming the technical difficulties inherent to the paramagnetic and easily oxidized materials under study. Thus, under very unfavorable food simulating conditions of alteration, the Cr contained in the original materials did not oxidize to Cr(VI) over the course of fabrication nor alteration of the glass and was well immobilized with Pb in the glass structure. Under normal conditions of use (significantly lower temperature and contact time), the expected releases of Pb and Cr should be well below the limits imposed by standardized tests (24h at 25°C). METHODS Glass preparation Four ingots of lead crystal glass with 50, 250, 500 and 2000 ppm of chromium oxide, as visible on the photographs in Fig. 1, were fabricated from a single batch of lead crystal glass. Out of each of these ingots, square shaped slabs measuring 5 × 5 × 2 mm 3 were cut and all faces were polished to 1 µm (roughness of the order of a few nanometers) to obtain perfectly geometrical and smooth surfaces. The slabs were used for µXRF and XANES analyses. A few dozens of grams of each glass was crushed, sieved and washed with acetone and absolute ethanol to obtain powders with particle size diameter ranging from 63 to 125 µm. The specific surface of each of these powders was measured with the BET method using Kr gas [11] and the powders were then used for the 330 days alteration experiment. The composition of the glasses was determined by Electronic Micro-Probe Analyzer (EMPA) and the results are displayed in Table 1. The standard deviation was calculated for each element of each glass based on 10 repetitions and the relative uncertainty is equal or below 5% of the given values for all elements, except Cr, for which the uncertainty rose up to 50% because of the very low quantities added. Leaching experiments Samples glasses were altered with two experiments following the same protocol of alteration, the first one using glass slabs and the second one using glass powder, yielding different glass-surface-area-to-solution-volume-ratios (SA/V ratio), which were determined geometrically in both cases by precisely measuring the glass slabs and using Eq. 1 for powders. In both cases, long term alteration in static mode was performed in perfluoroalkoxy alkane reactors (PFA), at 70 ± 3°C in 4% (v/v) acetic acid solution, which corresponds to a pH of 2.4 ± 0.1. Acetic acid solutions were prepared by diluting acetic acid (100%, Merck Suprapur) in 18 MΩ.cm ultrapure water. For the alteration of glass slabs with chromium oxide content the initial SA/V ratio obtained for the alteration of 5 slabs (5 × 5 × 2 mm 3 ) of each glass in the same reactor was 2.45 ± 0.03 m − 1 . After 330 days year of alteration, all the glass slabs were removed from the reactors and dried at 90°C for 2 hours before cooling down over night at room temperature and humidity. One altered slab of each glass was embedded in epoxy resin and polished to obtain cross-sections of the altered slabs that were then analysed by µ-XRF and XANES at the ESRF synchrotron. As this experiment, with a very low SA/V ratio, did not allow to measure precisely the leached out element of the glasses, the second experiment with high SA/V ratio was undertaken using about 10 grams of 63–125 µm calibrated powder and 500 g of acetic acid 4% (v/v) solution to reach a SA/V ratio of 500 m − 1 , thus increasing the amount of leached elements in solution. $$\:\frac{SAgeo}{V}=\frac{3.mglass}{Vsol.\rho\:.Rmean}$$ 1 With SA geo /V the glass-surface-area-to-solution-volume-ratio determined with the geometric approximation (m − 1 ), V sol the volume of solution in the experiment (m 3 ), mglass the mass of glass in the experiment (g), ρ the density of the glass (g.m − 3 ) and R mean the mean radius of glass particles in the experiment (m) The alteration solution was regularly sampled from the reactors during the first 112 days of the experiment and the concentrations of glass constituents in solution were analyzed by Inductively coupled Plasma - Atomic Emission Spectroscopy (ICP-AES) after acidification with nitric acid. A final verification sampling was carried out at 330 days. The solution withdrawal generated by the samplings is considered by recalculating the glass-surface-area-to-solution-volume-ratio after each sampling. For each solution sampling, the normalized mass loss of each element of each glass was calculated using Eq. 2. $$\:{NL}_{{geo}_{i,t}}=\frac{{C\left(i\right)}_{t}}{{\left(\frac{{SA}_{geo}}{V}\right)}_{t}{x}_{i}}$$ 2 With NL geoi,t the normalized mass loss of element i after t days of alteration (g.m − 2 .d − 1 ), C ( i ) t the concentration of element i in solution after t days of alteration (g.m − 3 ), SA geo /Vt the glass-surface-area-to-solution-volume-ratio determined with the geometric approximation after t days of alteration (m − 1 ), x i the mass fraction of element i in the pristine glass These normalized losses per element can be translated to equivalent thicknesses of glass altered thanks to Eq. 3 and enable the calculation of alteration rates through partial derivation with respect to time given in Eq. 4. $$\:Ethgeoi,t=\frac{NLgeoi,t}{\rho\:}$$ 3 With Ethgeoi,t the equivalent thickness of glass altered for element i after t days of alteration (m), NL geo,i , t the normalized losses of element i in solution after t days of alteration (g.m − 2 .d − 1 ), ρ the pristine glass density (g.m − 3 ). $$\:ri\left(t\right)=\frac{\partial\:NLgeoi,t}{\rho\:\partial\:t}$$ 4 With r i ( t ) the releasing rate of an element i for a given time of alteration (g.m − 2 .d − 1 ) and NL geoi , t the normalized losses of element i in solution after t days of alteration (g.m − 2 .d − 1 ). The diffusion coefficients for species with interdiffusion behavior were calculated using Eq. 5. $$\:Di=\pi\:{\left(\frac{ri\left(t\right)}{2\rho\:}\right)}^{2}$$ 5 With D i the diffusion coefficient of an element i for a given time of alteration (m 2 .s − 1 ), r i ( t ) the partial derivative of normalized losses of element i with respect to time (g.m − 2 .s − 0.5 ) and ρ the pristine glass density (g.m − 3 ). For this protocol, the overwhelming factor of uncertainty for the calculation of r i ( t ), ETh geoi,t , NL geoi,t is the ICP-AES determination of elemental concentrations in solution. These latter come out with a 10% relative uncertainty, which is then reflected on the calculated data. NMR spectroscopy NMR data on 29 Si were collected on a Bruker AVANCE II 500WB spectrometer operating at a magnetic field of 11.7 T, using a Bruker 4 mm (outer diameter of the rotor) cross-polarization MAS HX probe at a spinning frequency of 12.5 kHz. 29 Si MAS NMR spectra were acquired using a saturation-recovery pulse sequence with a recovery delay of 20 s (increasing the recycling delay did not alter the lineshape). The 29 Si NMR shifts were referenced against tetrakis(trimethylsilyl)silane powder (two lines at 9.9 ppm and 135.3 ppm with respect to tetramethylsilane). 207 Pb NMR spectra were acquired at a magnetic field of 7 T on a Bruker AVANCE II Spectrometer. Because of the very large width of the spectra (mainly due to a very large chemical shift anisotropy (CSA) 20 ), the variable-offset cumulative spectroscopy (referred to as VOCS) 20 , 31 has been employed under static conditions (i.e. non-spinning sample), using carrier frequency jump of 50 kHz (typically from − 150 kHz to + 150 kHz with the origin taken at the center of the spectrum). Typically 48000 scans have been accumulated with a recycle delay of 2 s. For some offset frequency values, spectra at recycle delays of 0.5 s, 2 s, 8 s and 16 s have been compared to quantitatively estimate the relaxation of the signal and the impact of the Cr content (which was found to shorten significantly the relaxation time of 207 Pb). µ-XRF and XANES at ESRF Measurements were performed at the scanning X-ray microspectroscopy end station of the beamline ID21 of the European synchrotron radiation facility (ESRF, Grenoble) 22 . A Si(220) double-crystal monochromator was used to scan the X-ray beam energy across Cr K-edge (5.976 keV). For the calibration, the first inflection point of the first-order derivative Cr K-edge XANES spectrum of a Cr metallic foil was set at 5.9900 keV. Photoinduced oxidation was evidenced by repeating XANES spectra on the same spot and observing growing intensity of pre-edge at 5.9935 keV indicative of oxidation into Cr(VI) occurring under beam exposition. To avoid these beam damage artefacts, especially in the targeted altered layer, two different modes of analyses were adopted: i) defocused beam, to sense large areas with a minimal dose of X-rays and ii) focused beam, µXANES, to target alteration layers specifically. In defocused mode, the beam size ranged from 100 to 350 µm, and acquisitions were carried out from 5.95 to 6.15 keV, with 500 steps of 0.4 eV. For XANES investigations, the incident beam was focused with a Kirkpatrick-Baez (KB) mirror system down to a spot size of 0.8 × 0.26 µm 2 ( h × v ) and the beam was attenuated with a 50 µm Al foil. The energy range was reduced to 5.985–6.15 keV, with steps of 0.6e V. All data were collected in vacuum. Optical absorption spectroscopy UV-visible-near IR transmission spectra were recorded on Cr-bearing glass samples at room temperature on thin slabs with both face polished with a double beam Perkin-Elmer Lambda-1050® spectrometer in the spectral range between 3030 and 40 000 cm − 1 with a wavelength (λ) step and spectral resolution of 0.92 cm − 1 (1 nm). After correction for signal jump at 11 600 cm − 1 due to detector change, the absorption spectra were normalized to sample thickness. The area analyzed was about 2 × 3.5 mm 2 sensing a large portion of the glass slabs and allowing a highly representative measurement of the optical absorbance. Declarations DATA AVAILABILITY The data that supports the findings of this study are available from the corresponding author upon reasonable request. ACKNOWLEDGEMENTS This study was supported by the French Agency for Research (ANR, PRCE program, grant 18-CE08-0025). We acknowledge the European Synchrotron Radiation Facility for provision of beam time on ID21 (proposal MA-4648) and we would especially like to thank ESRF instrumentation service and development division for their efforts in instrumental developments for EBS and ID21 refurbishment. µXRF and XANES datasets acquired in ESRF can be found under DOI 10.15151/ESRF-ES-579825745. Théo Caroff from IMPMC is acknowledge for his script for data processing optical absorption spectra and Déa Jaïs (IMPMC) for the transcription of the Cr(III) and Cr(VI) spectra from Bamford. AUTHORS CONTRIBUTION LB performed the leaching experiments. XANES and XRF measurements were carried out by MT and LB under the supervision of MC and data was curated by LB. TC performed the NMR studies. LG ran optical absorption spectroscopy and processed data. FA, SG and TC supervised the study and worked on the conceptualization, methodology and original draft. All the authors helped on the paper editing. COMPETING INTERESTS The authors declare no competing interests. References Chromium and Chromium Compounds. In: IARC MONOGRAPHS ON THE EVALUATION OF CARCINOGENIC RISKS TO HUMANS, VOL 49: CHROMIUM, NICKEL AND WELDING . World Health Organization: Geneva, 1990, pp 49–256. Guadagnino E, Sundberg P, Corumluoglu O. A collaborative study on the determination of hexavalent chromium in container glasses - A report of ICG/TC2 ‘Chemical Durability and Analysis’. Glass Technol 2001; 42 : 148–152. E.U. Commission Directive (EU) 2018/ 725 - of 16 May 2018 - amending, for the purpose of adaptation to technical and scientific developments, point 13 of part III of Annex II to Directive 2009/ 48/ EC of the European Parliament and of the Council on the safety of toys, as regards chromium VI, May 2018. . E.U. Commission Regulation (EU) 2020/1245 of 2 September 2020 amending and correcting Regulation (EU) No 10/2011 on plastic materials and articles intended to come into contact with food, March 2020. . E.U. Commission Regulation (EU) No 125/2012 of 14 February 2012 amending Annex XIV to Regulation (EC) No 1907/2006 of the European Parliament and of the Council on the Registration, Evaluation, Authorisation and Restriction of Chemicals (REACH), February 2012. . Angeli F, Jollivet P, Charpentier T, Fournier M, Gin S. Structure and Chemical Durability of Lead Crystal Glass. Environ Sci Technol 2016; 50 : 11549–11558. Lecanuet G, Rocca E, Hee P, Skaper M-A, Rapin C. Mechanism of alteration of the surface of lead crystal glass in contact with food: A chemical study of the surface layer. Appl Surf Sci 2022; 580 : 152281. Brunswic L, Angeli F, Charpentier T, Gin S, Asplanato P, Kaya H et al. Comparative study of the structure and durability of commercial silicate glasses for food consumption and cosmetic packaging. NPJ Mater Degrad 2024; 8 : 82. Collin M, Diallo B, Lecoq H, Ory S, Chauvet E, Pellerin N. Chemical durability of lead crystal glass: Comparison of short-term aqueous and atmospheric alteration at 90°C. Int J Appl Glass Sci 2021; 12 : 158–174. E.U. ISO 7086:2019 Glass hollowware in contact with food - Lead and cadmium emission, 2019. . Bunker B. Molecular Mechanisms for Corrosion of Silica and Silicate-Glasses. J Non-Cryst Solids 1994; 179 : 300–308. Gin S, Guo X, Delaye J-M, Angeli F, Damodaran K, Testud V et al. Insights into the mechanisms controlling the residual corrosion rate of borosilicate glasses. NPJ Mater Degrad 2020; 4 : 41. Villain O, Calas G, Galoisy L, Cormier L. XANES determination of chromium oxidation states in glasses: Comparison with optical absorption spectroscopy. J Am Ceram Soc 2007; 90 : 3578–3581. C. Ray Bamford. Colour generation and control in glass. Number v. 2 in Glass science and technology. Elsevier Scientific Pub. Co. : distributors for the U.S. and Canada, Elsevier North-Holland, Amsterdam ; New York, 1977. ISBN 978-0-444-41614-8. . Villain O, Galoisy L, Calas G. Spectroscopic and structural properties of Cr3+ in silicate glasses Cr3+ does not probe the average glass structure. J Non-Cryst Solids 2010; 356 : 2228–2234. Georges Calas, Laurence Galoisy, and Laurent Cormier. The Color of Glass. In Pascal Richet, Reinhard Conradt, Akira Takada, and Joël Dyon, editors, Encyclopedia of Glass Science, Technology, History, and Culture, pages 677–691. Wiley, 1 edition, February 2021. ISBN 978-1-118-79942-0 978-1-118-80101-7. doi:10.1002/9781118801017.ch6.2. . Christina Stålhandske. The impact of refining agents on glass colour. GLASTEKNISK TIDSKRIFT, 55(3), 2000. . Nath P, Paul A, Douglas R. Physical and Chemical Estimation of Trivalent and Hexavalent Chromium in Glasses. Phys Chem Glasses 1965; 6 : 203-. Stebbins JF, Kim N, Andrejcak MJ, Boymel PM, Zoitos BK. Characterization of Phase Separation and Thermal History Effects in Magnesium Silicate Glass Fibers by Nuclear Magnetic Resonance Spectroscopy. J Am Ceram Soc 2009; 92 : 68–74. Fayon F, Bessada C, Massiot D, Farnan I, Coutures JP. 29Si and 207Pb NMR study of local order in lead silicate glasses. J Non-Cryst Solids 1998; 232 : 403–408. Fayon F, Landron C, Sakurai K, Bessada C, Massiot D. Pb2+ environment in lead silicate glasses probed by Pb-L III edge XAFS and 207Pb NMR. J Non-Cryst Solids 1999; 243 : 39–44. Cotte M, Pouyet E, Salome M, Rivard C, De Nolf W, Castillo-Michel H et al. The ID21 X-ray and infrared microscopy beamline at the ESRF: status and recent applications to artistic materials. J Anal At Spectrom 2017; 32 : 477–493. Berry AJ, O’Neill HSC. A XANES determination of the oxidation state of chromium in silicate glasses. Am Miner 2004; 89 : 790–798. Iwamoto N, Makino Y. State of the Chromium Ion in Soda Silicate-Glasses Under Various Oxygen Pressures. J Non-Cryst Solids 1980; 41 : 257–266. Pantelouris A, Modrow H, Pantelouris M, Hormes J, Reinen D. The influence of coordination geometry and valency on the K-edge absorption near edge spectra of selected chromium compounds. Chem Phys 2004; 300 : 13–22. Farges F. Chromium speciation in oxide-type compounds: application to minerals, gems, aqueous solutions and silicate glasses. Phys Chem Miner 2009; 36 : 463–481. Calas G, Majérus O, Galoisy L, Cormier L. Crystal field spectroscopy of Cr3+ in glasses:: Compositional dependence and thermal site expansion. Chem Geol 2006; 229 : 218–226. Angeli, F., Brunswic, L., Charpentier, T., and Gin, S. Lead leaching in industrial crystal glasses: role of chemical composition, structure and surface treatments. Lead in Glassy Materials in Cultural Heritage, 2024: p. 297. . Ben Kacem I, Gautron L, Coillot D, Neuville DR. Structure and properties of lead silicate glasses and melts. Chem Geol 2017; 461 : 104–114. Liao C, Tang Y, Liu C, Shih K, Li F. Double-Barrier mechanism for chromium immobilization: A quantitative study of crystallization and leachability. J Hazard Mater 2016; 311 : 246–253. Massiot D, Farnan I, Gautier N, Trumeau D, Trokiner A, Coutures J. Ga-71 and Ga-69 Nuclear-Magnetic-Resonance Study of Beta-Ga2o3 - Resolution of 4-Fold and 6-Fold Coordinated Ga Sites in Static Conditions. Solid State Nucl Magn Reson 1995; 4 : 241–248. Additional Declarations No competing interests reported. Supplementary Files SUPPLEMENTARYINFORMATION.pdf Cite Share Download PDF Status: Published Journal Publication published 02 May, 2025 Read the published version in npj Materials Degradation → Version 1 posted Editorial decision: Revision requested 25 Nov, 2024 Reviews received at journal 22 Nov, 2024 Reviews received at journal 22 Nov, 2024 Reviewers agreed at journal 28 Oct, 2024 Reviewers agreed at journal 25 Oct, 2024 Reviewers invited by journal 24 Oct, 2024 Editor assigned by journal 24 Oct, 2024 Submission checks completed at journal 23 Oct, 2024 First submitted to journal 17 Oct, 2024 You are reading this latest preprint version Research Square lets you share your work early, gain feedback from the community, and start making changes to your manuscript prior to peer review in a journal. As a division of Research Square Company, we’re committed to making research communication faster, fairer, and more useful. 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Also discoverable on Platform About Our Team In Review Editorial Policies Advisory Board Help Center Resources Author Services Accessibility API Access RSS feed Manage Cookie Preferences © Research Square 2026 | ISSN 2693-5015 (online) Privacy Policy Terms of Service Do Not Sell My Personal Information {"props":{"pageProps":{"initialData":{"identity":"rs-5284279","acceptedTermsAndConditions":true,"allowDirectSubmit":false,"archivedVersions":[],"articleType":"Article","associatedPublications":[],"authors":[{"id":369990826,"identity":"f6bfaa45-8819-4f08-abe3-7fa1caceff07","order_by":0,"name":"Lea Brunswic","email":"","orcid":"","institution":"University of Montpellier","correspondingAuthor":false,"prefix":"","firstName":"Lea","middleName":"","lastName":"Brunswic","suffix":""},{"id":369990837,"identity":"282ea76f-f9e3-45fe-a429-45012a5c01e2","order_by":1,"name":"Frederic Angeli","email":"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAA90lEQVRIiWNgGAWjYBAC9gYGBgkwAoMCCTkwXYFHC88BFC0GEsZg+gxhLTBgwJDYQFCL9OGDNz7usZBnYD97+MUHA4v0/vbmBwwH9+DRwpeWbDnjmYRhA09emuUMA4ncGWeOGTAceIZbiz0Pj5k0zwGJBAaGHDNjHqCWDRIJBswfDuCxhYf/m/QfkBb+N2bGfwwk0g3kn39gOIBXCw+bNANIi0SO8WNgiCUYSPAYENDCZmzZc0DCsE3ijRljj4GE4YwzOQUH8Gthfnjjx4E6eX7+HOMPPyqAjPbjGx/g0wIHbEAEjyBiNIAB8wdiVY6CUTAKRsHIAgBvE0tc54sV5QAAAABJRU5ErkJggg==","orcid":"","institution":"University of Montpellier","correspondingAuthor":true,"prefix":"","firstName":"Frederic","middleName":"","lastName":"Angeli","suffix":""},{"id":369990838,"identity":"9fa1d618-ba1e-4140-97dc-699f99cfd5d6","order_by":2,"name":"Thibault Charpentier","email":"","orcid":"","institution":"University of Paris-Saclay","correspondingAuthor":false,"prefix":"","firstName":"Thibault","middleName":"","lastName":"Charpentier","suffix":""},{"id":369990840,"identity":"b89cabfb-0ecc-4173-9e3c-a8be3f02f185","order_by":3,"name":"Stephane Gin","email":"","orcid":"","institution":"University of Montpellier","correspondingAuthor":false,"prefix":"","firstName":"Stephane","middleName":"","lastName":"Gin","suffix":""},{"id":369990850,"identity":"1184fb81-9a2a-4353-af65-b4ec4534c696","order_by":4,"name":"Lea Gardie","email":"","orcid":"","institution":"Sorbonne University","correspondingAuthor":false,"prefix":"","firstName":"Lea","middleName":"","lastName":"Gardie","suffix":""},{"id":369990853,"identity":"6d1c7295-4eec-4fbb-98ca-ec7d35f10786","order_by":5,"name":"Mariona Tarrago","email":"","orcid":"","institution":"Université Paris Cité","correspondingAuthor":false,"prefix":"","firstName":"Mariona","middleName":"","lastName":"Tarrago","suffix":""},{"id":369990855,"identity":"5b81e414-8d74-4116-af15-7b315ea0b116","order_by":6,"name":"Marine Cotte","email":"","orcid":"","institution":"European Synchrotron Radiation Facility","correspondingAuthor":false,"prefix":"","firstName":"Marine","middleName":"","lastName":"Cotte","suffix":""},{"id":369990856,"identity":"3895d642-7576-40ae-8ba6-dcd96ad498ee","order_by":7,"name":"Remi Losno","email":"","orcid":"","institution":"University of Paris-Saclay","correspondingAuthor":false,"prefix":"","firstName":"Remi","middleName":"","lastName":"Losno","suffix":""},{"id":369990857,"identity":"aaf5bc85-9db0-4041-8385-21f36f293dd4","order_by":8,"name":"Laurent Cormier","email":"","orcid":"","institution":"Sorbonne University","correspondingAuthor":false,"prefix":"","firstName":"Laurent","middleName":"","lastName":"Cormier","suffix":""},{"id":369990858,"identity":"af0140a5-54cc-47a6-9865-73ffb7b5f2f8","order_by":9,"name":"Eric van Hullebusch","email":"","orcid":"","institution":"Université Paris Cité","correspondingAuthor":false,"prefix":"","firstName":"Eric","middleName":"van","lastName":"Hullebusch","suffix":""},{"id":369990859,"identity":"c3c439f5-21eb-41a5-9caf-512df34458e4","order_by":10,"name":"Daniel Neuville","email":"","orcid":"","institution":"Université Paris Cité","correspondingAuthor":false,"prefix":"","firstName":"Daniel","middleName":"","lastName":"Neuville","suffix":""}],"badges":[],"createdAt":"2024-10-17 16:23:23","currentVersionCode":1,"declarations":"","doi":"10.21203/rs.3.rs-5284279/v1","doiUrl":"https://doi.org/10.21203/rs.3.rs-5284279/v1","draftVersion":[],"editorialEvents":[{"content":"https://doi.org/10.1038/s41529-025-00586-7","type":"published","date":"2025-05-02T15:57:20+00:00"}],"editorialNote":"","failedWorkflow":false,"files":[{"id":67461504,"identity":"651a1f98-4815-4a41-b0f0-6b31493f74ac","added_by":"auto","created_at":"2024-10-25 09:40:21","extension":"png","order_by":1,"title":"Figure 1","display":"","copyAsset":false,"role":"figure","size":435176,"visible":true,"origin":"","legend":"\u003cp\u003ePicture of the studied glasses with different amounts of chromium oxide. Raw glass ingots are on the top of the image (5 cm wide and thick each) and polished slabs are at the bottom, each measuring 5 × 5 × 2 mm\u003csup\u003e3\u003c/sup\u003e.\u003c/p\u003e","description":"","filename":"Figure1.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/6b8e61b1dc7de91fe87699cc.png"},{"id":67461507,"identity":"29b92dbf-0dd0-4de4-bb9e-57c850c93b86","added_by":"auto","created_at":"2024-10-25 09:40:21","extension":"png","order_by":2,"title":"Figure 2","display":"","copyAsset":false,"role":"figure","size":119173,"visible":true,"origin":"","legend":"\u003cp\u003eEvolution of the equivalent thicknesses (ETh) of chromium colored lead crystal glasses for the main constituents: Si (a), Pb (b), Na (c), K (d) during alteration at 70 °C and pH = 2.4 in acetic acid 4 % (v/v) with an SA/Vgeo ratio of 500 m−1 (glass powder 63-125 mm). ETh calculations are based on ICP-AES analyses of the alteration solutions and calculated using equations 1, 2 and 3.\u003c/p\u003e","description":"","filename":"Figure2.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/07008c11c467992bb8582b1a.png"},{"id":67461510,"identity":"fd4cfd2f-1083-4ffb-9f5c-ae20727de220","added_by":"auto","created_at":"2024-10-25 09:40:22","extension":"png","order_by":3,"title":"Figure 3","display":"","copyAsset":false,"role":"figure","size":60184,"visible":true,"origin":"","legend":"\u003cp\u003eEvolution of the equivalent thicknesses (ETh) of chromium colored lead crystal glasses for Pb and Cr during alteration at 70 °C and pH = 2.4 in acetic acid 4 % (v/v) with an SA/Vgeo ratio of 500 m−1 (glass powder 63-125 mm).\u003c/p\u003e","description":"","filename":"3.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/eec910109362bb0c13570236.png"},{"id":67461505,"identity":"def379f0-25a0-4719-ae1d-ec3c8f116a2f","added_by":"auto","created_at":"2024-10-25 09:40:21","extension":"png","order_by":4,"title":"Figure 4","display":"","copyAsset":false,"role":"figure","size":205766,"visible":true,"origin":"","legend":"\u003cp\u003ea: Evolution of the equivalent thicknesses (ETh) of Pb as a function of square root of time from Cr lead crystal glasses. b: Diffusion coefficients of Pb after 14 days of alteration calculated from equation 5 as a function of the Cr content in the glass.\u003c/p\u003e","description":"","filename":"Figure4.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/422d1824ccaec628d8103933.png"},{"id":67461508,"identity":"2dcc29f3-c8d5-45c8-8188-4cba5b3d5150","added_by":"auto","created_at":"2024-10-25 09:40:22","extension":"png","order_by":5,"title":"Figure 5","display":"","copyAsset":false,"role":"figure","size":91465,"visible":true,"origin":"","legend":"\u003cp\u003eOptical absorption spectra for chromium colored lead crystal glasses. The position of the absorption bands characteristic of the two Cr oxidation states are indicated by the dotted experimental spectra obtained on reference oxide compounds by Bamford [18]. Spectra are normalized to their maximal intensity and to the thickness of the sample. Spectra have been shifted vertically for better readability.\u003c/p\u003e","description":"","filename":"Figure5.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/bbdc1ecf2227e2afb15e6ea7.png"},{"id":67461757,"identity":"1edd3c39-bd8d-4e1e-8919-d7dc5f21fdfa","added_by":"auto","created_at":"2024-10-25 09:48:22","extension":"png","order_by":6,"title":"Figure 6","display":"","copyAsset":false,"role":"figure","size":77570,"visible":true,"origin":"","legend":"\u003cp\u003e207Pb static NMR spectra performed at 7 T with a recycling delay of 2 seconds. Spectra are normalized to the same sample mass, using identical experimental conditions.\u003c/p\u003e","description":"","filename":"Figure6.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/5f23043f777f1f1b76e86e4e.png"},{"id":67461513,"identity":"5d11eee6-b742-483e-a541-37da21afae84","added_by":"auto","created_at":"2024-10-25 09:40:22","extension":"png","order_by":7,"title":"Figure 7","display":"","copyAsset":false,"role":"figure","size":466805,"visible":true,"origin":"","legend":"\u003cp\u003eCr K-edge X-ray absorption near-edge spectra of pristine (plain lines) and 330 days altered (dotted lines) glass slabs. Each spectrum resulted from the averaging of 2 to 8 spectra (for each sample the number of spectra averaged is indicated in the caption between brackets). a: XANES spectra of the Cr-bearing samples before and after alteration. The spectra are shifted vertically for better readability. b: XANES spectra obtained for BAC_Cr2000 before and after alteration and a spectrum from stichtite, a Cr(III) bearing mineral. c: XANES spectra obtained for BAC_Cr2000 before and after alteration and spectra from crocoite and fornacite, Cr(VI) bearing minerals. The position of the main peak is indicated as well as the position of the pre-edge features.\u003c/p\u003e","description":"","filename":"Figure7.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/6be0cd503ba10e8bb5463a6b.png"},{"id":67462778,"identity":"a0077f39-5654-41fd-8ce2-8ce1f8c6f33b","added_by":"auto","created_at":"2024-10-25 09:56:22","extension":"png","order_by":8,"title":"Figure 8","display":"","copyAsset":false,"role":"figure","size":323187,"visible":true,"origin":"","legend":"\u003cp\u003eXRF mapping and XANES spectra from a slab of Cr-bearing glass BAC_Cr2000 (0.028 mol% Cr) after 330 days of alteration at 70 °C, pH = 2.4. a: XRF mapping of K K-α with false colours from the edge of the altered slab. The depleted zone in K is considered as indicative of the altered layer and the locations of the XANES spectra shown in b are marked on the map. b: Cr K-edge experimental µXANES spectra from the altered zone (spectra altered_50 and altered_55) and the pristine zone (pristine_54) of the cross-section area presented in figure a. XANES spectra obtained on bulk slabs of pristine and 365-days altered BAC_Cr2000 are also given for comparison.\u003c/p\u003e","description":"","filename":"Figure8.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/d4174ffe3338e601eb869b11.png"},{"id":67461759,"identity":"4a7c5f9c-3fdd-424b-8c35-f475288010fe","added_by":"auto","created_at":"2024-10-25 09:48:22","extension":"png","order_by":9,"title":"Figure 9","display":"","copyAsset":false,"role":"figure","size":97860,"visible":true,"origin":"","legend":"\u003cp\u003eComparison of \u003csup\u003e29\u003c/sup\u003eSi MAS NMR spectra obtained on pristine (solid lines) and altered (dashed lines) chromium colored lead crystal glasses.\u003csup\u003e29\u003c/sup\u003eSi MAS NMR spectra performed at 11.72 T and normalized to the same sample mass, using identical experimental conditions.\u003c/p\u003e","description":"","filename":"Figure9.png","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/c212061057bf272da02b4965.png"},{"id":81987712,"identity":"eaada0a0-1f50-4b92-8d77-377d9b79cffb","added_by":"auto","created_at":"2025-05-05 16:05:08","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":2999465,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/fd895d12-9f95-4404-8d47-bc7ab58a3cb1.pdf"},{"id":67461758,"identity":"1c83de47-6df1-4083-bcec-5f1853afc833","added_by":"auto","created_at":"2024-10-25 09:48:22","extension":"pdf","order_by":1,"title":"","display":"","copyAsset":false,"role":"supplement","size":629070,"visible":true,"origin":"","legend":"","description":"","filename":"SUPPLEMENTARYINFORMATION.pdf","url":"https://assets-eu.researchsquare.com/files/rs-5284279/v1/55f4dd7b79e5521fac71918c.pdf"}],"financialInterests":"No competing interests reported.","formattedTitle":"Insight into the structure and chemical durability of Cr-bearing lead crystal glass","fulltext":[{"header":"INTRODUCTION","content":"\u003cp\u003eChromium is used as a colorant in the glass industry rendering different colours in function of its oxidation degree, notably blue for Cr(II), green for Cr(III) and yellow for Cr(VI). The latter was introduced in the 1970s as a replacement for uranium in tinting wine bottles, after uranium was banned due to well-documented human health risks. But in 2001, after working on Pb, Cd and Hg, a group of international experts gained interest for hexavalent chromium following a report by the World Health Organization\u003csup\u003e1\u003c/sup\u003e about the toxicity of Cr(VI) towards environment and human health. These experts highlighted the scientific challenge of accurately distinguishing between Cr(III), considered harmless, and Cr(VI) in various media, including solids and liquids, as well as inhibiting the oxidation of Cr(III) to Cr(VI).The latter must be carefully controlled and immobilized, particularly in the case of glass containers intended for food consumption or packaging, where prolonged contact between the glass and the edible contents occurs. A method was then proposed for the detection of Cr(VI) in daily glass containers with a claimed sensibility of 2 mg per kg of glass. The method consists in total dissolution of the glass through strong acidic attack and analysis of Cr(VI) by spectrophotometry\u003csup\u003e2\u003c/sup\u003e. About 20 years later, the European commission has lowered the authorized Cr(VI) content to 0.005 mg/kg for liquid or sticky toy material\u003csup\u003e3\u003c/sup\u003e.\u003c/p\u003e\n\u003cp\u003eAnother comparison can be made with plastic materials, since the European Regulation on articles intended to come into contact with food was amended in 2020\u003csup\u003e4\u003c/sup\u003e taking into account the great difficulty to differentiate Cr(III) from Cr(VI). Therefore two different regimes were promulgated,\u003cem\u003e\u0026nbsp;i)\u003c/em\u003e if it can be proved that the presence of hexavalent chromium in the plastic material can be excluded because it is not used or formed during the entire production process, a migrating limit of 3.6 mg/kg is applied but,\u003cem\u003e\u0026nbsp;ii)\u003c/em\u003e if it is not the case, then the second regime is enforced: a migration limit of 0.01 mg/kg corresponding to the detection limit for total chromium according to current tests performed by the National Reference Laboratories.\u003c/p\u003e\n\u003cp\u003eThe urge for lowering the authorized thresholds raises the question of the scientific limits for Cr(VI) detection routinely and draws attention to the fundamental understanding of the structural role and behavior of chromium in glass. Addressing these challenges from a materials science perspective, using advanced analytical techniques, could prevent the complete banning of chromium in all oxidation states from industrial use, provided it cannot be definitively demonstrated that Cr(III) cannot transform into Cr(VI). Currently, Cr(VI) is subject to authorization in Europe under Appendix XIV of the Registration, Evaluation, Authorization, and Restriction of Chemicals (REACh) regulation, which lists substances of very high concern (SVHC)\u003csup\u003e5\u003c/sup\u003e. This regulation compels industrial manufacturers to reconsider their use of chromium, which remains essential in its Cr(III) form, particularly in the long-standing process of producing green-colored lead crystal glass.\u003c/p\u003e\n\u003cp\u003eThe main goal of our study is to understand the effects of chromium on the structure and durability of lead crystal glass. The alteration of lead crystal glass has already been studied through various works in the literature, especially with acetic acid solution\u003csup\u003e6,7\u003c/sup\u003e and at the same leaching temperature, 70\u0026deg;C\u003csup\u003e6,8\u003c/sup\u003e. These works have already evidenced the rapid initial leaching of alkalis at the first stage of alteration which is then inhibited over time by the increase of the diffusion distance and the repolymerization of the silicate network with the formation of a diffusive barrier of a few hundreds of nanometers. The release of lead is significantly lower than that of alkalis, and its leaching rate becomes nearly negligible after the reorganization of the silicate network, indicating effective retention of lead in the altered layer over the course of several years\u003csup\u003e8\u003c/sup\u003e. But to date, the impact of the leaching of chromium on the other constitutive elements of lead crystal glass (Si,\u0026nbsp;Pb, Na and K) and on the solution chemistry have not been reported. The structure of Cr-free lead crystal glass of the same composition has already been examined extensively by solid-state high resolution Nuclear Magnetic Resonance (NMR)\u003csup\u003e6,8,9\u003c/sup\u003e. Building on from this knowledge, further structural characterizations would allow to determine the structural role of chromium and its interactions with the constitutive elements in a lead crystal glass matrix.\u003c/p\u003e\n\u003cp\u003eTo answer all these questions, 4 ingots of lead crystal glasses with roughly 50, 250, 500, 2000 ppm of chromium oxide (Cr\u003csub\u003e2\u003c/sub\u003eO\u003csub\u003e3\u003c/sub\u003e) were prepared by adding the coloring oxide to the plain crystal glass creating a palette of green hues from light tender green to deep forest green. These glasses were then leached in acetic acid 4 % (v/v), considered as the reference medium for food contact studies\u003csup\u003e10\u003c/sup\u003e, at 70 \u0026deg;C to accelerate alteration mechanisms, under the form of powder and slabs up to 330 days. Slabs were analyzed by micrometric X-Ray Fluorescence (\u0026micro;XRF) and X-Ray Absorption Near Edge Spectroscopy (XANES) at the Cr K-edge. These techniques allowed us to determine the oxidation degree of chromium in the pristine and altered glass, tracking potential dismutation mechanisms of this element induced by the alteration process. These results were supported by Optical Absorption Spectroscopy performed on the pristine glass slabs. Finally the structural changes of the pristine glass structure brought by the addition of chromium were uncovered by solid-state\u0026nbsp;\u003csup\u003e29\u003c/sup\u003eSi and\u0026nbsp;\u003csup\u003e207\u003c/sup\u003ePb NMR spectroscopy.\u003c/p\u003e"},{"header":"RESULTS","content":"\u003cp\u003e\u003cstrong\u003eGlass composition\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe glasses shown on Figure\u0026nbsp;1\u0026nbsp;were found to be homogeneous and fully vitreous under scanning electron microscopy (SEM) that is a micrometric scale. They were analyzed by electron micro probe analyzer (EMPA) and the results are available in Table\u0026nbsp;1\u0026nbsp;displaying Cr concentrations ranging from 0.002 mol% (BAC_Cr50) to 0.028 mol% (BAC_Cr2000) and minimal composition differences besides the Cr content.\u003c/p\u003e\n\u003cdiv align=\"\"\u003e\n \u003ctable border=\"0\" cellspacing=\"0\" cellpadding=\"0\" width=\"404\"\u003e\n \u003ctbody\u003e\n \u003ctr\u003e\n \u003ctd colspan=\"5\" valign=\"bottom\" style=\"width: 404px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eTable 1\u0026nbsp;\u003c/strong\u003e\u003cstrong\u003eComposition of the studied glass analysed by electron micro probe analyzer (EMPA) expressed in mol% of elements.\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd valign=\"bottom\" style=\"width: 79px;\"\u003e\n \u003cp\u003e\u0026nbsp;\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eCr 50\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eCr 250\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eCr 500\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eCr 2000\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eSi\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e26.8\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e26.8\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e26.9\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e26.8\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eNa\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.6\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.6\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.6\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e0.6\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eK\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e7.2\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e7.2\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e7.3\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e7.3\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003ePb\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e3.6\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e3.6\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e3.5\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e3.6\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eSb\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.1\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.1\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.1\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e0.1\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003ctr\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e\u003cstrong\u003eCr\u003c/strong\u003e\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.002\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.006\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 79px;\"\u003e\n \u003cp\u003e0.013\u003c/p\u003e\n \u003c/td\u003e\n \u003ctd style=\"width: 89px;\"\u003e\n \u003cp\u003e0.028\u003c/p\u003e\n \u003c/td\u003e\n \u003c/tr\u003e\n \u003c/tbody\u003e\n \u003c/table\u003e\n\u003c/div\u003e\n\u003cp\u003e\u003cstrong\u003eLeaching of chromium colored lead crystal glasses\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eDuring 330 days, glass powders of BAC_Cr50, BAC_Cr250, BAC_Cr500, BAC_Cr2000 were altered with a high SA/V\u003cem\u003egeo\u003c/em\u003e ratio (500 m\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e calculated from equation 1 giving access to the Equivalent Thickness (ETh) of glass altered per element from equations 2 and 3 over time. The ETh for Si, Pb, Na and K, the main glass constituents, are represented for 112 days in Figures 2a, 2b, 2c and 2d, respectively.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003eThe alkalis are released through an ion-exchange mechanism (linear release as function of the square root of time), as expected from the literature\u003csup\u003e6\u0026ndash;8\u003c/sup\u003e. Silicon showed the lowest alteration rate of all measured elements, about 100 times smaller than for alkalis, indicative of a slow hydrolysis reaction of the silicate network compared to the fast ion-exchange mechanism. This results in a linear release of Si as a function of time. There is no relation between Cr content in the glass and the alteration rates of Na, K, and Si. The increasing concentration of dissolved silica reduces the rate of Si‒O‒Si hydrolysis and favors the re-organization of the alteration layer\u003csup\u003e11\u003c/sup\u003e. Polymerization may contribute to the formation of a diffusive barrier, along with other phenomena, which could explain the sharp decrease in alkali alteration observed after 14 days\u003csup\u003e12\u003c/sup\u003e.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003eUnlike the other constitutive elements studied (Na, K and Si), the leaching of Pb showed a different behavior. A final sampling at 330 days confirmed the consistent long-term behavior of Pb and Cr. (Figure\u0026nbsp;3). Additionally, the Eth(Pb) showed a clear correlation with the Cr content in the glass, demonstrating a decrease in Pb leaching as the Cr content increased. Moreover, the behavior of Cr followed the linear release of Si (Figure\u0026nbsp;3). At 330 days, the Cr and Pb leached layer is about 200 nm and 500 nm, respectively.\u003c/p\u003e\n\u003cp\u003eThe evolution of Eth(Na, K, Pb) have been represented as a function of the\u0026nbsp;square root of time, as\u0026nbsp;displayed in\u0026nbsp;Supplementary Figure\u0026nbsp;1a\u0026nbsp;for Na,\u0026nbsp;1b\u0026nbsp;for K and Figure\u0026nbsp;4a\u0026nbsp;for Pb. The trend for Na and K are fully linear confirming\u0026nbsp;the diffusion controlled mechanism of alteration. For Pb, a domain of linearity between 0 and 14 days of alteration can be noticed in figure\u0026nbsp;4a, from which diffusion coefficients were calculated using equation\u0026nbsp;5\u0026nbsp;for each of the Cr-bearing glasses. These coefficients D(Pb) are presented in function of the logarithm of the molar content in Cr of the glasses in Figure\u0026nbsp;4b, exposing a linear correlation between the decrease of the diffusion coefficient of Pb and the logarithm of the molar Cr content in these glasses.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003ePristine glass structure and properties\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eFor many decades, various relationships between alteration behavior and glass structure have been highlighted and investigated by the glass community across a wide range of glass compositions, including lead crystal glass\u003csup\u003e6\u003c/sup\u003e. Since the results of the present work revealed differential leaching kinetics that depended on a single compositional variable, namely the Cr content, investigations into the redox state and structure of the pristine glasses were conducted. The oxidation degree of Cr was first determined by optical absorption spectroscopy to gain information on the configuration of Cr in the bulk pristine glasses. Then, the structure of glasses was addressed through \u003csup\u003e29\u003c/sup\u003eSi and \u003csup\u003e207\u003c/sup\u003ePb solid-state NMR.\u003c/p\u003e\n\u003cp\u003e\u003cem\u003eOptical absorption spectroscopy\u003c/em\u003e\u003c/p\u003e\n\u003cp\u003eFor Cr, the most common oxidation states found in silicate glasses are Cr(III) and Cr(VI) which have close but distinct absorption bands in the visible and near ultraviolet regions of the light spectrum\u003csup\u003e13\u003c/sup\u003e. The presence of both species in the Cr-bearing pristine glasses has been investigated by optical absorption spectroscopy and the results are shown in Figure\u0026nbsp;5. The spectra obtained on pure crystalline reference compounds of Cr(III) and Cr(VI) (extracted from Bamford, 1977\u003csup\u003e14\u003c/sup\u003e) are displayed on Figure\u0026nbsp;5. The spectrum of Cr(III) is characterized by two large Gaussian shaped bands of absorption centered at 15 000 and 22 000 cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e which are responsible for the green color of Cr(III)-bearing materials. They account for the spin-allowed, parity forbidden d\u0026ndash;d transitions of octahedral Cr\u003csup\u003e3\u003c/sup\u003e\u003csup\u003e+\u003c/sup\u003e: \u003csup\u003e4\u003c/sup\u003eA\u003csub\u003e2\u003cem\u003eg\u0026nbsp;\u003c/em\u003e\u003c/sub\u003e\u003cem\u003e\u0026rarr;\u0026nbsp;\u003c/em\u003e\u003csup\u003e4\u003c/sup\u003eT\u003csub\u003e2\u003cem\u003eg\u003c/em\u003e\u003c/sub\u003e and \u003csup\u003e4\u003c/sup\u003eA\u003csub\u003e2\u003cem\u003eg\u003c/em\u003e\u003c/sub\u003e\u003cem\u003e\u0026nbsp;\u0026rarr;\u003c/em\u003e\u003csup\u003e4\u003c/sup\u003eT\u003csub\u003e1\u003cem\u003eg\u003c/em\u003e\u003c/sub\u003e.\u0026nbsp;The most oxidized specie of Cr, Cr(VI), is identified by an unique Gaussian shaped band of absorption, centered at 27 500 cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e and yields yellowish colored glasses, especially when unmixed with other Cr species. The spectra obtained on pristine Cr-bearing glasses were collected on large portions of the glasses (about 7 mm\u003csup\u003e2\u003c/sup\u003e) and are presented above the reference spectra clearly showing the presence of Cr(III). The raising intensity of the bands located at 15 000 and 22 000 cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e went along with the increase of the total Cr-content in the glasses.\u003c/p\u003e\n\u003cp\u003eFrom the Beer-Lambert law, the absorbance of a glass depends on the molar extinction coefficient of its compounds, the length of the light path and the concentration of the optically active species, in our case Cr(III) and Cr(VI). It has been calculated that for Cr(III) in silicate alkali glasses, the molar extinction coefficient\u0026nbsp;\u0026epsilon;\u003cem\u003eCr\u003c/em\u003e(\u003cem\u003eIII\u003c/em\u003e)\u0026nbsp;is around 18-20 L.mol\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e.cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u0026nbsp;\u003c/sup\u003e\u003csup\u003e14\u0026ndash;16\u003c/sup\u003e\u003csup\u003e\u0026nbsp;\u0026nbsp;\u003c/sup\u003ewhereas for Cr(VI) the molar extinction coefficient associated with the absorption band at 27 500 cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e is around 4200 L.mol\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e.cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u0026nbsp;\u003c/sup\u003ein the same glass matrices\u003csup\u003e13,17,18\u003c/sup\u003e. Hence an absorbance more than 200 times greater for Cr(VI) compared to Cr(III) at equal concentrations and light path length. Considering our least concentrated sample, with a given light path and a given total Cr concentration of 0.002 mol%, the absorbance of equal concentrations of Cr(III) and Cr(VI), which depend directly on their respective molar extinction coefficients, is then 200 times more intense for Cr(VI) than Cr(III). Consequently, a 200 times lower concentration of Cr(VI) than Cr(III) can be detected. Since only two absorption bands are detected at 15 000 and 22 000 cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e, corresponding to Cr(III) signal only, it can be assumed that the detection limit for Cr(VI) is at least 200 times lower than the total Cr amount which has been attributed to Cr(III), that is 1\u003cem\u003e\u0026nbsp;\u0026times;\u003c/em\u003e 10\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e5\u0026nbsp;\u003c/sup\u003emol%. Thus, the optical absorption spectroscopy demonstrated that the Cr-bearing pristine glasses contained Cr(III) only with a detection limit for Cr(VI) of 1\u003cem\u003e\u0026nbsp;\u0026times;\u003c/em\u003e 10\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e5\u0026nbsp;\u003c/sup\u003emol%.\u003c/p\u003e\n\u003cp\u003e\u003cem\u003e\u003csup\u003e29\u003c/sup\u003e\u003c/em\u003e\u003cem\u003eSi and \u003csup\u003e207\u003c/sup\u003ePb NMR spectroscopy\u003c/em\u003e\u003c/p\u003e\n\u003cp\u003eThe distribution of Q\u003cem\u003e\u003csup\u003en\u003c/sup\u003e\u003c/em\u003e species in the glass is accessed via \u003csup\u003e29\u003c/sup\u003eSi MAS NMR, which was performed on Cr-bearing glasses. The results are\u0026nbsp;presented in\u0026nbsp;Figure\u0026nbsp;9\u0026nbsp;for the two extrema of Cr-bearing glasses showing a distribution centered on Q\u003csup\u003e3\u003c/sup\u003e and Q\u003csup\u003e4\u003c/sup\u003e species. Tetracoordinated silicate units Q\u003csup\u003e4\u003c/sup\u003e have four bridging oxygens (i.e. oxygen bonding two silicate units at a corner). A slight variation in the distribution of Q\u003csup\u003e3\u003c/sup\u003e and Q\u003csup\u003e4\u003c/sup\u003e species can be observed, with a slight decrease in Q\u003csup\u003e3\u003c/sup\u003e and a corresponding increase in Q\u003csup\u003e4\u003c/sup\u003e species as the Cr content increases. Surprisingly the addition of a paramagnetic compound like chromium oxide to the glass batch did not affect the intensity of the \u003csup\u003e29\u003c/sup\u003eSi MAS NMR spectra obtained for Cr-bearing glasses, but significant effect is observed on \u003csup\u003e207\u003c/sup\u003ePb signal intensity than that observed on \u003csup\u003e29\u003c/sup\u003eSi as displayed in Figure 6. The spectra were normalized to the same sample mass, with identical experimental conditions allowing direct quantitative comparison of the obtained results. Additionally, for the glass with the highest Cr content, the lineshape of the \u003csup\u003e29\u003c/sup\u003eSi MAS NMR spectrum did not vary with the recycle delay as shown in Supplementary Figure 2. Considering the paramagnetic nature of Cr(III), and according to previous studies using contrast in the NMR signal induced by differential spin-lattice relaxation rates, (see \u003csup\u003e19\u003c/sup\u003e for example), this suggests that no phase segregation occurs, which would have led to a preferential relaxation of specific Si sites.\u003c/p\u003e\n\u003cp\u003eThe growing intensity of the \u003csup\u003e207\u003c/sup\u003ePb NMR spectra observed in Figure 6 can only be related to the increase of the Cr content in the glass samples. This could be explained by the shortening of \u003csup\u003e207\u003c/sup\u003ePb relaxation time T\u003csub\u003e1\u003c/sub\u003e by paramagnetic Cr, leading to higher intensity signals. No detailed investigation of \u003csup\u003e207\u003c/sup\u003ePb T\u003csub\u003e1\u003c/sub\u003e were carried out, mainly because of the very long time required to collect the data (several days). The NMR lineshape, acquired under static, i.e. non-spinning conditions, is close to that of an environment dominated by a large CSA tensor, as already measured in lead silicate glasses\u003csup\u003e20,21\u003c/sup\u003e. Then, NMR pointed out the proximity between Pb and Cr atoms suggested by the increase \u003csup\u003e207\u003c/sup\u003ePb spectra intensity upon to the addition of Cr.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eStructure of altered glasses\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003e\u003cem\u003eXANES on bulk glasses\u003c/em\u003e\u003c/p\u003e\n\u003cp\u003eThe behavior of Cr in lead crystal glass exposed to harsh alteration conditions was investigated using X-ray Absorption Near Edge Spectroscopy (XANES) at the Cr K-edge on both pristine and altered glasses at the ID21 beamline of the European Synchrotron Radiation Facility (ESRF, France)\u003csup\u003e22\u003c/sup\u003e. While optical absorption spectroscopy established the absence of Cr(VI) at the pristine state, the potential changes in oxidation state caused by the local restructuring of the altered layer required to investigate Cr speciation specifically in the surface region. Two approaches were followed. First, XANES was performed with a large, unfocused beam (100-350 \u0026micro;m) directly at the surface of pristine and altered glass slabs. Then, \u0026micro;XANES analyses were obtained with a focused beam (0.26\u003cem\u003e\u0026times;\u003c/em\u003e0.8 \u0026micro;m\u003csup\u003e2\u003c/sup\u003e, v\u003cem\u003e\u0026times;\u003c/em\u003eh.), on cross-section of altered glass, both in the most external area and in a deeper region. In the first approach, photons are spread over a large area, decreasing the dose and consequently the risk of beam damage. However, it should be taken into account that at the Cr K-edge, the attenuation length of X-ray is 7 \u0026micro;m, larger than the alteration layer (6 \u0026micro;m). Therefore, a small contribution from deep, unaltered glass should not be neglected. In the second approach, the photons are laterally concentrated in a very small probe. Radiation tests were carried out by repeating XANES acquisitions at the same positions and revealed the formation of chromate, Cr(VI), under the beam. To slow down this oxidation reaction, different adaptations to the standard set-up were done. The beam intensity was reduced with a 50 \u0026micro;m Al attenuator; the energy step was increased from 0.4 eV (as used in unfocused mode) to 0.6 eV; the starting energy was increased from 5.95 keV to 5.985 keV, to avoid unnecessary exposure of the samples to photons. Finally, the beam fast shutter was opened only during data collection. Besides, spectra were collected as single scans, over different points, from the surface to the depth of the glass. A first \u0026micro;XRF map was systematically collected prior to \u0026micro;XANES spectra to locate this alteration layer. The first method yielded good quality spectra as shown in Figure\u0026nbsp;7,\u0026nbsp;however with merged signals of the pristine and altered glass. The second approach allowed to target alteration layers only but with a low X-ray dose to preserve the samples producing noisier spectra as exposed in Figure\u0026nbsp;8b.\u003c/p\u003e\n\u003cp\u003eFigure\u0026nbsp;7a\u0026nbsp;displays the superposition of the mean spectrum acquired on bulk pristine and 330 days altered glass for each of the Cr-bearing glass. The same shape of spectrum was observed for all the glasses although the least concentrated glasses in Cr (BAC_Cr50 and BAC_Cr250) yield, evidently, noisier spectra. Perfect good overlap of the pristine (solid lines) and altered (dashed lines) XANES spectra of each glass was observed with a slightly lower intensity of the main peak for the spectra collected on altered samples revealing small modification of Cr environment between the pristine and altered glasses. The same acquisitions were carried out on all the samples.\u003c/p\u003e\n\u003cp\u003eTo confirm the oxidation state of Cr in our glasses, the experimental pristine and altered spectra of BAC_Cr2000 were compared to mineral references of Cr(III): stichtite (a magnesium and chromium carbonate), and Cr(VI): crocoite (PbCrO4) and fornacite (Pb2Cu(CrO4)(AsO4)(OH)), both containing Pb, as our samples. The results are shown in figures\u0026nbsp;7b\u0026nbsp;and\u0026nbsp;7c, respectively. A good agreement can be noticed between the experimental spectra and the Cr(III) reference highlighting a key feature in the pre-edge region with a peak common to all spectra at 5.9913 keV. The features of this region of the spectrum, before the edge, are indicative of electronic transitions from orbital 1\u003cem\u003es\u003c/em\u003e to orbital 3\u003cem\u003ed\u003c/em\u003e of transition metal cations like Cr. The intensity of the peak at 5.9913 keV is notably low for all spectra which is expected from the inversion of symmetry of\u003cem\u003e\u0026nbsp;p\u0026nbsp;\u003c/em\u003eand\u003cem\u003e\u0026nbsp;d\u003c/em\u003e orbitals in the octahedral configuration imposed by Cr(III) valence. Regarding Cr(VI) which exhibits tetrahedral configuration, the geometry of orbitals\u003cem\u003e\u0026nbsp;p\u003c/em\u003e and\u003cem\u003e\u0026nbsp;d\u003c/em\u003e is favorable to their mixing resulting in an intense pre-edge at 5.9935 keV (Figure 7c). The post-edge region echoes the Cr local environment which varies a lot among references compounds as awaited. Regarding the edge region in figure 7b, an offset of 3 eV between the white-line position of our samples and the stichtite Cr(III) reference is discerned. Variation in the edge position is usually significant of different oxidation state.\u003c/p\u003e\n\u003cp\u003eIn this case the shift towards lower energies could have been interpreted as the presence of Cr(II) mixed with Cr(III) as described by Berry\u003cem\u003e\u0026nbsp;et al.\u003c/em\u003e\u003csup\u003e23\u003c/sup\u003e but the presence of Cr(II), characterized by a large absorption band spreading from 10 000 to 20 000 cm\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e \u003csup\u003e24\u003c/sup\u003e was not detected by optical absorption spectroscopy on the pristine glass (Figure 5). Most likely, these differences are significant of the different ligands of Cr between the references and the glasses of interest. Then, XANES spectra on the bulk pristine and altered Cr-bearing lead crystal glasses evidenced the presence of Cr(III), reinforcing the conclusions obtained by optical absorption spectroscopy in the pristine glasses.\u003c/p\u003e\n\u003cp\u003e\u003cem\u003e\u0026micro;XRF and \u0026micro;XANES on cross-sections\u003c/em\u003e\u003c/p\u003e\n\u003cp\u003eXRF mapping of polished cross sections of the altered slabs enabled the identification and localization of an alkali depleted layer outlining the pristine glass and corresponding to the alteration layer. An example of XRF mapping for potassium (K-K-\u0026alpha;) obtained on BAC_Cr2000 cross-section after 330 days of alteration is given in Figure\u0026nbsp;8a. The layer appeared of constant thickness and perfectly parallel to the edge of the sample despite the rugosity which arose from the sample preparation. The measured thickness of the potassium depleted altered layer was of 6.00\u003cem\u003e\u0026plusmn;\u003c/em\u003e0.25 \u0026micro;m, corresponding to the green area at the top in Figure\u0026nbsp;8a. The dark blue area represents the epoxy resin that embedded the sample and the yellow region designates the pristine glass with hues variations reflecting the local topographic rugosity created by the sample preparation and not actual gradients of concentration in potassium.\u003c/p\u003e\n\u003cp\u003eBy focusing the incident X-ray beam a resolution of 0.8\u003cem\u003e\u0026nbsp;\u0026times;\u003c/em\u003e 0.26 \u0026micro;m\u003csup\u003e2\u003c/sup\u003e (\u003cem\u003eh\u003c/em\u003e\u003cem\u003e\u0026nbsp;\u0026times;\u003c/em\u003e\u003cem\u003e\u0026nbsp;v\u003c/em\u003e) was obtained allowing \u0026micro;XANES analyses in the pristine glass and in the altered layer distinctively. Three points of interest were selected, their location is indicated in Figure\u0026nbsp;8a\u0026nbsp;and the corresponding XANES spectra are presented in Figure\u0026nbsp;8b\u0026nbsp;alongside the spectra obtained on bulk slabs of BAC_Cr2000 with a defocused beam. As anticipated due to the attenuated intensity of the beam used for focused XANES analyses on the cross-section, the spectra obtained display more background noise than those collected on the bulk glass using a defocused beam. Nonetheless, the comparison of spectra from the pristine glass, cross-section and bulk showed very similar shape and intensity, validating the presence of Cr(III) only in both cases. For the spectra obtained from the alteration layer of the cross-section (spectra \u0026apos;altered_50\u0026apos; and \u0026apos;altered_55\u0026apos;), the edge position remained consistent with that observed in the bulk glass analyses (spectrum \u0026apos;BAC_Cr2000 (5) altered\u0026apos;) and in the pristine glass, located at 6.0075 keV. The pre-edge region (5.9800 - 5.9950 keV) of the cross-section spectra is not very well defined because of the low dose of X-ray used in the focused mode to avoid photoinduced oxidation. The presence of Cr(VI), indicated by a pre-edge at 5.9935 keV with greater intensity than that expected for Cr(III)\u003csup\u003e13\u003c/sup\u003e, should be distinguishable from the background noise. The absence of distinct features in this region can be interpreted as evidence for the lack of Cr(VI). Consequently, \u0026micro;XANES allowed the identification of Cr(III) only in pristine and altered Cr-bearing lead crystal glass samples with a Cr intake up to 0.028 %mol.\u003c/p\u003e\n\u003cp\u003e\u003csup\u003e29\u003c/sup\u003e\u003cem\u003eSi NMR spectroscopy\u003c/em\u003e\u003c/p\u003e\n\u003cp\u003eAfter alteration, glass powder was sampled from each reactor. These powders were dried and analyzed by \u003csup\u003e29\u003c/sup\u003eSi MAS NMR. Figure\u0026nbsp;9\u0026nbsp;displays the structural changes in the silicate network induced during the leaching time. These changes are characterized by a shift towards lower chemical shifts after alteration meaning a higher amount of Q\u003csup\u003e4\u003c/sup\u003e species to the detriment of Q\u003csup\u003e2\u003c/sup\u003e and Q\u003csup\u003e3\u003c/sup\u003e species, all indicative of the increase of polymerization of the silicate network in the course of alteration. It corresponds to the strengthening of the most superficial part of the altered layer participating in the diffusive barrier effect responsible for the drop of the rate of alteration noticed in Figure 2 for Na, K and Pb after 14 days.\u003c/p\u003e\n\u003cp\u003eThe extent of polymerization can be inferred from the increase of the area of the Q\u003csup\u003e4\u003c/sup\u003e line. After alteration, Cr-rich glass BAC_Cr2000 had the largest proportion of Q\u003csup\u003e4\u003c/sup\u003e species compared to BAC_Cr50. Consequently, it can be assumed that the presence of Cr in the glassy matrix favored the polymerization of the glass in the course of alteration. Besides the slightly more polymerized network noticed for Cr-bearing glasses at the pristine state, this trend is then confirmed and amplified after alteration by the leaching mechanisms calling attention to the strong effect of Cr, even at low concentrations, on the structure of Cr lead crystal glasses.\u003c/p\u003e"},{"header":"Discussion","content":"\u003cp\u003eThe presence of Cr(III) only in the investigated glasses has been established using XANES and optical absorption spectroscopy. Moreover, extensive studies of Cr(III) in various other Cr-containing glasses using the same analytical techniques arrived at the following conclusions. On the one hand, XANES showed that Cr(III) was always found hexacoordinated with an octahedral geometry and low variations in its local environment\u003csup\u003e15,23,25,26\u003c/sup\u003e. On the other hand, optical absorption spectroscopy revealed the preferential localization of Cr atoms in cationic domains of the glass\u003csup\u003e27\u003c/sup\u003e with a preference for alkalis over earth-alkalis\u003csup\u003e15\u003c/sup\u003e. Overall, Cr(III) was not uniformly distributed within the glass networks but was located in specific, somewhat disordered sites\u003csup\u003e15\u003c/sup\u003e.\u003c/p\u003e\n\u003cp\u003ePrevious structural studies on lead crystal glass without Cr highlighted the presence of sites mixing Pb and K, written: Si\u0026ndash;O\u0026ndash;(Pb, K), near Non-Bridging Oxygens (NBOs) by\u0026nbsp;\u003csup\u003e17\u003c/sup\u003eO multi-quantum magic-angle spinning (MQMAS) NMR\u003csup\u003e6\u003c/sup\u003e. These sites exhibit the previously described characteristics for hosting Cr(III), namely a higher degree of chemical disorder in the cationic domains.\u0026nbsp;\u003csup\u003e207\u003c/sup\u003ePb static NMR spectroscopy successfully demonstrated the proximity of Pb and Cr within the glass network. In lead crystal glasses, the 10.6 mol% of PbO is too low to form a subnetwork of Pb units. Consequently, Pb is not considered as a network former, and glass network is composed of silicate units, within whose interstices Pb and alkali metals are localized\u003csup\u003e28,29\u003c/sup\u003e. Thus, Cr cations could be positioned near these NBO domains.\u0026nbsp;\u003csup\u003e29\u003c/sup\u003eSi MAS NMR spectroscopy points out a slight increase in polymerization as the Cr content increases. These findings support the description of Cr(III) as a network hardener, reinforcing the network polymerization of the pristine glass.\u003c/p\u003e\n\u003cp\u003eFrom the structural and alteration data, the specific role of Cr can be highlighted. Cr is partially retained near the cationic domains during alteration, also improving Pb retention though the role of network hardener. Pb and Cr entities are less accessible to protonated species, which reduces their mobility compared to alkali metals that are distributed throughout the entire glassy matrix. Consequently, their exchange and transport kinetics are slower compared to Na and K. The part of leached Cr and Pb favors the Si recondensation in the rich NBO mixing sites, leading in an increase of the glass polymerization within the altered layer, as observed by\u0026nbsp;\u003csup\u003e29\u003c/sup\u003eSi MAS NMR after leaching. The polymerization is clearly amplified when the Cr content in the glass increases.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003eThe fact that the release kinetics of Pb is lower than a purely diffusional behavior proportional to the square root of time may be linked to the increased polymerization in the alteration layer, which serves as an additional barrier. On the other hand, the behavior of Cr is released similarly to Si, in agreement with the role of a network hardener in the silicate network.\u003c/p\u003e\n\u003cp\u003eThe high sensitivity of lead crystal glass structure to very low contents of Cr can be outlined. In 2016, Liao\u003cem\u003e\u0026nbsp;et al.\u003c/em\u003e\u003csup\u003e30\u003c/sup\u003e reported a double barrier effect leading to the immobilization of Cr under the form of Cr(III) in glass-ceramic material where Cr(III) was retained in crystallized spinel structure and in the glassy matrix. In this study, we extend this conclusion to a fully amorphous material, demonstrating how Cr used as a colorant is well retained while 50 % of the alkalis are leached out of the glass developing micron-sized alteration layers.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003eThe results are favorable from a toxicological and environmental standpoint, supporting the absence of Cr(VI) in both the pristine and altered glasses. Additionally, only a small amount of Cr was measured in the leachate after 330 days of alteration under extremely harsh conditions (70 \u0026deg;C, pH = 2.4, SA/V\u003cem\u003egeo\u003c/em\u003e = 500 m\u003cem\u003e\u003csup\u003e\u0026minus;\u003c/sup\u003e\u003c/em\u003e\u003csup\u003e1\u003c/sup\u003e). Furthermore, the origin of the retention mechanism was clarified thanks to structural analysis tools like XANES at Cr K-edge and NMR of\u0026nbsp;\u003csup\u003e29\u003c/sup\u003eSi and\u0026nbsp;\u003csup\u003e207\u003c/sup\u003ePb nuclei, overcoming the technical difficulties inherent to the paramagnetic and easily oxidized materials under study.\u003c/p\u003e\n\u003cp\u003eThus, under very unfavorable food simulating conditions of alteration, the Cr contained in the original materials did not oxidize to Cr(VI) over the course of fabrication nor alteration of the glass and\u003cem\u003e\u0026nbsp;\u003c/em\u003ewas well immobilized with Pb in the glass structure. Under normal conditions of use (significantly lower temperature and contact time), the expected releases of Pb and Cr should be well below the limits imposed by standardized tests (24h at 25\u0026deg;C).\u003c/p\u003e"},{"header":"METHODS","content":"\u003cp\u003e\u003cb\u003eGlass preparation\u003c/b\u003e\u003c/p\u003e\u003cp\u003eFour ingots of lead crystal glass with 50, 250, 500 and 2000 ppm of chromium oxide, as visible on the photographs in Fig.\u0026nbsp;1, were fabricated from a single batch of lead crystal glass. Out of each of these ingots, square shaped slabs measuring 5 \u003cem\u003e×\u003c/em\u003e 5 \u003cem\u003e×\u003c/em\u003e 2 mm\u003csup\u003e\u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e\u003c/sup\u003e were cut and all faces were polished to 1 µm (roughness of the order of a few nanometers) to obtain perfectly geometrical and smooth surfaces. The slabs were used for µXRF and XANES analyses. A few dozens of grams of each glass was crushed, sieved and washed with acetone and absolute ethanol to obtain powders with particle size diameter ranging from 63 to 125 µm. The specific surface of each of these powders was measured with the BET method using Kr gas [11] and the powders were then used for the 330 days alteration experiment. The composition of the glasses was determined by Electronic Micro-Probe Analyzer (EMPA) and the results are displayed in Table\u0026nbsp;1. The standard deviation was calculated for each element of each glass based on 10 repetitions and the relative uncertainty is equal or below 5% of the given values for all elements, except Cr, for which the uncertainty rose up to 50% because of the very low quantities added.\u003c/p\u003e\u003cp\u003e\u003cb\u003eLeaching experiments\u003c/b\u003e\u003c/p\u003e\u003cp\u003eSamples glasses were altered with two experiments following the same protocol of alteration, the first one using glass slabs and the second one using glass powder, yielding different glass-surface-area-to-solution-volume-ratios (SA/V ratio), which were determined geometrically in both cases by precisely measuring the glass slabs and using Eq.\u0026nbsp;1 for powders. In both cases, long term alteration in static mode was performed in perfluoroalkoxy alkane reactors (PFA), at 70 ± 3°C in 4% (v/v) acetic acid solution, which corresponds to a pH of 2.4 ± 0.1. Acetic acid solutions were prepared by diluting acetic acid (100%, Merck Suprapur) in 18 MΩ.cm ultrapure water. For the alteration of glass slabs with chromium oxide content the initial SA/V ratio obtained for the alteration of 5 slabs (5 \u003cem\u003e×\u003c/em\u003e 5 \u003cem\u003e×\u003c/em\u003e 2 mm\u003csup\u003e\u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e\u003c/sup\u003e) of each glass in the same reactor was 2.45 \u003cem\u003e±\u003c/em\u003e 0.03 m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e. After 330 days year of alteration, all the glass slabs were removed from the reactors and dried at 90°C for 2 hours before cooling down over night at room temperature and humidity. One altered slab of each glass was embedded in epoxy resin and polished to obtain cross-sections of the altered slabs that were then analysed by µ-XRF and XANES at the ESRF synchrotron. As this experiment, with a very low SA/V ratio, did not allow to measure precisely the leached out element of the glasses, the second experiment with high SA/V ratio was undertaken using about 10 grams of 63–125 µm calibrated powder and 500 g of acetic acid 4% (v/v) solution to reach a SA/V ratio of 500 m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e, thus increasing the amount of leached elements in solution.\u003c/p\u003e\u003cdiv id=\"Equ1\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ1\" name=\"EquationSource\"\u003e\n$$\\:\\frac{SAgeo}{V}=\\frac{3.mglass}{Vsol.\\rho\\:.Rmean}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e1\u003c/div\u003e\u003c/div\u003e\u003cp\u003eWith \u003cem\u003eSA\u003c/em\u003e\u003csub\u003e\u003cem\u003egeo\u003c/em\u003e\u003c/sub\u003e\u003cem\u003e/V\u003c/em\u003e the glass-surface-area-to-solution-volume-ratio determined with the geometric approximation (m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e), \u003cem\u003eV\u003c/em\u003e\u003csub\u003e\u003cem\u003esol\u003c/em\u003e\u003c/sub\u003e the volume of solution in the experiment (m\u003csup\u003e\u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e\u003c/sup\u003e), \u003cem\u003emglass\u003c/em\u003e the mass of glass in the experiment (g), ρ the density of the glass (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 3\u003c/sup\u003e) and \u003cem\u003eR\u003c/em\u003e\u003csub\u003e\u003cem\u003emean\u003c/em\u003e\u003c/sub\u003e the mean radius of glass particles in the experiment (m)\u003c/p\u003e\u003cp\u003eThe alteration solution was regularly sampled from the reactors during the first 112 days of the experiment and the concentrations of glass constituents in solution were analyzed by Inductively coupled Plasma - Atomic Emission Spectroscopy (ICP-AES) after acidification with nitric acid. A final verification sampling was carried out at 330 days. The solution withdrawal generated by the samplings is considered by recalculating the glass-surface-area-to-solution-volume-ratio after each sampling.\u003c/p\u003e\u003cp\u003eFor each solution sampling, the normalized mass loss of each element of each glass was calculated using Eq.\u0026nbsp;2.\u003c/p\u003e\u003cdiv id=\"Equ2\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ2\" name=\"EquationSource\"\u003e\n$$\\:{NL}_{{geo}_{i,t}}=\\frac{{C\\left(i\\right)}_{t}}{{\\left(\\frac{{SA}_{geo}}{V}\\right)}_{t}{x}_{i}}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e2\u003c/div\u003e\u003c/div\u003e\u003cp\u003eWith \u003cem\u003eNL\u003c/em\u003e\u003csub\u003e\u003cem\u003egeoi,t\u003c/em\u003e\u003c/sub\u003e the normalized mass loss of element \u003cem\u003ei\u003c/em\u003e after \u003cem\u003et\u003c/em\u003e days of alteration (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 2\u003c/sup\u003e.d\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e), \u003cem\u003eC\u003c/em\u003e\u003csub\u003e(\u003cem\u003ei\u003c/em\u003e)\u003c/sub\u003e\u003cem\u003et\u003c/em\u003e the concentration of element \u003cem\u003ei\u003c/em\u003e in solution after \u003cem\u003et\u003c/em\u003e days of alteration (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 3\u003c/sup\u003e), \u003cem\u003eSA\u003c/em\u003e\u003csub\u003e\u003cem\u003egeo\u003c/em\u003e\u003c/sub\u003e\u003cem\u003e/Vt\u003c/em\u003e the glass-surface-area-to-solution-volume-ratio determined with the geometric approximation after \u003cem\u003et\u003c/em\u003e days of alteration (m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e), \u003cem\u003ex\u003c/em\u003e\u003csub\u003e\u003cem\u003ei\u003c/em\u003e\u003c/sub\u003e the mass fraction of element \u003cem\u003ei\u003c/em\u003e in the pristine glass\u003c/p\u003e\u003cp\u003eThese normalized losses per element can be translated to equivalent thicknesses of glass altered thanks to Eq.\u0026nbsp;3 and enable the calculation of alteration rates through partial derivation with respect to time given in Eq.\u0026nbsp;4.\u003c/p\u003e\u003cdiv id=\"Equ3\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ3\" name=\"EquationSource\"\u003e\n$$\\:Ethgeoi,t=\\frac{NLgeoi,t}{\\rho\\:}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e3\u003c/div\u003e\u003c/div\u003e\u003cp\u003eWith \u003cem\u003eEthgeoi,t\u003c/em\u003e the equivalent thickness of glass altered for element \u003cem\u003ei\u003c/em\u003e after \u003cem\u003et\u003c/em\u003e days of alteration (m), \u003cem\u003eNL\u003c/em\u003e\u003csub\u003e\u003cem\u003egeo,i\u003c/em\u003e\u003c/sub\u003e,\u003cem\u003et\u003c/em\u003e the normalized losses of element \u003cem\u003ei\u003c/em\u003e in solution after \u003cem\u003et\u003c/em\u003e days of alteration (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 2\u003c/sup\u003e.d\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e), ρ the pristine glass density (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 3\u003c/sup\u003e).\u003c/p\u003e\u003cdiv id=\"Equ4\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ4\" name=\"EquationSource\"\u003e\n$$\\:ri\\left(t\\right)=\\frac{\\partial\\:NLgeoi,t}{\\rho\\:\\partial\\:t}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e4\u003c/div\u003e\u003c/div\u003e\u003cp\u003eWith \u003cem\u003er\u003c/em\u003e\u003csub\u003e\u003cem\u003ei\u003c/em\u003e\u003c/sub\u003e(\u003cem\u003et\u003c/em\u003e) the releasing rate of an element \u003cem\u003ei\u003c/em\u003e for a given time of alteration (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 2\u003c/sup\u003e.d\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e) and \u003cem\u003eNL\u003c/em\u003e\u003csub\u003e\u003cem\u003egeoi\u003c/em\u003e\u003c/sub\u003e,\u003cem\u003et\u003c/em\u003e the normalized losses of element \u003cem\u003ei\u003c/em\u003e in solution after \u003cem\u003et\u003c/em\u003e days of alteration (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 2\u003c/sup\u003e.d\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e).\u003c/p\u003e\u003cp\u003eThe diffusion coefficients for species with interdiffusion behavior were calculated using Eq.\u0026nbsp;5.\u003c/p\u003e\u003cdiv id=\"Equ5\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equ5\" name=\"EquationSource\"\u003e\n$$\\:Di=\\pi\\:{\\left(\\frac{ri\\left(t\\right)}{2\\rho\\:}\\right)}^{2}$$\u003c/div\u003e\u003cdiv class=\"EquationNumber\"\u003e5\u003c/div\u003e\u003c/div\u003e\u003cp\u003eWith \u003cem\u003eD\u003c/em\u003e\u003csub\u003e\u003cem\u003ei\u003c/em\u003e\u003c/sub\u003e the diffusion coefficient of an element \u003cem\u003ei\u003c/em\u003e for a given time of alteration (m\u003csup\u003e2\u003c/sup\u003e.s\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 1\u003c/sup\u003e), \u003cem\u003er\u003c/em\u003e\u003csub\u003e\u003cem\u003ei\u003c/em\u003e\u003c/sub\u003e(\u003cem\u003et\u003c/em\u003e) the partial derivative of normalized losses of element \u003cem\u003ei\u003c/em\u003e with respect to time (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 2\u003c/sup\u003e.s\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 0.5\u003c/sup\u003e) and ρ the pristine glass density (g.m\u003csup\u003e\u003cem\u003e−\u003c/em\u003e 3\u003c/sup\u003e).\u003c/p\u003e\u003cp\u003eFor this protocol, the overwhelming factor of uncertainty for the calculation of \u003cem\u003er\u003c/em\u003e\u003csub\u003e\u003cem\u003ei\u003c/em\u003e\u003c/sub\u003e(\u003cem\u003et\u003c/em\u003e), \u003cem\u003eETh\u003c/em\u003e\u003csub\u003e\u003cem\u003egeoi,t\u003c/em\u003e\u003c/sub\u003e, \u003cem\u003eNL\u003c/em\u003e\u003csub\u003e\u003cem\u003egeoi,t\u003c/em\u003e\u003c/sub\u003e is the ICP-AES determination of elemental concentrations in solution. These latter come out with a 10% relative uncertainty, which is then reflected on the calculated data.\u003c/p\u003e\u003cp\u003e\u003cb\u003eNMR spectroscopy\u003c/b\u003e\u003c/p\u003e\u003cp\u003eNMR data on \u003csup\u003e\u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e\u003c/sup\u003eSi were collected on a Bruker AVANCE II 500WB spectrometer operating at a magnetic field of 11.7 T, using a Bruker 4 mm (outer diameter of the rotor) cross-polarization MAS HX probe at a spinning frequency of 12.5 kHz. \u003csup\u003e\u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e\u003c/sup\u003eSi MAS NMR spectra were acquired using a saturation-recovery pulse sequence with a recovery delay of 20 s (increasing the recycling delay did not alter the lineshape). The \u003csup\u003e\u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e\u003c/sup\u003eSi NMR shifts were referenced against tetrakis(trimethylsilyl)silane powder (two lines at 9.9 ppm and 135.3 ppm with respect to tetramethylsilane).\u003c/p\u003e\u003cp\u003e\u003csup\u003e207\u003c/sup\u003ePb NMR spectra were acquired at a magnetic field of 7 T on a Bruker AVANCE II Spectrometer. Because of the very large width of the spectra (mainly due to a very large chemical shift anisotropy (CSA)\u003csup\u003e\u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e\u003c/sup\u003e), the variable-offset cumulative spectroscopy (referred to as VOCS)\u003csup\u003e\u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e,\u003cspan citationid=\"CR31\" class=\"CitationRef\"\u003e31\u003c/span\u003e\u003c/sup\u003e has been employed under static conditions (i.e. non-spinning sample), using carrier frequency jump of 50 kHz (typically from − 150 kHz to + 150 kHz with the origin taken at the center of the spectrum). Typically 48000 scans have been accumulated with a recycle delay of 2 s. For some offset frequency values, spectra at recycle delays of 0.5 s, 2 s, 8 s and 16 s have been compared to quantitatively estimate the relaxation of the signal and the impact of the Cr content (which was found to shorten significantly the relaxation time of \u003csup\u003e207\u003c/sup\u003ePb).\u003c/p\u003e\u003cp\u003e\u003cb\u003eµ-XRF and XANES at ESRF\u003c/b\u003e\u003c/p\u003e\u003cp\u003eMeasurements were performed at the scanning X-ray microspectroscopy end station of the beamline ID21 of the European synchrotron radiation facility (ESRF, Grenoble)\u003csup\u003e\u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e\u003c/sup\u003e. A Si(220) double-crystal monochromator was used to scan the X-ray beam energy across Cr K-edge (5.976 keV). For the calibration, the first inflection point of the first-order derivative Cr K-edge XANES spectrum of a Cr metallic foil was set at 5.9900 keV. Photoinduced oxidation was evidenced by repeating XANES spectra on the same spot and observing growing intensity of pre-edge at 5.9935 keV indicative of oxidation into Cr(VI) occurring under beam exposition. To avoid these beam damage artefacts, especially in the targeted altered layer, two different modes of analyses were adopted: \u003cem\u003ei)\u003c/em\u003e defocused beam, to sense large areas with a minimal dose of X-rays and \u003cem\u003eii)\u003c/em\u003e focused beam, µXANES, to target alteration layers specifically. In defocused mode, the beam size ranged from 100 to 350 µm, and acquisitions were carried out from 5.95 to 6.15 keV, with 500 steps of 0.4 eV. For XANES investigations, the incident beam was focused with a Kirkpatrick-Baez (KB) mirror system down to a spot size of 0.8 \u003cem\u003e×\u003c/em\u003e 0.26 µm\u003csup\u003e\u003cspan citationid=\"CR2\" class=\"CitationRef\"\u003e2\u003c/span\u003e\u003c/sup\u003e (\u003cem\u003eh × v\u003c/em\u003e) and the beam was attenuated with a 50 µm Al foil. The energy range was reduced to 5.985–6.15 keV, with steps of 0.6e V. All data were collected in vacuum.\u003c/p\u003e\u003cp\u003e\u003cb\u003eOptical absorption spectroscopy\u003c/b\u003e\u003c/p\u003e\u003cp\u003eUV-visible-near IR transmission spectra were recorded on Cr-bearing glass samples at room temperature on thin slabs with both face polished with a double beam Perkin-Elmer Lambda-1050® spectrometer in the spectral range between 3030 and 40 000 cm\u003csup\u003e− 1\u003c/sup\u003e with a wavelength (λ) step and spectral resolution of 0.92 cm\u003csup\u003e− 1\u003c/sup\u003e (1 nm). After correction for signal jump at 11 600 cm\u003csup\u003e− 1\u003c/sup\u003e due to detector change, the absorption spectra were normalized to sample thickness. The area analyzed was about 2 \u003cem\u003e×\u003c/em\u003e 3.5 mm\u003csup\u003e\u003cspan citationid=\"CR2\" class=\"CitationRef\"\u003e2\u003c/span\u003e\u003c/sup\u003e sensing a large portion of the glass slabs and allowing a highly representative measurement of the optical absorbance.\u003c/p\u003e"},{"header":"Declarations","content":"\u003cp\u003e\u003cstrong\u003eDATA AVAILABILITY\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe data that supports the findings of this study are available from the corresponding author upon reasonable request.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eACKNOWLEDGEMENTS\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThis study was supported by the French Agency for Research (ANR, PRCE program, grant 18-CE08-0025). We acknowledge the European Synchrotron Radiation Facility for provision of beam time on ID21 (proposal MA-4648) and we would especially like to thank ESRF instrumentation service and development division for their efforts in instrumental developments for EBS and ID21 refurbishment. \u0026micro;XRF and XANES datasets acquired in ESRF can be found under DOI 10.15151/ESRF-ES-579825745. Th\u0026eacute;o Caroff from IMPMC is acknowledge for his script for data processing optical absorption spectra and D\u0026eacute;a Ja\u0026iuml;s (IMPMC) for the transcription of the Cr(III) and Cr(VI) spectra from Bamford.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAUTHORS CONTRIBUTION\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eLB performed the leaching experiments. XANES and XRF measurements were carried out by MT and LB under the supervision of MC and data was curated by LB. TC performed the NMR studies. LG ran optical absorption spectroscopy and processed data. FA, SG and TC supervised the study and worked on the conceptualization, methodology and original draft. All the authors helped on the paper editing.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eCOMPETING INTERESTS\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe authors declare no competing interests.\u003c/p\u003e"},{"header":"References","content":"\u003col\u003e\n\u003cli\u003eChromium and Chromium Compounds. In: \u003cem\u003eIARC MONOGRAPHS ON THE EVALUATION OF CARCINOGENIC RISKS TO HUMANS, VOL 49: CHROMIUM, NICKEL AND WELDING\u003c/em\u003e. World Health Organization: Geneva, 1990, pp 49\u0026ndash;256.\u003c/li\u003e\n\u003cli\u003eGuadagnino E, Sundberg P, Corumluoglu O. 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Ga-71 and Ga-69 Nuclear-Magnetic-Resonance Study of Beta-Ga2o3 - Resolution of 4-Fold and 6-Fold Coordinated Ga Sites in Static Conditions. \u003cem\u003eSolid State Nucl Magn Reson\u003c/em\u003e 1995; \u003cstrong\u003e4\u003c/strong\u003e: 241\u0026ndash;248.\u003c/li\u003e\n\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":true,"hasPassedJournalQc":"","hasAnyPriority":false,"hideJournal":false,"highlight":"","institution":"","isAcceptedByJournal":true,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":false,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"npj-materials-degradation","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"npjmatdeg","sideBox":"Learn more about [npj Materials Degradation](http://www.nature.com/npjmatdeg/)","snPcode":"41529","submissionUrl":"https://submission.springernature.com/new-submission/41529/3","title":"npj Materials Degradation","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"stoa","reportingPortfolio":"NPJ","inReviewEnabled":true,"inReviewRevisionsEnabled":true},"keywords":"","lastPublishedDoi":"10.21203/rs.3.rs-5284279/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-5284279/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eThe scientific understanding and demonstration of the immobilization of heavy metals (notably lead and chromium) in food contact materials is crucial for the safety of environment and humans. To tackle this issue lead crystal glasses doped between 50 and 2000 ppm of chromium oxide were carried out under severe aqueous alteration conditions (acetic acid 4% (v/v), pH 2.4, 70°C, 330 days). The increase in Cr leads to a decrease in the Pb release into the solution. The leached Cr content was lower than Pb, itself much lower than alkali ones. Structural characterization before and after alteration points out the presence of Cr(III) exclusively, with no redox changes in the course of alteration. Cr and Pb are partially retained during alteration near cationic domains, less accessible to protonated species. Cr favors the Si recondensation in the rich non-bridging oxygen (NBO) mixing sites, leading in an increase of glass polymerization within the altered layer.\u003c/p\u003e","manuscriptTitle":"Insight into the structure and chemical durability of Cr-bearing lead crystal glass","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2024-10-25 09:40:17","doi":"10.21203/rs.3.rs-5284279/v1","editorialEvents":[{"type":"communityComments","content":0},{"type":"decision","content":"Revision requested","date":"2024-11-25T22:55:42+00:00","index":"","fulltext":""},{"type":"editorInvitedReview","content":"","date":"2024-11-22T15:52:26+00:00","index":"hide","fulltext":""},{"type":"editorInvitedReview","content":"","date":"2024-11-22T12:23:33+00:00","index":"hide","fulltext":""},{"type":"reviewerAgreed","content":"67074746024420371187510154707345922726","date":"2024-10-28T07:35:18+00:00","index":"hide","fulltext":""},{"type":"reviewerAgreed","content":"227197979575492594210759344770586375831","date":"2024-10-25T10:09:39+00:00","index":"hide","fulltext":""},{"type":"reviewersInvited","content":"","date":"2024-10-24T12:54:56+00:00","index":"","fulltext":""},{"type":"editorAssigned","content":"","date":"2024-10-24T04:35:21+00:00","index":"","fulltext":""},{"type":"checksComplete","content":"","date":"2024-10-23T09:35:24+00:00","index":"","fulltext":""},{"type":"submitted","content":"npj Materials Degradation","date":"2024-10-17T16:19:13+00:00","index":"","fulltext":""}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"npj-materials-degradation","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"npjmatdeg","sideBox":"Learn more about [npj Materials Degradation](http://www.nature.com/npjmatdeg/)","snPcode":"41529","submissionUrl":"https://submission.springernature.com/new-submission/41529/3","title":"npj Materials Degradation","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"stoa","reportingPortfolio":"NPJ","inReviewEnabled":true,"inReviewRevisionsEnabled":true}}],"origin":"","ownerIdentity":"baa9f729-9c47-42eb-acca-2a228e39129e","owner":[],"postedDate":"October 25th, 2024","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"published-in-journal","subjectAreas":[{"id":39375433,"name":"Physical sciences/Materials science"},{"id":39375434,"name":"Physical sciences/Materials science/Condensed matter physics"},{"id":39375435,"name":"Physical sciences/Chemistry"},{"id":39375436,"name":"Physical sciences/Chemistry/Materials chemistry"}],"tags":[],"updatedAt":"2025-05-05T16:00:10+00:00","versionOfRecord":{"articleIdentity":"rs-5284279","link":"https://doi.org/10.1038/s41529-025-00586-7","journal":{"identity":"npj-materials-degradation","isVorOnly":false,"title":"npj Materials Degradation"},"publishedOn":"2025-05-02 15:57:20","publishedOnDateReadable":"May 2nd, 2025"},"versionCreatedAt":"2024-10-25 09:40:17","video":"","vorDoi":"10.1038/s41529-025-00586-7","vorDoiUrl":"https://doi.org/10.1038/s41529-025-00586-7","workflowStages":[]},"version":"v1","identity":"rs-5284279","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-5284279","identity":"rs-5284279","version":["v1"]},"buildId":"qtupq5eGEP_6zYnWcrvyt","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}