Electromagnetic window

Abstract

A ceramic electromagnetic window made of Si.sub.3 N.sub.4 particles which are bonded together by a metal phosphate binder that is an AlPO.sub.4 binder, a ZrP.sub.2 O.sub.7 binder, or mixtures thereof, wherein the Si.sub.3 N.sub.4 particles comprise from 55 to 85 volume percent of the ceramic material of the electromagnetic window with the metal phosphate binder comprising the remainder. By substituting Si.sub.3 N.sub.4 whiskers for some of the Si.sub.3 N.sub.4 particles a discontinuous fiber composite ceramic electromagnetic window is produced. The electromagnetic window may be a simple shape such as a flat or slightly curved sheet or a more complex shape such as a conical or spherical radome.

Description

BACKGROUND OF THE INVENTION

Future classes of advanced tactile missiles will require new ceramic materials for electromagnetic windows or radomes to meet stringent requirements arising from greater speeds and longer flight times. Such a ceramic material must have a high thermal stability, a low and thermally stable dielectric constant, a low coefficient of thermal expansion, resistance to high thermal shock, and resistance to erosion by rain.

Radome materials currently used are slip cast fused silica (SCFS) and Pyroceram 9606.TM. (2MgO.2Al.sub.2 O.sub.3.5SiO.sub.2, cordierite). While SCFS has excellent dielectric properties for radomes, the relatively low strength and rain erosion resistance of this material limits future application. Pyroceram 9606.TM. is more rain erosion resistant than SCFS, but is not as dielectrically stable with temperature.

Development of future electromagnetic window or radome materials is directed both toward improvement of the mechanical properties of SCFS and identification of new candidate ceramic materials. For example, materials in the system Si.sub.3 N.sub.4 --BN--SiO.sub.2 (Nitroxyceram) have the potential of being nearly as good as SCFC dielectrically and at least as good if not better than Pyroceram 9606.TM. in erosion resistance. However, this material requires expensive processing techniques such as hot isostatic pressing.

It would be desirable therefore to provide new ceramic materials for electromagnetic windows or radomes which possess the desired physical properties but which are relatively inexpensive to produce.

SUMMARY OF THE INVENTION

Accordingly, an object of this invention is to provide radomes and other electromagnetic windows composed of new materials.

Another object of this invention is to provide radomes and other electromagnetic windows that are stronger and more resistant to rain erosion than presently used radomes.

A further object of this invention is to provide radomes and other electromagnetic windows having excellent dielectric properties.

Yet another object of this invention is to provide radomes and other electromagnetic windows having excellent thermal properties.

A still further object of this invention is to provide radomes and other electromagnetic windows having good particle impact resistances.

These and other objects of this invention are accomplished by providing an electromagnetic window (e.g., radome, etc.) made of ceramic material in which silicon nitride (Si.sub.3 N.sub.4) particles are bonded together by a metal phosphate binder that is an aluminum phosphate (AlPO.sub.4) binder, a zirconium phosphate (ZrP.sub.2 O.sub.7) binder, or mixtures thereof.

The electromagnetic window is formed by die pressing or cold isostatic pressing (CIP) a mixture of the starting ingredients to form a green body and then firing the green body at a suitable temperature to produce the product electromagnetic window.

In a variation of the invention, Si.sub.3 N.sub.4 whiskers are substituted for part of the Si.sub.3 N.sub.4 powder (particles) and the same process is used to produce a discontinuous fiber ceramic composite electromagnetic window.

BRIEF DESCRIPTION OF THE DRAWING

The FIGURE is a graph of the flexural strength of zirconium phosphate bonded silicon nitride as a function of binder content and firing temperature and is discussed in the experimental section.

DESCRIPTION OF THE PREFERRED EMBODIMENT

The electromagnetic windows of the present invention are made of ceramic materials made of silicon nitride (Si.sub.3 N.sub.4) particles which are bonded together by a suitable metal phosphate binder that is an aluminum orthophosphate (AlPO.sub.4) binder, a zirconium phosphate (ZrP.sub.2 O.sub.7) binder, or a mixture of these binders. The metal phosphate binder is produced from precursors which are mixed with the Si.sub.3 N.sub.4 particles, formed into a green body of the desired shape and size, and then fired at temperature that converts the precursors into the metal phosphate binder. The electromagnetic windows may have simple shapes such as flat or curved planes (or sheets) or more complex shapes such as conical or spherical radomes.

The metal phosphate binder is preferably an aluminum orthophosphate (AlPO.sub.4) binder, a zirconium phosphate (ZrP.sub.2 O.sub.7) binder or a mixture of these two binders in any proportion. These binders produce ceramic composites which have good dielectric properties, strength, water resistance, and high temperature performance. ZrP.sub.2 O.sub.7 binders are preferred because they produce ceramic composites with greater strength.

The metal phosphate binders can be produced from either of two types of precursors. First, the precursor may be metal phosphate hydrates which decompose during firing to produce the corresponding metal phosphate binder. Specifically, AlPO.sub.4 hydrates decompose to produce AlPO.sub.4 as a binder and ZrP.sub.2 O.sub.7 hydrates decompose to produce ZrP.sub.2 O.sub.7 as a binder. The second type of precursor comprises a mixture of orthophosphoric acid (H.sub.3 PO.sub.4) and a metal oxide that is Al.sub.2 O.sub.3, ZrO.sub.2, or mixtures thereof which react during firing to produce the corresponding AlPO.sub.4, ZrP.sub.2 O.sub.7, or mixtures thereof as a binder. Note that the particle size of the Al.sub.2 O.sub.3 powder is preferably less that 0.1 microns and more preferably about 0.05 microns to produce AlPO.sub.4. The Al.sub.2 O.sub.3 particle size is critical as demonstrated by 0.3 micron sized Al.sub.2 O.sub.3 particles which produce aluminum metaphosphate, (AlPO.sub.3).sub.3, at a firing temperature of 700.degree. C. and a mixture of Al(PO.sub.3).sub.3 and AlPO.sub.4 at 900.degree. C. Because Al(PO.sub.3).sub.3 decomposes into AIPO.sub.4 and P.sub.2 O.sub.5 gas, it produces ceramic materials with poor strengths.

The Si.sub.3 N.sub.4 particle size is not critical. Any Si.sub.3 N.sub.4 particles which are suitable for the production of ceramic materials can be used to produce the electromagnetic windows (e.g., radomes, etc.) of this invention.

In the first step of the process, a mixture of the precursors for the metal phosphate binder is prepared. For an AlPO.sub.4 binder a mixture of AlPO.sub.4 hydrates and water or a mixture of 0.05.mu. Al.sub.2 O.sub.3 particles and 85% H.sub.3 PO.sub.4 can be used. For a ZrP.sub.2 O.sub.7 binder a mixture of ZrP.sub.2 O.sub.7 hydrates and water or a mixture of ZrO.sub.2 particles and 85% H.sub.3 PO.sub.4 can be used. The Si.sub.3 N.sub.4 particles are then mixed into the precursor mixture in an amount that will produce a monolithic ceramic material with the desired volume percent of metal phosphate binder. Preferably the volume percent of metal phosphate (AlPO.sub.4, ZrP.sub.2 O.sub.7, or mixtures thereof) binder will be from 15 to 45, more preferably from 20 to 40, still more preferably from 25 to 35, and most preferably about 30volume percent of the metal phosphate bonded Si.sub.3 N.sub.4 monolithic ceramic material with the Si.sub.3 N.sub.4 comprising the remainder. In other words, the Si.sub.3 N.sub.4 particles comprise preferably from 55 to 85, more preferably from 60 to 80, still more preferably from 65 to 75, and most preferably about 70 volume percent of the metal phosphate bonded Si.sub.3 N.sub.4 monolithic ceramic material with the metal phosphate binder comprising the remainder.

In the second step, the Si.sub.3 N.sub.4 particle/metal phosphate binder precursor mixture is put into molds and pressed into green bodies of the size and shape of the ceramic electromagnetic windows to be produced. Simple shaped electromagnetic windows, such as fiat or slightly curved planes, can be die pressed or cold isostatic pressed (CIP). More complex shaped electromagnetic windows, such as conical or spherical radomes, require CIP forming. Moreover, CIP is the more preferred pressing method because higher pressures can be used and stronger radomes can be produce. Wet bag CIP processes are particularly suitable for producing the radomes of this invention. Note if AlPO.sub.4 hydrate or ZrP.sub.2 O.sub.7 hydrate is used as the precursor, the moisture content of the Si.sub.3 N.sub.4 /precursor mixture may be too high for pressing. In that case, the mixture is dryed until the moisture content is suitable for pressing. A Si.sub.3 N.sub.4 /Al.sub.2 O.sub.3 /85%H.sub.3 PO.sub.4 or Si.sub.3 N.sub.4 /ZrO.sub.2 /85%H.sub.3 PO.sub.4 mixture formulated to produce about 40 or more volume percent of binder will be too plastic for die pressing and will be limited to CIP.

In the last step, the green body is fired in air or an inert atmosphere (e.g., nitrogen, argon, helium, etc.) or even in vacuum at a temperature of preferably from 700.degree. C. to 900.degree. C. and most preferably at about 900.degree. C. to convert the precursors into the metal phosphate binder. As shown in the figure, firing at 900.degree. C. produces a much stronger radome than firing at 700.degree. C. Firing at temperatures above about 900.degree. C. increases the cost of the process without significantly improving the radome.

The terms AlPO.sub.4 phosphate binder and ZrP.sub.2 O.sub.7 phosphate binder include more than the compounds AlPO.sub.4 and ZrP.sub.2 O.sub.7. The binders also include byproducts produced by the precursor reactions. For example, the firing of a Si.sub.3 N.sub.4 /ZrO.sub.2 /H.sub.3 PO.sub.4 produces mostly ZrP.sub.2 O.sub.7 but it also produces Si.sub.3 (PO.sub.4).sub.4 from reaction between H.sub.3 PO.sub.4 and SiO.sub.2 on the surfaces of the Si.sub.3 N.sub.4 particles and leaves some ZrO.sub.2 unreactive. In this case, the term ZrP.sub.2 O.sub.7 binder includes ZrP.sub.2 O.sub.7,ZrO.sub.2 and Si.sub.3 (PO.sub.4). The unreacted ZrO.sub.2 functions as a good filler material. Because of the greater reactivity of Al.sub.2 O.sub.3 with H.sub.3 PO.sub.4 at lower temperatures much more of the Al.sub.2 O.sub.3 forms AlPO.sub.4. however, the term AlPO.sub.4 binder still includes AlPO.sub.4, Al.sub.2 O.sub.3, and Si.sub.3 (PO.sub.4).sub.4. Note, despite the lower reactivity of ZrO.sub.2 with H.sub.3 PO.sub.4, it still produces the strongest binder.

Discontinuous fiber ceramic composites are prepared by replacing a portion of the Si.sub.3 N.sub.4 particles with Si.sub.3 N.sub.4 whiskers. The same metal phosphate binders are used for the discontinuous fiber ceramic composites as were used in the monolithic ceramic composites: AlPO.sub.4 binders, ZrP.sub.2 O.sub.7 binders, or mixtures thereof. These binders are prepared from the same precursors as are used for the monolithic ceramic composites. The metal binders preferably comprise from 20 to 40, more preferably from 24 to 35, and most preferably about 30 volume percent of the discontinuous fiber ceramic composite. The Si.sub.3 N.sub.4 whiskers comprise preferably from more than zero to 40, more preferably from 10 to 40 still more preferably about 25 to 35 volume percent of the discontinuous fiber ceramic composite. The Si.sub.3 N.sub.4 particles comprise the remainder of the discontinuous fiber ceramic composite. The mixing, pressing, and firing steps used to prepare the discontinuous fiber ceramic composite are the same as those used to prepare the monolithic ceramic composite.

The general nature of the invention having been set forth, the following examples are presented as a specific illustrations thereof. It will be understood that the invention is not limited to these specific examples but is susceptible to various modifications that will be recognized by one of ordinary skill in the art.

EXPERIMENTAL

Silicon nitride ceramics were prepared using aluminum and zirconium phosphate binders. Silicon nitride powder of 97.8% purity (2% oxygen), 90% alpha phase, and particle size 0.7 .mu.m was used in this study. The phosphate phases were formed in the materials as a result of the reaction of aluminum oxide and zirconium oxide with phosphoric acid. The powders used in the experiments were 0.05 .mu.m alumina (mixed gamma and alpha phases) and zirconia (3.2 and 22 m.sup.2 /g surface area). The phosphoric acid (H.sub.3 PO.sub.4 was 85 wt. % concentration, 99.99% purity.

Starting materials were combined in proportions to form 20-30 vol. % AlPO.sub.4 and ZrP.sub.2 O.sub.7 in Si.sub.3 N.sub.4 ceramic during firing. Each batch was mixed by first combining the Al.sub.2 O.sub.3 or ZrO.sub.2 with H.sub.3 PO.sub.4 and then adding Si.sub.3 N.sub.4. All raw mixtures were sieved through a 500 .mu.m screen. Specimens of size 5.times.5.times.60 mm were pressed at 50-100 MPa in a steel die and fired at temperatures up to 900.degree. C. in air.

The flexural strength of zirconium phosphate bonded silicon nitride is shown in FIG. 1 as a function of binder content and firing temperature. Strength of the ceramics increased with increasing binder content and firing temperature, with the highest strength of 96 MPa observed for specimens containing 30 vol. % ZrP.sub.2 O.sub.7 and fired at 900.degree. C. X-ray diffraction shows that the materials contained ZrP.sub.2 O.sub.7 as well as a significant amount of unreacted zirconium oxide (baddeleyite). The use of higher surface area zirconia (22 instead of 3.2 m.sup.2 /g) promoted the reaction between ZrO.sub.2 and H.sub.3 PO.sub.4, although the ceramics still contained some unreacted zirconia. However, the strength of ceramics based on the higher surface area ZrO.sub.2 was lower compared to strength for those based on 3.2 m.sup.2 /g zirconia, presumably due to the poor packing of the finer zirconia. The significant increase in strength of high surface area ZrO.sub.2 based materials after isostatic pressing is further evidence of the poor packing.

The results of dielectric property measurements on AlPO.sub.4 and ZrP.sub.2 O.sub.7 bonded silicon nitride are shown in Table 1. The room temperature dielectric constant of all materials was below 5, and the percent change to 1000.degree. C. was below 7%; the loss tangent of all materials was below 0.006. These dielectric properties make phosphate bonded silicon nitride materials promising candidates for advanced radome applications.

TABLE 1______________________________________Dielectric constant and Loss Tangent of phosphate BondedSilicon NitrideSpecimen Dielectric ConstantComposition % change LossSi.sub.3 N.sub.4 + 20.degree. C. to 1000.degree. C. Tangent______________________________________30% AlPO.sub.4 4.03 5.2 0.005530% AlPO.sub.4 /30% Si.sub.3 N.sub.4 whiskers 4.17 5.35 0.005030% ZrP.sub.2 O.sub.7 4.98 6.5 0.0031Radome Requirements <9 <7 <0.1______________________________________

Table 2 shows the changes in weight and dimensions of ceramic materials made of Si.sub.3 N.sub.4 particles with (a) 25 volume percent ZrP.sub.2 O.sub.7 binder and with (b) 30 volume percent AlPO.sub.4 binder after 5 minute exposure to temperatures from 1000.degree. to 1400.degree. C. Thermal exposure time and temperatures were chosen to simulate a possible service environment of tactical missile radomes. Zirconium phosphate bonded specimens experienced expansion beginning at 1150.degree. C., which increased to 17.7% at 1200.degree. C. This expansion was accompanied by a weight loss, which was significant over 1300.degree. C. The weight losses and expansion (bloating) of the specimens can be attributed to the combined effect of decomposition of silicon phosphate and oxidation of silicon nitride. Aluminum phosphate bonded specimens, on the other hand, experienced a much smaller weight loss and expansion. It is assumed that aluminum phosphate bonded silicon nitride contains a smaller amount of silicon phosphate. Alumina reacts with phosphoric acid at 100.degree. C., compared to 250.degree. C. for zirconia, therefore decreasing the amount of phosphoric acid which could react with the silica from silicon nitride. The smaller expansion at temperatures about 1300.degree. C. is due to partial sintering at these temperatures. No significant changes in phase composition were observed for either material at any temperature, aside from the partial transformation of residual monoclinic zirconia to the tetragonal phase.

TABLE 2______________________________________Weight and Dimensional Changes of Zr- and Al-PhosphateBonded Si.sub.3 N.sub.4 Ceramics After 5 Minute Thermal Exposures Zr Phosphate Al Phosphate Weight Linear Weight LinearTemperature Change Change Change Change(.degree.C.) (%) (%) (%) (%)______________________________________1000 -0.2 0 -- --1100 -0.15 0 -- --1150 +0.2 +2.2 -- --1200 -0.27 +17.7 -0.1 01300 -4.1 +15.9 -1.1 +4.31400 -5.7 +13.3 -2.8 +1.8______________________________________

A Si.sub.3 N.sub.4 whisker reinforced composite of 30 volume percent AlPO.sub.4 binder, 30 volume percent of Si.sub.3 N.sub.4 whiskers (grade SNW1-S from American Matrix), and 40 volume percent of Si.sub.3 N.sub.4 particles was prepared. For comparison a control sample monolithic ceramic material was made from 30 volume percent AlPO.sub.4 binder and 70 volume percent of Si.sub.3 N.sub.4 particles. Compositions were mixed using a centrifugal ball mill using a rubber coated steel media. Dry ingredients were mixed first, followed by addition of 85% H.sub.3 PO.sub.4 and further mixing. Disc-shaped specimens were die pressed at 10 MPa followed by isopressing at 350 MPa, and fired at 700.degree. C. in air. After firing, all specimens were sectioned into bars, ground, and polished to 6 microns. The introduction of Si.sub.3 N.sub.4 whiskers resulted in a decrease in strength in the composite. The monolithic composite control sample (30% AlPO.sub.4 /70% Si.sub.3 N.sub.4 particles) had a flexural strength of 85.0 MPa and an open porosity of 18.0% while the discontinuous Si.sub.3 N.sub.4 whisker composite (30% AlPO.sub.4 /30% Si.sub.3 N.sub.4 whiskers/40% Si.sub.3 N.sub.4 particles) had a flexural strength of 47.9 MPa and an open porosity of 20.0%. The discontinuous Si.sub.3 N.sub.4 has excellent dielectric properties as shown in table 1.

Obviously, other modifications and variations of the present invention may be possible in light of the foregoing 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.

Claims

1. A ceramic electromagnetic window comprising Si.sub.3 N.sub.4 particles which are bonded together by a metal phosphate binder that is an AlPO.sub.4 binder, a ZrP.sub.2 O.sub.7 binder, or mixtures thereof, wherein the Si.sub.3 N.sub.4 particles comprise from 55 to 85 volume percent of the ceramic material of the electromagnetic window with the metal phosphate binder comprising the remainder.

2. The electromagnetic window of claim 1 wherein the Si.sub.3 N.sub.4 particles comprise from 60 to 80 volume percent of the ceramic material.

3. The electromagnetic window of claim 2 wherein the Si.sub.3 N.sub.4 particles comprise from 65 to 75 volume percent of the ceramic material.

4. The electromagnetic window of claim 1 wherein the metal phosphate binder is an AlPO.sub.4 binder.

5. The electromagnetic window of claim 1 wherein the metal phosphate binder is a ZrP.sub.2 O.sub.7 binder.

6. An electromagnetic window comprising a ceramic composite comprising:

A. from 20 to 40 volume percent of a metal phosphate binder that is an AlPO.sub.4 binder, a ZrP.sub.2 O.sub.7 binder, or mixtures thereof;

B. from more than zero to 40 volume percent of Si.sub.3 N.sub.4 whiskers; and

C. the remainder of the ceramic composite of the ceramic composite being Si.sub.3 N.sub.4 powder.

7. The electromagnetic window of claim 6 wherein the metal phosphate binder comprises from 25 to 35 volume percent of the ceramic composite.

8. The electromagnetic window of claim 7 wherein the metal phosphate binder comprises about 30 volume percent of the ceramic composite.

9. The electromagnetic window of claim 6 wherein the metal phosphate binder is an AlPO.sub.4 binder.

10. The electromagnetic window of claim 6 wherein the metal phosphate binder is a ZrP.sub.2 O.sub.7 binder.

11. The electromagnetic window of claim 6 wherein the Si.sub.3 N.sub.4 whiskers comprise from 10 to 40 volume percent of the ceramic composite.

12. The electromagnetic window of claim 11 wherein the Si.sub.3 N.sub.4 whiskers comprise from 20 to 40 volume percent of the ceramic composite.

13. The electromagnetic window of claim 12 wherein the Si.sub.3 N.sub.4 whiskers comprise from 25 to 35 volume percent of the ceramic composite.