Open access peer-reviewed chapter

Raman Study of the Crystalline-to-Amorphous State in Alpha- Decay–Damaged Materials

By Ming Zhang

Submitted: April 16th 2016Reviewed: September 21st 2016Published: February 15th 2017

DOI: 10.5772/65910

Downloaded: 1219


The stabilization and immobilization of high‐level radioactive wastes in solid forms have become one of the most pressing industrial problems. Different crystalline mineral phases have been proposed as actinide‐bearing crystalline hosts for waste materials. Self‐radiation damage from alpha‐decay of the incorporated actinides (such as U, Th) and other rare earth elements can lead to metamict state (amorphous state) and can affect the durability and long‐term performance of these actinide‐bearing phases. To investigate the impact of radiation on the nuclear waste forms and to obtain a better comprehension of the damage process and amorphization mechanism are important. The issues of interactions between high‐energy particles and solids and radiation‐induced structural modifications in crystalline‐to‐amorphous state are, in fact, an important and active area of fundamental researches. To study metamict state and metamictization is also important for geochemistry as the U‐Pb isotope system is commonly used for age dating. Although radiation effect and naturally occurring radiation damage (the process is known as metamictization) have been the subject for many research investigations, there remain important and fundamental issues which need to be understood, for example, the structural changes at the atomic level caused by metamictization, the crystal structure of radiation‐induced amorphous phases, solubility and diffusion of radioactive elements in damaged host phases, the effect of pressure and temperature on metamictization process and interaction of water and fluids with nuclear waste forms. Raman spectroscopy is found to be a very powerful tool for study and analysis of the damage effect and metamictization. This chapter describes and reviews recent Raman applications in zircon and titanite, which are proposed for nuclear waste forms. These applications are focused on radiation effect and structural damage process caused by alpha‐decay process as well as recrystallization due to thermal annealing.


  • Raman spectroscopy
  • radiation damage
  • metamictization
  • actinide
  • zircon
  • titanite

1. Introduction

Today, there are over 430 commercial nuclear power reactors in 31 countries which provide over 10% of the world electricity [1]. As a result, huge amounts of highly radioactive nuclear wastes are produced each year. One of the critical issues in nuclear energy industry is the safe disposal of nuclear wastes, especially high‐level nuclear wastes (HLNW). The below are some minerals and synthetic materials proposed or developed as actinide‐bearing crystalline hosts for waste materials [24]: zircon (ZrSiO4), titanite (CaTiSiO5), baddeleyite (Zr,Hf,…)O2, hafnon (HfSiO4), perovskite [(Ca,Gd,…)(Al,Fe,Ti,…)O3], zirconolite [CaZrTi2O7 and CaZrSi2O7], apatite [Ca10(PO4)6(OH,F,Cl,B)2], pyrochlore [CaZrGd2Ti2O7, Gd2Zr2O7, and La2Zr2O7‐Nd2Zr2O7], monazite [(La,Ce,…)PO4], and garnet [(Ca,Fe,Gd,…)3 (Al,Fe,Si,…)5O12]. Among them, zircon is one of the most studied and modeled minerals. Currently, pyrochlore has attracted attention because of its radiation damage resistance.

Self‐radiation from alpha‐decay of the incorporated actinides can lead to lattice damage resulting in structural change and transformation from crystalline state to an amorphous or aperiodic state, that is, metamict state (the process is known as metamictization) [57].

The effects of radiation damage on the structure of metamict minerals can be seen as systematic changes of its physical properties [8]: an increase in cell parameters and broadening of X‐ray diffraction patterns [912]; a decrease in Raman and infrared intensities and dramatic band broadening [13, 14]; decreases in refractive index and birefringence [9, 15]; absorption of hydrous species [1619]; an increase in fracture toughness [20]; a decrease in density [9, 10]; a variation of TEM diffraction patterns [10, 21, 22]; an increase of leach rate [23]; changes in bulk modulus and hardness [24]; a change of 29Si NMR features [11, 25]; changes of diffuse X‐ray scattering from single crystals [6]; occurrences of Huang type diffuse X‐ray diffraction [26]; a change in EXAFS [27]; a variation of Mössbauer spectra [11, 28]; and a variation of positron annihilation lifetime [29]. Therefore, the durability and performance of these actinide‐bearing phases can be altered by self‐radiation damage from alpha‐decay of the incorporated actinides. To gain better comprehension of the effect of radiation on crystal structure at the atomic level, the related damage process and damage mechanism are issues of critical importance.

Vibrational spectroscopy (Raman and infrared (IR) spectroscopy) is a very powerful tool in the analysis and study of structural variations related to medium‐ and short‐range order [30]. Early analysis of alpha‐decay damaged materials by Raman spectroscopy can be traced back to about two decades ago [31, 32]. The main advantages of vibrational spectroscopy (Raman and infrared spectroscopy) [30] are their fast response time (which can be in the range of ~10-12 s), short correlation length scale (which is in the order of a few unit cells), and good sensitivity to hydrous and hydroxyl species (e.g., H2O and OH). In contrast to diffraction methods which are generally sensitive to periodicity of lattices and the crystallinity of a specimen, vibrational spectroscopy is mainly associated with the strength and length of interatomic bonds, as well as the atomic masses of the sample. Therefore, vibrational spectroscopy can give valuable information on phonon energy, bulk structure, chemical composition, and surface for not only crystalline materials, but also disordered phases. The method has, in fact, been widely applied in studying disordered and amorphous materials such as glasses.

This chapter illustrates recent applications of Raman spectroscopy in the study of radiation‐damaged or metamict zircon and titanite. Being different from simple identification of damaged phases with Raman techniques, the investigations are focused on important issues such as: What happens at the atomic level during radiation damage and recrystallization? What are the possible structural modifications during metamictization? And whether decomposition into oxides is the final result of radiation damage. The experimental results provide a better understanding of the mechanism of radiation damage and the recrystallization processes.

2. Effects of alpha‐decay radiation on Raman spectra of zircon and titanite

Zircon (ZrSiO4) is a common accessory mineral in igneous rocks, in metamorphic rocks, and as detrital grains in sedimentary rocks. The work [33] has showed that zircon crystallizes to a tetragonal structure with space group D4h19or I41/amd (with Z = 4), containing a chain of alternating, edge‐sharing SiO4 tetrahedra and ZrO8 triangular dodecahedra extending parallel to the c‐axis. Actinides such as U, Th and Pu can substitute Zr and locate in the Zr site. Because of their uranium and thorium content, some zircons undergo metamictization. Group theory predicts twelve Raman‐active normal modes in zircon at k = 0: 2A1g + 4B1g + B2g + 5Eg [34]. These Raman modes can be simply classified as internal modes and external modes. There are five (2B1g + 3Eg) external modes and seven (2A1g + 2B1g + B2g + 2Eg) internal modes. For Raman measurements of natural samples which are damaged by radiation of incorporated actinides, it is a good practice to use laser excitation with different wavelengths to ensure that spectral features recorded are due to phonon modes rather than features due to luminescence and impurities‐related color centers (e.g., the work [8] used 514, 488, 457 and 632 nm lasers in its Raman measurement). Nine of the twelve predicted Raman modes can be seen in the most crystalline natural zircon (Figure 1). They are internal modes: 1008 cm-1 (B1g, ν3 stretching of SiO4), 975 cm-1 (A1g, ν1 stretching), 439 cm-1 (A1g, ν2 bending), and 269 cm-1 (B2g, ν2 bending) and external modes: 393, 355, 225, 214 and 202 cm–1. The other predicted Raman bands appear too weak to be observed in a common experimental arrangement.

Figure 1.

Micro‐Raman spectra (with 488 nm excitation) of metamict zircon between 50 and 1100 cm-1 (Ref. [8], modified). The dosage is in the units of 1018 alpha‐events g−1.

The effect of alpha‐decay radiation damage on the structure of zircon is evidenced by a decrease in band frequencies, a line broadening of Raman modes and a decrease in Raman intensity (Figure 1). Well‐crystallized zircon samples have sharp and well‐resolved Raman modes. With increasing alpha‐decay radiation dose (the radiation dose of natural minerals is mainly related to sample's rock age and concentration of U and Th, and it can be calculated [9, 10]), the stretching modes of SiO4 tetrahedra near 975 and 1008 cm-1 become weaker and broader, while the lower frequency modes become gradually weaker and could hardly be analyzed for high‐dose cases. The broad Raman feature concurring near 950 cm-1 (the insert part in Figure 1) indicates the formation of amorphous phases in high‐dose samples. The behavior of the band also suggests that SiO4 tetrahedra remain in highly damaged zircon samples. As the 950 cm-1 feature is significantly away from the intense bands near 1008 cm–1 in terms of wavenumber, its appearance implies a new linkage of SiO4 tetrahedra.

The dose dependence of the frequency and full width at half maximum of the 1008 cm-1 stretching band of SiO4 are shown in Figure 2. The data indicate that the Si-O bond strength exhibits a weakness, while the specific volume of the crystal increases, although radiation damage does not destroy SiO4 and short‐range ordering associated with the tetrahedral framework remains. The observation suggests that the increase in bond distances is probably depolarized by a rotation of the SiO4 tetrahedra within the zircon structure. The data clearly show that the unit cell swelling in damaged zircon is associated with the SiO4 tetrahedra which formed new linkage and play an important role in the zircon structure rather than isolated molecular complexes.

Figure 2.

Phonon frequency and full width at half maximum (FWHM) of the ν3 stretching band (B1g) of SiO4 in radiation‐damaged zircon as a function of radiation dose (Ref. [8], modified). The lines are visual guides.

Raman band widths [full width at half maximum (FWHM)] and frequencies (especially those of the ν3 band of SiO4 near 1008 cm-1) in zircon have been used for investigating the relationship between U‐Pb isotopic discordance and metamictization [3537]. More work is desirable to gain a better understanding of the behavior of this band during radiation damage and recrystallization, and the potential influence of chemical impurities on the band.

Another good example of Raman study of alpha‐decay radiation damage is the application in metamict titanite. Titanite is a calcium titanium nesosilicate mineral, CaTiSiO5. Taylor and Brown [38] synthesized pure titanite, and their X‐ray data show that it is monoclinic (space group P21/a, Z = 4) with unit‐cell parameters a = 7.057, b = 8.707, c = 6.555 Å, β = 113.81°. The crystal structure of P21/a titanite phase contains chains of corner‐sharing TiO6 octahedra parallel along [1 0 0], which are cross‐linked by edge‐sharing CaO7‐polyhedra extending parallel to [1 0 1]. On heating, the P21/a phase undergoes a phase transition to an A2/a phase near 500 K [38]. The two phases have different optical active representations. For the P21/a phase Γoptic = 24Ag + 24Bg + 23Au + 22Bu (Ag and Bg are Raman‐active, and Au and Bu IR‐active), whereas for the A2/a phase Γoptic = 9Ag + 12Bg + 11Au + 13Bu [39]. Therefore, the P21/a phase is expected to have 48 Raman‐active modes, whereas the A2/a phase contains 21 Raman modes. Although pure synthetic titanite is in P21/a symmetry, some well‐crystalline natural titanite samples were surprisingly reported to be in the A2/a structure [11]. This significant difference in the total number of the Raman modes for the P21/a and A2/a phases is important and helpful for identifying the presence of the two phases [40].

Natural titanite occurs in igneous and metamorphic rock and incorporates a variety of impurity ions such as U, Th and other rare earth elements (REE). The structure of natural titanite is often metamict, as a result of self‐radiation damage associated with the alpha‐decay of the incorporated REEs. Raman spectra of crystalline or undamaged natural titanite (Figure 3) show spectral features similar to those of synthetic pure P21/a titanite as reported previously [39]. The Raman work [41] suggested that anisotropy is preserved upon metamictization and that the structural state of highly metamict titanite should not be considered as quasi‐amorphous. It was reported that the local structure of the amorphized regions contains a high degree of short‐range order [42]. The effect of alpha‐decay radiation on Raman spectrum of titanite is characterized by a dramatic decrease in intensity and line broadening (Figure 3). The intense Ti-O band near 605 cm−1 shows the largest intensity decrease, indicating radiation effect on the TiO6 octahedra. This change is consistent with the behavior of the infrared‐active Ti-O stretching mode near 670 cm−1, which is mostly affected by radiation damage and shifts to 710 cm−1 in heavily damaged titanite [43]. A Raman work on metamict titanite [44] proposed that radiation‐induced periodic faults in the crystalline matrix of metamict titanite are related to the disturbance of SiO4‐TiO6‐SiO4‐TiO6 rings comprising TiO6 octahedra from different chains, whereas the radiation‐induced amorphization is associated with the partial change of Ti coordination from octahedral to pyramidal and/or tetrahedral, which in turn violates the Ti-O-Ti intrachain linkages. In addition to these changes, radiation damage in titanite leads to the appearance of extra Raman signals (e.g., 574 cm−1) in intermediately damaged samples (Figure 3). This behavior is not seen in metamict zircon. These additional phonon modes in these partially metamict titanite samples are, in fact, characteristic Raman bands of the A2/a phase [40]. The results indicate that as a result of the radiation, the P21/a titanite first transforms to the A2/a structure, and then, with further radiation, the A2/a phase becomes an amorphous phase. Beirau et al. [45] reported in situ high‐temperature Raman data of radiation‐damaged titanite, and they found a structural anomaly near 500 K in partially metamict titanite, which was attributed to the P21/a‐A2/a transition. These above findings explained why some of natural crystalline titanites were found to appear the A2/a structure [11], rather than the P21/a phase. This could be due to the fact that natural titanite crystals commonly experienced radiation damage, which resulted in an alteration of the P21/a crystal structure [40].

Figure 3.

Raman spectra of fine powders of titanites (CaTiSiO5) with different degrees of radiation damage (Ref. [40], modified). The top spectra are from well‐crystallized samples, which show that the space group is the P21/a symmetry [40]. Metamictization causes a loss of spectral details and a line broadening in the spectra of titanites. The Ti-O stretching band near 605 cm−1 shifts to a higher frequency, while a extra band near 574 cm−1 (which is due to the A2/a phase) appears in partially damage samples. A relatively intense band is recorded near 675 cm−1 with a FWHM of about 80 cm−1 in heavily damaged titanite (in the bottom of the plot). The large FWFM indicates that this feature is related to radiation‐induced disordered or amorphous phase. Crystalline titanites have the bands near 858 and 912 cm−1, which are due to stretching vibrations of SiO4 tetrahedra. These bands shift to lower frequencies in intermediately damaged samples and appear as a broad feature near 845 cm−1 in heavily damage samples (bottom).

3. Issue of possible decomposition in radiation‐damaged zircon

In the study of radiation effect and metamict state, what happens at the atomic level is an unclear and important question. Researchers have focused on issues such as possible changes in the coordination number of Zr [27], radiation‐induced disordering rather than amorphization [31], damage‐related distorted and disoriented isolated silica tetrahedra [16], the fraction of amorphized phase [14, 46], as well as whether metamictization leads to phase separation or damaged minerals decompose into their oxides, and what is the structural state of the decomposed phases [47, 48]. This issue of radiation‐induced decomposition was, in fact, debated over decades [30]. Based on infrared data on metamict zircon, a two‐stage damage process was proposed [49]. It was suggested that the first stage produces, throughout the lattice, highly stressed and expanded zircon with distorted SiO4 tetrahedra, while the second stage was suggested to result in the decomposition of ZrSiO4 to ZrO2 and SiO2, probably together with some aperiodic ZrSiO4 [49]. However, the decomposition of damaged zircon was often reported in zircon samples only annealed experimentally at high temperatures, in which the decomposition commonly leads to different polymorphs of ZrO2 and glassy silica. Monoclinic ZrO2 was found in heavily damaged samples heated to 1373 K [50]. In a high‐temperature study, Vance and Anderson [15] observed cubic and tetragonal ZrO2 at 1073 and 1373 K, respectively. It was reported that highly metamict zircon contained randomly orientated ZrO2 when annealed at 1173 K, and further annealing at 1523 K resulted in monoclinic ZrO2, as well as a silica glass phase [51]. Ellsworth et al. [52] suggested that decomposition of metamict zircon into ZrO2 and glassy SiO2 could be one possible path for recrystallization. In contrast, a high‐temperature neutron work by [53] suggested that zircon decomposes into crystalline β‐cristobalite (rather than silica glass) and tetragonal ZrO2. An X‐ray powder diffraction study at high temperatures reported the appearance of pseudo‐cubic ZrO2 [54]. Meldrum et al. [55] observed a decomposition of zircon into tetragonal ZrO2 when irradiating zircon with heavy ions at around 950 K. As discussed by different works [56, 57], some of these previous works based on X‐ray diffraction measurements might have experienced difficulties in the determination of cubic and tetragonal ZrO2.

Vibrational (Raman and infrared) spectroscopy is a good analytical tool for resolving these problems related to decomposition of ZrSiO4 into ZrO2 and SiO2, as pointed out by Ref. [30], because Raman and infrared spectra of zirconia (ZrO2) have been well studied previously and also because vibrational spectroscopy has short length scales. ZrO2 has three common polymorphs at different temperatures. The room‐temperature phase is monoclinic, while the tetragonal and cubic phases occur at high temperatures [58]. The theoretical calculations [59, 60] have given the optical phonon modes (for zero wave vector) for each polymorph of zirconia ZrO2. The monoclinic ZrO2 has space group C2h5/P21/c and Z = 4, and it has eighteen Raman modes and fifteen infrared modes [9Ag(R) + 9Bg(R) + 8Au (IR) + 7Bu(IR)] (R indicating Raman‐active and IR indicating infrared‐active). In tetragonal ZrO2 (with space group D4h15/P42/nmc and Z = 2), the phase has six Raman modes and three infrared modes [A1g(R) + 2B1g(R) + 3Eg(R) + A2u(IR) + 2Eu(IR)]. For cubic ZrO2 (with space group Oh5/Fm3m and Z = 1), its vibrational spectra have only one Raman and one infrared modes [F2g(R) + F1u(IR)].

The data in Figure 1 indicate that it is apparent that there is a lack of signals of ZrO2 in highly damaged zircons. This shows that ZrO2 and SiO2 are not the final products of metamictization in zircon. Results from infrared spectroscopy of radiation‐damaged zircon [14, 47] also support this observation. As mentioned early, although decomposed zircons were commonly reported in lab‐treated samples, tetragonal ZrO2 was recorded in only one natural sample [8], with an unknown thermal history, among a large number of natural zircon samples with different degrees of damage analyzed in Refs. [14, 47, 48]. In order to explore and examine high‐temperature behavior of damaged zircon and the possible causes for decomposition in zircon, systematic works were carried out by different groups [47, 36, 61, 62]. These works show that thermal annealing of heavily damaged zircon at high‐temperature experiments may lead to the decomposition of metamict zircon into tetragonal ZrO2 and glassy SiO2 at 1200 K, and upon further heating tetragonal ZrO2 transforms to monoclinic ZrO2 near 1400 K. Undamaged and weakly damaged zircons are less likely to show decomposition during high‐temperature annealing. It was reported that the decomposition‐induced silica tended to evaporate on further heating [61, 63]. As naturally damaged samples might experience high‐temperature processes, some reported decomposed metamict zircon could be due to natural thermal annealing prior to experiments. In contrast to high‐temperature annealing, the presence of ZrO2 in some natural zircons might be due to the reaction of fluids with metamict zircons, because radiation damage may alternate the chemical stability of zircon. The observation of ZrO2 in dissolution experiments was reported in highly damaged zircon samples [64]. Raman data of hydrothermally leached metamict zircon [65] showed the formation of monoclinic ZrO2. In general, the decomposition of zircon into ZrO2 and SiO2 is related to radiation‐damaged zircons. Their crystal lattice is heavily damaged and has more defects. As a result, the durability of these heavily damaged samples is expected to be affected, and they are vulnerable to the impact of external physical and chemical conditions (e.g., water, solutions, high temperature, and even high pressure).

Raman data of metamict titanite (Figure 3) also show there is a lack of formation of oxides in highly damaged samples [40]. The findings are supported by X‐ray measurements and TEM [11] and infrared data [43]. The observation further shows that phase decomposition into oxides is not the final state of alpha‐decay damage in these materials, and the materials are safe to be used as nuclear waste forms. It has been found that decomposition of radiation‐damaged zircon is commonly related to high‐temperature heating (see a below section).

4. Metamict state versus glass state of CaTiSiO5 and ZrSiO4

One of the interesting issues related to radiation damage and metamictization is the similarities or differences between the amorphous phases produced by alpha‐decay radiation damage and those produced through thermally quenched glass melts. Previous studies [47] have led to unanswered questions and concerns: for example, What is the relationship between the structural characteristics of disordered materials and the type of irradiation or physical process used to produce them?

As a type of disordered or amorphous materials, metamict minerals were commonly considered as “glass‐like” materials in early studies on naturally occurring radiation effect and metamictization, and the metamict state was referred as a glassy state, which is somehow similar to that obtained by rapid quenching of high‐temperature melts [30]. With experimental data gathering, evidences have emerged that indicate their important differences between the aperiodic states. The dispersion depends on the physical processes, which produce the amorphous states. Vibrational spectroscopy (Raman and infrared) is very useful to study this issue because of its sensitivity to local structures.

Raman data of metamict titanite (CaTiSiO5) and its glass analogue (with the same chemical compositions) produced by quenching melts show that the two types of materials have different vibrational features (especially in the Ti-O and Si-O stretching regions) (Figure 4) [40], although they both are almost amorphous in terms of electron microscopy and X‐ray diffraction analysis. The CaTiSiO5 glasses produced from melts show a Si-O stretching band near 827 cm−1, while metamict titanite has a relatively weak band in a higher wavenumber, 844 cm−1. What is more, the quenched melts of CaTiSiO5 have a relatively strong band peaked near 709 cm−1, but this feature is almost absent in metamict titanite. The Raman observations are supported by the results for the same samples analyzed by infrared reflection and absorption spectroscopy [43]. These results suggest structural differences associated with Ti-O and Si-O bonds in the glasses and metamict phases. Interestingly, the glassy and metamict titanites also exhibit some similarities in a couple of band positions in the far infrared region (below 450 cm−1). For example, they both have bands around 170, 330 and 430 cm−1.

Zircon has a high melting temperature (above 2700–2800 K), and crystalline ZrO2 and a liquid of SiO2 may coexist for a composition of ZrSiO4 at a temperature region of ~1960 K and ~2670 K [66]. It is difficult to quench zircon melts without decomposition into ZrO2 and SiO2; however, glass‐like zircon (ZrSiO4) has been recorded with Raman spectroscopy in laser‐treated zircon in a study with laser melting, near the boundaries between the unmolten and molten regions (where a relatively large temperature gradient could exist) [67]. The large temperature gradient is expected to increase the quench rate and facilitate a “freeze” of the local configuration of the ZrSiO4 melts before the decomposition takes place. These experimental results indicate that the metamict state is different from the glassy state obtained by quenching melts. Apparently, the processes and structural states associated with metamictization and irradiation amorphization are more complex than those in common thermal glasses. The formation of the metamict state involves not only amorphization, but also defect accumulation caused by alpha‐particle damage and further radiation or irradiation may lead to damage as well as recrystallization.

Figure 4.

CaTiSiO5 glasses produced by quenching titanite melts (thermal glass‐1 and thermal glass‐2 are prepared by quenching CaTiSiO5 melts) show overall spectra patterns different from those of metamict titanite, especially in the region of 600 and 1100 cm–1 [Ref, [40], modified). This indicates the spectral dispersion related to Si-O and Ti-O vibrations in the two types of disordered materials. However, the two materials exhibit some local maximums with similar or close peak positions (indicated by dash lines) in the far infrared region (100 and 500 cm–1).

So far, although the issue remains under debates, there have been substantial evidences indicating characteristic discrepancies between two types of amorphous states (metamict and glass states) [68], for example: (i) the two types of materials commonly have spectral and structural discrepancies [40, 43, 69, 70]; (ii) high‐energy heavy ion irradiation may lead to significant modifications in local structures of glasses [7174]; (iii) upon heating, radiation‐damaged minerals tend to recrystallize epitaxially and recover to their original cryptographic orientations [48, 51, 75], while during high‐temperature treatments, glasses commonly undergo a glass transition; and (iv) for common glasses, their glass transition temperatures are roughly defined, while various responses at different temperatures are seen in metamict minerals. For example, radiation‐induced defects in metamict zircon may be annealed or healed at temperatures as low as 600 K accompanied by changes in the oxidation state of U ions; partial decomposition of ZrSiO4 into SiO2 and SiO2 in heavily damaged zircon may take place at 1050 K; diffusion and conversions of hydrogen‐related species together with dehydroxylation may occur between 1200 and 1600 K (e.g., [16, 18, 52, 76, 77], see for the transition point [6]).

5. Effect of thermal annealing on metamict zircon and titanite

Thermal annealing of metamict minerals at high temperatures is commonly used in studies of radiation‐damaged minerals [30]. Its aims are to restore the original crystal structure for the purpose of studying recrystallization temperature, activation energy, types of radiation‐induced local defects and phase identification, and to obtain a good comprehension of the recrystallization process and mechanism. Extensive studies were carried out to investigate changes at the atomic level in metamict materials during high‐temperature annealing [10, 15, 36, 40, 44, 47, 48, 50, 52, 54, 55, 65, 75, 7881]. However, controversies remain regarding the recrystallization path and activation energy.

Thermal annealing results in recrystallization of metamict zircon (Figure 5). The effect of annealing temperature on the structural recovery of damaged zircon can be clearly seen in the frequency and FWHM of the ν3 Si-O stretching (B1g) as a function of temperature (Figure 6). With increasing annealing temperature, the frequency of this mode shows, systematically, a large increase in the region between 800 and 1050 K and a weaker increase with temperature above 1050 K. This is due to the healing of the defective lattice and the recrystallization of remaining crystalline domains. Highly damaged zircon tends to decompose into tetragonal ZrO2 and SiO2 near 1100 K, and the transformation of tetragonal ZrO2 into monoclinic ZrO2 is reported at higher temperatures [47]. The findings may explain the cause of some previously reported ZrO2 and SiO2 in natural zircon, which likely experienced natural heating processes.

Spectroscopic data [47, 48, 61] revealed different recrystallization processes between partially and heavily damaged zircons, that is, the recrystallization process depends on the cumulative radiation dose (Figure 5, 6a and 6b). Being similar to metamict zircon [47], the thermal response of the damaged titanite (CaTiSiO5) is affected by their initial degrees of damage, that is, at the same treatment conditions, weakly or partially damaged samples are more likely to recover to crystalline titanite as compared with highly metamict samples [40]. Intermediately and heavily damaged titanite samples show a recovery of Ti-O and Si-O bands after annealing at 1300–1400 K, and these recovered crystals are consistent with the P21/a symmetry, although in terms of band widths, they are far from a fully recovering [40]. Similar results were reported by the work of another group [44] who thermally treated a metamict titanite sample, which has an accumulated radiation dose of 1.2 × 1018 alpha‐event/g by multistep annealing up to 1173 K, and found it was insufficient to recover the crystalline structure of the studied sample. The failure of a full recovery from the damage in thermally treated metamict titanite is also revealed by infrared spectroscopy [43]; however, the physics behind this remain unclear.

Figure 5.

Raman spectra recorded from weakly metamict (dose = 1.8 × 1018 alpha‐events g−1), intermediately metamict (dose = 3.5) and highly metamict zircon (dose = 13.1) thermally treated in N2 up to 1700 K and then punched (Ref. [47], modified).

Figure 6.

Phonon frequency and FWHM of the Raman ν3 Si-O stretching (B1g) in zircon (ZrSiO4) with different degrees of damage as a function of annealing temperature (Ref. [47], modified with unpublished data).

The thermally induced structural recovery and recrystallization of metamict zircon and titanite is also characterized a recovery of the anisotropy of the sample, which is restored during annealing, as evidenced by the recovery of orientational dependence of IR (as well as Raman) spectra along with the original crystallographic orientations as shown in Figure 7, which indicates an epitaxial recrystallization. This behavior indicates that in highly metamict zircon and titanite, crystalline nanodomains with original crystallographic orientations might still exist.

Figure 7.

Orientational dependence of polarized infrared spectra of radiation‐damaged zircon crystal (dose = 3.8 × 1018 alpha‐events g−1) annealed between 292 and 1700 K (Ref. [48], modified). The interval of the angle between the c‐axis and the incident radiation E is 10°. The arrows indicate the appearance of an extra signal near 790 cm−1, suggesting a possible intermediate phase. Thermal annealing results in a recovery of the anisotropy of the damage zircon crystal to its original crystallographic orientations.

In conclusion, Raman spectroscopy, as shown above, is a very powerful tool for study of radiation damage in actinide‐bearing phases and for estimation of their long‐term durability of their physical properties and chemical stability. This type of Raman applications can provide a better understanding of the mechanism of radiation damage and thermal recrystallization processes. It has a wide usage in condensed mater physics, material science, nuclear material sciences, mineralogist, and geochemistry. It has also been used analysis other radiation‐damaged minerals, such as fergusonite [82, 83], actinide‐bearing monazite [32], titanoaeschynite (Nd) and nioboaeschynite (Ce) [84], uranyl titanate mineral davidite‐(La) [85], aeschynite‐(Y) and polycrase‐(Y) [86], and steenstrupine [87], and pyrochlore (Zietlow et al., personal communication).

© 2017 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution 3.0 License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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Ming Zhang (February 15th 2017). Raman Study of the Crystalline-to-Amorphous State in Alpha- Decay–Damaged Materials, Raman Spectroscopy and Applications, Khan Maaz, IntechOpen, DOI: 10.5772/65910. Available from:

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