US 6137025 A
Disclosed is a ceramic composition for the immobilization of actinides, particularly uranium and plutonium. The ceramic is a titanate material comprising pyrochlore, brannerite and rutile.
1. A ceramic composition to immobilize actinides comprising:
pyrochlore (X2 Ti2 O7) at greater than 50% volumetric ratio, where X is selected from the group consisting of Ca, Gd, Hf, Sm, and actinides;
up to about 50% by volume brannerite (YTi2 O6), where Y is an actinide;
up to about 50% by volume zirconolite (CaATi2 O7 ), where A is selected from the group consisting of Zr, Hf, Gd, and Sm;
up to about 20% by volume rutile (TiO2);
and up to about 1% by volume actinide oxide.
2. The ceramic composition according to claim 1, wherein:
said actinides are at no greater than 32 weight percent.
3. The ceramic composition according to claim 2, wherein:
said actinides are selected from the group consisting of U, Pu, Th, Np and Am.
4. The ceramic composition according to claim 3, wherein:
said actinides are uranium and plutonium.
5. The ceramic composition according to claim 4, wherein:
the ratio of uranium to plutonium is 2:1 by weight percent.
6. The ceramic composition according to claim 1, wherein:
said pyrochlore volumetric ratio is about 80%;
said brannerite volumetric ratio is about 12%;
said zirconolite volumetric ratio is about 0%;
said rutile volumetric ratio is about 8%;
and said actinide oxide volumetric ratio is less than 0.5%.
7. The ceramic composition according to claim 6, further comprising:
up to about 10% volumetric ratio other phases wherein said other phases are selected from the group consisting of silicate, whitlockite, monazite, perovskite, magnesium titanate, ilmenite, pseudobrookite, corundum, calcium uranium vanadate, hafnium titanate, magnesium aluminum titanate, magnetoplumbite, and calcium aluminum titanate.
8. A ceramic composition to immobilize uranium and plutonium comprising:
about 10.0% by weight CaO;
about 35.8% by weight TiO2 ;
about 10.6% by weight HfO2 ;
about 8.0% by weight Gd2 O3 ;
about 23.7% by weight UO2 ;
and about 11.9% by weight PuO2.
9. ceramic composition to immobilize uranium and plutonium comprising:
CaO, TiO2, HfO2, Gd2 03, UO2, and PuO2 ;
the molar ratio of Hf to Pu being greater than or equal to unity;
the molar ratio of Gd to Pu being greater than or equal to unity;
the molar ratio of UO2 to PUO2 being 2:1;
the weight % of UO2 and PuO2 being no greater than 36%;
said CaO being about 10% by weight;
and said TiO2 being about 35% by weight.
The United States Government has rights in this invention pursuant to Contract No. W-7405-ENG-48 between the U.S. Department of Energy and the University of California.
This application claims the benefit of U.S. Provisional Application Ser. No. 60/090,312, filed Jun. 23, 1998, entitled "Ceramic Composition and Process for Immobilization of Actinides ", which is incorporated herein by this reference.
1. Field of the Invention
The present invention relates generally to a new ceramic composition for immobilizing actinides, in particular plutonium, thorium, and uranium. The present invention relates particularly to a ceramic composition comprising pyrochlore, brannerite and rutile. The ceramic composition is attractive for immobilization of excess plutonium because of its extremely low leachability, the existence of natural mineral analogues that have demonstrated actinide immobilization over hundreds of millions of years in wet geological environments, and the high solid solubility of actinides in the ceramic thus providing a relatively low overall waste volume. Incorporation of plutonium into ceramic provides a form that is relatively easy to store but renders retrieval of the plutonium to be more difficult than other immobilized forms.
2. Description of Related Art
Because of their extreme durability, ceramic forms have been studied extensively since the late 1970s for the immobilization of high level waste (HLW). The material called Synthetic Rock (SYNROC) is a titanate-based ceramic composed approximately of 30% zirconolite, 30% hollandite, 30% perovskite and 10% rutile. In the HLW application, actinides partition into the zirconolite and perovskite phases. U.S. Pat. No. 4,274,976 (Ringwood), U.S. Pat. No. 4,329,248 (Ringwood), U.S. Pat. No. 4,645,624 (Ramm, Ringwood) and U.S. Pat. No. 4,808,337 (Ramm et al.) disclose the immobilization of HLW in synthetic rock.
A form of synthetic rock to immobilize spent fuel (SYNROC-F) was reported by S. E. Kesson and A. E. Ringwood, "Safe Disposal of Spent Nuclear Fuel ", Radioactive Waste Management and the Nuclear Fuel Cycle, Vol. 4(2), pp. 159-174, October 1983. This form of SYNROC consisted of 90 wt % uranium pyrochlore, 5 wt % hollandite and 5 wt % rutile.
A variant of SYNROC-F, namely SYNROC-FA, was reported by A. G. Solomah, P. G. Richardson and A. K. McIlwain, "Phase Identification, Microstructural Characterization, Phase Microanalyses and Leaching Performance Evaluation of SYNROC-FA Crystalline Ceramic Waste Form ", Journal of Nuclear Materials 148, pp. 157-165, 1987. This form of SYNROC consisted of uranium pyrochlore, perovskite, uraninite and hollandite.
A cold press and sinter process is used in the production of mixed oxide (MOX) fuel from uranium and plutonium. The MOX process uses pressing pressures in excess of 20,000 psi and sintering temperatures of 1,700 deg C in a 4% H2 atmosphere on a 24 hour cycle. Because the final product is to be used as fuel, impurities in the feedstock cannot be tolerated.
An object of this invention is to provide a ceramic material for immobilization of actinides, including plutonium, uranium, thorium, americium and neptunium, said immobilized actinides then being suitable for storage in an underground repository.
The desired characteristics of such a ceramic material include: a) low leachability, b) high solid solubility of actinides in the ceramic, c) ability to incorporate "high-fired" PuO2 of various particle sizes, with particle size less than 2 millimeters, preferably less than 150 microns, d) sufficient compositional flexibility to incorporate significant concentrations of Pu and neutron absorbers (such as gadolinium and hafnium) as well as varying impurities in the feed streams, e) thermal stability during high level waste glass pouring in can-in-canister configurations, f) high chemical durability in the geologic repository environments both before and after undergoing radiation damage from alpha decay, g) difficult recoverability of plutonium from the ceramic to impede proliferation.
The present invention relates to a ceramic composition comprising pyrochlore, brannerite and rutile. A pyrochlore matrix provides the means to incorporate a higher concentration of plutonium than a zirconolite matrix. SYNROC compositions have contained hollandite, which the present composition does not. Other compositions have utilized reactive plutonium (such as dissolved plutonium) whereas the present composition starts with unreactive ("high fired") plutonium. The present composition also tolerates up to 55.7 wt % impurities in the actinide feedstocks. The present composition has been found to be stable when subjected to high level waste glass pouring in a storage canister. More specifically the mineralogical composition remains unchanged and the pellets retain their physical integrity.
FIG. 1 illustrates the processing regime for the inventive ceramic; and
FIG. 2 illustrates the phase boundaries in the zirconolite, and plutonium, uranium pyrochlore system.
ANSTO--Australian Nuclear Science and Technology Organization
deg C--temperature measured in degrees Celsius
DWPF--Defense Waste Processing Facility
HLW--High Level Waste
LLNL--Lawrence Livermore National Laboratory
ppm--parts per million
psi--pounds per square inch
SEM--scanning electron microscopy
SRS--Savannah River Site
vol %--volume percent
wt %--weight percent
ZPPR--Zero Power Physics Reactor
actinide oxide--a mineral phase of the form AnO2, where An is generally U, but can include Th, Np, Pu and Am
brannerite--a mineral phase of the form CTi2 O6 where C is an actinide selected from the group consisting of U, Pu, Th, Np, and Am.
calcining--heating materials to high temperatures to drive off water and other volatile substances
high fired--heated or fired at temperatures greater than 650 deg C
hollandite--a mineral phase having the approximate composition BaAl2 Ti6 O16
monazite--a mineral phase having the approximate composition CePO4
perovskite--a mineral phase having the approximate composition CaTiO3
pyrochlore--a cubic mineral phase of the form: A2 Ti2 O7, where A can be any of a range of ions, including Ca, Gd, Hf, Sm, U, Pu, Th, Np and Am.
simulated DWPF thermal cycle--a thermal cycle that simulates the pouring and cooling of high level waste glass around cans containing the ceramic, in the DWPF as part of the DOE disposition process
tonnes--metric tons, 1000 kilograms
whitlockite--a mineral phase having the approximate composition Ca3 (PO4)2
zirconolite--CaATi2 O7 where A is selected from the group consisting of Zr, Hf, Gd and Sm
A novel formulation of titanate-based minerals has been discovered to be capable of effectively immobilizing actinides. Said actinides include plutonium, uranium, thorium, americium and neptunium, preferably uranium and plutonium. Other radioactive materials such as transuranic and high-level wastes that contain significant amounts of actinides may be immobilized in this ceramic composition where said actinides in the waste have been concentrated prior to immobilization in the ceramic form.
This formulation consists primarily of pyrochlore, brannerite and rutile. Immobilization in the baseline formulation is accomplished by elemental substitution of the plutonium into lattice sites of pyrochlore. Pyrochlore provides the means to incorporate higher quantities of actinides than with zirconolite. This formulation demonstrates the ability to incorporate a high uranium and plutonium concentration (elemental up to 32 wt %, in oxides form up to 36 wt %) without significant changes in properties or mineralogy. Neutron absorber loadings (gadolinium, hafnium, samarium) are not affected by interchanging uranium for plutonium. Pyrochlore is less susceptible than zirconolite to long term, radiation induced damage effects from alpha decay of the plutonium that would lead to enhanced dissolution of the waste form during exposure to groundwater. Naturally occurring pyrochlores can retain actinides for billions of years even when extensive secondary alteration due to contact with fluids at temperatures less than 100 deg C has occurred.
The ceramic form has been found to be two to four orders of magnitude more durable than alternate glass forms as measured by dissolution rates in aqueous solution. Plutonium in the immobilized form cannot be extracted and purified by currently existing standard processes, such as the PUREX process. Significant changes in the head end processing would be required.
The immobilization form is capable of incorporating "high-fired" plutonium oxide 2 millimeters in diameter or less, preferably less than 150 microns, directly into the form. The milled actinide powder particle size is 50 microns or less, preferably nominally 20 microns. The immobilization form is capable of incorporating a wide variety of impurities relevant to the plutonium disposition mission, up to 55.7 wt %. Impurity compositions up to 13 wt % in the product form were tested with no apparent detriment to the form.
FIG. 1 shows a preliminary processing regime that defines the compositional space in which the ceramic is generated. The amount of pyrochlore is greater than 50% volumetric fraction, preferably 80% volumetric fraction. The amount of brannerite is up to 50% volumetric fraction, preferably 12%. The amount of zirconolite is up to 50% volumetric fraction, preferably 0%. The amount of rutile is up to 20% volumetric fraction, preferably 8%. The amount of actinide oxide is up to 1% volumetric fraction, preferably less than 0.5%. Other phases may also be present, up to 10% volumetric fraction, preferably 0%. Said other phases can be silicate, whitlockite, monazite, perovskite, magnesium titanate, ilmenite, pseudobrookite, corundum, calcium uranium vanadate, hafnium titanate, magnesium aluminum titanate, magnetoplumbite, or calcium aluminum titanate. The process is further described in patent application entitled "Process For Making A Ceramic Composition For Immobilization Of Actinides", by inventors: Bartley B. Ebbinghaus, Richard A. Van Konynenburg, Eric R. Vance, Martin W. Stewart, Philip A. Walls, William Allen Brummond, Guy A. Armantrout, Paul G. Curtis, Beverly F. Hobson, Joseph Farmer, Connie Cicero Herman, David Thomas Herman, which is incorporated herein by reference.
To maintain criticality control, especially where the actinide is plutonium, the ceramic should contain an adequate amount of neutron absorbers (such as hafnium, gadolinium and samarium). The preferred amounts are defined as overall molar ratios of Hf-to-Pu and Gd-to-Pu such that both are equal to or greater than unity.
To depict on a ternary phase diagram the processing regime in which the ceramic is formed (See FIG. 1), the number of variables had to be reduced from 6 (the number of oxide components) to 3. Since UO2 and PuO2 are known to be interchangeable in the formulation without changing the compositional phase boundaries, they can be considered as one oxide (AnO2), thus reducing the number of variables to 5. The form is designed to contain excess rutile, which is essentially pure TiO2, so its activity is fixed at unity, thus reducing the number of variables to 4. Gd is known to partition relatively evenly between the primary actinide-bearing phases, pyrochlore, zirconolite, and brannerite. Consequently, the Gd can be factored out without inducing too much error, thus reducing the number of variables to the desired value of 3. The resulting ternary phase diagram is depicted in FIG. 1. Perovskite is abbreviated as "Pe." Pyrochlore is abbreviated as "Py." Zirconolite is abbreviated as "Z." Brannerite is abbreviated as "B," and HfTiO4 is abbreviated as "Hf." The "acceptable" processing regime is identified by the diagonal lined region in FIG. 1. In the process planned for actual disposition, UO2 and PuO2 will be added to a preblended mixture of the other components. The composition of the preblended mixture would fall at approximately 0.25 units of HfO2 and 0.75 units of CaO. Addition of UO2 and/or PuO2 would cause the resulting mixture to fall on a straight line between this point and the AnO2 point. The intersection of this imaginary line with the identified "acceptable" processing range indicates that there is a fairly wide range of UO2 and/or PuO2 compositions that lie within the "acceptable" range.
Baseline Formulation Chemistry
The pyrochlore-based baseline product form is observed to be composed of about 80 vol % pyrochlore, about 12 vol % brannerite, and about 8 vol % rutile. Zirconolite can also be present, but it is not generally observed when the sample is well reacted and when there are no feed impurities present. Pyrochlore and zirconolite are very closely related minerals. The primary difference in the structures arises from the way the characteristic layers of TiO6 octahedra are stacked. Zirconolite actually has several structural polytypes that also differ in the way the characteristic layers are stacked: zirconolite-2M, zirconolite-3T, and zirconolite-4M (polymygnite) to name those that have actually been observed in this ceramic form. The number corresponds to the number of layers before the stacking repeats itself and the letter stands for the crystal symmetry, M for monoclinic and T for trigonal. When the layers are aligned in a body-centered fashion, the pyrochlore phase is formed.
The phase relationship between pyrochlore and zirconolite and its polytypes is one important part of defining the baseline formulation. To depict the phase relationships, a pseudo-ternary diagram is given in FIG. 2. The end points are zirconolite (CaZrTi2 O7 or CaHfTi2 O7), Pu-pyrochlore (CaPuTi2 O7 or its surrogate CaCeTi2 O7), and U-pyrochlore (CaUTi2 O7). The open points are data from Ce-loaded samples, and the solid points are data from the Pu-loaded samples. The squares contain Hf and Zr, and the diamonds contain U only. The circles are data from the Zr-loaded samples, and the triangles are from the Hf-loaded samples. Many of the samples contain Gd, which had to be factored out in order to depict all the data on one ternary diagram. For simplicity the Gd was all assumed to be entirely on the Ca site, which is accurate in many cases. As a result of this assumption, FIG. 2 is more correctly described as a ternary plot consisting of the three components, (1) Pu or Ce, (2) Hf or Zr, and (3) U. The baseline composition in this diagram is at approximately 0.49 units of U, 0.25 units of Pu, and 0.26 units of Hf.
FIG. 2 clearly shows that the equilibrium phase behavior of Hf and Zr and of Ce and Pu are for all practical purposes indistinguishable. Closer inspection reveals that the equilibrium phase behavior of U is also identical to that of Ce and Pu, i.e., the pyrochlore phase boundary is independent of the total U, Pu, and Ce composition. Note that with a comparable offset adjustment in the U-loading, the Pu-loading in the form can be adjusted anywhere from 0 to about 32% without appreciably changing the mineralogy in the baseline form. The regime above 0.7 units of Ce, Pu, and U is the pyrochlore single-phase regime. The region above about 0.8 units of Hf and Zr is the single phase zirconolite regime (-2M). There is some scatter in the zirconolite boundary. This is due at least in part to a temperature effect. At around 1400 deg C, the boundary appears to be closer to about 0.75 formula units, and at around 1200 deg C, the boundary appears to be closer to about 0.85 formula units. An intermediate phase generally occurs at about 0.5 formula units of Hf or Zr. This is the zirconolite-4M phase. This phase is generally not observed in samples with impurities.
Microprobe analyses on a number of samples have been averaged to give the nominal atomic compositions of the primary phases in the ceramic form. The nominal atomic compositions are given in Table I. For zirconolite and pyrochlore, the total metal composition is normalized to 4. For brannerite, the total metal composition is normalized to 3, and for rutile and actinide oxide, it is normalized to unity. The corresponding amount of oxygen based on the assumed oxidation states shown is given in the 0 equivalent column. In the ideal structures, the oxygen equivalents for pyrochlore, zirconolite, brannerite, rutile, and actinide oxide are 7, 7, 6, 2, and 2, respectively.
TABLE I__________________________________________________________________________Elemental compositions in baseline formPhase Ca Gd Hf U Pu Ti Al Total Metal O equiv.__________________________________________________________________________Pyrochlore 0.905 0.217 0.265 0.432 0.237 1.905 0.037 4.00 6.964 Zirconolite 0.741 0.147 0.839 0.133 0.116 1.842 0.181 4.00 7.093 Brannerite 0.071 0.110 0.135 0.534 0.212 1.888 0.050 3.00 5.849 Rutile 0.000 0.000 0.083 0.010 0.000 0.900 0.007 1.00 1.997 Actinide Oxide 0.079 0.045 0.029 0.426 0.381 0.015 0.025 1.00 1.886 Assumed Oxidation State 2+ 3+ 4+ 4+ 4+ 4+ 3+__________________________________________________________________________
One of the interesting features in the compositions shown in Table I is that although the phase boundaries appear to be the same for the use of either UO2 or PuO2 in the formulation, the elemental partitioning between the phases is different. Notice that U is enriched relative to Pu in the brannerite phase and depleted relative to Pu in the zirconolite phase. These enriched and depleted relationships are based on comparison to the approximate 2-to-1 ratio of U-to-Pu in the dominant pyrochlore phase, which corresponds to the U-to-Pu ratio in the ceramic composition as a whole.
Actinide Oxide Dissolution Kinetics
Dissolution of "high-fired" PuO2 or PuO2 1 /UO2 into the ceramic form seems to be affected significantly by temperature and process impurities, and to a lesser extent by the relative abundance of the primary phases. Note that all "high-fired" PuO2 used in these tests was heated to 1000 deg C for 4 hours in an air atmosphere and all the "high-fired" PuO2 /UO2 was heated to 950 deg C for 2 hours in an argon atmosphere.
In earlier formulation work, a zirconolite-rich formulation was being developed, and data on actinide dissolution kinetics was obtained for this formulation. In addition to the matrix phase of zirconolite, the form contained Ba-hollandite, rutile, and pyrochlore. In this set of experiments performed at LLNL, the "high-fired" PuO2 was sieved through a 600 mesh sieve (i.e., the particles were less than 20 microns diameter) and the precursors were then dry mixed by hand in a V-shaped mixer. A half dozen pellets were pressed at between 30 and 80 MPa and fired at 1300 deg C for 4 hours. After the first firing, the product densities varied from about 89 to 96% of the theoretical maximum (4.9 g/cm3). The samples were then separated into 3 pairs and fired at 1300, 1350, or 1400 deg C for 4 hours. One of each pair was then subjected to a simulated DWPF thermal cycle. Results of the thermal treatment tests are discussed later. All of the product pellets were analyzed using an SEM/microprobe. The pellets with the 1300 deg C final firing temperature had large chunks of "unreacted" PuO2 up to about 20 microns in diameter. The PuO2 is termed "unreacted" in this case since it was found to be essentially pure PuO2. The pellets fired at 1350 deg C had a small amount of "reacted" PuO2, typically 3 microns in diameter or less. The PuO2 is termed "reacted" in this case because it was found to contain significant and consistent amounts of Gd and Zr. Only one "reacted" PuO2 grain barely larger than 2 microns diameter was found in the sample with the final firing temperature of 1400 deg C. From these data it is clear that 1300 deg C is an inadequate temperature to achieve PuO2 dissolution into the zirconolite-rich ceramic form. However, 4 hours at 1350 deg C appears to be adequate time and temperature to achieve dissolution of PuO2 particles up to about 20 microns in diameter into the zirconolite-rich ceramic matrix. Apparently, the reaction kinetics increase significantly between 1300 and 1350 deg C. It is not known for certain, but the significant increase in reaction kinetics is believed to be the result of a minor liquid phase that forms at temperatures greater than about 1325 deg C.
Of course, the current baseline formulation is pyrochlore-rich, not zirconolite-rich. In more recent work performed at ANSTO, a mixture of "high-fired" PuO2 /UO2 (1 part Pu per 2 parts U) was dry-milled with ceramic precursors, pressed into pellets at about 90 MPa and fired at temperatures ranging from 1275 to 1400 deg C for 4 hours. The PuO2 /UO2 feed material was composed of a number of large agglomerates greater than 10 microns, but less than about 20 microns in diameter. Most firings were performed in an argon atmosphere, but some were performed in air. The results suggest that the particle size requirements for the pyrochlore-based form are less stringent than for the previously mentioned zirconolite-rich form. Enhanced dissolution was generally observed as the temperature was increased, but even at 1300 deg C the PuO2 /UO2 dissolution was satisfactory, much better than in the previously mentioned work on the zirconolite-rich formulation. All residual PuO2 /UO2 in the pyrochlore-rich ceramic form fell into the category of "reacted," i.e., it contained significant and relatively consistent amounts of Gd and Hf.
Two other important general observations have been made. First, the residual "reacted" PuO2 /UO2 in the pyrochlore-rich formulation is essentially always observed to be encapsulated within the brannerite grains. This indicates that by decreasing the amount of the brannerite component in the formulation, enhanced PuO2 and/or UO2 dissolution can be obtained. Second, feed impurities such as silica enhance PuO2 and/or UO2 dissolution considerably. Since feed impurities can also aid densification, their presence in limited quantities can be advantageous to the ceramic form. Note that although a reactive "low-fired" PuO2 was never tested, it has been found that a sufficiently small PuO2 and/or UO2 particle size and good mixing are more than sufficient to achieve dissolution of PuO2 and/or UO2 into the ceramic form. Therefore, any enhanced dissolution into the ceramic form that could be gained by using "low-fired" PuO2 is not required.
Feed Impurity Tolerances
Tolerance of the ceramic form to the range of feed impurities expected is an important part of making the ceramic form a viable and attractive candidate for Pu disposition. A relatively large amount of work was conducted in this area at LLNL, SRS, and ANSTO. A set of 10 Pu-sample compositions and 10 Ce-sample compositions were prepared according to the general procedure described in the experimental section. Pu-sample compositions are given in Table II. Composition A-0 is the baseline ceramic form. Compositions A-1 to A-6 correspond to various general categories of feed material that are expected. A-1 corresponds to typical impure oxides. Nominally about 5 metric tons (MT) of currently declared U.S. excess Pu falls into this category. A-2 corresponds to the composition of Pu from the Zero Power Physics Reactor (ZPPR) plates. Nominally about 3 MT of current excess Pu falls into this category. A-3 corresponds to the composition of atypical impure metal. Nominally about 2 MT of current excess Pu falls into this category. A-4 corresponds to the composition of atypical clean metal. Nominally about 1 MT of current excess Pu falls into this category. A-5 corresponds to the composition of U/Pu oxides. Nominally about 1 MT of current excess Pu falls into this category. A-6 corresponds to the composition of Pu alloys. Nominally about 1 MT of current excess Pu falls into this category. A-7 is an overall estimated average composition for the 17 MT excess Pu case. A-8 is an estimated most extreme case. A-9 is an intermediate case between A-7 and A-8 that corresponds roughly to one of the extreme compositions tested in the competing glass formulation work.
TABLE II__________________________________________________________________________Compositions of samples fabricated in the feed impurity tests (Totals may not exactly equal 100% because of rounding.)A-0 A-1 A-2 A-3 A-4 A-5 A-6 A-7 A-8 A-9 wt % wt % wt % wt % wt % wt % wt % wt % wt % wt %__________________________________________________________________________Base Feed MaterialsCaO 9.95 9.67 9.89 9.73 9.92 9.85 9.83 9.80 8.65 9.44 TiO2 35.87 34.88 35.64 35.08 35.77 35.50 35.43 35.34 31.20 34.04 HfO2 10.65 10.35 10.58 10.41 10.62 10.54 10.52 10.49 9.26 10.11 Gd2 O3 7.95 7.73 7.90 7.77 7.93 7.87 7.85 7.83 6.91 7.54 UO2 23.69 23.03 23.54 23.17 23.63 23.45 23.40 23.34 20.60 22.48 PuO2 11.89 11.56 11.81 11.63 11.86 11.77 11.75 11.71 10.34 11.28ImpuritiesAl2 O3 0.63 0.20 0.22 0.11 1.04 0.32 1.59 0.50 MgO 0.19 0.23 0.02 0.46 0.18 0.13 0.87 0.44 CaCl2 0.37 0.16 2.19 0.66 Ga2 O3 1.27 0.14 0.14 0.57 Fe2 O3 0.17 0.14 0.16 0.08 0.50 0.15 Cr2 O3 0.04 0.02 0.02 0.13 0.08 NiO 0.08 0.09 0.04 0.33 0.13 CaF2 0.21 0.12 1.30 0.44 K2 O 0.15 0.04 0.07 1.05 0.32 Na2 O 0.16 0.06 0.47 0.14 MoO2 0.05 0.44 0.30 0.11 0.47 0.28 SiO2 0.51 0.19 1.50 0.46 Ta2 O5 0.05 0.15 0.06 0.64 0.19 B2 O3 0.04 0.34 0.17 WO2 0.14 0.06 1.64 0.49 ZnO 0.11 0.01 0.07__________________________________________________________________________
Sample preparation and characterization work were shared among the various participating sites. Samples A-1 to A-6 were generally prepared only at one site, whereas samples A-0, A-7, A-8, and A-9 were prepared at two or three different sites. At least one Ce-sample and one Pu-sample of each composition were successfully prepared. All of the Ce-samples and most of the Pu-samples have since been characterized to determine the product phase assemblages. All of the samples reacted well and formed pyrochlore as the dominant phase, even sample A-8, which had 13 wt % impurities in the product. Several trends were observed. Si could not be incorporated significantly into any of the primary ceramic phases. SiO2 forms a separate glassy phase that contains significant amounts of Ca, Al, Ti, and other impurities but little or no Pu or U. The same effect seems to be observed for P. P2 O5 was not intentionally added to the form, but was found to be present at about 200 ppm in the TiO2 starting material. P2 O5 forms a separate phase (presumably whitlockite) that is rich in Ca and P. In general, all other impurities were either vaporized or accommodated into at least one of the primary ceramic phases. Compositions that were low in impurities produced ceramics that were for the most part rich in brannerite and lean in zirconolite, and compositions that were rich in impurities produced ceramics that were for the most part lean in brannerite and rich in zirconolite. As mentioned earlier, the impurities seem to enhance the reaction kinetics considerably. Compositions with the highest impurity levels had the least amount of actinide oxide in the product, as low as 0.04 vol %, and compositions with the lowest impurity levels had the greatest amount of actinide oxide in the product, as high as 0.6 vol %. Based on image analysis of the SEM images obtained, the compositional range observed in the suite of impurities tests was as follows: pyrochlore--62 to 90 vol %, brannerite--0 to 22 vol %, zirconolite--0 to 25 vol %, rutile--0 to 16 vol %, actinide oxide--0.004 to 0.6 vol %, and silicate glass--0 to 6 vol %, as shown in Table III.
Note that these samples were fired at 1350 deg C for 4 hours in an argon atmosphere. Sample compositions with CeO2 used 0.634 times the PuO2 mass listed in order to keep the molar compositions the same.
TABLE III______________________________________Product Mineralogy Baseline Observed Range Acceptable Range Mineralogy (vol %) (vol. %) (vol %)______________________________________Pyrochlore 80 62-90 >50 Brannerite 12 0-22 0-50 Zirconolite 0 0-25 0-50 Rutile 8 0-16 0-20 Actinide Oxide 0.5 0.04-0.6 0-1 Silicate and other 0 0-6 0-10 phases______________________________________
Many of the samples were analyzed by electron microprobe analysis. These data were used to generate the preliminary partitioning coefficients given in Table IV. As is readily seen, the more common impurities, namely Al, Cr, Fe, Ni, Ga, and Mg, partition preferentially into zirconolite. A few impurities partition preferentially into the pyrochlore phase, namely Mo, Ta, and W. Na, K, and Zn tend to vaporize and/or to partition into the silica-rich glassy phase, but the little that remains in the primary phases does seem to partition selectively. Some data are also given for the relative partitioning of impurities into brannerite compared to pyrochlore. With the possible exceptions of Ni and Zn, the impurities do not seem to partition significantly into the brannerite phase.
TABLE IV______________________________________Approximate partitioning coefficients for various impurities. Element Xzirconolite /Xpyrochlore Xbrannerite /Xpyrochlore______________________________________Al 16 2.3 Cr 15 -- Fe 3 1 Ga >30 -- K <0.05 -- Mg 3.0 <0.1 Mo 0.10 0.20 Na <0.1 0.2 Ni 1.5 2 Ta <0.1 <0.1 W 0.020 -- Zn 4 5______________________________________
The partitioning coefficient is given as the mole fraction of the element in the phase of interest divided by the mole fraction of the element in the pyrochlore phase.
The maximum impurity levels demonstrated are as shown in Table V.
TABLE V______________________________________Maximum Impurity Levels Demonstrated Product Equivalent Impurity Concentration (wt %) Feed Concentration (wt %)______________________________________Al2 O3 10.0 48.3 B2 O3 1.0 7.8 BaO 2.3 16.3 CaCl2 2.19 15.8 CaF2 10.0 48.3 CaO 10.0 48.3 Cr2 O3 10.0 48.3 Cu2 O 10.0 48.3 Fe2 O3 10.0 48.3 Ga2 O3 15.3 60.2 K2 O 1.05 8.9 MgO 10.0 48.3 MnO2 10.0 48.3 MoO3 10.9 50.7 Na2 O 0.47 4.3 Nb2 O5 10.7 50.2 NiO 10.0 48.3 P2 O5 5.1 31.0 PbO 0.5 4.2 SiO2 1.50 12.7 SnO2 4.1 26.6 Ta2 O5 13.0 55.8 WO3 16.4 62.3 ZnO 10.0 48.3 Max.Tot. 13.0 55.7______________________________________
Max. Tot. is the maximum combined total of impurities that was tested. Product concentration is the concentration of the impurity in the immobilized product. Equivalent feed concentration is the equivalent feed concentration of the impurity in the PuO2 feed.
Stability with Respect to the DWPF Pour
Since it is planned that cans containing the ceramic will be enveloped in molten glass during the glass pouring operation at the DWPF, it is important to know that the ceramic will remain stable during this process. Tests in this area fell into two basic areas: evaluation of potential mineralogical and compositional changes during the heating and the slow cool-down, and evaluation of potential cracking during the rapid heat-up.
The heating and slow cool down process was simulated by heating the product forms to between 1000 and 1200 deg C and cooling at between 1 and 2 deg C per minute. In every case, no mineralogical change was observed. Phase compositions before and after thermal treatment were analyzed by electron microprobe or quantitative EDS analysis. In every case, there was little or no compositional change. Any small compositional differences observed were well within the statistical variations expected. Compositions before and after one of the thermal treatment tests are given in Table VI. In this particular test, the previously mentioned zirconolite-rich samples were used. These were the samples with the final firing temperature of 1350 deg C. One of the two samples was then subjected to a simulated DWPF thermal heating and cooling cycle: heat to 1000 deg C, hold for 15 minutes, cool to 500 deg C at 2 deg C per minute, then cool to ambient at 1 deg C per minute or slower. There were five phases in the sample: zirconolite, pyrochlore, rutile, hollandite, and "reacted" PuO2. Only the compositions for the Pu-bearing phases are given in Table IV. Under the column of DWPF, a "no" means that the data are from the sample that was not subjected to the simulated DWPF thermal cycle and a "yes" means that the data are from the sample that was subjected to the simulated DWPF thermal cycle. Note that the compositional analyses are surprisingly close, even for the "reacted" PuO2.
A test was also performed in which molten DWPF-type glass was heated to about 1100 deg C and was then poured directly onto bare non-radioactive ceramic pellets to determine qualitatively how badly the ceramic would crack because of the thermal shock. In short, the cracking was minimal. Out of 7 pellets, ranging from 2.5 to 4 cm in diameter, only one pellet cracked into two separate pieces. All the other pellets remained intact, with little or no observed cracking.
TABLE VI__________________________________________________________________________Effect of DWPF heating and cooling cycle on mineralogical composition (Compositions determined by electron microprobe analysis. Totals may notexactly final column because of rounding.)Phase DWPF CaO BaO GdO1.5 ZrO2 PuO2 TiO2 AlO1.5 Total__________________________________________________________________________Zirconolite No 0.612 0.000 0.238 0.799 0.194 1.757 0.399 4.000 Zirconolite Yes 0.633 0.000 0.234 0.805 0.201 1.732 0.394 4.000 Pyrochlore No 0.713 0.022 0.255 0.225 0.617 2.131 0.037 4.000 Pyrochlore Yes 0.739 0.037 0.238 0.230 0.622 2.089 0.045 4.000 PuO2 No 0.000 0.007 0.044 0.188 0.717 0.044 0.000 1.000 PuO2 Yes 0.000 0.008 0.044 0.186 0.724 0.040 0.000 1.000__________________________________________________________________________
From the data on impurity effects it is possible to generate a preliminary set of feed impurity specifications. It was learned that most impurities fell into one of four categories: (1) volatiles, (2) zirconolite stabilizers, (3) pyrochlore stabilizers, and (4) glass formers. The preliminary specification limits are given in Table VII. The limits given are all based on impurity sample A-9 (5.1 wt % impurities in the product) except for the limit on pyrochlore stabilizers, which is based on sample A-8 (13 wt % impurities in the product). The limits are reported in total moles per mole of PuO2. Molar ratio is used rather than weight ratio since the impurities substitute into the ceramic form on an atomic basis and not on a weight basis. It is expected with further testing that the draft limits given in Table VII can be relaxed considerably.
TABLE VII______________________________________Preliminary specification limits on feed impurities. Category Moles per mole PuO2 Impurities______________________________________Volatiles 0.60 NaCl, KCl, CaCl2, CaF2, MgF2, etc. Zirconolite 0.75 AlO1.5, FeO1.5, stabilizers GaO1.5, CrO1.5, MgO, ZrO2, HfO2, etc. Pyrochlore stabilizers 0.40 WO2, MoO2, TaO2.5, NbO2.5 Glass formers 0.30 SiO2, BO1.5______________________________________
Following immobilization of the actinides in ceramic form, the ceramic may be loaded into cans. The cans may then be loaded into canisters, with high level waste glass poured into the canisters around the cans.
Obviously numerous modifications and variations of the present invention are possible in the light of the above teachings. It is therefore to be understood that within the scope of the appended claims the invention may be practiced otherwise than as specifically described therein.