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Best limo company in Mesquite
You would have expected the best limo company in Mesquite to have an excellent selection of cars. However, no matter how good they are, you are unlikely to spot any of these limos in their fleet. Limousines have always been luxury vehicles which cater to any kind of excess but the cars are described here go well beyond the normal definition of lavish and include an array of features and amenities and technology. The ones that go over the top are the souped up limos which are also arguably the most expensive. With features like hot tubs, mini pools and any gadget that you could conceivably imagine, it is a pretty good bet that you could probably set up house in some of these vehicles and live in them.
The Million Euro Mini is estimated at a price of $1.35 million.Kazakhstan's Princess Regina Abdurazakova owns the most expensive Mini Cooper in the world and this one of a kind. The limo isn't a mini at all and possesses a pink body covered in over a million Swarovski crystals. In addition, every wheel of the car has a crysta inset in its center which is over over 3 inches in diameter. If this is not enough, the window films of the limo contain approximately 50 grams of pure gold. Inside, the Million Euro Mini is equipped with 20 parking cameras, 30 parking sensors, 70 TFT screens, and a 47-inch television.
The American Dream estimated at $4 million is a custom built limousine designed and built by the famous car designer and collector Jay Ohrberg. For many years this vehicle has held the distinction of being the longest limo on the planet because it has a length of 100 feet and has 26 wheels. Think of this vehicle as a kind of mobile mini luxury pad because it has a sun deck and a Jacuzzi, a swimming pool, more than one king size bed, and a helipad. Sadly it is now languishing in a parking lot and there are no takers in sight.
. Maybach Landaulet has an estimated price of $1.4 million.The Maybach Landaulet's style is based on a limousine model that Maybach made in the 1920s, and it oozes sophistication and elegance. Though it is not a stretch limo, it still costs well over $1 million and this is partly due to being equipped with gold flecked granite inlays and a 612 hp bi-turbo V12 engine. The interior is covered in soft white leather with the consistency of butter and there's a retractable roof that allows passengers to bask in the sun.
The Sultan of Brunei's Rolls Royce Silver Spur Limo has an estimate price of $14 million.One of the most expensive limos in the world belongs to the Sultan of Brunei and while many heads of state and royalty ride in limos, but this one is actually the pick of the bunch for its opulence. The exterior of this car alone is a triumph of flamboyance and it's actually covered in pure 24 carat gold and was specially designed just for the royal family. As part of the Sultan's huge car collection, his Rolls Royce limo stands out for being the epitome of decadence and it contains just about anything that one could think of to put inside a limousine.


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Home biography Gerina Piller
Gerina Piller Biography
Facts of Gerina Piller
1985 , March-29
Quick Timeline of Gerina Piller
1985 Born in Roswell, New Mexico, United States
2003 Won the state golf championship
2007 Became the Conference USA individual champion
2007 Was named the Player of the Year
2007 Turned professional
2009 Earned conditional status on the LPGA Tour for 2010
2010 Was ranked 5th on the Futures Tour money list
2011 Married to Martin Piller
2015 Was ranked 29th on the Women's World Golf Rankings
Detail Timeline of Gerina Piller
March 29 , 1985
Born in Roswell, New Mexico, United States
Talented and enthusiastic lady, Gerina Piller was born as Gerina Michelle Mendoza Piller in the mid 1980s in Roswell, New Mexico, United States of America to Alan Stevenson and Rita Stevenson. She is now living in Fort Worth, Texas, United States.
Won the state golf championship
As a child, Gerina got enrolled at Goddard High School. She earned her high school graduation from there in 2003. That year she was also crowned with the state golf championship and named as an all-state volleyball player.
Became the Conference USA individual champion
After her high school, she joined University of Texas at El Paso (UTEP). There she was also active in golf. During her senior year, she won four tournaments. In 2007, she became the Conference USA individual champion.
Was named the Player of the Year
She had an outstanding career as a collegiate golfer at the University of Texas El Paso. In 2007, she received several awards and honors. In 2007, she was named as Player of the Year. That year she was also named as the UTEP Female Athlete of the Year.
Turned professional
After an outstanding career at University of Texas at El Paso (UTEP), she turned pro in September 2007. As she was disqualified for the LPGA Tour in 2007, she went on playing on the Futures Tour the following year.
Earned conditional status on the LPGA Tour for 2010
She also got disqualified for the LPGA Tour for the next two years but she finally got a conditional status on the LPGA Tour for 2010. In 2010, she was ranked 2nd in iMPACT Classic and the USI Championship.
Was ranked 5th on the Futures Tour money list
She was placed 2nd in iMPACT Classic and the USI Championship in 2010, that year she was listed on the Futures Tour money list. They ranked her on the 5th position. That year she earned full playing privileges on the LPGA Tour for 2011.
Married to Martin Piller
In January 2011, Gerina got married to Martin Piller. Martin Piller is also a professional golfer from United States. In 2010, he won the Stadion Athens Classic at UGA. It's been more than half a decade they have been bonded into this married life.
Was ranked 29th on the Women's World Golf Rankings
At the end of 2007, she turned professional. At the end of 2008, she was ranked 630 on the Women's World Golf Rankings. In 2012, she was ranked 95th and at the end of 2015, she kissed the 29th position.
In January 2011, Gerina got married to Martin Piller. Martin Piller is also a professional golfer from United States. In 2010, he won the Stadion Athens Classic at UGA. It's been more than half a decade they have been bonded into this married life. Her nationality is American and she is of mixed ethnicity.
As a child, Gerina got enrolled at Goddard High School. She earned her high school graduation from there in 2003. That year she was also crowned with the state golf championship and named as an all-state volleyball player. After her high school, she joined University of Texas at El Paso (UTEP). There she was also active in golf. During her senior year, she won four tournaments. In 2007, she became the Conference USA individual champion and she was also named as Player of the Year. That year she was also named as the UTEP Female Athlete of the Year. After an outstanding career at University of Texas at El Paso (UTEP), she turned pro in September 2007. As she was disqualified for the LPGA Tour in 2007, she played on the Futures Tour the following year. She also got disqualified for the LPGA Tour for the next two years but she finally got a conditional status on the LPGA Tour for 2010. In 2010, she was ranked 2nd in iMPACT Classic and the USI Championship. She is five feet and seven inches in her height. She is now aged 31 years old. Her net worth is in millions.
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Q: What do percentiles tell us about exponential families I have a question in my lecture slides which asks the following

Exponential families of distributions, such as the normal, Poisson,
  and binomial distributions, are characterized by a very
  fast (exponentially) decreasing density around their mode. How are the
  standard deviation and the percentiles 25/75 related, in terms of the
  relative distance to the mean?

I could see how the distributions are computed but could not understand how different measures relate and influence each other.

A: If you look at the relation between those two quantities for the Poisson, you get somewhat of an equivalence:

For a comparison, if you represent 4 times the standard deviation (range of the Normal 95% interval) against the 95% interquantile range, you get the following:

And here is a similar representation for the exponential distribution, with a rather close connection between standard deviation and interquartile range:

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US5698857A - (Barium hafnate: Cu) phosphors and phosphor screens - Google Patents
(Barium hafnate: Cu) phosphors and phosphor screens Download PDF
radiographic
Patrick Maddock Lambert
Gregory S. Jarrold
David Paul Trauernicht
Carestream Health Inc
Eastman Kodak Co
1995-12-19 Application filed by Eastman Kodak Co filed Critical Eastman Kodak Co
1995-12-19 Assigned to EASTMAN KODAK COMPANY reassignment EASTMAN KODAK COMPANY ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: JARROLD, GREGORY S., LAMBERT, PATRICK M., TRAUERNICHT, DAVID P.
2007-07-27 Assigned to CREDIT SUISSE, CAYMAN ISLANDS BRANCH, AS ADMINISTRATIVE AGENT reassignment CREDIT SUISSE, CAYMAN ISLANDS BRANCH, AS ADMINISTRATIVE AGENT FIRST LIEN OF INTELLECTUAL PROPERTY SECURITY AGREEMENT Assignors: CARESTREAM HEALTH, INC.
2007-07-27 Assigned to CREDIT SUISSE, CAYMAN ISLANDS BRANCH, AS ADMINISTRATIVE AGENT reassignment CREDIT SUISSE, CAYMAN ISLANDS BRANCH, AS ADMINISTRATIVE AGENT SECOND LIEN INTELLECTUAL PROPERTY SECURITY AGREEME Assignors: CARESTREAM HEALTH, INC.
2008-03-07 Assigned to CARESTREAM HEALTH, INC. reassignment CARESTREAM HEALTH, INC. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: EASTMAN KODAK COMPANY
2011-04-04 Assigned to CARESTREAM HEALTH, INC. reassignment CARESTREAM HEALTH, INC. RELEASE OF SECURITY INTEREST IN INTELLECTUAL PROPERTY (FIRST LIEN) Assignors: CREDIT SUISSE AG, CAYMAN ISLANDS BRANCH
G21—NUCLEAR PHYSICS; NUCLEAR ENGINEERING
G21K—TECHNIQUES FOR HANDLING PARTICLES OR IONISING RADIATION NOT OTHERWISE PROVIDED FOR; IRRADIATION DEVICES; GAMMA RAY OR X-RAY MICROSCOPES
G21K4/00—Conversion screens for the conversion of the spatial distribution of X-rays or particle radiation into visible images, e.g. fluoroscopic screens
C09—DYES; PAINTS; POLISHES; NATURAL RESINS; ADHESIVES; COMPOSITIONS NOT OTHERWISE PROVIDED FOR; APPLICATIONS OF MATERIALS NOT OTHERWISE PROVIDED FOR
C09K—MATERIALS FOR MISCELLANEOUS APPLICATIONS, NOT PROVIDED FOR ELSEWHERE
C09K11/00—Luminescent, e.g. electroluminescent, chemiluminescent materials
C09K11/08—Luminescent, e.g. electroluminescent, chemiluminescent materials containing inorganic luminescent materials
C09K11/67—Luminescent, e.g. electroluminescent, chemiluminescent materials containing inorganic luminescent materials containing refractory metals
C09K11/671—Chalcogenides
C09K11/673—Chalcogenides with alkaline earth metals
G21K2004/06—Conversion screens for the conversion of the spatial distribution of X-rays or particle radiation into visible images, e.g. fluoroscopic screens with a phosphor layer
(Barium halfnate:Cu) phosphors and phosphor screens. The phosphor screens include a support and a luminescent portion. The phosphor includes oxygen and a combination of species characterized by the relationship: (Ba1-q Mq)(Hf1-z-e Zrz Mge):yT where M is selected from the group consisting of Ca and Sr and combinations thereof; T is Cu; q is from 0 to 0.15; z is from 0 to 1; e is from 0 to 0.10; z+e is from 0 to 1; and y is from 1×10-6 to 0.02.
This application is related to a U.S. Ser. No. 08/574,481, entitled: "(BARIUM HAFNATE:Ti,Ce,Pb) PHOSPHORS, PHOSPHOR SCREENS, AND PHOSPHOR PREPARATION METHODS", filed concurrently herewith, by Patrick M. Lambert, Gregory S. Jarrold, and Philip S. Bryan; which is hereby incorporated herein by reference.
The invention relates to phosphors and phosphor screens and more particularly relates to improved activated barium hafnate phosphors and screens including those phosphors.
Phosphors have long been used in a variety of articles that can be referred to as "phosphor screens" or "phosphor-based radiation converters", articles that include a support and a phosphor-containing luminescent portion, and function to screen or capture X-rays and other high energy radiation for emission at a longer wavelength, either immediately or on a delayed basis following secondary stimulation. Information represented by the modulation of the captured radiation is reproduced in the emitted longer wavelength radiation. (As a matter of convenience, these articles are referred to generically herein as "phosphor screens" or "screens". Specific types of phosphor screens are further identified herein by commonly used designations, for example, "intensifying screens", "storage screens", "scintillators".)
Many types of phosphor screen are used to detect image-wise X-radiation absorption by a target interposed between the phosphor screen and an X-ray source. A widely used variety of phosphor screen is a radiographic phosphor panel or screen. These articles are rigid or flexible sheet or plates having a thin luminescent layer that contains a radiographic phosphor. Flexible radiographic phosphor screens are generally exposed while flat, but can be utilized while bent into a cylinder or more complex shape, particularly for industrial applications. Like many other crystalline materials, radiographic phosphors have a crystal matrix which allows for the replacement of some atoms by other similar atoms, but does not readily accept other atoms or moieties. Radiographic phosphor screens can be classified, based upon their phosphors, as prompt emission screens and image storage screens.
Intensifying screens are the most common prompt emission screens. Intensifying screens are used to generate visible light upon exposure of the intensifying screen to X-radiation. A sheet of photographic film is positioned to intercept the visible light generated and commonly is pressed against the intensifying screen within a light-tight cassette. Other prompt emission screens operate similarly, but in place of the photographic film have some other means for visualizing the X-radiation.
In intensifying screen/film technology, there is a need for efficient phosphors that absorb X-radiation and emit longer wavelength light in spectral regions matching native silver halide sensitivity. A developable latent image is formed in a silver halide emulsion layer of a radiographic element when it is imagewise exposed to radiation. Silver halide emulsions, however, more efficiently absorb and, consequently, are more responsive to longer wavelength electromagnetic radiation than to X-radiation. Silver halides possess native sensitivity to both the near ultraviolet and blue regions of the spectrum. Consequently, it is accepted practice to employ intensifying screens in combination with silver halide emulsion layers. An intensifying screen contains on a support a fluorescent layer that absorbs the X-radiation more efficiently than the silver halide and emits to the adjacent silver halide emulsion layer longer wavelength electromagnetic radiation in an image wise pattern corresponding to that of the X-radiation received. While the phosphor layer and the emulsion layer can be integrated into one element, in most instances the adjacent silver halide layer is coated on a separate support to form a separate radiographic element. In this way, the intensifying screen, which is not permanently altered to any significant degree by exposure, can be reused. The most common arrangement for X-radiation exposure is to employ a dual coated radiographic element (an element with silver halide emulsion layers on opposite sides of a support); each emulsion layer being mounted adjacent a separate intensifying screen.
The useful native sensitivity (i.e., maximum absorption capability) of silver halide emulsions lies in the near ultraviolet (300-400 nm) and blue (400-500 nm) portions of the spectrum. The native sensitivity of silver chloride is negligible beyond 450 nm, with the sensitivity dropping approximately 2 orders of magnitude between 380 and 420 nm. The native sensitivity of silver bromide is negligible beyond 500 nm, with sensitivity dropping approximately 2 orders of magnitude between 450 and 490 nm. The native sensitivity of silver bromoiodide (3 mole % iodide) is negligible beyond 550 nm, with sensitivity dropping approximately 2 orders of magnitude between 470 and 530 nm. Thus, not only do silver halides fail to absorb efficiently in the green portion of the spectrum, the absorption of silver halides in the longer wavelength regions of the blue spectrum is relatively limited.
Green-emitting intensifying screens have found wide application with silver halide emulsions, however, this requires the sensitization of the silver halide by adsorbed spectral sensitizing dyes. The disadvantages of such a systems include added expense, since the dyes are complex organic compounds which, on a weight basis, are more expensive than silver, and are not recoverable for reuse. Also, emulsion addenda that adsorb to silver halide grain surfaces, such as antifoggants and stabilizers, can displace the dyes, leading to reduced spectral sensitivity.
High density X-ray phosphors are also particularly desired in screen/film systems to deliver improved image quality. The X-ray absorbing properties of these phosphors allow the construction of thinner screens, which, because of the shorter total path length to the adjacent silver halide emulsion layer(s), yield less blurring or spreading of the X-ray image. For a given phosphor particle size, an increase in image sharpness is apparent. Alternatively, the thickness of the phosphor layer can remain unchanged and the quantum noise of the system improved by increased X-ray absorption.
Scintillators utilize prompt emitting phosphor crystals of large or relatively large size. These phosphor screens can be flat or can have complex shapes, and sometimes utilize only a single very large crystal. Scintillators are used in high energy physics and medical applications. The material demands usually include the following:
1) High luminescence response to incident radiation or particles. Only in the case of the electromagnetic calorimeters used for high-energy physics experimentation is this requirement relaxed. The emission wavelength should be matched to the detector response (photomultipliers, proportional counters, Si photodiodes). For example, high energy physics calorimeters require only that lamdaem >300 nm, while integrating techniques such as CT require lamdaem >450 nm.
2) Very rapid relaxation times. For example, in high energy calorimeters, decay times of less then 20 ns are required, while in positron emission tomography (PET) relaxation times must be <1 ns. Other applications, such as computed tomography (CT) and gamma-ray cameras have less stringent decay time requirements (up to 100's of microseconds).
3) High radiation stopping power for size minimization. Materials with low-stopping power are needed as large pieces, in some cases single crystals up to 25 cm in length are required.
4) High transmittance. Crystals of excellent optical clarity are generally needed so that the majority of the emitted light can be conveniently collected at an edge or face of the element.
5) Low afterglow. This is particularly important in CT systems.
6) Good radiation hardness.
The scintillators are usually coupled to light detectors such as photomultipliers or silicon photodiodes. For example, in computed tomography, a rotating, fan-shaped X-ray beam transects the patient, and then interacts with the scintillator element, which, in turn, is coupled to a Si photodiode with a maximum response in the 500-1000 nm range. The emitted light is then proportional to the incident X-ray. The scintillator elements can be fashioned as single crystals, or as sintered polycrystalline pieces of high optical clarity.
Some Aspects of the Luminescence of Solids, F. A. Kroger, Elsevier, Amsterdam (1948) p. 161, teaches that a BaZrO3 host showed no luminescence at room temperature or -180° C. "A New Family of Self-activated Phosphors", D. E. Harrison, et al., J. Electrochem. Soc., Vol. 110 (1), (1963) pp. 23-28 describes BaZrO3 (and another material) as "non luminescent compounds".
"Fluorescence of Eu2+ -Activated Silicates", G. Blasse, et al., Philips Res. Repts., Vol. 23, (1968) pp. 189-200 teaches that BaZrO3 :Eu2+ exhibits a broad green prompt luminescence (centered at approximately 495 nm) and that this is an example of an emission with Eu2+ in a cubic site. "Energy Transfer in Oxidic Phosphors", G. Blasse, Philips Res. Repts., Vol. 24, (1969) pp. 131-144 teaches as to BaZrO3 :Eu2+ that: "As the luminescence of BaZrO3 :Eu2+ is very weak, neither the value of xc nor of ts has been determined." "On the Luminescence of Hafnium Compounds", W. J. Schipper, et al., Mat. Res. Bull., Vol. 29, (1994) pp. 23-30 discloses that the "efficient" green luminescence reported for a BaZrO3 :Eu2+ could not be reproduced.
Some Aspects of the Luminescence of Solids, F. A. Kroger, Elsevier, Amsterdam (1948) p. 161, teaches that BaZrO3 activated with 1 mole percent titanium showed deep blue luminescence at -180° C., but no emission at room temperature. U.S. Pat. No. 2,542,336 to Kroger et al., teaches phosphors containing titanium as an activator and having a matrix composed of one or more of the oxides of zirconium, hafnium, thorium, germanium and tin and optionally including either acid oxides or basic oxides or both. Disclosed basic oxides are the oxides of sodium, potassium, rubidium, cesium, lithium, barium, calcium, strontium, magnesium, beryllium, and zinc. Disclosed acid oxides are SO3, B2 O3, P2 O5 and SiO2. Titanium-activated zirconium oxide, magnesium stannate, calcium zirconate and zirconium phosphate are each specifically disclosed. "Investigations on the Luminescence of Titanium-activated Stannates and Zirconates", A. J. H. Macke, J. Solid State Chem., Vol. 18, (1976) pp. 337-346 discloses a study of the luminescence of BaZr0.99 Ti0.01 O3. A broad emission centered at 2.87 eV (432 nm) was observed, but only at or below liquid nitrogen temperature. "On the Luminescence of Hafnium Compounds", W. J. Schipper, et al., Mat. Res. Bull., Vol. 29, (1994) pp. 23-30 teaches that a violet-blue emission was observed (at 410 nm) at 4.2° K for BaHfO3 :Ti. The emission was not observed at temperatures above about 250° K. The article also states: "HfO2 and BaHfO3 do not luminesce . . . Upon doping with Ti, emission in the blue spectral region appears, except for HfP2 O7 :Ti. The titanate luminescence is largely quenched at room temperature, limiting the use of these materials as X-ray or X-ray storage materials."
"Proprietes de luminescence des zirconates alcalinoterreux purs ou actives par l'ion Pb2+ ", J. Chanewaye, et al., C. R. Acad. Sc. Paris, Vol. 271, (1970) p. 486 discloses a study of zirconates of the type MZrO3 with and without Pb2+ at 77° K. The BaZrO3 host showed a broad emission at 424 nm at this temperature and Pb2+ activated host material showed a very broad emission at approximately 580 nm. CaZrO3 :Pb2+ was cited as the most intense of the lead-activated compounds, with a severe intensity decrease observed at room temperature. "Influence of Crystal Structure on the Luminescence of Ions with s2 Configuration", G. Blasse, et al., J. Solid State Chem., Vol. 20, (1977) pp. 63-65 discloses that BaZrO3 :Pb2+ exhibited a green luminescence (centered at 495 nm) at 77° K. The luminescence was quenched at 260K.
U.S. Pat. No. 4,994,205 to Bryan, et al. teaches the phosphor HfO2 :Ti and an intensifying screen for producing a latent image in a silver halide radiographic element when imagewise exposed to X-radiation. The screen contains a phosphor having a hafnia host containing zirconia in concentrations higher than those found in optical grade hafnia. The phosphor can include as an activator one or a combination of titanium, rare earth, and alkali metal ions. Phosphor preparation processes are also described.
U.S. Pat. No. 5,112,700 to Lambert, et al. teaches the phosphor HfGeO4 :Ti. The titanium activated Hf--Zr germanate phosphor disclosed emits electromagnetic radiation principally in the spectral region to which silver halide exhibits native sensitivity. To maximize the intensity of emission the ratio of host metals satisfies the relationship:
D.sub.1-x Ge.sub.1-x
where D is the combined sum of zirconium and hafnium and x is 0.25 to -0.70. An X-ray intensifying screen is disclosed containing the phosphor composition.
There is a continuing need for improved phosphors and phosphor screens in which high density phosphors can exhibit prompt emissions of secondary radiation in useful wavelength ranges and with good speed.
The invention is defined by the claims. The invention, in its broader aspects, provides (Barium hafnate:Cu,Eu,Dy,Sm,Ho,Er,Tm) phosphors and phosphor screens. The phosphor screens include a support and a luminescent portion. The phosphor includes oxygen and a combination of species characterized by the relationship:
(Ba.sub.1-q M.sub.q)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e):yT
where M is selected from the group consisting of Ca and Sr and combinations thereof; T is selected from the group consisting of Cu, Eu, Dy, Sm, Ho, Er, and Tm and combinations thereof; q is from 0 to 0.15; z is from 0 to 1; e is from 0 to 0.10; z+e is from 0 to 1; and y is from 1×10-6 to 0.02.
It is an advantageous effect of at least some of the embodiments of the invention that improved phosphors and phosphor screens are provided which can exhibit prompt emissions of secondary radiation in useful wavelength ranges and with good speed.
The above-mentioned and other features and objects of this invention and the manner of attaining them will become more apparent and the invention itself will be better understood by reference to the following description of embodiments of the invention taken in conjunction with the accompanying figures wherein:
FIG. 1 is a diagrammatical cross-section of an embodiment of the phosphor screen of the invention configured as a radiographic phosphor screen.
FIG. 2 is a partially schematic diagrammatical cross-section of another embodiment of the phosphor screen of the invention configured as a scintillator.
The phosphor screen of the invention is an article of manufacture that includes a support and a phosphor-containing luminescent portion. The phosphor screen is generally described herein as if the phosphor screen were in the shape of a horizontally disposed flat plate. It is to be understood, however, that the phosphor screen is not limited to any particular shape and that directional terms refer only to relative positions, not an absolution orientation relative to the environment. For example, in different embodiments, the phosphor screen has the form of a rigid planar panel, or a flexible sheet able to assume a variety of shapes, or a rigid cylindrical tube, or a complex three dimensional shape. Similarly, in different embodiments, the luminescent portion has small or large crystals or even a single crystal; held in place by a layer of binder, or adhered in place, or held in place mechanically by fasteners or the like.
The phosphor of the invention is a crystalline material. The structure of crystalline materials on a "molecular level" can be categorized in a number of ways. Crystal structures can be categorized, in some cases, by analogy to various minerals. Oxides which crystallize in the undistorted, simple perovskite structure are usually represented by the formula ABO3. The A atom is in the center of a cube and B atoms at each corner. Crystal structures can also be categorized by use of: (1) crystal system, (2) lattice type, and (3) point and space symmetry. The crystal system of a material is the basic geometry of the "unit cell": the smallest repeating unit which has the same symmetry as larger portions of the material. Crystalline materials are assigned to seven crystal systems: cubic, hexagonal, tetragonal, orthorhombic, monoclinic, trigonal, and triclinic; each of which is distinguished by the length and spatial relationships of the cell axes.
Bravais lattice types elaborate on the unit cell descriptions of crystal systems. Lattice types looks to the same array of lattice points as the crystal system, but also looks to positions in the center of the unit cell (body-centered), on the faces (face-centered), and at the vertices (primitive). As in crystal systems, the lattice points and other positions used in classification are geometric positions that may or may not coincide with the positions of atoms in the unit cell. There are 14 Bravais lattice types. Crystal system and Bravais lattice types can be used in combination to describe crystalline materials, with the exception that some combinations of crystal system and Bravais lattice type are redundant or geometrically incompatible.
Point and space symmetry refers to the use of symmetry elements to define a material. Symmetry elements are operations such as reflections and rotations that transform a structure to an orientation that is indecipherable from the original orientation. The combination of Bravais lattice type with point and space symmetry results in what is referred to as the "space group". There are 230 space groups which represent the combination of the 14 Bravais lattice types with the three dimensional symmetry elements. The structure of a crystal can be thought of as a draping of the ions or atoms of the compound within the geometry and symmetry indicated by the space group designation. The locations of the atoms or ions are given as fractional atomic coordinates within the unit cell parameters. The space group Pm3m has the following fractional atomic coordinates:
______________________________________    A atom = 0, 0, 0    B atom = 0.5, 0.5, 0.5    Oxygens           = 0.5, 0.5, 0           = 0.5, 0, 0.5           = 0, 0.5, 0.5______________________________________
The categorization of a particular crystalline material into a particular crystal system and space group is limited by the resolution of the diffractometer or camera used. Such materials are sometimes described in more exact terms as having a distortion from or substantial resemblance to the geometric model of a particular crystal system and space group. On the other hand, the phosphor of the invention can be referred to simply as having a cubic perovskite structure and Pm3m space group, since within the resolution limits of high resolution X-ray powder diffraction using Cu.sub.α1 irradiation, the phosphor of the invention does not depart from the geometric model. (The high resolution X-ray powder diffraction technique utilized was Gunier-DeWolfe utilizing standard irradiation inclusive of Cu.sub.α1 (wavelength=1.54051 Å).) Minute variances from the atomic positions indicated by cubic perovskite structure and Pm3m space group, could exist; but such differences are too small to be expressed as additional or split lines in the high resolution X-ray powder diffraction pattern. It is expected that other embodiments of the phosphor of the invention will also have this same cubic Perovskite structure and Pm3m space group, within the same resolution limits; however, even if such embodiments showed a deformation, those phosphors would still be classified as having a substantially cubic Perovskite structure and Pm3m space group.
The phosphor of the invention includes oxygen and a combination of species characterized by the relationship:
(Ba.sub.1-q M.sub.q)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e):yT    (formula I)
The same designations appearing elsewhere herein have the same meanings unless specifically stated to the contrary. Grouped species, for example the species defined by M, are to be understood as inclusive of combinations of species in that group. M is thus Ca or Sr or a combination of the two. Ca and Sr act much like "contaminants" in the phosphor of the invention, that is, Ca and Sr do not appear to provide an advantage when present; but, in relatively low concentrations, do not reduce the magnitude of luminescence. The concentration or mole fraction of M, the value of q, is from 0 to 0.15. Preferred ranges for Ca and Sr differ. This is discussed below in greater detail.
Limits on mole fractions expressed herein for the various atoms of the phosphor, do not represent useful ranges for the preparation of crystalline materials, nor even useful ranges for the preparation of materials which are capable of exhibiting luminescence under laboratory conditions. The limits expressed herein instead represent ranges for the preparation of phosphors that exhibit sufficient prompt luminescence, to be useful in practical phosphor screens, such as intensifying screens and scintillators. Many materials exhibit luminescence that is measurable, but is at to low a level for use in practical articles or is present only at very low temperatures.
Formula I can be rewritten substituting in Ca and Sr:
(Ba.sub.1-a-b Ca.sub.a Sr.sub.b)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e):yT (formula II)
In formulas I and II, the mole fractions of Ca and Sr are subtracted from the mole fraction of Ba. On the other hand, the mole fraction of the other alkaline earth metal in the formulas, Mg, is subtracted from the mole fraction of hafnium. This is believed to be an accurate representation of the phosphor. It has been determined with reasonable certainty that calcium and strontium substitute into the crystal lattice at barium sites, whereas magnesium substitutes at hafnium sites. This effect is believed to be predominantly a question of the size of the Mg ion. (Hafnium sites are also shared by zirconium. Hf and Zr are very similar in size and it is well known that Zr substitutes into Hf lattice sites in many materials.) The claimed invention is not limited by explanations or theories presented herein. Thus, for example, in what is considered the unlikely event that the above explanation is incorrect and Mg substitutes into the Ba site rather than the Hf--Zr site; the above formulas although cumbersome are still valid, and the scope of the claims is unchanged.
The value of e, the mole fraction of Mg, is from 0 to 0.10. A preferred range for e is from 0 to 0.05. The value of z, the mole fraction of Zr, is from 0 to 1 or more preferably from 0 to 0.75. It is preferred, from the viewpoint of economical starting materials, to have z in the range of from 1×10-5 to 1.
It is currently preferred that the phosphor of the invention be prepared from precursors fired in the presence of a particular flux or addenda. The flux has precursors containing an alkali metal or mixture of alkali metals or a percursor containing germanium or percursors for both alkali metal or metals and germanium. The flux reduces the temperature at which precursor materials must be fired to prepare the phosphor of the invention by as much as 1000° C. This is important practical advantage.
The phosphor produced using such flux retains a portion of alkali metal or metals and/or germanium from the flux. It is hypothesized that the alkali metal or metals and/or germanium act as inert components in the phosphor. As previously noted, the scope of the claimed invention is not limited by any such explanation or theory presented herein. Taking into account the flux materials, formula II can be rewritten:
(Ba.sub.1-a-b Ca.sub.a Sr.sub.b)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e).jQ:yT (formula III)
Q is one or more alkali metals or germanium or the combination of one or more alkali metals and germanium. The value of j is from 1×10-6 to 0.05.
It is preferred that the alkali metal is lithium and it is more preferred that Q is a combination of Li and Ge. Formula III can be rewritten to include Li and Ge:
(Ba.sub.1-a-b Ca.sub.a Sr.sub.b)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e).wLi.xGe:yT (formula IV)
The value of w, is from 0 to 0.05, preferably from 1×10-6 to 0.05, and more preferably from 1×10-6 to 0.025. The value of x is from 0 to 1.5×10-3, or preferably from 1×10-6 to 1×10-3, and more preferably from 1×10-4 to 7×10-4.
In formulas I-IV, T represents one or more of the activators: Cu, Eu, Dy, Sm, Ho, Er, and Tm. The Examples demonstrate activation provided by these species. The value of y, the mole fraction of activator, is from 1×10-6 to 0.02. A preferred range for y is from 2×10-4 to 0.02. Preferred activators are Cu, Dy, Sm, Ho, and Er and combinations thereof. More preferred activators are Dy, Sm, Ho, and Er and combinations thereof. In contrast, Comparative Examples 60-63 demonstrate that some other lanthanides provide little or no activation.
Referring now to FIG. 1, the phosphor screen 10 of the invention, in particular embodiments, is a radiographic phosphor screen (sometimes also referred to as a radiographic panel) having a support 12 and a luminescent layer 14 overlaying the support 12. An overcoat layer 16, although not required, is commonly located over the luminescent layer 14 for humidity and wear protection.
The luminescent layer includes the composite phosphor in the form of a polycrystalline mass. Typically, a mass of individual particles are distributed in a binder, which gives the mass structural coherence and retains the mass on the support. The size and shape of the phosphor particles are determined, in the same manner as other phosphors, by requirements of a particular use and factors such as manufacturing constraints. Convenient parameters for a phosphor particulate useful in radiographic screens are a median particle size of from 1 to 40 micrometers.
Useful binders are those conventionally employed in the art. Binders are generally chosen from a wide variety of known organic polymers which are transparent to x-rays, stimulating light (for storage screens), and emitted light. Binders commonly employed in the art include sodium o-sulfobenzaldehyde acetal of poly(vinyl alcohol); chlorosulfonated poly(ethylene); a mixture of macromolecular bisphenol poly(carbonates) and copolymers comprising bisphenol carbonates and poly(alkylene oxides); aqueous ethanol soluble nylons; poly(alkyl acrylates and methacrylates) and copolymers of poly(alkyl acrylates and methacrylates with acrylic and methacrylic acid); poly(vinyl butyral); and poly(urethane) elastomers. These and other useful binders are disclosed in U.S. Pat. Nos. 2,502,529; 2,887,379; 3,617,285; 3,300,310; 3,300,311; and 3,743,833; and in Research Disclosure, Vol. 154, February 1977, Item 15444, and Vol. 182, June 1979. Research Disclosure is published by Kenneth Mason Publications, Ltd., Emsworth, Hampshire P010 7DD, England. Particularly preferred binders are poly(urethanes), such as those commercially available under the trademark Estane from Goodrich Chemical Co., the trademark Permuthane from the Permuthane Division of ICI, and the trademark Cargill from Cargill, Inc.
Any conventional ratio of phosphor to binder can be employed. Generally thinner phosphor layers and sharper images are realized when a high weight ratio of phosphor to binder is employed. Preferred phosphor to binder ratios are in the range of from about 7:1 to 25:1 for screen constructions intended to withstand commercial exposure repetitions without loss of structural integrity. For limited or single exposure applications, any minimal amount of binder consistent with structural integrity is satisfactory.
For the highest attainable speeds a white support, such as a titania or barium sulfate loaded or coated support can be employed. Particular reflective supports which offer a balance of speed and sharpness are those containing reflective microlenslets, such as are disclosed in U.S. Pat. No. 4,912,333 to Roberts, et al. In those instances in which it is desired to reduce the effective thickness of a phosphor layer below its actual thickness the phosphor layer is modified to impart a small, but significant degree of light absorption. If the binder is chosen to exhibit the desired degree of light absorption, then no other ingredient of the phosphor layer is required to perform the light attenuation function. It is specifically noted that the less structurally complex chromophores for ultraviolet absorption particularly lend themselves to incorporation in polymers. A separate absorber can be incorporated in the phosphor layer to reduce its effective thickness. The absorber can be a dye or pigment capable of absorbing light within a desired spectrum. Black dyes and pigments such as carbon black are, of course, generally useful with phosphors, because of their broad absorption spectra. With storage screens, it is preferable to include a dye or pigment which absorbs some of the stimulating radiation, generally provided by a laser; but mostly reflects emitted light. U.S. Pat. No. 4,491,736, to Teraoka, teaches the use of such materials in storage screens.
Apart from the phosphor layers and the assembly features described above, the screen can be of any conventional construction. Screens typically have one or more flexible or rigid support layers. Flexible layers are most commonly polymeric. The most common polymeric supports are films of high dimensional integrity, such as poly(ethylene terephthalate) film supports. In a nonflexible screen, support is provided by one or more polymeric layers and by a rigid plate of aluminum or the like.
Metal layers, such as aluminum, enhance reflection. Paper supports, though less common than film supports, are known and can be used for specific applications. Dyes and pigments are commonly loaded into supports to enhance absorption or reflection of light. Air can be trapped in supports to reflect ultraviolet and visible light. Supports and the subbing layers used to improve coating adhesion can be chosen from among those employed for silver halide photographic and radiographic elements, as illustrated by Research Disclosure, Vol. 176, December 1978, Item 17643, Section XVII, and Research Disclosure, Vol. 184, August 1979, Item 18431, Section I.
The overcoat layer comprises a binder chosen using the criteria described above for the binder in the luminescent layer. The overcoat binder can be the same binder as in the luminescent layer or different and can also be chosen from polymers useful for supports. Polymers conventionally employed for film supports can be used in the overcoat layer. For example, cellulose acetate is an overcoat commonly used with the poly(urethane) binders. Overcoat polymers are often also used to seal the edges of the phosphor layer. A suitable overcoat is disclosed in U.S. Pat. No. 5,401,971.
While anticurl layers are not required for the screens, they are generally preferred for inclusion. The function of the anticurl layer is to balance the forces exerted by the layers coated on the opposite major surface of a support which, if left unchecked, could cause the support to assume a non-planar configuration, that is, to curl or roll up on itself. Materials forming the anticurl layers can be chosen from among those identified above for use as binders and overcoats. Generally an anticurl layer is formed of the same polymer as the overcoat on the opposite side of the support.
Any one or combination of conventional screen features compatible with the features described herein can, of course, be employed. Conventional storage screen constructions are disclosed in U.S. Pat. No. 4,380,702 to Takahashi et al, the disclosure of which is hereby incorporated by reference. Conventional intensifying screen constructions are disclosed in Research Disclosure, Vol. 184, August 1979, Item 18431, hereby incorporated herein by reference.
The radiographic screens are formed by conventional coating techniques. Phosphor powder and addenda are mixed with a solution of a resin binder material and coated by means such as blade coating onto a substrate. U.S. Pat. No. 4,505,989, to Umemoto et al, the disclosure of which is hereby incorporated herein by reference, describes suitable techniques known in the art for preparing a radiographic screen..
The phosphor screen of the invention, in some embodiments, is what can be referred to as a "large crystal device". In contrast to a radiographic screen, the mass of small phosphor particles is replaced by a relatively small number of large crystals or even a single very large crystal. The support and binder are replaced by a mechanical structure that holds the crystal or crystals in a desired orientation. The large crystal device can also include a light responsive element, such as an array of photodiodes. The crystals are arranged so that the longest dimension of each crystal is aligned with the direction of incident radiation. This maximizes the thickness, and thus the radiation stopping power, of the phosphor "layer". The crystals together define a surface that faces the direction or directions from which incident radiation is to be received. In many applications, such as computed tomography, it is desirable to capture only radiation incident from a single direction, the direction of the collimated beam used to image the subject matter. In these applications, the crystals define a plane. In some other applications, such as high energy physics detectors, it is desirable to capture radiation emitted in many directions from a particular location and the crystals therefore define a complex curved surface centered upon the site of origin of events to be detected. These multidirectional detectors are otherwise substantially similar to the unidirectional detectors previously described.
FIG. 2 is a partially schematic diagram of another configuration of the phosphor screen 10 of the invention: a unidirectional large crystal device. A series of large crystals 22 of the phosphor of the invention are arranged in parallel orientation, with respective crystal faces all aligned in the same directions. At the rear end face 24 of each crystal 22 is a photodetector 26 that is disposed to receive radiation emitted by the respective crystal 22 secondary to absorption of x-rays or other primary high energy radiation and transmit a signal through a signal line 28. The front end faces 30 are each substantially perpendicular to the detected radiation and each define a light path 32 extending outward from the respective front end face. Extending forward from the front end faces 30 of the crystals 22 is a collimator 34 of a material such as lead. The collimator has an array of collimator elements 36 bordering each light path 32 on two or more sides (only two sides are shown). The collimator elements 36 absorb incident radiation that is not substantially parallel to a respective crystal 22. The collimator can function as a support for the phosphor crystals and photodetectors; however, it is preferred that a separate support 38 hold the crystals 22, collimator 34, and photodetectors 26 in their relative orientations. The support 38 can take a variety of shapes and be made from a variety of materials. A primary consideration is ordinarily the ability of the support to maintain the various components in stable relative relation during use.
It is expected that relatively large crystals of the phosphor of the invention can be prepared by the following method. A physical mixture would be first prepared by mixing: from about 0.15 to about 0.45 mole fraction BaCO3 or BaO; from about 0.25 to about 0.60 mole fraction BaF2, from about 0.15 to about 0.40 mole fraction B2 O3, and MO2 (M is Hf or Zr or both) in the range of from about 0.5 to about 10 wt % relative to the total weight of reactants. Outside these ranges, the yield of crystals is expected to be low, or non-existent. Higher concentrations of BaF2 would be expected to corrode the platinum crucible, making preparation impractical. Higher concentrations of B2 O3 would be expected to cause the formation of large crystals of BaM(BO3)2, where M is Zr, Hf, or both. It is expected that in a preferred embodiment of the invention, the physical mixture would also include GeO2 at about the same concentration as the MO2 to improve the size and quality of phosphor crystals produced. The physical mixture would be heated to a temperature of from about 1150° C. to about 1550° C. for from 2 to about 22 hours. The resulting product would then be cooled at a rate of from about 0.1° C./hr to about 25° C./hr. Slower cooling is expected to yield larger crystals of higher optical purity. Larger crystals would also be expected with the use of accelerated crucible rotation as described in Scheel, J. Crystal Growth, Vol. 8, pages 304-306 (1971). A perferred rotation program is 0-60-0 rpm acceleration/decceleration over a period of 60 sec.
The following Examples and Comparative Examples are presented to further illustrate and elucidate some preferred modes of practice of the invention. Unless otherwise indicated, all starting materials were commercially obtained.
The relative luminescence response of the phosphor powder was measured by packing the phosphor powder into aluminum planchettes (2 mm high×24 mm diameter) at a coverage of about 1 g/cm2 and exposing the sample to filtered X-radiation. The X-ray source was a tungsten target tube in a XRD 6 generator operating at 70 kVp and 10 mA. The filtration consisted of 0.5 mm copper and 1.0 mm aluminum. The luminescence response was measured at a temperature of approximately 300° K, using an IP-28 photomultiplier tube at 500 V bias. The voltage from the photomultiplier was measured with a Keithley high impedance electrometer and is proportional to the total light output of the sample.
Emission spectra were obtained with an instrument consisting of an Instruments S. A. Model HR 320 grating spectrometer coupled with a Princeton Applied Research Model 1421 intensified linear diode array detector. The data acquisition and processing was controlled by a Princeton Research Model 1460 OMA III optical multichannel analyzer. Spectra were corrected for the spectral response of the detector-spectrograph combination. Samples were placed in planchettes as described above and irradiated with X-rays from a tungsten target tube operated at 70 kVp and 10 mA. Spectra were repeated with and without the filtration described above. Colors of the emissions, reported herein, are based upon the perception of the experimenter without additional colorimetric analysis.
The stoichiometry given in the table headings is nominal and is only meant to indicate intentional substitution. No conclusions regarding lattice vacancies/interstitials or oxygen content are implied.
COMPARATIVE EXAMPLE 1 BaHfO3
The phosphor was prepared by the combination of one mole of HfO2 (0.26 mole % Zr4+) and 0.5 mole portions of BaCO3 (99.99%) and BaF2 (99.9% or better purity) in an agate mortar with acetone as a grinding aid. The ground powder was placed in an alumina crucible and fired in air for 8 hours in a box furnace at 1100° C. Following recovery and regrinding of the charge it was refired in the same furnace at 1280° C. for eight hours. The X-ray powder diffraction pattern of the charge showed the cubic perovskite BaHfO3 as the major phase, with a small amount of hafnia as impurity.
The sample showed an emission spectrum dominated by an ultraviolet peak centered at approximately 315 nm, and a very weak peak centered at 410 nm which was attributed to titanium impurities. The relative prompt emission response of this material was set to equal 100. Values for prompt emission in other examples and comparative examples are relative to that value.
Preparation of BaHf(C2 O4)3.nH2 O: Solution A was prepared from 61.428 g (0.15 mole) of HfOCl2.8H2 O (RGS, 0.26 mol % Zr) in 500 ml MeOH (anhydrous reagent grade). Solution B was prepared from 52.478 g (0.1575 mole) BaBr2.2H2 O (reagent grade) in 400 ml of methanol. Solution C was prepared from 198.545 g (0.1575 mole) of H2 C2 O4.2H2 O (reagent grade) in 500 ml of methanol. Solution B was poured into solution A followed by vacuum filtration. Solution C was then added slowly (30 minutes) to the combined A+B solution with stirring. The precipitate was aged at 60° C. for 1 hr. The material was collected by vacuum filtration and air-dried for two days. The dried material was washed twice with 600 ml of methanol and air-dried.
For the preparation of the undoped compound of Comparative Example 2, the precursor described above was decomposed in air in a box furnace at 1250° C. The X-ray powder diffraction pattern of the final product showed only the cubic BaHfO3 pattern. A 3.636 g (0.01 mole) portion of this fired material was mixed with following flux components: 0.275 g (0.0025 mole) Li2 SO4 (99.7%), 0.0259 g (0.001 mole) LiF (99.9% or better purity), 0.0523 g (0.0005 mole) GeO2 (99.999%), in an agate mortar and pestle. Acetone was used as a grinding aid. The resulting mixture was placed in an alumina crucible and covered with an alumina lid and placed in the center zone of a 3 inch diameter alumina tube in a horizontal tube furnace. A high purity CO2 atmosphere (1.5 liter/min) was used throughout the process. After purging, the sample was heated to 1300° C. in 3 hours, held for 6 hours and then cooled over 6 hours to room temperature. The relative prompt emission response is indicated in Table 1.
EXAMPLES 3-9 BaHfO3 :Dy3+
Examples 3-9 were prepared in substantially the same manner and concurrently with Comparative Example 2, with the exception that, for each of Examples 3-9, an appropriate aliquot of a 0.1M or 1.0M Dy(NO3)3 (99.9% or better purity) aqueous solution was added to a 3.636 g of the BaHfO3 source and the flux mixture described above. The materials were ground in an agate mortar and pestle with acetone. The dried materials were then processed under CO2 as described above. The X-ray powder diffraction pattern of the final materials showed BaHfO3 as the major phase. The x-ray excited spectrum was obtained for Example 5 and is reported in Table 7. The Dy3+ emission spectrum showed three intense peaks at approximately 480, 580 and 670 nm. The relative prompt emission responses of Examples 3-9 are shown in Table 1.
TABLE 1______________________________________BaHfO.sub.3:y Dy.sup.3+Example or ComparativeExample         Value of y                    Relative response______________________________________Comparative Example 2           0.0       77Example 3       0.0001   900Example 4       0.0002   917Example 5       0.0005   1007Example 6       0.001    904Example 7       0.005    921Example 8       0.01     850Example 9       0.02     527______________________________________
EXAMPLE 10 BaHfO3 :0.0005Dy3+
A BaHfO3 source was prepared from the combination of HfO2 (RGS; 0.249 mol % Zr) and BaCO3 (99.99%) in an agate mortar and pestle with acetone as a grinding aid. The ground mixture was fired to 1250° C. as described above. The charge was then reground with an aliquot of 0.1M Dy(NO3)3 aqueous solution (0.05 mole %), 100 mole % Li2 SO4 (99.7%), 18.75 mole % GeO2 (99.999%), and 10 mole % Li2 CO3 (99.997%) in acetone. The air-dried sample was then heated at 1300° C. in 1.5 liters/m CO2. The relative response of the phosphor was 1487. The relative response of a commercial Gd2 O2 S:Tb3+ screen (Lanex Regular™ marketed by Eastman Kodak Company of Rochester, N.Y.) under identical conditions is 4197. (The sensitivity of the IP-28 photomultiplier used for the major Dy3+ emission peaks was significantly lower than for the major 545 nm emission in the Lanex Regular screen.)
EXAMPLE 11 BaHfO3 :0.0005Sm3+
A BaHfO3 source was prepared from the combination of HfO2 (RGS; 0.249 mol % Zr) and BaCO3 (99.99%) in an agate mortar and pestle with acetone as a grinding aid. The ground mixture was fired to 1250° C. as described above. The charge was then reground with an aliquot of 0.1M Sm(NO3)3 aqueous solution (0.05 mole %), 100 mole % Li2 SO4 (99.7%), 3.0 mole % GeO2 (99.999%), and 10 mole % Li2 CO3 (99.997%) in acetone. The air-dried sample was then heated at 1300° C. in 1.5 liters/min CO2. The emission spectrum was obtained and is reported in Table 7. The emission spectrum exhibited peaks at 565, 600, 650, and 700. The relative response of the phosphor was 206. (The sensitivity of the IP-28 photo-multiplier was not linear throughout the visible region, and was particularly weak in the red region of the spectrum where the Sm3+ emissions lie.)
EXAMPLES 12-24 BaHf1-z Zrz O3 :0.0015Sm3+
A BaHf1-z Zrz O3 source was prepared by grinding the appropriate amounts of either HfO2 (optical grade; 0.0087 mole % Zr or RGS; 0.249 mol % Zr) or ZrO2 (RGS: 0.004 mole % Hf) with BaCO3 (99.99%) in an agate mortar and pestle with acetone. After firing to 1250° C., the sources were ground with the flux mixture described in Comparative Example 2 and an aliquot of 0.1M Sm(NO3)3 aqueous solution, and fired to 1300° C. in CO2 as described above. The relative responses are shown below in Table 2.
The examples show efficient activation of the BaHfO3 host by Sm3+ from optical grade levels of Zr4+ incorporation to complete substitution (BaZrO3). A comparison of the integrated intensity from 515-700 nm in the emission spectra (50 kVp, filtered) showed that the phosphor of Example 16 gives approximately 82 percent the light output of a commercial Lanex Regular screen, marketed by Eastman Kodak Company of Rochester, N.Y.
TABLE 2______________________________________BaHf.sub.1-z Zr.sub.z O.sub.3 :0.0015Sm.sup.3+Example      Value of z                  Relative response______________________________________12           0.000087  29413           0.0002    28014           0.001     32015           0.00249   33016           0.005     29817           0.01      30018           0.025     32819           0.05      32020           0.10      34221           0.25      31022           0.50      27423           0.75      22624           1.00      172______________________________________
EXAMPLE 25 BaHfO3 :0.0005Ho3+
The sample was prepared in substantially the same manner as in Example 10, with the exception that a 0.1M Ho(NO3)3 (99.9% or better purity) solution was used. The emission spectrum was obtained and is reported in Table 7. The relative response of the phosphor was 1045.
EXAMPLES 26-36 Ba1-b Srb HfO3 :0.001Ho3+
Samples were prepared from HfO2 (RGS, 0.249 mole % Zr), BaCO3 (99.99%), and SrCO3 (99.999%). The powders were ground and fired as above at 1250° C. The fired charges were then ground with an aliquot of a 0.1M Ho(NO3)3 aqueous solution (99.9% or better purity) followed by the 1300° C. firing under CO2 with the Li2 SO4 /LiF/GeO2 flux mixture described in Comparative Example 2. The relative responses are shown below in Table 3:
TABLE 3______________________________________Ba.sub.1-b Sr.sub.b HfO.sub.3 :0.001Ho.sup.3+Example       Value of b                  Relative response______________________________________26            0        115727            0        135728            0.0005   118129            0.0025   113530            0.01     111731            0.025    112932            0.05     139333            0.05     135734            0.075    105935            0.10     115336            0.15     1224______________________________________
EXAMPLES 37-42 Ba1-a Caa HfO3 :0.001Ho3+
Samples were prepared as in Examples 26-36, with the substitution of CaCO3 (phosphor grade) for SrCO3. The relative responses are shown below in Table 4.
TABLE 4______________________________________Ba.sub.1-a Ca.sub.a HfO.sub.3 :0.001Ho.sup.3+Example       Value of a                  Relative response______________________________________37            0        121538            0.0005   124239            0.0025   123140            0.01     117541            0.025    127642            0.05     1034______________________________________
EXAMPLES 43-48 BaHf1-e Mge O3 :0.001Ho3+
Samples were prepared as above in Examples 26-36 with Mg(CH3 CO2)2 (reagent) used instead of SrCO3 and substitution at Hf4+ rather than Ba2+. The relative responses are shown below in Table 5.
TABLE 5______________________________________BaHf.sub.1-e Mg.sub.e O.sub.3 :0.001Ho.sup.3+Example       Value of e                  Relative response______________________________________43            0        147844            0.0005   119845            0.0025   105846            0.01     102547            0.025    120748            0.05     1458______________________________________
EXAMPLE 49 Intensifying Screen Comprised of BaHfO3 :0.001Ho3+
A 50 g charge were prepared from an equimolar mixture of HfO2 (RGS, 0.249 mole % Zr) and BaCO3 (99.99%). The powders were ground together with acetone in an agate mortar. The dried charge was fired in air in a box furnace at 1250° C. The x-ray powder diffraction of this material showed only the BaHfO3 perovskite pattern. The fired charge was then ground with 1.35 ml of 0.1M Ho(NO3)3 aqueous solution and 100 mole % Li2 SO4 (99.7%), 18.75 mole % GeO2 (99.999%), and 10 mole % Li2 CO3 (99.997%) in acetone. The dried mixture was then fired for 6 hours at 1300° C. in a 1.5 liter/min CO2 flow. The cooled ingot was washed four times with 500 ml of hot distilled water and then collected by vacuum filtration. The dried powder was sieved through a 45 micrometer metal sieve. The relative response of the material was 1778.
35 grams of the above powder were added to 12.82 grams of a 13% Permuthane™ solution in a methylene chloride and methanol mixture to produce a dispersion with 21 parts of phosphor to 1 part of binder by weight. The mixture was blended for 20 minutes at 2000 rpm with a Dispermat. The dispersion was coated on white ESTAR™ at 93 g/ft2. The relative response of the coating was 1497. A comparison of the integrated intensity from 515-585 nm in the emission spectra (50 kVp, filtered) shows that the screen gives approximately 79 percent the light output of a commercial Lanex Regular screen.
EXAMPLE 50 BaHfO3 :0.0005Er3+
The sample was prepared in substantially the same manner as Example 10, with the exception that a 0.1M Er(NO3)3 (99.9% or better purity) solution was used. The x-ray excited spectrum is reported in Table 7. The relative response of the phosphor was 907.
EXAMPLE 51 BaHfO3 :0.0005Tm3+
The sample charge was prepared as in was Example 10, with the exceptions that a 0.05M Tm(NO3)3 (99.9% or better purity) solution was used, and the flux mixture was composed of 100 mole % Li2 SO4 (99.7%) and 10% Li2 CO3 (99.997%). The x-ray excited spectrum is reported in Table 7. The relative response of the phosphor was 263.
EXAMPLE 52 BaHfO3 :0.0005Eu3+
The sample was prepared by grinding with acetone the following powders: HfO2 (RGS, 0.0249 mole % Zr4+), BaCO3 (99.99%), EuCO3, 100 mole % Li2 SO4 (99.7%) and 10 mole % Li2 CO3 (99.997%). The sample was then heated to 1300° C. for 6 hours under 1.5 liter/min CO2. The recovered sample showed red luminescence which indicated the presence of Eu3+. The emission spectrum was obtained and is reported in Table 7. The relative response of the sample was 42.
The sample from Example 52 was refired at 850° C. for 6 hours in 4% H2 argon atmosphere flowing at 1.5 liter/min. The emission spectrum was obtained and is reported in Table 7. The spectrum of the sample showed a broad green emission centered at approximately 460 nm, in addition to a spike approximately 600 nm from residual Eu3+. The recovered phosphor gave a relative response of 298.
COMPARATIVE EXAMPLE 54 BaHfO3
An undoped BaHfO3 source was prepared at 1250° C. as in Example 10. The relative response is reported in Table 6.
EXAMPLES 55-57 BaHfO3 :0.001Cu
Portions of the undoped BaHfO3 source prepared in Comparative Example 54 were ground with appropriate amounts of CuBr (reagent) and 10 mole % Li2 SO4 (99.7%) and 10 mole % LiF ((99.9% or better purity)). The dried powders was fired at 1350° C. in CO2 as described above. The copper-doped compositions exhibited green luminescence. It is believed that the emitting species is Cu+. The relative responses are shown below in Table 6 and the emission data for Example 55 in Table 7.
TABLE 6______________________________________BaHfO.sub.3:y Cu.sup.+Example or Comparative     RelativeExample           Value of y                      response______________________________________Comparative Example 54             0         40Example 55        0.0005   466Example 56        0.0015   518Example 57        0.0045   324______________________________________
EXAMPLE 58 BaHfO3 :0.0005Dy.0.001Ho
The sample was prepared in substantially the same manner as in Examples 3-8. HfO2 (RGS, 0.249 mole % Zr) and BaCO3 (99.99%), and Ce(NO3)3.6H2 O (99.9% or better purity) were admixed. The undoped precursor mixture was fired as above at 1250° C., and then ground with an aliquot of 0.1M Ho(NO3)3 (99.9% or better purity), 0.1M Dy(NO3)3 (99.9% or better purity), and the Li2 SO4 /LiF/GeO2 flux mixture. The mixture was fired at 1300° C. under CO2. After washing, the relative response was 1117.
EXAMPLE 59 BaHfO3 :0.002Sm.0.003Ho
The sample was prepared in substantially the same manner as in Example 58, by the combination of HfO2 (RGS, 0.249 mole % Zr), BaCO3 (99.99%), Ho(NO3)3.6H2 O (99.9% or better purity), Sm(NO3)3.6H2 O (99.9% or better purity) and the Li2 SO4 /LiF/GeO2 flux mixture. The ground mixture was fired at 1300° C. under CO2. After washing, the relative response was 578.
COMPARATIVE EXAMPLE 60 BaHfO3 :0.0005Pr
The sample was prepared in substantially the same manner as in Example 10 with the exception that Pr(NO3)3 (99.9% or better purity), was used in place of Dy(NO3)3 and GeO2 was not added. The relative response of the sample was 32.
COMPARATIVE EXAMPLE 61 BaHfO3 :0.0005Tb
The sample was prepared in substantially the same manner as in Comparative Example 60, except Tb(NO3)3 (99.9% or better purity) was used in place of Pr(NO3)3. The relative response of the sample was 44.
COMPARATIVE EXAMPLE 62 BaHfO3 :0.0005Gd
The sample was prepared in substantially the same manner as in Comparative Example 60, except Gd(NO3)3 (99.9% or better purity) was used in place of Pr(NO3)3. The relative response of the sample was 78. More than 90 percent of the luminescence intensity was explainable as being due to an impurity level Ti4+ emission.
COMPARATIVE EXAMPLE 63 BaHfO3 :0.0005Nd
The sample was prepared in substantially the same manner as in Comparative Example 60, except Nd(NO3)3 (99.9% or better purity) was used in place of Pr(NO3)3 and 50 mole percent rather than 100 mole percent Li2 SO4 was used. The relative response of the sample was too weak to measure.
Results comparing the different activators in the same host are collected in Table 7. The relative responses listed are at the same activator concentration, however, this concentration is not optimal for all the listed phosphors. The phosphors of the invention provide surprisingly good prompt emissions that are surprisingly different from the comparable europium activated phosphors.
TABLE 7______________________________________BaHfO.sub.3: 0.0005TExample  Activator             Peak emission-color                            Relative response______________________________________Example 5    Dy.sup.3+             480, 580, 670-yellow                            1007Example 11    Sm.sup.3+             565, 600, 650, 700-                            206             reddish-orangeExample 25    Ho.sup.3+             550 (broad)-yellowish                            1045             greenExample 50    Er.sup.3+             530, 555 (doublet)-                            907             yellowish-green______________________________________Example 51    Tm.sup.3+             365, 450-500 (doublet),                            263             655-greenExample 52    Eu.sup.3+             600-red         42Example 53    Eu.sup.2+             460 (broad)-blue-green                            298Example 55    Cu       550 (broad)-green                            466______________________________________
While specific embodiments of the invention have been shown and described herein for purposes of illustration, the protection afforded by any patent which may issue upon this application is not strictly limited to a disclosed embodiment; but rather extends to all modifications and arrangements which fall fairly within the scope of the claims which are appended hereto:
1. A radiographic phosphor screen comprising a support and, coated on the support, at least one layer forming a luminescent portion and an overcoat layer, said luminescent portion and overcoat layer including a binder that is transparent to X-radiation and emitted light and said luminescent portion including phosphor particles in a weight ratio of phosphor particles to binder of 7:1 to 25:1, said phosphor comprising oxygen and a combination of species characterized by the relationship:
wherein
M is selected from the group consisting of Ca and Sr and combinations thereof;
T is Cu;
q is from 0 to 0.15;
z is from 0 to 1;
e is from 0 to 0.10;
z+e is from 0 to 1;
y is from 1×10-6 to 0.02.
2. The phosphor radiographic screen of claim 1 wherein y is from 2×10-4 to 0.02.
3. The phosphor radiographic screen of claim 1 wherein said phosphor is x-ray luminescent at a temperature of 300° K.
4. The phosphor radiographic screen of claim 1 wherein said phosphor comprises oxygen and a combination of species characterized by the relationship:
(Ba.sub.1-a-b Ca.sub.a Sr.sub.b)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e):yT
a is from 0 to 0.05;
b is from 0 to 0.15;
a+b is from 0 to 0.15;
z is from 1×10-5 to 1;
z+e is from 1×10-5 to 1;
5. The phosphor radiographic screen of claim 4 wherein z is from 0 to 0.75.
6. The radiographic phosphor screen of claim 1 wherein said phosphor consists essentially of oxygen and a combination of species characterized by the relationship:
(Ba.sub.1-a-b Ca.sub.a Sr.sub.b)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e).wLi.xGe:yT
w is from 0 to 0.05;
x is from 0 to 1.5×10-3 ;
w+x is from 1×10-6 to 0.05; and
7. The phosphor radiographic screen of claim 6 wherein w is from 1×10-6 to 0.05.
8. The radiographic phosphor screen of claim 6 wherein w is from 1×10-6 to 0.025.
9. The radiographic phosphor screen of claim 6 wherein x is from 1×10-4 to 7×10-4.
10. The radiographic phosphor screen of claim 1 wherein said phosphor is crystallized as the cubic Perovskite structure (Pm3m space group) as determined by X-ray powder diffraction using Cu.sub.α1 irradiation.
11. The radiographic phosphor screen of claim 1 further characterized as a radiographic intensifying screen.
12. A phosphor comprising oxygen and a combination of species characterized by the relationship:
13. The phosphor of claim 12 wherein y is from 2×10-4 to 0.02.
14. The phosphor of claim 12 wherein said phosphor comprises oxygen and a combination of species characterized by the relationship:
15. The phosphor of claim 14 wherein z is from 2×10-4 to 1.
16. The phosphor of claim 14 wherein z is from 2×10-4 to 0.75.
17. The phosphor of claim 12 wherein said phosphor is crystallized as the cubic Perovskite structure (Pm3m space group) as determined by X-ray powder diffraction using Cu.sub.α1 irradiation.
(Ba.sub.1-a-b Ca.sub.a Sr.sub.b)(Hf.sub.1-z-e Zr.sub.z Mg.sub.e).wQ:yT
Q is at least one of Li and K;
w is from 1×10-6 to 5×10-2 ; and
19. A phosphor consisting essentially of oxygen and a combination of species characterized by the relationship:
20. The phosphor of claim 19 wherein w is from 1×10-6 to 0.05.
21. The phosphor of claim 19 wherein w is from 1×10-6 to 0.025.
22. The phosphor of claim 19 whereto x is from 1×10-4 to 7×10-4.
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