Phase Equilibria of Stored Chemical

Energy Reactants

L P. Cook

E. R. Plante

R. S. Roth

J. W. Hastie

U.S. DEPARTMENT OF COMMERCE

National Bureau of Standards

Center for Materials Science

Gaithersburg, MD 20899

September 1984

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PHASE EQUILIBRIA OF STORED CHEMICAL

ENERGY REACTANTS

Ocfoo

po.

L. P. Cook

E. R. Plante

R. S. Roth

J. W. Hastie

U.S. DEPARTMENT OF COMMERCE

National Bureau of Standards

Center for Materials Science

Gaithersburg, MD 20899

September 1984

Prepared for Department of the Navy

Office of Naval Research

Arlington, VA 22217

U.S. DEPARTMENT OF COMMERCE, Malcolm Baldrige, Secretary

NATIONAL BUREAU OF STANDARDS, Ernest Ambler, Director

Phase Equilibria of Stored Chemical Energy Reactants

Annual Report

For the Period May 25, 1983 “ May 25, 198^1

L. P. Cook, E. R. Plante, R. S. Roth and J. W. Hastie

Inorganic Materials Division

Center for Materials Science

National Bureau of Standards

Gaithersburg, Md 20899

July 25, 1984

Prepared for the Department of the Navy

Office of Naval Research

Arlington, VA 22217

Under Contract No. N0001 4-83-F-01 1

7

APPROVED FOR PUBLIC RELEASE; DISTRIBUTION UNLIMITED

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Phase Equilibria of Stored Chemical Energy Reactants

Table of Contents

Abstract 1

I. Background and Review of Li-Al-O-H System 2

A. Objective of Study 2

B. Phases Reported in Li-Al-O-H System 3

C. Thermodynamic Analysis ^

II. Sample Preparation and Materials Handling of Li20/Al203 Mixtures... 6

III. DTA Experiments in the System Li20-LiA102. 7

A. Experimental Method 7 B. Results 8

C. Interpretation 9

IV. Quench Experiments and Crystallographic Studies in the

Li20-Al203 System 10

A. Previous Studies 10

B. The High-Alumina Portion of the System 12

C. Neutron Diffraction Study of L1A1303 13

D. The High-Lithia Portion of the System 1

V. Mass Spectrometric Vapor Pressure Measurements in the System

1> i20-Al20o 15

A. Literature Survey 15

B. Mass Spectrometric Method 17

C. Thermodynamic Treatment 18

D. Vaporization of LiA102-LiAl50g 21

E. Li and O2 Pressure Data 2H

F. Vaporization of LiA1^0g-Al203 24

G. Discussion 26

VI. Solution and Phase Equilibria Models for the Li20-Al203 System.... 29

A. Basis of the Model 29

B. Thermodynamic Data Base 31 C. Results 32

VII. Needs for Future Research in the Li-Al-O-H System 33

VIII. References Cited 35

IX. Appendix 1. Modeling of Viscosities in Multiphase Mixtures 38

X. Appendix 2. Literature Search on the System Li-Al-O-H 40

XI. Tables 60

XII. Figures 78

XIII .Distribution 104

Abstract

The reaction of lithium aluminum alloy with water at high temperature

is considered in terms of phase equilibria in the system Li-Al-O-H. A

thermodynamic analysis of the system reveals the potential importance of

lithium hydride as a reaction product. Major needs for experimental phase

equilibria data are outlined, and a determination of the Li20-Al203 phase

diagram is given top priority.

Experimental methods for preparation and handling of atmospherically

sensitive LI2O/AI2O3 mixtures are given. DTA investigation of the system

Li20-LiA102 has yielded information on equilibrium melting behavior, and

the lower limit of melting in the system appears to be 1055 ° ± 10 °C, with

the eutectic located near (Li20)j5 (Al203)25 (mole %)

.

Quenching experiments with x-ray crystallographic analysis for the

high lithia portion of the system have been inconclusive, possibly due to

non-quenchable, rapidly reversible solid-state phase transitions. DTA data

suggest appreciable solid solution of alumina in Li20, yet there is no

direct evidence of this from the x-ray powder diffraction patterns. Also

the a/ 8 transition in Li^AlOi^ has been particularly difficult to locate

consistently.

On the high alumina end of the system Li20-Al203, experiments in

sealed Mo capsules have shown that the eutectic temperature is near

1630 °C, that LiA 102 melts congruently near 1750 °C, and that LiAl^Og melts

incongruently near 1750 °C. Neutron diffraction analysis of LiAl^Og,

cooled rapidly from 1600 °C, shows a 1:3 ordering of Li:Al in the octahedral

sites, with extra peaks of undetermined origin.

1
Mass Spectrometrically determined vapor pressure data are reported for

mixtures of LiA102-LiAl508 and LiAl508~Al203. The results are in reasonable agreement with literature values, but Indicate the need for more

information on solid solution limits. Heats of reaction for the vaporization processes are reported. A preliminary thermodynamic model for

prediction of sol id- liquid- vapor equilibria has been developed and tested

by comparison with the experimental data.

Needs for future research in the systems Li20-Al203 and Li-AlLi20-Al203 are outlined. The utility of such research in understanding the

combustion of mixtures in the Li-Al-O-H system is emphasized. Two

Appendices describe the modeling of viscosities in multiphase mixtures, and

the results of a computerized literature search on the system Li-Al-O-H.

I. Background and Review of Li-Al-O-H System (L.P Cook)

A. Objective of Study

Among the stored chemical energy propulsion systems currently under

consideration those using lithium as a reactant, or lithium alloyed with

other light metals such as aluminum, appear to offer the most promise in

terms of energy release per unit mass (1). One such system under development is actually a two stage process (2):

2LiU) + H20(g) Li20(c) + H2(g) [1]

H2(g) + 1 /2 02(g) H20(g). [2]

2
Both reactions release substantial heat. A variant of this scheme uses a

lithium aluminum alloy as the reactant and, In place of reaction [1], the

reaction Is;

LlAKfi,) + 2H20(g) L1A102 (c) + 2H2(g). [3]

This reaction produces a higher enthalpy yield owing to the high stability

of L1A102 (c).

During the testing of prototype combustors based on these reactions,

it has become apparent that a detailed knowledge of the chemistry for all

phases is needed for optimum design and operation. Factors which must be

accommodated include heat flow associated with phase separation and the

build up of solid products, and the transport of volatile species between

regions in the combustor. The aim of this project is to provide fundamental chemical data pertaining to the oxidation of lithium aluminum

alloy by water.

B. Phases Reported in Li-Al-O-H System

The phase equilibrium chemistry of reaction [3] is potentially

complex. However, as written the phases in this reaction contain three

components, LiAl, H and 0, and can be plotted on a triangular diagram, as

in figure 1-a. A somewhat more convenient representation is figure 1-b,

which is actually a truncated, distorted version of figure 1-a, with oxygen

plotting at infinity in the compositional plane. The possible production

of other phases is apparent in figure 2 where the reaction plane has been

plotted in the quaternary reciprocal system Li-Al-H-Li20-Al203-H20. Table 1

3
lists phases reported in this system. Of these phases only the ones having

stability at temperatures near combustor operation (e.g., - 1100 K) have

been plotted in figure 2. The lithium aluminum hydrides, for example,

apparently dissociate at relatively low temperatures.

Figure 2 may be visualized as a triangular prism In which the edges

are binary systems and the sides are ternaries. Phase diagrams have been

published for the Li-LiH portion of the Ll-H binary (3) and for the Li-Al,

and AI-AI2O3 binaries (4,5). The solubility of oxygen in lithium metal has

been determined as a function of temperature (6). A calculated diagram (7)

provides an estimate of phase relations in the Li20-Al203 binary. Phase

relations at low temperatures have been partially studied for the ternary

system Li20-Al203“H20 (8). This leaves the four ternary sides of the

system in figure 2, as well as the interior quaternary relations, which are

largely unstudied. However, as Table 1 Indicates, thermochemical data are

available for many of the phases in figure 2.

C. Thermodynamic Analysis

Thermochemical data from the literature have been used to calculate

the reactions in Table 2, which have in turn been used to derive the

schematic phase relations shown in figure 3. The phases Li^AlOn and

LiAlgOg have not been Included in the calculations due to Incomplete data.

The compositional extent of melt phases based on LIH and LlOH is unknown.

The possibility of ternary melts in the system Li20-Al203“H20 may be real

at pressures approaching 100 atm. Given those limitations, the results in

4
figure 3 provide only an estimate of the major features of phase compatibility in the system. Information in figure 3 has been combined with

the single quaternary reaction in Table 2 to produce figure

From figure ^ it can be seen that the reaction plane in figure 1 is

not ternary due to the presence of LiH and Al-rich alloy. Figure 5

indicates the products which would result from reaction of LiAl alloy with

H2O, according to relations in figure Instead of occurring as reaction [3], the actual combustion reaction may occur in two stages;

5LiAl(jl) + 2H20(g) 4LiH(S,) + 4A100 + LiA102(c) [4a]

LiH(S,) + Al(jl) + 2H20(g) > LiA102(c) + 5/2 H2(g) [4b]

Many of the substances involved would not be at unit activity; in particular, the molten aluminum would contain some lithium.

In order to make quantitative predictions of the course of reaction in

combustors, experimental data must be taken on the thermal stability and

compositional extent of liquids, and on the distribution of tie lines in

figures 3 to 5. The compound LiA102 is central to reactions [3], [4a] and

[4b], and so a systematic investigation of the system Li20-Al202 has

received top priority. Detailed knowledge of melting relations may, in

conjunction with partitioning data for Li-Al-Li20-Al202, reveal possibilities for manipulation of combustion reactions to produce molten products,

if desired.

5
Our experimental approach to the system Li20-Al203 utilizes a combination of methods. We supplement classical quenching methods and powder

x-ray diffraction analysis with DTA and with Knudsen cell effusion mass

spectrometry. The latter method gives data on enthalpy of vaporization

which can be related to the phase equilibrium data via solution models.

Figure 6 indicates the phase diagram regions covered by the various

experimental and theoretical techniques.

II. Sample Preparation and Materials Handling of LI2O/AI2O3 mixtures

(L. P. Cook)

Depending upon whether compositions were in the Li20-L1A102 or the

L1A102-A1203 portion of the system, the sources of lithia were Li202 and

LI2CO3, respectively. The reagent grade carbonate, dried at 160 °C under

vacuum and weighed in a dry box, could be used to prepare all compositions

in the alumina rich end of the system by mixing with 0.3 pm alpha alumina

(Linde k)'^ under acetone, drying, and calcining in a covered Pt crucible at

approximately 1000 °C. However, for compositions containing more than

50 mole % Li20, decarbonation was incomplete, even under high vacuum.

Attempts to use LiNO^ were also unsuccessful, and so a method for

synthesizing high purity Li20 starting material was sought, as lithia

proved to be unavailable commercially. Oxidation of powdered lithium metal

at ^00 °C was attempted, but this was also unsuccessful, apparently due to

1 Certain commercial equipment, instruments, or materials are identified in

this paper in order to adequately specify the experimental procedure.

Such identification does not imply recommendation or endorsement by the

National Bureau of Standards, nor does it imply that the materials or equipment identified are necessarily the best available for the purpose.

6
a kinetic problem. The procedure outlined in (9) was successfully employed

to produce Li202, which was subsequently decomposed under vacuum at 800 °C.

This yielded a highly pure Li20, as judged from the x-ray powder pattern

and the negligible weight loss under high vacuum up to its melting point,

which agreed well with that reported by (9) as 1^138 ± 15 °C. Lithia

prepared in this way was weighed out with LiA 102 ; mixtures of about 1 g

were homogenized dry using a mortar and pestle in a dry box.

Nearly all manipulations involving these materials were completed in a

dry box under an atmosphere of dry N

2 or Ar purged with a recirculating

purifier capable of reducing H

2 O and O2 to less than 1 ppm. This includes

weighing of mixtures, loading capsules and cells for quench runs and for

DTA or Knudsen effusion experiments, opening sealed quench run capsules,

and preparing x-ray slides. X-ray work was completed in a special cell

which allowed continuous purging by a stream of dry nitrogen.

III. DTA Experiments in the System Li20-LiA102 (L. P. Cook)

A. Experimental Method

A Mettler^ thermoanalyzer was employed for DTA work—this allowed

simultaneous monitoring of weight change to better than 0.01 mg during all

phases of an experiment. The sample arrangement is illustrated in

figure 6. Platinum cells with tight fitting lids were used for unknowns as

well as for the alumina reference material (MBS SRM No. 7^2 ) . Cells were

cleaned by boiling in HCl solution and then distilled water prior to

insertion of each new composition. Cells were weighed in a dry box on a

7
precision microbalance before and after addition of 70 to 100 mg of

powdered sample, and after fitting of the lid. Loaded cells were then

transferred to the thermoanalyzer in a sealed container, quickly inserted

and pumped to 10~5 torr. Following this process, the system was backfilled

with gettered argon, and during the DTA experiments argon was flowed

through the system at 5 cc/min. This procedure served to minimize the

presence of water vapor.

B. Results

Results of DTA experiments are given in Table 3. These experiments

were carried out at a heating rate of 10 ®C/min, and in most cases samples

were repeatedly cycled through a range of several hundred degrees to

observe the reproducibility of the thermal effects. The approximate

magnitudes of thermal affects are indicated in Table 3 by noting the

amplitude of the differential signal where the events were relatively well

defined.

Several choices exist as to the manner in which the temperatures of

DTA effects are defined. Selection of the best method depends to a certain

extent upon the experimental geometry. For the apparatus employed here, it

was found that best results were obtained by defining the temperature of

the event as shown in figure 7» using the heating part of the cycle. Using

this method, calibration runs were within the experimental error of the

accepted values for the melting point of NaCl (800.5 °C). Many of the

temperature values in Table 3 have uncertainties associated with them;

these are derived from statistical analysis of data gathered during thermal

8
cycling. Additionally, runs were completed on replicate samples of 60/40,

65/35, 70/30, 75/25 and 80/20 mol % Li20/Al203 to confirm the reality of

the thermal effects observed.

C. Interpretation

Results of DTA experiments are also plotted in figure 8. The nonreversible exothermic effects occurring between 450 and 550 °C are thought

to correspond to reaction of Li20 and LiA102 to form Li5A10ij. The fact

that this is observed for all compositions except 55/45 may indicate solid

solution of Li20 in LiA102. The irreversible endothermic effect between

775 and 825 °C occurs over a large range of compositions and is probably

related to a polymorphic inversion in Li^AlOn (10,11). A very weak,

apparently reversible effect occurring near 750 °C and detected for the

80 /20 , 70/30 and 60/40 compositions, is possibly related to a polymorphic

inversion in LiA102 (12,13). The endothermic effect at about 1055 ®C for

compositions between Li^AlOij and LiA102 corresponds to the temperature of

eutectic melting. Although a run was not made at the Li^A10i| composition,

the 80/20 run suggests incongruent melting (see Fig. 9). In general,

liquidus temperatures have not been observed using DTA in this system.

Therefore the higher temperature peak in figure 9 probably corresponds to

the incongruent melting of Li^A10i|. However this temperature is not in

perfect agreement with those on the Li20 rich side of Li^AlO^, and further

experimentation seems advisable.

Due to the tendency of Li20-rich melts to extensively wet platinum

cells and flow out around the covers, the high temperature portion of the

run for the 95/05 composition had to be terminated after one cycle, and no

9
information on reversibility could be obtained. In this run no indication

of the incongruent melting of Li^AlOn was observed. This composition shows

a rather gradual melting event suggestive of the melting of a solid

solution in close proximity to 95/05 (see Fig. 10). Existence of such a

solid solution could explain why the melting of Li^AlOii was not observed.

Further interpretation of these and other DTA results must await accummulation and interpretation of detailed x-ray powder diffraction data.

IV. Quench Experiments and Crystallographic Studies in the Li20-Al203

System (R. Roth, M. Zocchi^ and L. Cook)

This system can be naturally divided into two parts, LiA 102 -Al203 and

Li 20-LiA 102 . The high AI2 O

3 portion is a refractory system with melting

points above 1600°C and with few problems related to hydration by atmospheric moisture. On the other hand, the high Li20 portion melts beginning

near 1050 °C, and the sample must be protected from atmospheric moisture

and carbon dioxide at all times.

A. Previous Studies

Hummel _et , (1^) reported synthesis studies on the system

L 1A 102 -A 1202 and noted only the compound LiAl^Og occurring between LiA 102

and AI2 O

2

. A partial phase diagram for the system LiA 102 “Al202 was

reported in 1961 by Strlckler and Roy (15)i in which the melting point of

LiA 102 was indicated as 1700 °C and that of L 1 A 1508 tentatively as 1950 ®C.

^Guest Worker, NBS Reactor Division.

10
A eutectic between these compounds was tentatively Indicated at 1670 ®C.

More recently the JANAF Tables (16) have adopted the melting point of

Strickler and Roy (15) for LiA102 after reviewing melting point determinations up to about the year 1979. The compound LiA102 crystallizes in at

least two forms at one atmosphere, a high temperature tetragonal Y

form (12) stable above about 600 °C, and a hexagonal form which may be

stable at lower temperatures (13). Additionally Chang and Margrave (17)

report a third B form of L 1A 102 at high pressure, with all the aluminium in

tetrahedral coordination. Subsequently, Fischer (18) has reported the

synthesis of B LiA102 at atmospheric pressure. The compound LiAl^Og was

investigated by Collongues (19), Lejus and Collongues (20) and Datta and

Roy (21). The latter authors postulated a first order phase transition at

1295 °C, and there has been some controversy regarding this matter (22,23).

Lejus and Collongues (20) postulate substantial high temperature solid

solution in LiAl^Og.

On the high lithia side. La Ginestra _et , (24) reported the

existence of both Li^AlOij and Li^AlOg, although published powder patterns

exist only for the former, which has two polymorphs, both studied by

Stewner and Hoppe (10, 11). Guggi _et al. , (25) report a melting point of

1320 °C for Li^A102|. Byker, _et , (7), who carried out a thermodynamic

analysis of the system, and estimated a preliminary phase diagram, conclude

that Li^AlO^ may have no thermodynamic stability in the system.

11
B. The Hlgh-Alumina Portion of the System

Only one intermediate phase has been found in the subsystem LiA102~

AI2O3, at the composition Li20^5Al203 (LiAl505). It has a spinel-like

x-ray diffraction pattern. Specimens of four compositions were prepared

with Li20:Al203 ratios of 1:1, 1:2, 1:4.78 and 1:5. These specimens were

prepared by mixing Li20 with either a-Al203 or Y-AI2O3 and firing at about

700 °C in air for 24 hours. All further heat treatments were made by

preparing specimens from these calcines in a dry box and firing in air at

various temperatures. The specimens were then transferred to the dry box

via a dessicator and prepared for x-ray diffraction under flowing N2.

Results are summarized in Table 4.

Heat treatments above 1600 °C were performed by sealing a small

portion of the specimen in a Mo tube in a He atmosphere. These tubes were

then heated in the high temperature furnace in 95N2:5H2. This furnace

employs a W resistance heater and a W-Re thermocouple, calibrated by

embedding a small Pt wire in AI2O3 in a sealed Mo tube. The specimens were

heated at various temperatures near the melting point of Pt (1769 ®C) and

the thermocouple was found to need no appreciable correction. Although it

was not possible to quench specimens from the tungsten furnace, specimens

could be cooled to less than 1000 °C in several seconds by turning off the

furnace power. Following this the Mo capsules were opened and characterized optically and by x-ray diffraction in a dry atmosphere. The melting

point determinations were made by visual observation of the specimen after

removal from the Mo tube. Results are summarized in Table 5 and figure 11.

The compound L1A102 probably melts congruently at about 1750 °C ±25 °C.

The compound LiAl^Og also melts at approximately the same temperature but

12
probably incongruently. Specimens at the 1 :2 ratio were observed to melt

at considerably lower temperatures than the single phase specimens and the

eutectic temperature is about I63O °C ± 20 °C. We have not yet established

whether there is a measurable amount of solid solution in either of these

phases. The elements are low in atomic number and x-ray diffraction does

not allow identification of a small amount of second phase.

C. Neutron Diffraction Study of LiAl^Og

Neutron diffraction provides a method for determination of structure

in compounds comprised of light elements not having appreciable x-ray

scattering power. Analysis of neutron diffraction data can yield detailed

structural information without the necessity for single crystal growth and

x-ray precession analysis. A large batch of LiA1^03 was prepared for

neutron diffraction analysis in order to test for Li:Al site order in the

spinel structure. The specimen was quickly cooled from about 1600 °C and

should represent the high temperature order/ disorder state. The neutron

diffraction pattern, unlike the corresponding x-ray pattern, showed many

peaks which could not be attributed to the phases LiAl^Og or AI2O2

(Fig. 12). The "spurious" peaks which can be indexed on the basis of a

primitive unit cell with a = 8.09 A, were eliminated from the pattern and

the structure of LiA1^03 was refined by the Rietveld method (See Table 6

and Fig. I3). The results show that the structure is similar to LiFe303

and the structural formula can be written as Al3( Li2jAl-| 2)0^2 involving a

1 :3 ordering of the cations in the octahedral sites. Space group is

or P^^32. There is no sign of Li"^ in tetrahedral sites.

13
D. The High-Llthia Portion of the System

Initially, the subsystem Li20-LiA102 was investigated using Li2C03 as

a starting material. Specimens were contained in Au foil envelopes and

inserted into 1 cm diam. Vycor glass tubes under Ar. Each tube was then

evacuated and heated in a split, nicrome furnace with a maximum temperature

capability of about 900 °C. After most of the CO2 had evolved at this

temperature with the system under roughing pump vacuum, an ion pump was

used to complete final CO2 evolution until the evacuated chamber reached at

least 10~^ torr. The specimen was then quickly cooled to room temperature

by shutting off the furnace. The specimen, evacuated tube and the valve

maintaining the vacuum in the tube were taken to the Ar atmosphere dry-box.

The specimen was then x-rayed under controlled atmosphere conditions.

Results of the x-ray examination are shown in Table 7. Because of incomplete reaction this method was determined to be unsatisfactory for preparation of starting materials and Li20, prepared as outlined in Section II,

was used for the remainder of the experiments.

Six compositions were prepared in the high Li20 portion of the system

by dry mixing of Li20 and precalcined LiA102. Small portions of these

specimens were sealed in Pt tubes and quenched in air from various temperatures between 700° and 1050 °C. However, the results of these heat

treatments are inconclusive (see Table 8). Compositions containing 95 and

90 percent Li20 show only Li20 and LiA102 or melted material. Compositions

between 85 and 55 percent Li20 show inconclusive results for the phase

transition between a and 3 Li^AlOij. Apparently this transition cannot be

14
reproduc ibly quenched from any given temperature although both phases were

never found to exist in the same diffraction pattern. Further work is

needed to characterize this transition.

V. Mass Spectrometric Vapor Pressure Measurements in the System

Li20"Al203 (E. R. Plante)

This section deals with vapor pressure measurements made over several

two-phase regions in the lithium aluminate system. Also, in the course of

this work, a literature search of the previous vapor pressure data related

to the lithia-alumina system was carried out.

A. Literature Survey

Vapor pressure measurements in the lithia-alumina system have been

reported by Hildenbrand et al., (26) and summarized later by Potter

et al., (27). These torsion effusion studies provided total vapor pressure

data over the LiA102-LiAl50g system (26). In addition, mass spectrometric

ion current measurements of Li"*" and O2'*’ over the same two- phase system

showed that, in this part of the phase diagram, Li and O2 comprised about

98 percent of the vapor composition. These workers also summarized data

obtained over the LiA1^0g-Al202 system. From these data they derived

values for the heats of the vaporization reactions which can also be used

to calculate standard heats of formation of LiA102(c) and LiAl50g(c) using

auxiliary thermodynamic data.

15
Popkov and Semenov ( 28 ) reported Li(g) pressures obtained by mass

spectrometry. They described the process in terms of the vaporization of

LiA102 to form AI2O3 even though this does not represent an equilibrium

condition.

Guggi, Neubert and Zmbov ( 29 ) made mass effusion measurements over

LiA102 which gave Li pressures higher than those of Popkov and

Semenov ( 28 ). Because of reduction or reaction of the LiA102 with their

metallic effusion cells, and the supposition that Pt absorbed Li(g), they

concluded that the true pressures of Li must lie between those of ( 26 ) and

their measured pressures using a Mo cell.

In a second paper, Guggi et al., ( 25 ) reported measurements over

three, two-phase (condensed) regions in the lithia-alumina system using

mass spectrometry. These data include Li pressures over the Li^AlOijLiA102, LiA102-LiAl50g and LiAl503-Al203 regions. Ikeda et al., published

similar measurements to those of Guggi et al., which can be found in a

preliminary report (30) and a final paper (31 ) which includes additional

details of the measurements.

Other auxiliary sources of data are the JANAF ( 16 ) thermochemical

tables, which give detailed thermochemical data for LiA102(c) and LiA102(Jl)

as well as auxiliary thermochemical data, and the review paper on the

lithia-alumina system by Byker et al., ( 7 ).

16
B. Mass Spectrometer Method

Vapor pressure measurements were made using the classical Knudsen

effusion method coupled with a modulated beam, quadrupole mass spectrometer. In the classical Knudsen method the pressure is related to the rate

of effusion by the expression,

where, for species i, is the partial pressure, m^ the mass loss in time

period At, c the Clausing factor which corrects for flow through a nonideal orifice, a the orifice area, R the gas constant and T the temperature

in Kelvin. With a mass spectrometer species detector, the partial pressure

Pj^ is determined from the positive ion current using the expression

where k is a mass spectrometer constant dependent on species identity.

These relationships are based on the condition of molecular effusion

which requires that the mean free path be much larger than the orifice

diameter. For practical orifice sizes of about 0.5 mm and typical temperatures and molecular weights, these relations are valid to pressures up to

about 10”^ atm.

Elimination of from equations [5] and [6] gives an expression

relating the mass spectrometer constant to known or measured quantities

which is.

1/2

[5]

[ 6 ]

17
k = [nii(2TrR)'' ^2]/[caAt • [ 7 ]

In practice, the sum of mass losses for a number of experiments at different temperatures and time periods are observed and only the most abundant

isotope having an atomic abundance ratio is routinely monitored. Thus

the mass spectrometer constant becomes,

ki = [Ai.mi(2TTR)^/2]/[caMi1/2 li+ At-Tl/2]. [g]

This method of determining the mass spectrometer constant has the advantage

that the pressure is independent of assumptions concerning ionization cross

sections and mass discrimination effects. For the vaporization experiments

described here, the vapor contains primarily Li and O2, which simplifies

the use of expression [8].

C. Thermodynamic Treatment

Equilibrium vapor pressure data can be used to obtain thermodynamic

functions using the second or third law methods. The third law method uses

known or estimated entropy data, together with the measured Gibbs energy

changes, to calculate heats of reaction or heats of formation of key

products or reactants. One method of application of the third law treatment is to use tabulated free energy functions (Gibbs functions) to

calculate a heat of reaction at a reference temperature (usually 298.15 K).

This is done using the formula

18
C9]

0 0 where ~(G.p-H293 )/T are tabulated Gibbs functions summed over products (p)

less reactants (r) and K is the equilibrium constant for the reaction under

consideration.

The second law method makes use of the measured Gibbs energy data (in

this case the free energy for a vaporization reaction) to evaluate both the

heat or enthalpy of reaction and the entropy change of the reaction. In

this study we have chosen to evaluate the second law values by use of the

expression:

in which the known Gibbs functions and measured equilibrium constant on the

left hand side are used to determine, by least squares, AH® (298) and B as

slope and intercept respectively. It can be shown that B equals AS°(298,

3rd law) - AS® (298, 2nd law) and that AH® (298) evaluated as the slope is an

accurately adjusted second law heat.

Whether to select the second or third law heats depends to some extent

on how well the Gibb's functions are known. It is widely recognized that

second law values are very sensitive to temperature or composition errors.

In the case of the lithium aluminates there appear to be other problems

which cause unexplained temperature trends in the data and most studies in

the literature have given more weight to the third law values.

p-iAH®(298) ____ + B

T

[ 10 ]

19
JANAF (16) lists Gibbs functions for all the gaseous species of

interest as well as Li20 (c) and LiA 102 (c) and these data are used in this

report. However, Gibbs function data are not available for LiAl^Og nor for

hi^AlOii in the temperature range of interest.

Venero and Westrum (32) have measured the heat content of LiAl^O0 up

to 5^0 K. Most of the literature studies have assumed that the Gibb's

function (fef) of LiAl^Og can be set equal to the expression,

fef (LiAl^Os) = 0.5 fef (Li20 ) + 2.5 fef (AI2 O

3

). [11]

but Hildenbrand _et , (26) as well as Potter (27) assumed that

fef (LiAl^Og) = fef (L 1A 102 ) + 2.0 fef (AI2 O

3

). [ 12 ]

O 0 At 500 K, Venero and Westrum (32) obtain a value of (G.p-H298 )/T equal

to 42.67^ cal/mol K compared to ^11.851 for equation [11] and 4^.018 for

equation [12]. Byker _e^ ^. , (7) estimated free energy functions for

LiAl^Og at higher temperatures. At 1800 K the various estimates are

110.642 from Byker ^ al . , 107.735 from Hildenbrand _et , and

105.750 cal/mol K using summation of Li20 and AI2O

3

functions. Probably

the most logical choice would be to select the estimates of Hildenbrand

since they fall near the mean of the other estimates. However, for the

present, we have used the linear combination of Li20 and AI2 O

3 data for

both the LiAl^Og and Li 5 A 10 ij Gibbs function data.

20
D. Vaporization of LiA102 - LiAl503

The phase diagram indicates that compositions falling in the

LiAlO2-LiAl5O0 two phase area should undergo univariant incongruent

vaporization. The vaporization reaction for this region of the phase

diagram can be written as

5/4 LiA102(c) = Li(g) + 1/4 02(g) + 1/4 LiAl508(c). [13]

Preliminary data were obtained using a Pt effusion cell having an

effusion orifice with an effective area of 4.3 x 10~3 cm^. The results of

these experiments appeared to indicate that the rate of effusion was under

control of a kinetic rather than thermodynamic process. In retrospect, it

appears likely that much of the preliminary data was affected by the

inclusion of small impurities such as Li2C02 or Li20 in the initial sample.

The effect of volatile impurities will increase the apparent weight loss

and increase the magnitude of the mass spectrometer constant thus making

the estimated partial pressures too high. A second experimental sequence,

in which a new mass spectrometer constant was determined, gave Li pressures

close to those expected for this two phase region.

Further measurements were carried out using an Ir crucible having an

effective orifice area of 5.1 x 10"^ cm^. The sample used in these

experiments contained fewer impurities than that used in the preliminary

measurements although the C02^ mass spectral ion was observed through the

21
early stages indicating decomposition of unreacted Li2 C03 . These data

showed less tendency to be time dependent than the preliminary measurements.

There was, however, a reproducible tendency for the pressures to be

higher especially at the lower temperatures when temperatures were varied

during an experimental sequence in an upward rather than downward direction. This behavior is shown in figure 14 for the results from the 9011

and 901 D data analyzed in Table 9 and is typical of most of the up versus

down temperature sequences.

It is difficult to account for this type of behavior in terms of a

thermodynamic process. The most plausible explanation is that the orderdisorder transformation of LiAl^Og described by Lejus and Collongues (20),

which is accompanied by a sizable volume change, disturbs the sample in the

Knudsen cell sufficiently to increase the amount of impurities able to

evaporate when the temperature is again cycled upward. It was also noted

that at the beginning of an upward temperature cycle, higher than expected

Li'*' ion currents were observed. These signals were also strongly time

dependent. Since at the lower temperatures, the rate of Li loss from the

samples is very small, it would not be consistent for the decay in Li'*'

signals to be due to composition change. But this observation would be

consistent with the uncovering of previously encased impurities which could

then evaporate.

Figures 15 and 16 show representative Li partial pressure data for increasing (I) and decreasing (D) temperature run chronology, respectively.

A few points below 10”7 atm have been omitted to reduce the scale require22
merits of the graphs. Overall, the scatter in the data is about

± 25 percent which is characteristic of a system in which some processes

are not under thermodynamic control.

The results of a second and third law analysis of data selected with

respect to time and temperature direction are listed in Table 9 in chronological order. For reaction [13] it can be shown that for effusive flow,

Pli = 1.86 Pq^, giving an equilibrium constant of .S6)^ .

The heat and entropy changes for reaction [I3] at 298 K as well as the

third law heat of reaction, using the sum of Li20(c) and Al203(c) Gibbs

functions to estimate the Gibbs function of LiAl^O0, are tabulated for each

experimental run. It is concluded that the most reliable thermodynamic

values for the heat of reaction from this treatment is that from run 902D

because this experiment gives the most satisfactory agreement between the

2nd and 3rd law heat of reaction. Also, the suspected role of impurities

in the evaporation process would tend to increase the apparent Li pressure.

It should be noted that in general the 2nd law heat of reaction is significantly lower for increasing, as opposed to decreasing, temperature runs.

Over the course of this experimental series the sample underwent a

change in bulk composition from essentially 100 wt. % LiA102 to 64 wt$

LiA102 and 36 wt % LiAl^Og. Further measurements on a sample in this two

phase region would be useful to aid in confirming the role of impurity

vaporization.

23
E. Li and O

2 Pressure Data

As noted previously, it is possible to simultaneously determine both

Li and O

2 partial pressures. The value of the mass spectrometer sensitivity constant for O

2 was estimated from that determined by weight loss for

Li using the equation

*^02 = *^Li (oLi * "^Li * ^Li )/(°02 * "^02 * ^©2

^

where Oj^ is the ionization cross section of species i, the relative

transmission factor, and the species isotopic abundance factor. The

cross section of Li was based on Mann's maximum cross section and corrected

by the ratio of the I''^niax/^^30 30 eV ionizing energy used, while the

O

2 cross section was taken to be 1.10 based on literature values. Measurements of the transmission factor were made using a rare gas mixture of

known composition and component ionization cross sections. For the 901

D

data the average PLi'^P02 1.92 which agrees very well with the

theoretical value of 1.86. The Li and O

2 pressures for the 901 D data set

in figure 17 indicate a constant ratio with temperature, as expected for a

well behaved thermodynamic system.

F. Vaporization of LiAl^Og - AI2 O

2

The LiAl^Og - Al20^ region of the phase diagram is also a two-phase

area which should undergo univariant-incongruent evaporation. The vaporization reaction for this region of the phase diagram can be written as,

LiAl508(c) = Li(g) + 1 /M 02 (g) + 5/2 Al203(c). [15]

24
Vaporization experiments, starting with essentially stoichiometric LiAl^os,

were carried out in the same fashion as for the LiA102~LiAl508 study.

The vaporization behavior in this region of the phase diagram is

similar to that in the LiA102-LiAl508 region except that there is a greater

tendency for a decreased vaporization rate with time. The Li partial

pressure data are shown in figure 18 for data taken with temperatures

increased from point to point during a series while figure 19 shows data

obtained when temperatures were decreased. The scatter in the data is

comparable to that for the LiA102-LiAl50g region except that for experiments following the 1 0^ID series the pressures decreased more rapidly with

time.

The results of a second and third law analysis of the data are listed

in Table 10. As with the LiA102~LiAl508 data there is a tendency for pressures to be higher when temperatures are varied in an experimental run in

an upward direction as opposed to varying temperatures in a downward

direction. Figure 20 illustrates this effect for data taken in the 9121,

the 91 2D, and the 10^11 series. Here, for simplicity these data sets are

labelled run 1 inc T, run 1 dec T and run 2 inc T. Note that after the run

1, dec T experiment there has been a recovery in the Li pressure giving

better agreement with the run 1 inc T data than the run 1 dec T data. It

appears that factors other than the usual time dependent effects are

present.

There is clearly a relationship between these effects for the

LiA102-Li5A108 and Li5A108-Al203 phases and it may be related to the phase

change in which LiAl^Og (ordered spinel) is transformed to LiAlgOg

25
(disordered structure). It is also possible that there is a solid

solubility range on either or both sides of the LiAl^osCc) range and that

the reestablishment of equilibrium is fast in one direction but slow in the

other.

To select the most reliable results for reaction [ 15 ] from the

Table 10 data we should note that the decrease in pressure from run to run

can be due to (a) evaporation of traces of impurities initially present in

the sample such as LiA102, or unreacted L 13003 or Li20, as well as (b)

surface depletion effects due to formation of AI2O3 on the surface of the

sample or (c) a solid solution range of LiAl^Og. Lacking definitive

information concerning these possibilities, the most reliable results are

considered to be those near the beginning of the experimental series. Also,

there is reasonably good agreement between 2nd and 3rd law heats of

reaction only for data taken during runs where the temperature was decreased between experimental points. From this argument we believe that

the results from experiment lO^D are the most reliable for the heat

reaction determination.

G. Discussion

The AH° values for the vaporization reactions listed in Table 11 may

be used, together with auxiliary data (Table 12 ), to derive standard heats

of formation from the elements for each of the high temperature compounds

found in the lithia-alumina system, as shown in Table 13 -

Potter et al., (27) used different free energy functions from those

used here and their results were adjusted to account for this difference.

Also, Ikeda et al., ( 31 ) used an unusual method of expressing the vaporiza26
tion reactions and their data were reevaluated using the Li pressures only.

As mentioned previously, free energy function data for Li^A10i}(c) and

L'iA1^03(c) are not available in the temperature range of the experiments

and a linear combination of Li20(c) and Al203(c) data was used to estimate

these quantities.

0 It should be noted that AH^ LiAl508 can be obtained directly from

0 reaction [C]. This quantity can then be used to calculate AH^ LiA102

0 using the AH for reaction [B] . However, the calorimetric value of AH^.

LiA102 is thought to be quite reliable and can be used with reaction [B]

0 to yield a second value of AH^ LiAl^Og. For these calculations we have

used the reference data shown in Table 12 from JANAF (16). Table 13

O gives results for AH^ LiAl508 using reactions [B] and [C] and also the

O 0 calorimetric value of AH^. LiA102. It may be noted that the values of AHf

LiAl^Og agree better when calculated from reaction [C] than from those

0 using the calorimetric value of AH^ LiA102 and reaction [B]. This is due

to the addition of deviations for the combined reaction, and the direct observations using reaction [C] are considered more reliable. Values for AH^.

Li^AlOii have similarly been derived from the results of Guggi _et jd. , (25)

and Ikeda_et_^., (31) using reaction [A] and the calorimetric value of

O AHj. L1A102, as shown in Table 13. At the present time it seems likely that

these values cannot be correct because the Li pressures reported by

Ikeda _et , (31) and those back calculated from the work of

Guggi _et j^. , (25) appear to exceed the vapor pressure of Li over pure

Li20 (c).

27
To summarize, the vapor pressure data from the present work agree

reasonably well with the literature but the behavior of the samples across

the composition ranges is more complex than generally assumed. Analysis of

the thermodynamic data obtained from the vapor pressure measurements is

hampered by the lack of thermodynamic functions for the LiAl^Og and Li5 A 10ij compounds. The extent of solid solubility of LiA1^08 appears to be

uncertain and may be difficult to determine by many experimental methods

because of the order-disorder transition near 1 300 °C. Measurement of the

Li pressure across a more extensive region of the LiA102 - LiAl508 and

LiAl^Og ~ AI2 O

2 region is desirable. It seems possible that some of the

results observed in the current study are due to impurity effects. We note

that a lower pressure than that selected from the data in this study would

bring the heats of formation of LiA1^08 obtained using equations [ 13 ] and

[15] closer together. However, a more definitive thermodynamic analysis of

the vapor pressure data requires quantification of the following likely

effects: (a) evaporation of impurities, (b) solid solution in either

LiA1^08 or LiA102 and (c) surface depletion. Data in the high lithia

region, especially the Li^AlOij compound appears unsatisfactory and measurements of at least the solid state should be made on this material using

microbalance and/or mass spectrometric techniques.

28
VI. Solution and Phase Equilibria Models for the Li20-Al203 System

(J. W. Hastie and W. S. Horton3 )

Given the experimental complexity of the phase equilibrium behavior in

the Li20-Al203 system, it is desirable to develop a theoretical framework

to guide and enhance the experimental program. In a previous attempt to

empirically model the phase diagram for Li20-Al203, Byker et al., ( 7 ) used

the Redlich Kister equations to provide an empirical fit to partially

complete phase diagram and related thermodynamic data. The validity of

these equations to ceramic systems has never been established and the

resulting phase equilibria data are often highly questionable and can

seriously disagree with experimental evidence, as discussed by us in detail

elsewhere (33).

In previous work on various Na20, K2O, Si02, AI2O3 mixtures we have

shown that a chemically based Ideal Mixing of Complex Components (IMCC)

model can correctly predict the solution activity and vaporization properties and, to a lesser accuracy, the liquidus and solidus phase equilibria

( 3 ^). From this earlier experience we believe that the IMCC approach,

should also be applicable to the Li20-Al202 system.

A. Basis of the Model

The rationale and theoretical basis for the mixing model used in this

study has been presented elsewhere ( 33 ). To summarize, the key features of

the model are as follows. We attribute large negative deviations from

^NBS Consultant 29
ideal thermodynamic activity behavior to the formation of stable complex

liquid (and solid) components such as LiA102, LiAl508 and Li5A10n. The

terminology of components and complex components refers to the usual

reference state oxides, e.g., Li20 or AI2O2 and to their compounds (liquid

or solid), e.g., LiA102 (i.e., Li20»Al203), respectively. The component

and complex component oxides formed are assumed to mix ideally, in accordance with Raoult’s law. Hence thermodynamic activities and mole fractions

are equivalent quantities with this model. It should be noted that

alternate definitions of ideality, such as the Temkin model, require

structural assumptions that are not necessary in the present treatment. The

component liquids considered here are distinctly different from the

hypothetical associated species used in other modeling approaches. For the

most part, the component liquids are established neutral, stable, thermodynamic compounds, appearing in phase diagrams in equilibrium with congruently melting solids, and also in reference tables of thermodynamic

functions. The free energies of formation (AG^) are either known or can be

estimated for these complex component liquids (and solids). By minimizing

the total system free energy one can calculate the equilibrium composition

with respect to these components. Thus, for instance, the mole fraction of

Li20 present (X*Li20) in equilibrium with LiA102, and other complex liquids

(and solids) containing Li20, is known. As we have shown previously for

similar oxide systems, the component activities can, to a good approximation, be equated to these mole fraction quantities. Thus physical interactions among the complex components are considered negligible compared with

the strong chemical interactions leading to their formation.

30
From the assumption of Ideal Mixing of Complex Components (IMCC), it

also follows that lithium partial pressures can be obtained from their

thermodynamic relationship to activities. Thus, for example, in the binary

L'i 20 -Al203 system,

?Li = (2 • X *Li20-Kp)‘^-^ C16]

where Kp is the stoichiometric dissociation constant for reaction of pure

Ci 20 (liquid or solid) to yield Li and O2

.

In the following discussion we test the model, and its accompanying

thermodynamic data base, by comparing predicted Pj^j^ data with experimental

values. Thermodynamic activities and phase compositions are also calculated using this model. The model is constrained to obey the Gibbs-Duhem

activity and Gibbs phase rule relationships.

B. Thermodynamic Data Base

In practice, application of the IMCC model requires a thermodynamic

data base for the component and complex solids and liquids. The SOLGASMIX

computer program ( 33 ) used for calculation of the equilibrium composition,

and hence activities, utilizes a data base of the type given in Table 1 4.

The coefficients to the AG^. equation were obtained mainly by fitting

AGj. vs T data available in JANAF (16). In a few instances, the literature

thermodynamic data have been re-evaluated within the experimental error

limits which typically are 1 to 3 kcal/mol; e.g., see the earlier work of

Hastie_^^., (34). For cases where no literature data were available for

the liquids, we estimated the thermodynamic functions in the manner

31
described earlier (3^). Usually, data available for the corresponding

solid phase were converted to liquid functions by estimating the melting

enthalpy or entropy.

Application of the IMCC theory to predictions of phase equilibria

requires a thermochemical data base for all possible solid, liquid, and

vapor components and phases. We have converted all pertinent available

literature thermodynamic data for the Li-Al-0 system to the form used in

the SOLGASMIX computer program for free energy minimization, as shown in

Table 14. The Gibbs energies of formation (AG^.) corresponding to the

coefficients of Table 14 are given in Table 15. The thermodynamic data

base as represented in Table 14 should be considered an interim set. We

expect to refine these thermodynamic functions in future work to resolve

differences between JANAF and the results of more recent workers, including

the present work.

C. Results

With the current interim data base of Table 14, we have calculated the

likely phase equilibria behavior of the Li20-Al203 mixtures. Representative data are shown in Table 16 and figures 22 and 23. Of particular note

in figure 23 is the region between about 1900 and 1920 K where solid LiA102

and liquid coexist. Table 17 summarizes the principal reactions for this

phase- transit ion region. The thermodynamic activity of liquid Li20

increases markedly with increasing temperature over this transition

interval, leading to a rapid rise in Li partial pressure (Pli), as shown in

figure 23. We believe that the reason for this unusual behavior will be

clarified when additional components are included in the theoretical

32
data-base, and when the thermodynamic functions derived from various

sources are refined to provide a single self-consistent set of data-base

thermodynamic functions. The comparison between the experimental Li partial

pressure curve and the predicted result is considered satisfactory and is

within the combined errors of the data-base thermodynamic functions and the

experimental work.

Preliminary model results for other compositions are given in

figure 22, in comparison with the interim phase boundaries based on the experimental results. Note that the model generally predicts the correct

phase behavior.

In future studies we will use this chemical approach to optimize the

thermodynamic model data base by application of existing computer methods (35, 36 ) which couple experimental phase diagram data with solution

activities and compound thermodynamic functions.

VII. Needs for Future Research in the Li-Al-O-H System

In this report we have presented data on the phase equilibria and

vapor pressures in the system Li20-Al202, with ancillary modeling. From

this work a number of problem areas needing further study have been defined

including: solid solution of AI2 O

2

in Li 20 ; the a/3 transition in Li^AlOi^;

solid solution vs. order/disorder in LiAl^Og; and mass spectrometry of the

composition Li^AlO^. These problems will be addressed by us in future

work. A thermochemically optimized diagram for the system Li20-Al202 will

be produced. This diagram will be combined with the known phase diagram

for Li-Al to yield, with minimal experimental work, a diagram for the

33
system Li-Al-Li20-Al203. This system will depict equilibria between metal

alloy reactants and oxide products in the stored chemical energy conversion

scheme. Additionally, we plan to determine the extent to which molten LiH

dissolves LiAl, Li20, LiA102 and LiOH. Similarly important are solubilities and activities of LiA102, Li20, and LiH in LiOH melts. The basic

data thus derived will allow a second generation of predictions and

calculations for the Li-Al-H-Li20-Al203-H20 subsystem of the quaternary

system Li-Al-O-H .

34
VIII. References Cited

1. Bush, K. L. and Merrill, G. L. , SCEPS - An Advanced Thermal Power

Plant for Torpedoes, AIAA/SAE/ASME 17th Joint Propulsion Conference,

Colorado Springs, Col., (1981)

2. SCEPS II. A New High-energy Undersea Propulsion System, Garrett

Pneumatic Systems Division, Report No. ^11-3675 (1982).

3. Veleckis, E. , Van Deventer, E. H. , and Blander, M., J. Phys. Chem. 7^

[19], 1933 (1974).

4. McAlister, A. J. , Bull. Alloy Ph. Diag. 3. [2] 177 (1982).

5. Wriedt, H. A., Bull. Alloy Ph. Diag. (in press).

6. Yonc, R. M., Maroni, V. A., Strain, J. E. , and Devan, J. H. , J. Nucl.

Mat. T9_ [2] 354 (1979).

7. Byker, H. J. , Eliezer, N. , and Howald, R. A., J. Phys. Chem. 83 [18]

2349 (1979).

8. Kotsupalo, N.P., Pushnyakova, V. A., and Berger, A. S. , Zh. Neorg.

Khim. ^

[9] 251 4 (1978).

9. Ortman, M. S. and Larsen, E. M. , J. Amer. Ceram. Soc. 66_ [9] 645

(1983).

10. Stewner, F. , and Hoppe, R. , Z. Anorg. Allgem. Chem. 380 [7] 241

(1971).

11. Stewner, F. , and Hoppe, R. Z. Anorg. Allgem. Chem. 381 [4] 149

(1971).

12. Marezio, M. and Remeika, J. P., J. Chem. Phys. £4 [8] 3143 (1966).

13 . Marezio, M., Acta Cryst. J_9_ [3] 396 (1965).

14. Hummel, F. A., Sastry, B. S. R. and Wotring, D., J. Am. Ceram. Soc. ^ [ 3 ] 88 (1958).

15 . Strickler, D. W. and Roy, R. , J. Am Ceram. Soc. ^ [5] 228 (1961 ).

16. Stull, D. R. and Prophet H. , JANAF Thermochemical Tables, Second Ed . ; U. S. Govt. Printing Office, Washington, DC, NSRDS-NBS 37, (1971). See

also later supplements for 1971-1981 (J. Phys. Chem. Ref. Data)

17 . Chang, C. H. , and Margrave, J. L. , J. Am. Chem. Soc., 90 [8] 2020

(1968).

18. Fischer, A. K. , Inorg. Chem. 16 [4] 974 (1977).

35
19. Collongues, R. , Ann. Chim. ^ [7~8] 395 (1963).

20. Lejus, A. M. and Collongues, R. , C. R. Acad. Sci. 25^ [7] 2005

(1962).

21 .

22 .

23.

2H.

Datta, R. K. and Roy, R. , J.

Hafner, S. and Laves, F. , J.

Roy, R. and Datta, R. K. , J.

Am. Ceram. Soc. 46 [8] 388 (1963).

Am. Ceram. Soc. ^[7] 362 (1964).

Am. Ceram. Soc. 47 [7] 362 (1964).

La Ginestra, A., Lo Jacono, M. and Porta, P. , J. Thermal Anal. ^ [1] 5

(1972).

25. Guggi, D., Ihle, H. R. and Neubert, A., Proc 9th Symp. Fusion Tech.,

Pergamon Press, Oxford, U.K. (1967) pp. 635*644.

26. Hildenbrand, D. L. , Theard, L. P., Hall, W. F. , Ju, F. , Viola, F. S.

,

and Potter, N. D. Ford Motor Company, Aeronutronic Division, Publication No. U-2055, March 15 (1963).

27. Potter, N. D., Boyer, M. H., Ju, F., Hildenbrand, D. L. and Murad, E. AFOSR 70-21 1TR, 1970, NTIS-71 5567.

28. Popkov, 0. S. and Gemenov, G. A., Russian J. Phys. Chem. [2] 266

(1970).

29.

30.

31.

Guggi, D., Neubert, A. and Zmbov, K. F. , Proc.

Thermodyn., Montpellier, France, Paper III/23»

Ikeda, Y., Ito, H. , Matsumoto, G. and Hayashi,

Tech. 17., [8] 650 (1980).

Ikeda, Y., Ito, H. , Matsumoto, G. and Hayashi,

[1-2] 47 (1981).

4th Int. Conf. on Chem.

p. 124 (1975).

H. , J. Nucl. Sci. and

H. , J. Nucl. Matls. 97,

32. Venero, A., and Westrum, Jr.,E. F. , J. Chem. Thermo. J_, [8] 693

(1975).

33. Hastie, J. W. and Bonnell, D. W. , A Predictive Phase Equilibrium Model

for Multicomponent Oxide Mixtures. Part II; Oxides of Na-K-CaMg-Al-Si, High Temp. Science, in press (1984).

34. Hastie, J. W., Horton, W. S., Plante, E. R., and Bonnell, D. W.

Thermodynamic Models of Alkali Vapor Transport in Silicate Systems,

lUPAC Conf., Chemistry of Materials at High Temperature Harwell, U.K.,

August 1981 ; High Temp. —High Press. _1_4 [6], 669 (1982).

35. Lukas, H. L. , Weiss, J., Krieg, H., Henig, E. T., and Petzow, G., High

Temp—High Press. 14 [5], 607 0 982).

36
36. Lin, P. L. , Pelton, A. D., Bale, C. W. , and Thompson, W. T. , CALPHAD ^

[2] , i47 (1980).

37. Gambill, W. R. , Chem. Eng. ^[3] 123 (1966); 6^ [3] 127 (1966); 66

[4] 151 (1966).

38. Brandes, E. A., Ed., Smithell’s Metals Reference Book, Sixth Ed. ; London, Butterworths (1983).

39. Kendall, J. , and Monroe, K. P., J. Am. Chem. Soc. ^[1] 1 (1917); 3^

[ 3 ] 787 (1917); 39 [5] 1802 (191 7); 43. [1] 115 (1921).

40. Steinour, H. H. , Ind. Eng. Chem. 36 [2] 840 (1944); 36 [2] 901 (1944).

37
IX. Appendix 1. Modeling of Viscosities in Multiphase Mixtures (L. Grabner)

Empirical relations have been applied in the past to model a variety

of multiphase systems (37). A literature survey failed to reveal any data

on viscosities of lithia-alumina melts; however the viscosities of molten

Li and A1 are well known (38).

In situations where two liquids mix ideally, then the relation

proposed many years ago by Kendall and Monroe (39) applies well:

1/3

= X1U1

/3 1/3

X2M2 [17]

where X^ and X2 are the mole fractions of the two components in the mixure

and and )i2 their viscosities. This assumes the absence of strong

interactions between components. Viscosity data for pure Li and A1 have

been plotted in figure 23. At 1200 K, viscosities calculated for Al/Li

mixtures using equation [17] are shown in figure 2H.

For multiphase systems, most efforts to correlate suspension viscosity

have resulted in relatively simple equations giving Ug, the viscosity of

the liquid-solid mixture, in terms of the viscosity of the suspending

liquid, and the volume fraction of the solid particles, <j)g. The

relations proposed are many. They are listed in (37). Of these, the

relation proposed by Steinour (40):

38
[ 18 ] =

'--»s

is favored for values of 4)g < o.i|. A graph of equation [18] is given in

figure 25.

39
X. Appendix 2. Literature Search on the System Li-Al-O-H (L. Cook)

A comprehensive computerized literature search was designed with the

aid of NBS library staff. Various combinations of the elemental and oxide

components of the system Li-Al-O-H were used as descriptors, such as Li-0,

Li-Al-0, Li20-Al203 , Li20-H20, Li-Al-H and Li-Al-H-0. Additionally,

certain compound names were used in the search, such as lithium aluminate

and lithium alumium hydride. No restrictions (other than to avoid duplication) were made on these searches, so that all references, as for example

with keywords lithium aluminate and water, would be retrieved regardless of

other keywords present.

The data bases searched included Metadex (1966-1983) i Chemical

Abstracts (1967~1983), DOE Energy (197^-1983) and Compendex (1970-1983).

The search generated approximately 2000 references. This large number

stems partly from technological interest in the system Li-Al-O-H for

applications such as nuclear fusion, advanced batteries, hydrogen storage

and metal organic synthesis. The majority of these references were neither

of direct nor indirect application to the problem of reaction in the system

Li-Al-O-H, and were eliminated, leaving the remainder, which have been

loosely grouped below according to chemistry. No attempt has been made to

annotate this bibliography, but titles are included for the aid of the

interested reader.

40
( A) The System llthia-alumina

1. Lithium aluminates—crystal chemistry

Abritta, T. ; Melamed, N. T. ; Neto, J. M. ; and Barros, F. de S. , 1979,

The optical properties of chromium(+3) ion in lithium aluminate

(LiA1^03) and lithium gallium oxide (LiGa50g): J. Lumin, V. 18-19,

pt. 1, p. 179-182.

Abritta, T. ; Neto, M. ; Barros, de S. ; and Melamed, N. T. , 1983; The

fluorescence of chromium(+3) in ordered and disorded lithium aluminum

oxide (LiAlcOg): Inst. Fis., Univ. Rio de Janeiro, Brazil, Report No.

UFRJ-IF-07/83, in p.

Agarkov, B. N. and Batalova, S. Sh. , 1970, Low-induction ferrites of

the lithium system: Elektron. Tekh. Nauch.-Tekh. Sb. Ferrit. Tekh.,

No. 3, p. 14-20.

Aubry, J. and Klein, F. , 1970, Lithium aluminate: Chim. Ind., Genie

Chim., V. 103, No. 13, p. 1643-4.

Baranov, M. N. and Kustov, E. F. , 1973, Optical spectra of iron group

ions in aluminum lithium oxide (LiAlcOg) single crystals: Opt.

Spektrosk., V. 34, No. 4, p. 726-8.

Brabers, V. A. M., 1976, Infrared spectra and ionic ordering of the

lithium ferrite-aluminate and chromite systems: Spectrochim. Acta, V.

32A, No. 11, p. 1709-11.

Datta, R. K. and Roy, R. , 1968, Order-disorder in M magnesium aluminate. The systems: MgAl204-LiAl508, MgAl20n_NiAl20n and NiAl20i|-

ZnAl20ij: Amer. Mineral., V. 53, P* 1456-75.

Doerhoefer, K. , 1979, A reindexing of the x-ray powder diffraction

pattern of 3-lithium aluminate: J. Appl. Crystallogr . , V. 12, No. 2,

p. 240-1

.

Doman, R. C. and McNally, R. N. , 1973, Solid solution studies in the

magnesium oxide-lithium metaaluminate system: J. Mater. Sci., V. 8,

No. 2, p. 189-91 .

Famery, R. ; Bassoul, P. ; Delamarre, C. ; Queyroux, F. ; and

Gilles, J. C., 1982, Precipitation of metastable phases with periodic

antiphase structure in lithium aluminum oxide (LiAlc08)-alumina system

Philos. Mag., V. 45A, No. 1, p. 63"80.

Famery, R. ; Queyroux, F. ; Gilles, J. C.; and Herpin, P., 1979, Structural study of the ordered form of lithium aluminum oxide (LiAl^Og): J

Solid State Chem., V. 30, No. 2, p. 257-63-

41
Firsov, Yu. P., 1979, Effect of heat treatment conditions on the

formation of the defect state in spinel solid solutions: Tr. VNIl Khim.

Reaktivov i Osobo Chist. Khim., No. ill, p. 154-5.

Follstaedt, D. M. and Biefeld, R. M. , 1978, Nuclear-magnetic-resonance

study of lithium(+1 ) motion in lithium aluminates and lithium hydroxide: Phys. Rev. B: Condens. Matter, V. 18, No. 11, p. 5928-37.

Fritzer, H. P. ; Sliuc, E. ; and Torkar, K., 1973, Spectroscopic studies

and phase relations in the system lithium oxide-aluminum oxide-chromium(III) oxide: Monatsh. Chem., V. 104, No. 1, p. 172-81.

Gessner, W. and Mueller, D., 1983, Coordination of aluminum in

B-lithium aluminate (LiA 102 ): Z. Anorg. Allg. Chem., V. 505, p.

195-200.

Gula, E. ; Kolodziejczyk, A.; Obuszko, A.; and Pszczola, J. , 1973,

Possibility of the existence of iron(+3) ions with lowered magnetic

moment in lithium f errites-aluminates: Acta Phys. Pol. A, V. 43, No. 1, p. 175-6.

Hoppe, R. and Koenig, H. , 1977, On the crystal structure of 3-lithium

aluminate (Li^AlOn): Z. Anorg. Allg. Chem., V. 430, p. 211-17.

Ignat'ev, I. S. ; Lazarev, A. N. ; and Kolesova, V. A., 1976, Normal

vibrations of aluminates with tetrahedrally coordinated aluminum atoms:

Izv. Akad. Nauk SSSR, Neorg. Mater., V. 12, No. 7, p. 1230-9.

Jarocki, E. and Kubel, W. , 1973. Structural investigations and the

problem of bisquare exchange in the ferrite-lithium aluminate

LiO ^Fe-] yAlO 364 : Zesz. Nauk. Akad. Gorn.-Hutn., Krakow, Zesz. Spec.,

V. hs. p! 211-20.

Kolesova, V. A., 1974, Infrared absorption spectrum of lithium

ortho-aluminate Li^AlO/i: Zh. Neorg. Khim., V. 19, No. 10, p. 2898-9.

Malve, A.; Gleitzer, C. ; and Aubry, J., 1971, Lithium aluminate-lithium

ferrate system. Detection of a LicAl4

/ 7 Feo /704 compound: C. R. Acad.

Sci., Ser. C, V. 273, No. 15, p. 888-90.

McNicol, B. D. and Pott, G. T. , 1973, G. T. , Luminescence of manganese

ions in ordered and disordered lithium aluminum oxide: J. Lumin., V. 6,

No. 4, p. 320 - 34 .

Melamed, N. T. ; Barros, F. de S., Viccaro, P. J. ; and Artman, J. 0.,

1972 , Optical properties of Fe^'*' in ordered and disordered LiAlc 03 : Phys. Rev. B, V. (3)5, No. 9, P. 3377-87.

Melamed, N. T. ; Viccaro, P. J. ; Artman, J. 0.; and Barros, F. de S.

,

1970 , Fluorescence of FeB'*' in ordered and disordered phases of LiAl^Og:

Proc. Int. Conf. Lumin., p. 384-67.

42
Neto, J. M. ; Abritta, T. ; Barros, F. de S. ; and Melamed, N. T. , 1981,

Comparative study of the optical properties of FeS'*’ in ordered LiGa^og

and LiAl508 : J. Lumin., V. 22, No. 2, p. 109-120.

Pakhomova, N. L. and Kozlov, V. A., 1982, Magnetic anisotropy and

exchange interactions in lithium- aluminum ferrites: Izv. Vyssh. Uchebn.

Zaved., Fiz., V. 25, No. 11, p. 54-7.

Petrov, M. P. ; Szymczak, H. ; Wadas, R, ; and Wardzynski, W. , 1971,

Crystal field of low symmetry in LiAl^Og + Cr^"^: Electron Technol.,

V. 4, No. 1-2, p. 75-90.

Petrov, M. P. ; Szymczak, H. ; Wadas, R. ; and Wardzynski, W. , 1971,

Low-symmetry crystal field in lithium spinel; J. Phys. (Paris), V. 32,

No. 2-3.

Polyakov, V. P. , 1971, Magnetic short-range order and Curie temperature

of ferrimagnetic spinels containing lithium ions: Elektron. Tekh.

Nauch.-Tekh. Sb. Ferrit. Tekh., No. 4, p. 12-17.

Pott, G. T. and McNicol, B. D., 1971, Phosphorescence of Fe^"*' doped

lithium aluminate (LiAl^Og): Chem. Phys. Lett., V. 12, No. 1, p. 62-4.

Pott, G. T. and McNichol, B. D., 1973, Luminescence of chromium(+3)

ions in ordered and disordered lithium aluminum oxide (LiAl^Og):

J. Solid State Chem., V. 7, No. 2, p. 132-7.

Semenov, N. N. ; Merkulov, A. G. ; and Fomin, A. G. , 1967, Low-temperature modification of lithium aluminate: Redk. Shchelochnye Elem., Sb.

Dokl. Vses. Soveshch., 2nd, Novosibirsk, (Plyushchev, V. E., Ed.)

p. 100-9.

Stel ' mashenko, M. A.; Rubai* skaya, E. V.; Perveeve, A. I., Shlyakhina,

L. P. ; and Nekhoroshev, G. V., 1973, Crystal lattice distortion effect

on the magnetic anisotropy of lithium- aluminum ferrites: Izv. Vyssh.

Uchev. Zaved., V. 16, No. 5, p. 113-16.

Stewner, F. and Hoppe, R. , 1971, Crystal structure of a-lithium

aluminate: Z. Anorg. Allg. Chem., V. 380, No. 3, p. 241-3.

Stewner, F. and Hoppe, R. , 1971, Crystal structure of &-LicA10i^: Z. Anorg. Allg. Chem., V. 381, No. 2, p. 149-60.

Vicarro, P. J. ; Barros, F. de S. , and Oosterhius, W. T. , 1972, Paramagnetic Fe^"^ in lithium aluminate. Magnetic field effects in the

Moessbauer spectrum; Phys. Rev. B, V. (3)5, No. 11, p. 4257-64.

Wadas, R. ; Wardzinski, W. ; Petrov, M. P., and Szymczak, H. , 1971,

Crystalline field in LiAl^Og : Cr^"^ : Paramagn. Rezonans 1944-1969, Vses.

Yubileinzyz Knof. (Rivkind, A. I., Ed.) p. 60-2.

43
Waychunas, G. A. and Rossman, G. R. , 1983, Spectroscopic standard for

tetrahedrally coordinated ferric iron: IronS^-doped Y-lithium

aluminate: Phys. Chem. Miner., V. 9, No. 5, p. 212-15.

Zhilyakov, S. M. and Rodinov, S. I., 1973, Temperature of the orderdisorder transition in the lithium ferrite-aluminate system: Dokl.

Yubilein, Nauchno-Tekh. Konf., Radiofiz. Fa,., Tomsk Univ., No. 3, p. 1111-19.

2. Lithium aluminates—vapor pressure and thermodynamic properties

Broers, G. H. J. and Van Ballegoy, H. J. J., 1969, Phase equilibria in

Li-Na-K carbonate/ aluminate systems: Third international symposium on

fuel cells, Brussels, p. 77-86.

Guggi, D. ; Ihle, H. ; Neubert, A.; and Woelfle, R. , 1976, Tritium

re-lease from lithium meta- aluminate, its thermal decomposition and

phase relationships. Y-lithium meta-aluminate-lithium aluminum oxide

(LiAlcOg). Implications regarding its use as a blanket material in FRT:

Radial. Eff. Tritium Technol. Fusion React . , Proc. Int. Conf. (Watson,

J. S. and Wiffen, F. W., Eds.), V. 3, p. ill 6-32.

Guggi, D. ; Ihle, H. R. ; and Neubert, A., 1976, Thermal stability of

solid lithium compounds proposed for use in CTR blankets: Comm. Eur.

Communities, (Rep.), No. EUR 5602, Proc. 9th Symp. Fusion Technol.,

p. 635-1111.

Guggi, D. J. ; Neubert, A.; and Zmbov, K. F. , 1975, Vaporization

be-havior of Y-lithium metaaluminate: 4th Conf. Int. Thermodyn. Chim.

,

(C. R.) (Rouquerol, J. and Sabbah, R., Eds.), V. 3, p. 124-31.

Ikeda, Y. ; Ito, H. ; and Matsumoto, G. , 1980, Thermal stability of

lithium aluminates by high temperature mass spectrometry: J. Nucl. Sci.

Technol. (Tokyo, Japan), V. 17, No. 8, p. 650-653.

Ikeda, Y. ; Ito, H. ; and Matsumoto, G., 1981, Vaporization and thermochemical stability of lithium aluminates: J. Nucl. Mater.

(Netherlands), V. 97, No. 1-2, p. 47-58.

Iwamoto, N. ; Ikeda, Y. ; Kamegashira, N. ; and Makino, Y., 1979, Vaporization behavior in the lithium oxide-aluminum oxide system: Trans. JWRI

(Japan) V. 8, No. 2, p. 287-288.

Vasil* ev, V. G. ; Borisov, S. R. ; Ryazantseva, N. N. ; and Vashman, A. A., 1980, Investigation of physicochemical properties of irradiated

lithium inorganic compounds: lithium oxide, lithium aluminate and

lithium silicates: At. Energ. (USSR), V. 48, No. 6. p. 392-394.

Vasil'ev, V. G. ; Shulyatikova, L. G. ; Tymonyuk, M. I.; Shiskov, N. V.;

Kozlova, N. M. ; and Zhmak, V. A., 1980, Synthesis and physicochemical

properties of lithium aluminate, titanate, niobate, silicates and

oxide: Izv. Akad. Nauk. SSSR Neorg. Mater., V. 1 6, No. 2, p. 332-334.

44
Veleckis, E. ; Yonco, R. M. ; and Maroni, V. A., 1979, Current status of

fusion reactor blanket thermodynamics, Argonne Natl. Lab., Report No.

ANL-78-109, 3^ p.

Venero, A. F. , 1976, The thermodynamic properties of the spinels

lithium aluminate and lithium ferrite: Diss. Abstr. Int. B, V. 37,

No. 7, p. 1277-8.

Venero, A. F. and Westrum, E. F. , Jr., 1975, Heat capacities and

thermodynamic properties of lithium ferrate (LiO^^Fe2 lithium

aluminate (LiO

5 AI2 50ij) from 5 to 545 K: J. Chem. Thermodyn., V. 7,

No. 7, p. 693-702.

Yudin, B. F. ; Lapshin, S. A. ; Polonskii, Yu. A. ; and Mosilenskii, V. I., 1976 , Thermodynamics of the processes of reduction of AI2 O

2

, Y2 O

3

and SC 2 O0 in lithium vapor: Izv. Akad. Nauk. SSSR Neorg. Mater., V. 12,

No. 11, p. 1985-1990.

3 . Lithium aluminates—processing

Arendt, R. H. and Curran, M. J. , 1980, Molten salt synthesis of lithium

meta-alumina powder (Patent): General Electric Co., Patent No. US

4, 201 , 760.

Bauman, W. C. ; Lee, J. M. ; and Burba, J. L. , III, 1980, Crystalline

lithium aluminates (Patent): Dow Chemical Co., Patent No.

US 4,384,296 A.

Bauman, W. C. and Lee, J. M., 1980, Crystalline lithium aluminates

(Patent): Dow Chemical Co., Patent No. US 4,348,297 A.

Burba, J. L. , III, 1980, Crystalline lithium aluminates (Patent): Dow

Chemical Co., Patent No. US 4,348,295 A.

Burba, J. L. , III, 1980, Lithium aluminates for gas chromatograph

columns (Patent): Dow Chemical Co.. Patent No. US 4,321,065 A.

Burmakin, E. I.; Cherei, A. A.; and Stepanov, G. K. , 1981, Solid

electrolytes in the lithium germanate (Li 2|Ge0 i|)- aluminum oxide system:

Izv. Akad. Nauk SSSR, Neorg. Mater., V. 17, No. 10, p. 1837-40.

Cockayne, B. and Lent, B., 1981, The Czochralski growth of single

crystal lithium aluminate, LiA102: J. Cryst. Growth, V. 54, No. 3, p. 546-50.

Dietrich, W. C., 1968, Determination of lithium in lithium aluminate:

U. S. At. Energy Comm., Report No. Y-1 601 , 22 p.

Dixon, S. , Jr., 1975, Nonlinear properties of aluminum-substituted

lithium ferrite: AIP Conf. Proc., V. 24, p. 485-6.

45
Eichinger, G., 1981, Decomposition mechanisms of some lithium ionic

conductors: Solid State Ionics, V. 2, No. p. 289"295.

Ermenin, N. I. ; Vilyugina, M. D. ; and Makarenkov, V. N. , 1982, Behavior

of lithium in the decomposition of aluminate solutions: Izv. Vyssh.

Uchebn, Zaved., Tsvetn. Metall., No. 3» P* 36-9.

Gazza, G. E. , 1972, Hot-pressing of LiAl^Os: J. Amer. Ceram. Soc., V. 55, No. 3, p. 172-3.

Gurwell, W. E. , 1966, Characterization of lithium- aluminate powders in

J.O. 909 and J.O. 911: DOE Report, No. RL-GEN-1 1 42( W/Del) , 19 p.

Johnson, R. T. , Jr. and Biefeld, R. M., 1979, Ionic conductivity of

lithium aluminum oxide (Li^ AIO 4 ) and gallium oxide (Li^GaOij) in moist

air environments: potential humidity sensors: Mater. Res. Bull., V. 14,

No. 4, p. 537-42.

Kinoshita, K. ; Sim, J. W. ; and Ackerman, J. P., 1978, Preparation and

characterization of lithium aluminate: Mater. Res. Bull., V. I 3 , No. 5, p. 445 - 455 .

Kinoshita, K. ; Sim, J. W. ; and Kucera, G. H. , 1979, Synthesis of fine

particle size lithium aluminate for application in molten carbonate

fuel cells: Mater. Res. Bull., V. 14, No. 10., p. 1357~1368.

Klein, F. ; Gleitzer, C. ; and Aubry, J., 1979, Some properties of

Y-lithium aluminate with regard to its utilization as an electrolyte

support for a high temperature fuel cell: Silic. Ind., V. 44, No. 11,

p. 257-64.

Kvachkov, R. ; Yanakiev, A. ; Puliev, Kh. ; Balkanov, I. ; Yankulov, P. D.

;

and Budevski, E., 1981, Effect of the starting aluminum oxide and of

the method of preparation on the characteristics of lithium-stabilized

3 -aluminum oxide ceramics: J. Mater. Sci., V. 16, No. 10, p. 2710-16.

Maslova, E. I.; Samsonova, T. I.; and Strukulenko, N. A., 1967,

Interaction of oxides in a lithium oxide-aluminum oxide-ferric oxide

system at sintering temperatures: Redk. Shchelochnye Elem., Sb. Dokl.

Vses. (Plyushchev, V. E. , Ed.), p. 230-41.

Mason, D. M. and Van Drunen, J., 1976, Production of 3 -lithium

aluminate (LiA 102 ) (Patent): Inst, of Gas Tech., Patent No.

US 3,998, 939.

Owen, J. H. ; Randall, D. ; Watson, J. S. ; Wiffen, F. W. ; Bishop, J. L.

;

and Breeden, B. K. (Eds.), 1976, Equilibrium and kinetic studies of

systems of hydrogen isotopes, lithium hydrides, aluminum and LiA 102 : International conference on radiation effects and tritium technology

for fusion reactors (Gatlinburg, TN) , DOE Report No. CONF-750989-P3,

p. 433 -457 .

46
Scott, A. J. ; Wessol, D. E. ; and Judd, J. L. , 1983, Preliminary

neutronic calculations for fusion blanket testing in the engineering

test reactor: Nucl. Technol. Fusion, V. 3, No. 1, p. 129~136.

Sharabati, H. ; Hecker, R. ; and Joneja, 0. P., 1982, Tritium breeding

measurements in a lithium aluminate blanket assembly using thermoluminescent dosimeters: Nucl. Instrum. Methods Phys. Res., V. 201, No.

2-3, p. i|45-449.

Sim, J. W. ; Singh, R. N. ; and Kinoshita, K., 1980, Testing of sintered

lithium aluminate structures in molten carbonate fuel cells; J.

Electrochem. Soc., V. 127, No. 8, p. 1766-8.

Sinyh, R. N. ; Dusek, J. T. ; and Sim, J. W. , 1981, Fabrication and

properties of a porous lithium aluminate electrolyte retainer for

molten carbonate fuel cells: Am. Ceram. Soc. Bull., V. 60, No. 6, p. 629-635.

Sooki-Toth, G. ; David, P. ; Lukacs, J. ; Molnar, I.; Horvath, P.

;

Krajcsovics, F. ; Keszler, J. ; Gal, S. ; Pungor, E. ; and Tomor, K. , 197^,

One-step production of Y-lithium metaaluminate electrolyte of hightemperature fuel cells (Patent): Villamosipari Kutato Intezet-Budapesti

Muszaki Egyetem, Patent No. Hungary Teljes HU 9936.

Van der Straten, P. J. M. and Metselaar, R., 1980, Liquid phase

epitaxial growth of lithium ferrite aluminate films: J. Cryst. Growth,

V. 48, No. 1, p. 114-20.

Youngblood, G. E. ; Virkar, A. V.; Cannon, W. R. ; and Gordon, R. S.

,

1977, Sintering processes and heat treatment schedules for conductive,

lithia-stabilized 3-AI2O0 : Am. Ceram. Soc. Bull., V. 56, No. 2, p.

206-21 0.

Yunker, W. , (Ed.), 1976, Extraction of tritium from lithium aluminate:

DOE Report No. HEDL-TME-76-8I , 79 p.

4. Li20—AI2O2

Bruening, D. ; Guggi, D. ; and Ihle, H. R. , 1983, The diffusivity of

tritium in the system lithium oxide-aluminum oxide: Comm. Eur. Communities, (Rep.), No. EUR 7983, Fusion Technol. , 1982, V. 1, p. 543-8.

Byker, H. J. ; Eliezer, I.; Eliezer, N. ; and Howald, R. A., 1979,

Calculation of a phase diagram for the lithium oxide-aluminum oxide

(LIOq^ ^-A10.|

^ 5) system: J. Phys. Chem., V. 83, No. 18, p. 2349“55.

Efros, M. D.; Oboturov, A. V.; and Ermolenko, N. F., 1969, Effect of

lithium oxide additives on the sorption and catalytic properties of

aluminum oxide: Vests! Akad. Navuk Belarus. SSR, Ser. Khim. Navuk, No.

3. p. 98-101.

47
Eliseev, V. B. ; Lyutsareva, L. A.; Pivnik, E. D. ; and Fokina, I. I.,

1979, Properties of b-alumina doped with lithium oxide: Fiz. Khim.

Elektrokhim. Rasplavl. Tverd. Elektrolitov, Tezisy Dokl. Vses. Konf.

Fiz. Khim. lonnykh Rasplavov Tverd. Elektrolitov, V. 3, ^1 P.

Eremin, N. I.; Vilyugina, M. D. ; and Makarenkov, V. N. , 1981,

Solubility of lithium oxide in aluminate solutions: Izv. Vyssh. Uchebn.

Zaved., Tsvetn. Metall., No. 6, p. 26-9.

Eremin, N. I.; Vilyugina, M. D. ; and Makarenkov, V. N. , 1981,

Solubility of lithium oxide in aluminate solutions (translation): Sov.

Non-Ferrous Met. Res., V. 9. No. 6, p. 457-^60.

Eremin, N. I.; Vilyugina, M. D. ; and Makarenkov, V. N. , 1982, The

behavior of lithium during decomposition of aluminate solutions: Izv.

V.U.Z. Tsvetn. Metall., No. 3, P* 36-39.

Fischer, A. K., 1977, Atmospheric pressure synthesis for g-lithium

aluminum oxide: Inorg. Chem., V. 16, No. 4, p. 974.

Fruma, A.; Ciomartan, D. ; Brasoveanu, I.; and Nicolescu, I. V., 1973,

Structure of lithium- and titanium-doped aluminum oxide: Rev. Roum.

Chim., V. 18, No. 5, p. 803 -

8 .

Surdeanu, T. ; Stancovschi, V.; Marinescu, A.; and Crisan, D., 1981,

Reactivity of some aluminas in the production of ceramic products of

lithium oxide-stabilized 6~alumina: Mater. Constr. (Bucharest), V. 11,

No. 2, p. 98-100.

Torkar, K. ; Fritzer, H. P. and Krischner, H. , 1965, Reaction behavior

of various aluminum oxides with lithium carbonate: Sci. Ceram., V. 2,

No. 15, p. 19 -32 .

Vilyugina, M. D. ; Makarenkov, V. N. ; and Eremin, N. I., 1983, A study

of lithium oxide in aluminate solutions at elevated temperatures: Izv.

V. U. Z. Tsvetn. Metall., No. 5, p. 72-74.

5. Li20-Al202 with third component

Abdullaev, G. K. ; Rza-Zade, P. F. ; and Mamedov, Kh. S. , 1983, Lithium

oxide- aluminum oxide-boron oxide system: Zh. Neorg. Khim., V. 28, No.

3, p. 759 - 63 .

Aleixandre-Ferrandis, V.; Fernandez-Navarro, J. M. ; and FernandezArroyo, G. , 1969, Compounds of the phosphorus pentoxide-aluminum

oxide-lithium oxide system. I. Identification by x-ray diffraction and

dilatometry: Bol. Soc. Espan. Ceram., V. 8, No. 4, p. 435-57.

Aleixandre-Ferrandis, V. ; Fernandiz-Navarro, J. M. ; and FernandezArroyo, G. , 1969, Phases in the phosphorus pentoxide-alumina-lithium

oxide system. II. Infrared and DTA study: Bol. Soc. Espan. Ceram.,

V. 8, No. 5, p. 511 -23 .

48
Burmakin, E. I.; Stepanov, G. K. ; and Pazdnikova, L. P., 1978, Structure of solid electrolytes in lithium silicate (Lii^siOii) -aluminum oxide

and lithium silicate (Lij|SiOij) -aluminum oxide-lithium oxide systems:

Tr. In-ta Elektrokhimii Ural'sk. Nauch. Tsentr AN SSSR, No. 27,

p. 72-7.

Cismaru, D. and Manolescu, D., 1970, Structure studies of solid solutions in the system Al203 -Cr203 -Li20 : Rev. Roum. Chim. , V. 15, No. 2, p. 291-5.

Efros, M. D. ; Oboturov, A. V.; Ermolenko, N. F. ; and Kramarenko, F. G.

,

1971, Effect of lithium oxide on the phase composition, structure and

sorption properties of mixed aluminum and zinc oxides: Dokl. Akad. Nauk

Beloruss. SSR, V. 15, No. 3, p. 228-31.

Enriquez, J. L. ; Quintana, P. ; Vazquez, J. ; and West, A. R. , 1982,

Subsolidus phase equilibriums in the systems lithium oxide-sodium

oxide-zirconium oxide and lithium oxide-aluminum oxide-zirconium oxide:

Trans. J. Br. Ceram. Soc., V. 81, No. 4, p. 118-21.

Ermolenko, N. F. ; Efros, M. D. ; Kramarenko, F. G. ; Lemeshonok, G. S. ; and Kuz’mich, E. I., 1970, Effect of lithium oxide on phase transformations in the aluminum oxide-nickel monoxide system: Kinet. Katal.,

V. 11, No. 6, p. 1577-80.

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Conf. Liq. Met. Technol. Energy Prod., V. 2, No. 2, p. 18~9 to I 8

- 7 .

Migge, H. , 1983 , Thermodynamic stability of aluminum ceramics in

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Technol. V. 1, p. 655-61.

Pavlyuchenko, M. M. and Popova, T. I., 1969, Effect of the gas phase

on the thermal stability of lithium peroxide: Dokl. Akad. Nauk

Beloruss. SSR, V. 13, No. 2, p. 133~5.

Rohde, L. E. ; Choudhury, A.; and Wahlster, M., 1971, New investigations on the Al-0 equilibrium in iron melts: Arch Eisenhuttenwesen, V. 42, No. 3, p. 1 65-1 74.

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58
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59
1

Table 1 . Phases in the System Li-Al-H-Li20-Al203-H20

i!

I (a) Solids with Published x-ray Powder Diffraction Data^

Phase Thermochemical Data as f(T)^^ Comments^

Li X melts 453.7 K

A 1 X melts 933.5 K

LI3AI2 melts incongruently 793 K ( 4 ) LiAl X melts 973 K ( 4 )

melts incongruently 608 K ( 4 ) LiH X melts 961 .

8

K

LiAlijH^^

LiAlHii X decomposes 4 l 0 K

Li

3 AlH5

AIH3

L i 20 X melts 171 1 K ( 9 )

AI2O3 X melts 2327 K

aLi^AlOii

8Li^A10ij

aLiA102

BLiA102

yLiA102 X melts 1973 K

L iAl^Og

LiOH X melts 744.3 K

Li0H*H20

ai(oh)3

60
Table 1. Phases in the System Li-Al-H-Li20 -Al203 -H20 (continued)

Phase

Li(S,)

AKS,)

^2(8)

LiH(Jl)

Li20(S,)

AI2O3 ( £,

)

LiA102(jl)

H20(g)

LiOH(jO

(b) Selected Gases and Liquids

Thermochemical Data as f(T)^

X

X

X

X

X

X

X

X

X

^Source of x-ray data is Powder Diffraction File , 1 983 : JCPDS—International Center for Diffraction Data, Swarthmore, PA.

^Source of thermochemical data is JANAF Thermochemical Tables ; Nat.

Stand. Ref. Data Ser., Nat. Bur. Stand., ^ (June 1971; updates from

Dow Chemical Company)

.

“^Unless otherwise noted, data on melting or decomposition came from footnote ’b’ above.

61
Table 2. Calculated Reactions at HOOK in the System Li-Al-H-Li20-Al203 -H20

Conditions

Subsystem (atm) Reaction - - AG{^(Kcal)

Li-Al-H 1 1/2-H2(g) + LiAKS,) LiH(S,)+Al(S,) -0.038

Li-Al-H 10 1/2-H2(g) + LiAl(£) ^ LiH(fi,) + AlOO -2.555

Li-Al-H 100 1/2-H2(g) + LiAl(£) ^ LiH(S,) + AlOO -5.071

Li20-Al203 ~H20 1 2LiOH(iO + Al203(c) -> 2LiA102(c) + H20(g) -27.101

Li20 -Al203 -H20 10 2Li0H(£) + Al203(c) ^ 2LiA102(c) + H20(g) -22.071

Li20 -Al203 -H20 100 2Li0H(Jl) + Al203(c) ^ 2LiA102(c) + H20(g) - 17.070

L i~A 1~L i20“Al203 1 i1Li(jO + 2Al203(c) 3LiA102(c) + LiAl(S,) -49.157

L i~Al“L

i

20~Al203 1 2Li20(c) + HAlU) ^ LiA102(c) + 3LiAl(ji) - 15.687

L i~Al“L

i

20“Al203 1 2Li20(c) + LiAl(£) -> J4Li(i!,) + LiA102(c) -9.627

L i“Al~L

i

20 ~Al203 1 3LiAl(j^) + 2 Al203 (c) ^ 3LiA102(c) + HAlU) - 43.097

Li-H-Li20-H20 1 2Li(iO + H20(g) ^ LiOH(jl)+LiH(JO -34.439

Li-H-Ll20-H20 10 2Li(£) + H20(g) -> LiOH(iO + LiHOO -39.469

Li-H-Li20-H20 100 2Li(S,) + H20(g) ^ LiOHCiO + LiHOO -44.470

Li-H-Li20-H20 1 Li20(c) + H2(g) Li0H(JO + LiHOO +29.042

Li-H-Li20-H20 10 Li20(c) + H2(g) LiOH(iO + LiH(£) +34.075

Li-H-Ll20-H20 100 Li20(c) + H2(g) ^ LiOH(ji) + LiH(£) +39.108

Li-H-Li20-H20 1 Li20(c) + LiH(jO -> Li(S,) +.Li0HOO +32.148

Li-H-Li20-H20 10 LiH(iO + H20(g) ^ Li0H(ji,) + H2(g) -

31 .33

H-AI-H2O-AI2O3 1 3H2(g) + Al203(c) 3H20(g) + 2Al(i!,) + 183.335

Li-Al-H-Li20-Al203

-H2 O

1 LiA102(c) + i|LiH(iO 2Li20(c) + LiAKS,)

+ 2 H2 (g)

+ 15.839

L i~A 1~H“L i20“A

I

2 O3 -H2 O

10 LiA102(c) + ALiHOO - 2Li20(c) + LiAKiO

+ 2 H2 (g)

+25.905

Li-Al-H-Li20-Al203

“^20

100 LiA102(c) + ilLiHOi) 2Li20(c) + LiAl(iO

+ 2H2(g)

+35.971

^Calculated using data in JANAF tables; data for LiAl(Jl) estimated using ideal

solution approximation; hydrogen assumed to behave ideally.

62
Table 3 . DTA effects observed in the Subsystem Li20-LiA102

Composition (mol$) Temp. («>C) Type^ Magnitude^* Comments

(Li20)ioo 14^16 ± 3 N 81

( Ci20)g5( Al202)5 480 X(H) 4

( L.i20)95( Al202)5 540 X(H) 6

( Ci20)95( Al203)5 790 N(H) 15

(Li20)g5( Al203)5 1210 N — Onset of event

( Li20 )g 5

( AI2 O3

)

5 1365 N 15 Estimated termination

(Li20 )gQ( AI2 O

3 ) 1 Q 465 X(H) 4

( Li 20 )gQ( AI2 O

3 ) 1 Q 527 X(H) 8

(Li20)go(Al203)io 778 N(H) 18

( Li20 )gQ( AI2 O

3

) 1 Q 1110 N 33

( Li20 )gQ( AI2 O

3

) 1 Q 1300 N 5

( L.i 20 )g 5

( AI2 O

3 ) 1 5 455 X(H) 12

( Li 20 )g 3

( AI2 O

3

)

1

3

500 X(H) 8

( Li20 )gg( AI2 O

3

)

1

3

775 N(H) 24

(Li20 )g 5 (Al203 )i 5 1126 ± 10 N 1 60

(Li 20 )go( Al203)2o 482 X(H) 8

(Li20)go(Al203)2o 525 X(H) 6

(Li20)go(Al203)2o 81 5 N(H) 31

(Li20)go(Al203)2o 947 ± 1 N 2

(Li20)go(Al203)2o 1057 ± 3 N 90 i Two peaks overlap

partially

(Li20 )gQ( Al203)2o 1095 ± 10 N 20 }

( Li20)y3( Al203)25 478 X(H) 16

( Li20 ) yg( AI2 O

3

) 25 520 X(H) 8

63
Table 3. DTA effects observed in the Subsystem Li20 -LiA 102 (continued)

Composition (mol?) Temp. (°C) Type Magnitude

(Li20 )y5

( Al203)25 81 0 N(H) 19

( Li20 )y5

( Al203)25 1026 ± 6 N 224

( bi20 )yQ( AI2O3) 30 470 X(H) 12

( Li20 )yQ( Al203 ) 3 Q

521 X(H) 3

( 1^120)70(41203)30 805 N(H) 22

( 0120)70(41203)30 950 N(H) 1

(Li20 ) 7 o( Al203)3o 1050 ±2 N 85

(Li20 )g^( Al203)35 480 X(H) 3

( Li20)g5( Al203)35 525 X(H) 4

( Li20 )g 5

( AI2 O3) 35 81 5 N(H) 7

( Li20 )g 5

( AI2 O3) 35 1053 N 49

(0120)60(41203)40 480 X(H) 3

(0120)60(41203)40 520 X(H) 2

(0120)50(41203)40 816 N(H) 8

(0120)60(41203)40 956 ± 10 N 1

(0120)60(41203)40 1056 ± 4 N 48

( 0 i 20 ) 66 ( AI2 O

3

) 46 1054 ± 5 N 19

Comments

= endothermic

X = exothermic

(H) = initial heating cycle only

*^Approximate amplitude of thermal excursion, in mV

64
Table 4. Sequential Heat Treatments of High Alumina Compositions^

Composition

(mole ratio)

Li 2 C0 o :Al202

Heat

Treatment (°C) Duration (hr) X-ray analysis

50:50 500 40 Li 2 C03 + AI2 O

3 + L 1A 102

50:50 700 16 a-LiA 102 + y-LiA 102 + AI2 O

3

( +tr .Li 2 C03 )

50:50 700 24 a-LiA 102 + y-LiA 102

50:50 800 3 y-LiA 102

50:50 850 5 y-LiA 102

50:50 1000 60 y-LiA 102

50:50 1 400 4 y-LiA 102

50:50 1 500 0.5 y-LiA 102

1

50:50 1600 1 y-LiAL02 (no melting)

50:50 575 768 a-LiA 102 (+tr.Al203 + tr.Li2 C03 ) — — — — — — — — — — — — — - —— - — — - “ " ~~

33:67 700 20 (not x-rayed)

33:67 1 000 72 y-LiA 102 + LiAl^Og

33:67

f

1 000 1 y-LiA 102 + L 1A 1503

>

- _ (no melting)

(17.3) : (82.7) 700 24 LiAl^Og

(17.3):(82.7) 1000 168 LiAl^Og

(17.3):(82.7) 1400 16 LiAl^Og + unidentified peak

(17.3):(82.7) 1600 1 LiAl^Og + unidentified peak

(17.3):(82.7) 1 600 ,2

(sealed capsule)

|

LiAlcOg (unidentified peaks

disappeared)

(17.3):(82.7) 1 600 12

Y (unsealed capsul^ 1

(16.7):(83.3) 700 24 LiAl^Og (no unidentified peaks)

(16.7):(83.3) 1000 168 LiAl^Og (no unidentified peaks)

(16.7):(83.3) 1400 16 LiAl^Og (no unidentified peaks)

Y

(16.7):(83.3) 1600 1 LiAl 50g (no unidentified peaks

and no melting)

65
Table ^4 (continued)

^Unless otherwise noted, these experiments were performed in a rapid-fire

muffle furnace using a large smple (up to several grams) in a covered Pt

crucible; mechanical homogenization was completed between heatings at lower

temperatures for many of the experiments.

66
Table 5. Experiments in Sealed Mo Tubes, in Tungsten Furnace

Composition

(Mole ratio Li20:Al203)

50:50

50:50

50:50

33:67

33.67

33:67

33:67

33:67

17:83

17:83

17:83

Temperature (°C) Duration

1725 3

1765 3

1805 3

1600 1 1725 3

1805 1

1 665 1 1630 1

1725 3

1765 '1

1805 1

(hr) Observtions

no melt

partial melt

complete melt

no melt

complete melt

complete melt

complete melt

sintered or possible

partial melt

no melt

sintered or possible

partial melt

partial melt

67
Table 6. Results of Rietveld Refinement^ of LiAl^Og

(a) Summary

Space Group =

Rw = 0.077

a = 7.9036(1) A

Structural formula = A0^^( Lii|Ali 2)^^®32

(b) Tetrahedral cations*^»^

8 A1 at position 8(c) at (x, x, x); with: x = -0.001 Il(6)

B = 0.23(6)

(c) Octahedral cations

12 A1 at position 12(d) at (1/8, x, 1/4-x); with: x = 0.3689(5)

B = 0.35(8)

4 Li at position il(b) at (5/8, 5/8, 5/8); with: B = 2.3(^)

(d) Anions

2U 0 at position 2^(e) at (x, y, z); with: xy

zB

0.1145(3)

0.1330(3)

0.3842(2)

0.28(4)

8 0 at position 8(c) at (x, x, x); with: x = 0.3854(3)

(e) First coordination distances D (in A)

A1 in 12(d) to 2 0 in 24(e)

A1 in 12(d) to 2 0 in 24(e)

A1 in 12(d) to 2 0 in 8(c)

1 .850(4)

1.911(2)

1.943(7)

A1 in 8(c) to 3 0 in 24(e)

A1 in 8(c) to 1 0 in 8(c)

Average of 6 distances 1.901 t 0.042

1.77(5)

1.83(7)

Average of 4 distances 1.785 ^ 0.026

Li in 4(b) to 6 0 in 24(e)

68

2.042(2)
Table 6 (continued)

(f ) Second coordination sphere D( in A)

A1 in 12(d) to 4 A1 in 12(d) 2.829(3)

A1 in 12(d) to 2 Li in il(b) 2.761(3)

A1 in 12(d) to 2 A1 in 8(c) 3-32(3)

A1 in 12(d) to 2 A1 in 8(c) 3-27(3)

A1 in 12(d) to 2 A1 in 8(c) 3-23(3)

Li in 4(b) to 6 A1 in 12(d) 2.761(3)

Li in 4(b) to 6 A1 in 8(c) 3-287(3)

A1 in 8(c) to 3 A1 in 12(d) 3-23(3)

A1 in 8(c) to 3 A1 in 12(d) 3-27(3)

A1 in 8(c) to 3 A1 in 12(d) 3-32(3)

A1 in 8(c) to 3 A1 in 8(c) 3-409(5)

A1 in 8(c) to 1 A1 in 8(c) 3-461(5)

A1 in 8(c) to 3 Li in 4(b) 3-29(1)

^Rietveld, H. M., J. Appl. Crystallogr. £[1]65 (1969).

*^Hahn, T. (Ed.), International Tables for Crystallography . Volume A; Dordrecht,

Holland, D. Reidel Publ. Co. (1983), P- 638 .

is isotropic thermal parameter.

69
Table 7. Results of Calcining High-Lithia Compositions Under Vacuum^

Composition

(Mole ratio Li20 :Al203 )

Temperature

(°C)

Duration

(hr)

X-ray

Analysis

90:10 900 56 YLiA102, SLi5A10ij,

Li20 , unidentified phase

83:17 700 6 aLi^AlOii, 3LiA10i(,

L1 I 2

O, Li2C02» YLiA102

83:17 800 6 Li20, YLiA102» 3Li5A10ij

83:17 800 6 othicA10i|, 3Li5A10i|,

YLiA102, Li20

83:17 900 23 YLiA102, 3Li5A10i,

75:25 800 15 Lii20, YLiA102» 3hi5A10i}

^Lithium carbonate starting material; final vacuum 5 X 10"6 torr.

70
Table 8. Results of Quenching Experiments in Sealed Pt Tubes

Composition Heat Treatment^ Phases Present in

(Mole % Li20) (°C) X-ray pattern^

95 900 Li20 + YL 1A 102 (+ tr. LiOH)

95 1000° Li20 +

' 1^^102 (+ tr. LiOH) + A unidentified phase with peak at 23.70

95 1 050 Li20 + YLiA 102 (+ tr. LiOH) + unidentified phase with peak at 23.70

90 900 Li20 + YLiA 102 (+ tr. LiOH)

85 700 aLi

5 A 104 (+ tr. LiOH)

85 750 aLi^AlOif (+ tr. LiOH)

85 800 aLi^AlOii (+ tr. LiOH) + unidentified

phase with peak at 22.20°

85 850 aLi^AlOii (+ tr. LiOH)

85 900 BLi^AlOn (+ tr. LiOH)

85 900 BLi^AlOii (+ tr. LiOH)

80 700 BLi^AlOij + YLiA102 (• tr. LiOH)

80 700 oLi^AlOij + YLiA102 ( + tr. LiOH)

80 750 ctLi^AlOij YLiA102 (• tr. LiOH)

80 800 BLi^AlOii + YLiA102 ( + tr. LiOH)

80 850 otLi^AlOii + YLiA102 (* tr. LiOH)

80 850 BLi^AlOij + iLiA102 (' tr. LiOH)

80 900 BLi^AlOij + YLiA102 (• tr. LiOH)

80 900 3Li5A10i, + XUIO2 ( + tr. LiOH)

80 900 otLi^AlOii + YLiA102 (* tr. LiOH)

75 800 BLi^AlOii + YLiA102

75 1000 BLi^AlOij + YLiA102

60 900 YLUIO2 (+ tr. LiOH) 4 undentified phase

with peak at 18.60°1

55 900 YLUIO2

+ BLiAlOn

55 900 YLiA102 + BLiAlOii

^imes of heat treatment were variable, from a few hours to a few days

'^X-ray work completed using CuKa radiation

^runs partially melted

71
Table 9. Second and Third Law Heats of Reaction and Second Law Entropy

of Reaction for Equation (14).

Experiment AH(298)

kcal/mol

AS(298)

Gibbs/ mol

AH(298) 3rd law

kcal/mol

825D 131 .4 ± 5.2^ 48.21 ± 3.30 115.3 ± 0.3

8261 88.1 ± 6.5 22.89 ± 3.95 113.5 ± 0.6

82612 103.2 ±1.0 31 .29 ± 0.59 115.0 ± 0.3

826D 109.0 ± 0.8 34.28 ± 0.48 11 5.7 ± 0.2

901 I 97.8 ±1.1 28.93 ± 0.63 113.6 ± 0.4

901 D 110.7 ± 1.4 35.75 + 0.79 115.0 ± 0.1

9021 101 .9 ±1.4 30.21 ± 0.87 115.3 ± 0.3

902D 115.2 ± 0.9 36.97 ± 0.53 117.3 ± 0.1

^ Uncertainties are standard errors

Table 10. Second and Third Law Heats of Reaction

of Reaction for Equation (15).

and Second Law Entropy

Experiment AH(298)

kcal/mol

AS(298)

Gibbs/mol

AH(298) 3rd law

kcal/mol

91 21 126.

1

+ 9.1^ 41 .62 ± 5,.57 124.9 ± 0..3 91212 108.7 ± 2.7 31.45 ± 1 ,.59 125.0 ± 0.,4

91 2D 127.

1

± 4.1 40.55 ± 2,.35 127.6 ± 0.,2

1041 110.3 ± 1.9 32.28 ± 1

.

.91 125.6 ± 0.,4

104D 130.3 ± 1.6 42.25 ± 0,.92 127.8 ± 0..1 1051 124.5 + 3.0 39.12 ± 1 ,.66 127.6 ± 0..3 105D 131 .3 ± 1.5 41 .92 ± 0..84 129.3 ± 0., 1 10141 106.3 ± 1.9 27.1 4 ± 1 ,.11 130.8 ± 0.,8

101 71 102.4 ± 3.5 25. 16 + 1 ..90 131 .2 ± 1

.

.0 1017D 124.4 ± 1 .0 36.16 ± 0..56 133.2 ± 0.,2

^ Uncertainties are standard errors.

72
Table 11. Third Law Heats of Reaction (at 298K) from Various Workers.

Reaction A Reference kcal

Reaction B

kcal

Reaction 0

kcal

Guggi (25) 109.4 119.9 128.3

Ikeda (31) 107.3 118.5 125.3

Potter (27) 120.8 131 .8

This Work 117.3 127.8

Reactions

A. 1/4 Li5A104(c) = Li(g) + 1/4 02 (g) + 1/4 LiA102(c)

B. 5/4 LiA102(c) = Li(g) + 1/4 02 (g) + 1/4 LiAl50s(c)

C. LiAl508(c) = Li(g) + 1/4 02 (g) + 5/2 Al203(c)

Table 12. Reference Thermodynamic Data (8)

Material AH^ (298.15), kcal/mol

^ 1203 ( 0 , a) -400.500

Li(g) 38.140

Li20(c) - 143.100

LiA102(c) -284.100

Table 13 . Heats of Formation (at 298K) from Vapor Pressure Data

-AhJ. LUI5 O

8

0 — AH^ LiA102

0 -AHf LiAl^Oi^

Reference kcal/mol kcal/mol kcal/mol

Reaction 0 Reaction B Reaction B Reaction A

This work 1090.7 1104.9 281 .3

Potter (27) 1094.7 1090.9 284.9

Guggi ( 25 ) 1094.5 1 094.5 283.4 568.9

Ikeda (31) 1088.2 1100.1 281 .7 560.7

JANAF (16) 284.1

Average 1091 .2 1097.6 282.8

73
Table

1^1.

Gibbs

Enegies

of

Formation

for

Lithium-Aluminum-Oxygen

Compounds

(Model 3

Data

Base)

LO CO oo

cy. CJV ,

o CO CO t CM CO VO

T cr> o t- in oo O CJV in cr> Ov C7V OO

ITi LO oo in od CTv o VO o\ in oo o OO o in CM in in in in in VO oo VO oo CO 0- vO oo VO oo

-=r CO CO CO CM OO in CO in VO oo

C\J1 1 1 CM1 T

CM1 001 T

CM o oo cr> VO in oo CO in

ITi CO VO 0- CTV ,

VO C-- ^

VO Ov

VO LTl CMn ,<T> CM CM CT\ C-- o^ , CM 0- o VO CO C7V CO CO

cr. 0- Ol ^ VO t~- ^ VO oo

VO CTv CTiO (OV in

Cd oo >- CM o >- o CMO o in o O O O o o ,

O O ^o o o O o o o o O O o o o o O o o o o O O o o 01 01 01 01 o 01 01 o 01 O 01 01 o

CO

E-2 VO OV o in in VO CJV in in a\ VO ,

Cd CM cr> CO ,

0- OO CM

T

o CM in

M oo OO in oo CM o vO o VO VO o VO VO o CO in M Q LTi oo ,

C3V ::T CM CJv o T CXd CTV ov ov CM CM CTv CM O in T ELi Cd VO oo oo in r— oo CM o in O CM o CM O r— 1 V

1 ^ r— o

CO ir> vO in CM CTv o OO CM

O

C-- VO o ov 0- OV t- oo in C7V ooO

LO 0C5 CM o C7V CTv OJO r— in , VO , oo ^

OV CTv C7V CTv in

O o OO OO in in oo O in OO in ,

CM CO c~- t- CM o CO in CM in in CO 1>- CM CO CO oo t oo oo 1 OO CM O o o o o o o o o o o o o O o o o o o o o o o o o o ^ VO 00 t

c- (Ov CTv o VO in OV CO o OvJ CTv oo OO o CM CTV VO OV

DQ in CO OV

O CO ,— t CTv in ,oo CJV XT a\ oo in T oo CT> CM in vO CM CM t- in Ov ^ in VO CM C3V T c~- CM 001 t-1 t-1 CM1 tr-1 CM1 1 CM1 1 CM1 in1 001 o o o o O o O O O o o o o o o o o O o O O o o o o o o o o O o O O o o o o o o o o o o O O o o o o

in o CTv ,— CO VO Ov oo VO in

"SC oo oo CM CM in OO CM in oo oo (JV in OO (Ti in O oo CM in oo CM VO CJV 00 OO VO t Ov VO 1 •=r oo CO VO oo OO o in oo VO o VO ,

o o ,— V— CO ,

oo oo oo VO o

CM CM 1 OJ '

<=.? oi

N CO CO X—N

CO •—

CO c>? s CO CO oo r—

N

Id /«-N bO oo

V /- o?

O o CM o CO o M bO bO V—' o oo 'W' in rH o cn in 'w' fH o o rH o o 1^ < o rH o <

Cd o CM CM < CM CM <c in < CM < CM in

Ou •rH •«—f

•rH iH •rH •rH 1—

H

•rH •rH •rH 00 J j J J < J J J < J J J

74

Coefficients

are

quoted

in

joules

to

yield

rounding

of~

400 J

(0.1

kcal)

and

are

for

the

following

equation:
Table

15.

Gibbs

Energy

of

Formation

(kcal/mol)

at

Temperatures

(K)

for

Model

3

Data

Base

in in C7^ CT« o~ -=r o in in CM Oo o CM o^ o in CO in -=r MO on on b- on o CO CM ^ -=T in o b- b- in b- oo o• CO CO on MO b- b- b- in b- on o

C\J 1 on in on in on CM in on on in MO

1 ^

1 CM

1

1 MO

1 m 1 CM

1 MO

1

1 OJ

1 m m (7\ VD .=r o (OO CM M) MO b- o^ in CM MO in in o CO in JT ^ o CM CM CO COO CM oo .=r o on in JT o

o

CM vO O MO COO MO CM ^

CJO CO b- CO

<\l 1 , ^ MO on in •=r on MO on 3T in b1

1 OJ1

1 MO

1 on1 1 CM

1 MO1

1 CM

1

CO MO in o on CM in o JT CJO o 0- CM CO coo -cr CJO on 3T in t

o o CM CM .=r 1— T CO CM in o T ir> o CM in oj in o CM MO b- .=r on CJO t

d

eg 1 r— ^ MO .=r MO in on MO ::r in MO CO

1

1 CM

1

1 MO

1 m1 1 CM1 M)

1

I CM

1

CO CM oo MO CO MO OJ CM in

^

<T> CO CO in in on on CO CJO on CO on o ^— cr> c7^ in MO 0- in CO b- O MO MJ on o

o cn on on CO on in in r— CO b~ o rr o

C\J 1 1

ZT MO .=r MO MO .=r MO JIT b- MO CJO

1

1 CM1

1 MO

1 on1 T

CM

1 MO

1

1 CM

1

CO on erv o O OJ CJO oo b- CO JT o

on CTi in MO MO .=r CO t

b- in CO on MO o in CO CO O o oo in MO oo b- cn MO

tn

CTi on CM in 0- Oo MO CM o ^ CO o

t— 1 «— ^3- 0- -=T MO b- -=r b- in 00 MO o 1

1 CM1

1 MO

1 on

1 1 CM

1 MO1

1 on

1

CTi C3^ C~- CO MO c- on 00 in b- in on 00

in o^ OJ CM CO on MO o MO CM in CJO b- o o^ 0- 0- on -or on -=0 CM in CO CJO CJO o

o

o> m t— in O CM r— MO -T CM ^ ,—

r— 1 t— in OO in b- in CJO b- X—

1

1 OJ1

1 MO

1 on

1 T

CM

1 MO

1

1 on

1

0- 00 MO in MO in b- on CM M> O CM vO CM 0- CO on CM CJO O o in b- o on 0- in MO coo MO (OO CO b- ^— MO in

in CO o coo oco on in on in o CO T- in

1— 1 t— =T in b- CJO in CO in o CM

1 CM1

1 MO

1 on1 T

CM

1 b1

1 on

1

C7^ T- O o M) MO in b- MO CJO CM o .=r O 0- CM r— MO r CO CJO CO O b- j o c~- on o .=T CO on in CM in CM OJ CO

r— .=r C7^ CM CO on o .=r CM in CJO OJ

1 in CO in b- o MO CO M) r— b- on T

CM

1

1 b1 on

1 1 OJ1 b1

1 on

1

=T on coo MO .=r in MO CJO CM (JO o CO 00 b- O on 3T b- ^— M> CM in in m o 0- o on COO o MO CM r— T- CM oo MO

ein CO on in O CM CM in CO MO MO CM CM

1 in COO MO OO r— MO CO MO CM CO T1 CM

1

1 b1 on

1 I CM

1 b1

1 on

1

W CO oi y«—

V

Nw'' CO —

s

—s o? CO y=r 0 00 on .=r bO CM o O OJ o CO o V.wX bO bO O onw in'—

1

o on LTo-y

'w' O >-1 o o rH < rH o r—

1

o <

O (\ CM< c\ CM< in< CM< CM in

•iH •iH *<—} «iH »—

1

•iH •rH •(—1 1-f < -j <

75
Table

16.

Representative

Computer

Model

Output

for

the

Equimolar

Li20

-Al

203

Mixtur

c» >sD ^ on o

in ov 05

O <D

D. o O b- on o ov on o ^

t^ ov o o •=r o o o on CO OO o Cb VO OV CM ,

^ o CJ5 ^ O o o on on o OO ^

b- CTi o <T> b- o o

bOo ^

in OV OO 00 t— C7\ o OO 0C5 CO in

r—1 1 CM on CM CM on

CO

O =r CM CM o rH b- O 00 on b- o

CO o o on in C3V o OO o CTl o 00 in T- in CM o o o o on CM VO o ^

in in t o lOV VO o CJ5 ^ o o o OO »- o on -:3- on VO CO on VO VO CO 05 o

on CM ov ^ ^ Cb in on C7V o bl 1 ^ t>- 00 b- in OO b- o

E- 1 t— CM 1 VO on

— CM VO 1 on 1 1 1 1 1 1 1 1 O<

in

O vO in on CM CM o on b- CM o o o ^ O o o o o O O o o o o o o o o o o o o o o O O o o o o o o >H 1 1 1 1 1 1 1 1 1 1 1 + 1 1 1 1 1 E- CTl ,

on 00 in ,

VO in o ^ o in in on

n CTi CT> o in OO in ,

OO OO <y\ VO o X « X

— VO > CO CM o CO ::T OO OO on cri on b- o OO in OO b- M cr> CM OO on Cjv in CM T CO b- VO o VO o o VO bCT> in CO on OO OO in t

on b- o on cjv o CJ5 00

O< o^ QO CM in on OO •- on VO on bl VO zoM

r- in o VO in E-> O on CM CM o o o t— o o o o o O O o o o o o o o o o O O S

E- 1 CT> 1 1 on 1 OO 1 in 1 1 1 VO 1 1 in

«a: CT> cri o in OO in ^

CO OO CTi VO

OO CM o OO =r OO CO on CJN on ba. o^ CM CO on cr> in CM ^

OO b- VO

o^

m 00 on OO CO

Os in •- on ^ bCOi tC. CO CM in «- •- on OO O in 0- o VO in O o o t— o o O o o o o o J + 1 1 1 1 1 in b- in in o o to- on ^

in on o o O o o o S o VO Ov OO c- o o O o o o \ o on o CO in OO 1 1 1 1 1 + o CM OO on ov in vO b- O in ib- in o o o o o o in OO on OO CO o , on b- VO o o o o o

t>- OO CM in o OV o o o o o r— C-- OO CM in r— OO CO in OV o o o o o

OO VO o cr> o o o o o , CM OO CM o ,

,

— o o o o J o o o o c Q + + + + 3 S o o o o o o o O o O o o o o o o o S- \ o o o o o o o O o O o o o o o o o * o o o o o o o O o O o o o o o o o t. X o o o o o o o O o O o o o o o o o 05 o o o o o o o O o O o o o o o o o 4-> :3 T— , , D.eoo e CM

4-> y—S

y—V

y—

N

y—\

CM

CO y—No? o? y—N 05 05 \

LTl o? y^ 05 y—N

M ^ o O? y»“«s CO -=r w05 00 nc • y—V

bO CM

w o? o o CM

O 05 o 1 T y*-V /—V

bO bO y—V o (Y>LOi—1 O on in^ rH yr^N o

bO bO o bO r-H o o rH < rH

O >H o *=C o? 1—1

II II NwX N.-y'

O C\ CM < CM OvK in < OvK CM in^

J- •rH •rH •rH CM •rH t 1 •rH •rH •rH •rH rH »rH •rH •rH rH -j

E- CL, < -j

O < J -J < j < o

II

76

Computer

notation

used

for

exponents,

eg.

1.00000+001
77
1/2 02 1/2 02 1/2 02

Figure 1

Alternative representations of Phases in the (Li, Al) alloy reaction

system.

78
1/2 02 1/2 02

Figure 2

Representation of important phases in the Li-Al-H-Li20-Al20-H20

portion of the system Li-Al-O-H.

79
H20(g) Al 203 (c)

Flgxire 3

Schematic 1100 K phase diagrams

for the ternary boundary systems

of figure 2 (based upon calcula**

tions in Table 2)

.

60
LiOH(^) H^OCg)

Figure ^

Major features of phase compatibility in the system Li-AlH-Li20-Al203-H20 at 1100 K: extent of solutions is not

indicated.

81
LiA102 ^2°

Figure 5

Predicted products of the equilibrium reaction of (LiAl) alloy with

water at 1100 K.

82
T

CC)

2200

2000

1800

1600

1400

1200

1000

800

600

400

200

LisO - AI2O3 SYSTEM

Liquid

X'

\

\ ^DTA/7GA

) r-\

\—L

J

/

XQuAay

nch

iO

X—r^y Crya|t

_w_

Knudsen Effusioa

Predictive Solution Model

in

allogrpphy iJ 1. 0

U2O

20 40 60

Mol. %

80 100

AI2O3

Figure 6

Interim phase diagram based on the approaches used in investigating

various portions of the phase diagram (indicated in the boxed areas).

83
L I ] 0 I 2

centimeters

Figure 7

Experimental geometry for DTA measurements showing Pt Cells, Pt-10$

Rh thermocouples, and the alumina support structure.

84
differential

signal

<- increasing temperature

Figure 8

Method used in defining temperature of thermal affects.

85
(Oo) 1

U2O Mol. % AI2O3

Figure 9

Plot of DTA effects, with tentative interpretation.

86
differential

signal

decreasing temperature -c Increasing temperature

Figure 10

DTA analysis of (Lion^o^ / a i s 20)80 (Al203)20 composition.

87
differential

signal

Figure 11

DTA analysis of (Li20 )g 5 (Al203)5 composition.

88
(Oo) 1

2200

2000

I

'

' ^ Liquid

1

^ " a-Al203 _

1800|

i + LIq _

^ 1:1+LIq ~ ^ ^ '1:5+Llq ^ ^ 1:5 +

1 600< >— 0 < > a-Al 203 —

1:1 + 1:5

1400 —

1200 —

1000 —

800 —

600 —

400

in ~

200

I 1 1 \

1 50 60 70 80 90 100

Ll20*Al203 Mol. % AI2O3

Figure 12

Results of high temperature experiments in sealed capsules for

alumina-rich compositions. Solid, half-filled and empty circles

represent, respectively, complete, partial and no melting.

89
JwAj H

1

,

1 1 100 *

110*

Figure 13

Neutron diffraction pattern for

LiAl 50g annealed at 1600 °C.

Degrees 20 vs. intensity.

Horizontal tics correspond to

intensity of 1000. A mono- chromatic beam with mean neutron

wavelength of 1.5416(3) A was

used.

90
•o

0

4

If

17

0

Otc/gtn

T0trahsdral atwrtruM

O ]

]

OcXahtd>inl vacoACilA

OclahtdAoi. dXKium

Ootahtdral alttwimmi

20 12 4

Figure

Projected structure of LiA 1^ 03 , from Rietveld refinement (see Fig. 13

and Table 6). Numbers indicate ”Z" coordinates in thirty-seconds. Oxygen

coordinates are at left and right of atom positions, octahedral vacan- cies and octahedral lithium are at top, and octahedral aluminum is at

bottom. Open or dashed symbols indicate atoms beneath oxygen.

91
TEMPERATURE K

2000 1000 1600 1400

ioVt k

Figure 15

Li pressure versus 10^/T for increasing and decreasing tempera

ture series, 9011 and 901 D, showing non-reproducibility in Li

pressure with increasing or decreasing temperature run chronol

ogy.

92
2000

TEMPERATURE (K)

1667

io-< _

3 10-5

*—<

oc3

inui

a:

a.

T—r—

r

a

C>Ag

1

1 T

LiAIOj - LiALjOa

O 8261

62612

a 911 o 921

U29

O

A

cP

io-« _ a

o o

1111

o

J I L lOVT (K)

Figure 16

Ll pressure versus IoVt over LiAlOj - LlAljOa for series of data

taken with increasing temperature increments between data

points.

93
2000

TEUPERATURE (K)

1667 M29

10 -

3 10-5

t—<

UJ

(ED

V)

(/I ui

(T

a.

10-«

~r 1 r n 1—\—

1

—I—

O

>-iAL02 - LIAI5O a _ 8250 - ° A 8260 ”

- 910 -

- A 920 -

“

- -

_ _

_

O

«g)

- 0

1

»

I

- ©A -

- o „

-

aao

1

1 1 ] 1 1 1 1 ) 1 1 s 6 7 10VT (K)

Figure 17

Li pressure versus lO^I/T over LiA102 - LiAlsOft for series taken

with decreasing temperature between data points.

94
TEMPERATURE (K)

2000 1667 M29

Figure 18

Plot of Li and O

2 pressure versus 10^/T from the 901 D data obtained

over LiA102 -LiAl508 demonstrating constant ratio of Li/02 pressures.

95
TEMPERATURE (K)

2000 1667 M29

Figure 19

Li pressure versus 10^/T for increasing temperature series observed

over LiAl503 - AI2O3.

96
2000

TEMPERATURE (K)

1667 1429

10 -

ee. z>v%

ViUl

ac

a.

to-«

1—1—1—1 r

1

1

' 1 '

1

1

j UAI5O5 ~ ^^2^3 -

“ 09120 : A 1040 - a 1050 - A « 10170

0 ° 0

A

- A -

- A a - D

A

-

A

“ a

r 0

-

:

“ A

-

- 0 -

A A

_ 0

1 1 1 1 1 1 1 K!) 1 1 1 1 ioVt (k)

Figure 20

Li pressure versus 10^/T for decreasing temperature series over LiAl50Q _ A 1203.

97
Figure 21

LI pressure versus lo'l/T showing effect of temperature variation on experimental slope in the LiAljOg - AlgO, phase region. See text for Identification of run 1 and 2 in terms of Table 15 notation.

98
2000

1900

2 1600

O

•a

E

1700

1600

• Liquid

O Liquid Solid O Two Solids

y

/

/ / _

Liquid

• /

/ /o-AljOj

LIq.

Uq- O V ,4 Uq.«

U2OAI2O,

70 60

Mol. X Al20j AI2O,

Figure 22

Comparison of model prediction (data points) and experimental phase

diagram data (lines) for Li20 AI2O0 - AI2O3 mixtures. The ratio 1:1

resplotlvely"

‘•‘20-A1203 and L120.5A1203.

99
Li

Partial

Pressure

(atm)

TEMPERATURE K

2000 1900 1800

Figure 23

Comparison of predicted (Model 3) and experimental (Knudsen

effusion mass spectrometrlc) Li partial pressures and phase

boundaries for the equimoloar Li20-Al20^ mixture.

100
fj.

(centipoise)

Figure 24

Effect of temperature on the viscosities of Li and A1 melts.

101
Figure 25

Calculated viscosities of Al/Li liquid mixtures at 1200 K.

102
Ms/Ml

Figure 26

Effect of volume fraction of solids on viscosity of a liquid suspension.

103

DL/A32/84/316

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0.». DEPT. OF COMM. 1. BIBLIOGRAPHIC DATA

SHEET I See Instructions)

PUBLICATION OR 2 REPORT NO.

NBSIR 84-2940

. Performing Organ, Report NoJ 3. Publication Date

September 1984

4. TITLE and subtitle

PHASE EQUILIBRIA OF STORED CHEMICAL ENERGY REACTANTS

Annual Report

5. AUTHOR(S)

L. P. Cook, E. R. Plante, R, S. Roth, and J. W. Hastie

6. PERFORMING ORGANIZATION (If joint or other than NBS, see instructions)

national bureau of standards

DEPARTMENT OF COMMERCE

WASHINGTON, D.C. 20234

7. Contract/Grant No. N00014-83-F-0117

8. Type of Report & Period Covered

Annual Report

9.

SPONSORING ORGANIZATION NAME AND COMPLETE ADDRESS (Street, City, State, ZIP)

Department of the Navy, Office of Naval Research, Arlington, VA 22217

10. SUPPLEMENTARY NOTES

I I Document describes a computer program; SF-185, FIPS Software Summary, is attached.

11.

ABSTRACT (A 200-word or less factual summary of most significant information. If document includes a significant

bibliography or literature survey, mention it here) xhe reaction of lithium aluminum alloy with Water at

high temperature is discussed in terms of phase equilibria in the system Ll-Al-O-H. A

thermodynamic analysis of the system reveals the potential importance of lithium hydride as a reaction product. Major needs for experimental phase equilibria data are

outlined, and a determination of the LizO-AlaOa phase diagram is given top priority.

DTA investigation of the system LiaO-AlOa has yielded Information of equilibrium

melting behavior, and the lower limit of melting in the system appears to be

1055® ± 10 ®C, with the eutectic located near (Li20)?5 (Al 203 ) 2 s (mole%) . DTA data

suggest appreciable solid solution of alumina in Li 20 . On the high alumina end of the system Li20-Al203 » experiments in sealed Mo capsules have shown that the eutectic temperature is near 1650 ®C, that LIAIO2 melts congruently near 1750 ®C, and that LiAlsOe melts incongruently near 1750 ®C. Neutron diffraction analysis of LiAlsOa cooled rapidly from 1600® shows a 1:3 ordering of L1:A1 in

the octahedral sites, with extra peaks of undetermined origin.

Mass Spectrometrically determined vapor pressure data are reported for LI 2 O, and

mixtures of L1A102 -LiAlsOe and LiAls 08 -Al203 . A thermodynamic model for fitting and

prediction of vapor pressure and phase equilibrium data is described.

Appendices are given for the modeling of viscosities in multiphase mixtures, and

describing results of a computerized literature search on the system Ll-Al-O-H.

12

.

KEY WORDS (Six to twelve entries; alphabetical order; capitalize only proper names; and separate key words by semicolon s) activities; LIAIO2 ; LiAlsOe; Li20-Al203 ; mass spectrometry; phase diagram;

x-ray crystallography

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