agency jgo~5oo · thin dry sand ring. exothermic hot topping was used for all large cylinders, none...
TRANSCRIPT
0
AMRA CR 64-04/30
Control of Cast Grain Size of Steel Castings-Effectof S ttre and Nonmetallics on Proerties
Final ReportAugust 1, 1963-January 31, 1968
by
Peter F. WieserNathan ChurchJohn F. Wallace
DISTRIBUTION STATEMENT AApproved for Public'Release
Distribution UnlimitedJanuary, 1968
Department of MetallurgyCase Western Reserve University
University CircleCleveland, Ohio 44106
"Contract No. DA-33-0ii-AMC-273 (Z)
Distribution of this Document is Unlimited
,U.-S.ARMY MATERIALS RESEARCH AGENCYWATERTOWN, MASSACHUSETTS 02172
4 c o JGO~5Oo x
Control of Cast Grain Size of Steel Castings-Effect of Structure and Nonmetallics on Properties
AMRA CR 64-04/3
by
Peter F. WieserNathan ChurchJohn F. Wallace
January, 1968
Department of MetallurgyCase Western Reserve University
University CircleCleveland, Ohio 44106
D/A Prcject No. 1C024401A328
AMCS Code No. 5025.11.294Metals Research for Army Material
Distribution of this Document is Unlimited
U.S. ARMY MATERIALS RESEARCH AGENCY
WATERTOWN, MASSACHUSETTS 02172
i
ABSTRACT
Fhis project was concerned with determining theinfluence of micro-structural refinement on the mechan-ical properties of cast high strength 4335 steel. Thestrength levels investigated were approximately 250,000psi tensile strength and 205,000 psi yield strengthobtained with a liquid quench and temperi-ng treatment.The steel was cast in unidirectionally solidified cylin-ders and conventional sand mold keel blocks.
It was determined that the addition of approximately0.10% Ti to the steel subsequent to deoxidation providedconsideable structural refinement. This structuralrefinement consists of changing the usual columnarstructure to equiaxed and of refining the spacing of thesecondary dendrite arms. Such refinement was accompaniedby improvements in the tensile ductility and impactresistance of the steel. This improvement in propertieswas particularly marked on specimens located with theirlong axis perpendicular to the direction of heat flow.Structural refinement improved both the level of mechan-ical properties and reduced their directionality.
Studies of the micgro-structure of the cast steeldetermined that nonmetallic inclusions were the primaryfactor (in the absence of microshrinkage) in determiningthe level of ductility. The loss in ductility thatoccurred because of the presence of these nonmetallicinclusions was reduced by low sulfur contents and bymeans of combined deoxidation treatments. The bestdeoxidation treatments were found to be calcium-manganese-silicon or zircon-silicon added together with aluminum.Improved ductility was also obtained with the finalsecondary dendrite arm spacing that is obtained by rapidsolidification rates and by grain refinement withtitanium. J
ii
TABLE OF CONTENTS
Page
Abstract
Table of Contents iii
Introduction 1
Procedure and Materials 2
Results and Discussion 6
General Summary 7
Distribution 9
iii
INTRODUCTION
The control of the solidification process is a basic stepin obtaining the potential mechanical properties of a casting.The as-cast structure and presence of heterogeneities such asporosity and nonmetallic inclusions or nonequilibrium segregatesdetermine the degree to which the properties inherent in thecasting are realized. The type and fineness of the as-caststructure is determined by the composition, solidification timeand the state of nucleation during solidification. The presenceof heterogeneities in steel is primarily governed by the thermalgradient in the liquid during solidification, the chemical comp-osition and the deoxidation practice.
Grain refinement is one method to control the solidificationprocess. Nonferrous alloys are frequently grain refined to achievebetter strength, ductility, resistance to cracking and hot short-ness. Similarly, cast irons are frequently grain refined tocontrol the structure and its properties. A detailed review ofthis subject was presented in earlier reports. Grain refinementof steel is commercially applied only in some industries. Theapplication of a moving electromagnetic field during solidificationhas been reported to refine the structure of continuously caststrands and to improve the surface condition, reduce macroporosityand the tendency for hot tearing. Macrorefinement (conversion ofa columnar dendritic structure to an equiaxed structure) has beenobtained in some instances by applying a particular melting,deoxidation or inoculation practice. In spite of these reports,grain refinement has not assumed the important role in the steelfoundry industry which it has achieved in the nonferrous or castiron industry.
Recently, a technique of grain refining high strength, lowalloy steel of the type AISI 4335 was developed. This techniqueconsists of inoculating the melt with titanium. A suitabletitaiuum inoculation reduces the dendrite spacing of the castingand produces an equiaxed dendritic structure in a casting, whichwould normally solidify in a columnar dendritic manner. Suchrefinement improves the tensile ductility as measured by thereduction in area and toughness measured by Charpy V-notchimpact specimens.
The present investigation was undertaken to achieve thefollowing objectives: 1) improvement of the degree of refine-ment without introducing embrittling, nonmetallic inclusions;2) establishment of the relation between wall thickness, orequivalently solidification time and structure of properties;3) influence of melting variables such as deoxidation practiceon the structure, inclusions and properties; 4) determinationof the influence of the mode of solidification (equiaxed versuscolumnar dendritic) on the segregation behavior of solute elementsand on the incidence of microporosity.
1
PROCEDURE AND MATERIALS
The alloy used in this investigation is a high strength, lowalloy steel of AISI 4335 type with the following nominal compo-sition:
C% M__% Si% Cr% Mo% Ni%
0.30 0.60 0.20 0.70 0.20 1.65to to to to to to
0.35 0.80 0.35 0.90 0.30 2.00
The steel was generally melted at a sulfur level of 0.013 percentwith 0.01 percent phosphorus. Exceptions to this analysis willbe referred to in the text whenever necessary. The steel wasmelted from closely controlled charge materials using 50 and100 pound, magnesia lined, high frequency induction furnaces.The primary charge of low sulfur iron was rapidly melted and aCO boil initiated and maintained for at least two minutes byadding pig iron. Pig iron was used to maintain the boil and toadjust the carbon content after blocking the teat with ferro-silicon and ferromanganese. Standard ferroalloys and electrolyticnickel were employed to introduce the necessary alloying elements.A protective atmosphere was maintained during the preparation ofthe heat by directing a stream of argon at the melt through arefractory cover. Final deoxidation was performed by adding0.10 percent aluminum prior to tap. During the phase of theinvestigation of the effect of deoxidation practice all deoxidi-zers were wrapped in light gaqe steel and plunged below thesurface of the melt.
Unidirectionally solidified cylindrical castings andstandard keel blocks were employed as test castings. Thecastings were poured directly from the furnace into moldsthrough a pouring dish. The cylindrical castings were usedin two sizes weighing 45 and 11 pounds. ThLse castings willbe referred to as the large and small cylindrical castingrespectively. The bottom of the mold cavity was formed bya graphite chill block; the rest of the mold cavity was formedby an exothermic sleeve separated from the Chill block by athin dry sand ring. Exothermic hot topping was used for alllarge cylinders, none was employed for the smaller cylinders.The standard keel block cAstings with 1" x 1" x 8" long legswere cast in dry sand molds with a small amount of exothermichot topping.
The castings were usually produced in pairs from a singlemelt, first the base or uninoculated casting was poured, thenthe melt was treated and the inoculated casting poured. Theferrotitanium employed for grain refinement was plunged similarto the deoxidizers mentioned earlier. The time between inoculation
2
3
and pouring was held uniformly at two or three minutes. Thepouring temperature ranged from 28000 to 2950°F for largecylinders as discussed in the text. For small cylinders andkeel blocks, a uniform pouring temperature of 2900OF wasselected. The pouring temperature was closely controlled byimmersion thermocouples.
Macro and microexamination of the structure was conductedin all castings. Humphrey's reagent was used to develop thedendritic structure. The details of the cast structure wereimproved in some cases by isothermal transformation heattreatment. This consisted of austenitizing and quenching tothe isothermal transformation temperature of 1200*F andresulted in ferrite-pearlite dendrites and a martensiticmatrix. The primary dendrite and secondary arm spacingswere measured at various heights of the cylindrical castingsas indicated in the text. The secondary dendrite arm spacingof keel block legs was measured 3/16 inches from the castsurface at 3/4 inches from the bottom of the leg. The amountof nonmetallics was quantitatively determined employing a
* two-dimensional systematic point count method.
A microanalysis was conducted on specially preparedmetallographic specimens employing an electron microprobe,model 400, built by the Materials Analysis Company. Specimensused for microprobe analysis were isothermally transformed toprovide maximum detail in the etched structure. When solutemaxima were determined, the specimens were isothermally trans-formed up to 90 minutes in order to transform all of thestructure, except the areas exhibiting a solute maximum toferrite plus pearlite. The material exhibiting a solutemaximum transformed to martensite during the following quenchin water. The path along which the composition was to bedetermined was marked by micro hardness impressions. Thespecimens were then repolished and analyzed. The microprobetraces were revealed by etching the specimens with 3 percentnital.
All microprobe analyses were made by p6int counting,integrating for ten seconds. The distance between pointsvaried from 2 to 20 microns depending on the accuracy required.In areas exhibiting a solute maximum the distance betweenpoints was two to five microns. The microprobe was operatedwith a potential difference between filament and target of25 KV, the specimen current was 0.03 microamperes, the take-off angle was 350, the beam diameter was held between one andtwo microns. The elements manganese and chromium were analyzedquantitatively using specimens of known composition as standards;qualitative analyses were made for titanium.
The method used to determine solute minima and maximacon!:.isted of conducting point counts along diagonal pathsthrough the dendrite center into the geometrical centerbetween adjacent dendrites of a columnar dendritic specimen.For equiaxed strtctures, the analysis was restricted tospecimens which were slightly over inoculated so that thespecimen contained titanium sulfides instead of the usualmanganese sulfides. The reason for sel-ecting these specimenswas to permit using counts along random paths withoutmistaking concentration peaks from sub-surface inclusionswith true manganese maxima.
Microradiographic techniques were used to determine therelative amount of porosity in various unidirectionallysolidified castings. Specimens 1/2 x 1/2 x 0.0025 inchesthick were radiographed using unfiltered copper and cobaltK-alpha radiation respectively. The two types of radiationwere selected to distinguish between porosity and nonmetallicinclusions. The inclusions in this steel are mostly (FeMn)O°A1203, manganese sulfides and various oxides; they do notshow up in radiographs using unfiltered cobalt radiation.The operating conditions were as follows: specimen and filmto source distance 18 inches; for the copper target, thevoltage was 35 KV, current 23mA, exposure time 17 sec; forthe cobalt target the voltage was 45 KV, current 6mA, exposuretime 25 sec. Contract Process Ortho negative film wasemployed which permitted good resolution of porosity up toa magnification of 50X. The amount of porosity was determinedas the number of pores per unit area of specimen. Conversionto volume percent can be readily performed if the pores areessentially spherical. This was not the case and only a relativemeasure was employed. The resolution obtained with thisprocedure permitted detection of pores of 4 microns indiameter or larger.
Two .212" diameter tensile specimens were utilized: onehad the gage length machined to a 2" radius with a 0.212"specimen diameter; the second had a constant diameter overthe gage length. Ductility measurements were limited toreduction in area for radiused specimens. Both the reductionin area and elongation were determined for other specimens.The tensile properties of cylindrical castings weremeasured both normal and parallel to the chill, referred toas vertical and horizontal specimens respectively. Theproperties of keel blocks were measured with specimens whoseaxes were parallel to the long direction of the keel blockleg.
The heat treatment conducted for the specimens aftersectioning the casting was as follows: homogenizing for2 hours at 2200 0 F, air cool; normalizing for 2 hours at 1750*F,
5
air cool; spheroidizing over night at 11500 F, air cool. Thespecimens were then rough machined and heated to 400 0 F, heldfor 9 hours and air cooled, followed by austenizing for 1 hourat 16501F, cooling to 1500 0 F, holding for 1 hour and subsequentquench in oil, a double temper treatment of 2 hours at 400OFwith a subsequent oil quench concluded the heat treatment.
RESULTS AND DISCUSSION
The detailed results and a discussion of these resultsare presented in the three interim technical reports thathave been submitted on this contract. These reports areall concerned with the area of control of grain size andthe relation between microstructure and mechanical proper-ties in cast, high strength 4335 steel. In addition to theinterim technical reports submitted, three publications inthe technical literature have resulted from this contract.These are the following:
Wallace, J. F., Church, N., and Wieser, P., "Controlof Cast Grain Size of Steel Castings," Modern Cast-ings, April, 1966, p. 129, AFS Trans., Vol. 74, p.113.
Wallace, J. F. and Wieser, P. F., "Grain RefinementCast Steel by Vacuum Melting," Cast Metals ResearchJournal, March, 1966, Vol. 2, No. 1, p. 1.
Wallace, J. F., Church, N, and Wieser, P., "GrainRefinement of Steel Castings," Journal of Metals,June, 1967, p. 44.
This latter paper was granted the outstanding paper awardfor 1966 by the AIME Electric Furnace Conference of theIron and Steel Division. This paper will also appear in the1966 Electric Furnace Proceedings of AIME.
6
GENERAL SUMMARY
This work is summarized by presenting the abstracts from eachof the interim technical reports submitted on this material.
A. Report of September, 1964
Techniques for the quantative evaluation of refinement ofa high strength cast steel have been evolved and used to test theeffectiveness of various inoculants in achieving microstructuraland macrostructural refinement. Of the various materials testedonly titanium additions produced significant refinement of boththe micro and macrostructure.
Comparison of the tensile properties of the basic steelwith that of a refined steel shows that large additions (0.2-0.6 w/o) of titanium are sufficient to decrease the reductionin area sharply. Further data on castings partially refined w'ithsmall (o.10 w/o) titanium additions indicate that an improvementin reduction of area is obtained compared to the results with acolumnar structure solidified under similar thermal conditions.
B. Report of November, 1965
Inoculation techniques were developed to refine the ascast structure of high strength steel. Titanium was found tobe the most effective inoculant. Large titanium additions(0.6%) form sulfides which embrittle the steel. Small titaniumadditions (0.1%) together with controlled superheat and molddesign may produce significant refinement. Under these conditionsthe structure of unidirectionally solidified castings was changedfrom columnar to equiaxed and the reduction in area increased byapproximately 25% for specimens oriented vertically to thedirection of heat .flow and increased about 75% for horizontallyoriented specimens. A small improvement in reduction in areaof keel block castings was obtained by this method. Some cimprove-ment in toughness was also obtained by this grain refinement.The influence of vacuum melting on the cast structure of thesame steel was investigated. A hypothesis explaining themechanism of refinement by vacuum'melting was proposed.
C. Report of May, 1967
The relation of dendrite structure, nonmetallics andmicroporosity to solidification time and refinement by inoculationwas investigated and correlated to mechanical properties of AISI4335 steel castings.
The dendrite spacing is determined by solidification timeand significantly influenced by solute content. Titanium andboron effectively refine the secondary dendrite spacing; selenium,
7
8
tellurium and sulfur have the opposite effect. Titaniuminoculation also nucleates equiaxed dendrites, therbyreducing or eliminating the columnar dendritic structure;the elements boron, selenium, tellurium, and sulfur mayincrease the length of columnar dendrites. This effectis hypothesized to result from entrapment and deactivationof nuclei in the segregates of these elements. The amountof nonmetallics or the solidification time are related tothe ductility of unidirectionally solidified castings.Improvements in ductility from grain refinement can beexpressed by the change in dendrite spacing. Refinementof the dendritic structure improves ductility, presumablyby the reduction in particle size and the improved dis-tribution of nonmetallics. Microprobe analysis indicatesno significant differences in the segregation behavior ofthe elements manganese and chromium from inoculations. Ahypothesis concerning the formation of dendrite arms waspostulated based upon measurements of solute distributionand existing theories of dendrite arm formation.
DISTRIBUTION
No. of-Copies To
Office of the Director, Defense Research andEngineering, The Pentagon, Washington, D. C. 20301
1 ATTN: Mr. J. C. Barrett1 Mr. Donald MacArthur
20 Commander, Defense Documentation Center, CameronStation, Bldg. 5, 5010 Duke Station, Alexandria,Virginia, 22314
2 Defense Metals Information Center, BattelleMemorial Institute, Columbus, Ohio 43201
National Aqronautics and Space Administration,Washington, D. C. 20546
1 ATTN: Mr. B. G. Achhammer1 Mr. G. C. Deutsch1 Mr. R. V. Ihode
National Aeronautics and Space Administration,Marshall Space Flight Center, Huntsville, Alabama 35812
1 ATTN: R-P&VE-M, Dr. W. Lucas1 M-F&AE-M, Mr. W. A. Wilson, Bldg. 4720
1 U.S. Atomic Energy Commission, Office of TechnicalInformation Extension, P.O. Box 62, Oak Ridge,Tennessee 37830
Chief of Research and Development, Department of the
Army, Washington, D. C. 20310
2 ATTN: Physical and Engineering Science Division
Headquarters, Aeronautical Systems Division, Wright-Patterson Air Force Base, Wright-Patterson Air ForceBase, Ohio 45433
5 ATTN: ASRCEE
Chief, Office of Naval Research, Department of theNavy, Washington, D. C. 20360
1 ATTN: Code 423
9
10
Commander, U.S. Naval Research Laboratory,.AnacostiaStation, Washington, D. C. 20390
1 ATTN: Technical Information Officer
Commanding General, U.S. Army Material Command,
Washington, D. C. 20315
1 ATTN: AMCRD-RC-M
Commanding General, U.S. Army Electronics Command,Fort Monmouth, New Jersey 07703
2 ATTN: AMSEL-RD-MAT
Commanding General, U.S. Army Tank-Automotive Center,Warren, Michigan 48090
2 ATTN: Tech Data Coord Br., SMOTA-RTS1 SMOTA-RCM.I
Commanding General, U.S. Army Weapons Command, Rock
Island, Illinois 61201
1 ATTN: Research and Development Directorate, AMIWE-RDR
Commanding General, Deseiýt Test Center, Fort Douglas,Utah 84113
1 ATTN: Technical Document Center
Commanding General, White Sands Missile Range, WhiteSands, New Mexico 88002
1 ATTN: STEWS-WS-VT
Commanding Officer, Aberdeen Proving Ground, Maryland,21005
1 ATTN: Technical Library, Bldg. 3!3.
1 Commanding Officer, U.S. Army Research Office (Durham),Box CM, Duke Station, Durham, North Carolina 27706
Commanding Officer, Frankford Arsenal, Bridge and TaconyStreets; Philadelphia, Pennsylvania 19137
1 ATTN: Library Branch, C-25001 Mr. H. Markus, SMUFA-1320
Commanding Officer, Picatinny Arsenal, Dover, New Jersey
07801
1 ATTN: SMUPA-VA6
11
Commanding Officer, Watervliet Arsenal, Waterv21.et,New York 12189
1 ATTN: SWEWV-RDT, Tech Information Services Office
1 Commanding Officer, U.S. Army Aviation MaterialLaboratories, Fort Eustis, Virginia 23604
Commanding Officer, USACDC Ordnance Agency, AberdeenProving Q'rpund, Maryland 21005
2 ATTN: Library, Bldg. 305
Commanding Officer, U.S. Army Edgewood Arsenal, EdgewoodArsenal, Maryland, 21010
1 ATTN: Dir. of Eng., & Ind. Serv., Chem-Mun Br.(Mr. F. E. Thompson)
Redstone Scientific Information Center, U.S. ArmyMissile Command, Redstone Arsenal, Alabama 35809
4 ATTN: Chief, Documents Section
U.S. Army Aviation School Library, USAAVNS-P&NRI,1 Fort Rucker, Alabama 36360
Department of the Army, Ohio River Division Labora-tories, Corps of Engineers, 5851 Mariemont Avenue,Cincinnati, Ohio 45227
1 ATTN: ORDLB-TR
Commanding Officer, U.S. Army Materials ResearchAgency, Watertown, Massachusetts 02172
5 ATTN: AMXMR-AT1 AMXMR-AA1 AMXMR-MX, Mr. N. Reed1 AMXMR-RX, Dr. R. Beeutkes, Jr.r1 AMXMR-RP, Mr. G. A. Darcy, Jr.1 AMXMR-TP, Mr. P. A. G. Carbonaro5 AMXMR-TP, Casting & Cermets Branch
American Foundrymen's Society, Golf & Wolf RQads,
Des Plaines, Illinois 60016
1 ATTN: Mr. S. C. Massari
Dartmouth College, Hanover, New Hampshire 03755
1 ATTN: Professor G. A. Colligan
12
Harvard University, Cambridge, Massachusetts 02139
ATTN: Professor Bruce Chalmers
Investment Casting Institute, 3525 West Peterson Road,Chicago, Illinois 60645
ATTN: Mr. R. E. Pritchard
Massachusetts Institute of Technology, Cambridge,Massachusetts 02139
1 ATTN: Professor M. C. Flemings
Northeastern University, 360 Huntington Avenue,Boston, Massachusetts 02115
1 ATTN: Professor John Zotos
Northrop Corporation, Norair Division, Hawthorne,California 90250
1 ATTN: Mr. A. J. Iller
Steel Founder's Society, Westview Towers, 21010 CenterRidge Road, Rocky River, Ohio 44116
ATTN: Mr. C. W. Briggs
Tufts University, Mediford, Massachusetts 02155
ATTN: Professor K. Van Wormer, Jr.
University of Michigan, Ann Arbor, Michigan 48104
1 ATTN: Professor R. A. Flinn
Security ClassificationDOCUMENT CONTROL DATA- R&D
(Security classification of title, body of abstract and indexing annotation must be entered when the overall report is claaslifed)
I1. ORIGINATING ACTIVITY (Corporate author) 2a EOTSECURITY C LASSIFICATION
Case Western Reserve University UncROassifiUP
Cleveland, Ohio 44106. .oup
3. REPORT TITLE
Control of Cast Grain Size of Steel Castings-Effect ofStructure and Nonmetallics on Properties
4. DESCRIPTIVE NOTES (Type of report and inclusive date@)
Final ReportS. AUTHOR(S) (Last name, first name, initial)
Wieser, Peter F.Church, NathanWallace. John F.
6. REPORT DATE 7a. TOTAL NO. OF PAGES 7b. No. or lqir,
_January. 1968 151Sa. CONTRACT OR GRANT NO. Sa. ORIGINATOR'S REPORT NUMMER(S)
DA-33-019-AMC-273 (Z)b. PROJECT NO. AMRA CR 64-04/3
SD/A Project No. 1C024401A328o. 9b. ITNERRMPORT NO(S) (Any othernumbere that may be aessined
AMCS Code No. 5025.11.294d.
10. AVA ILABILITY/LIMITATION NOTICES
Distribution of this document is unlimited
11. SUPPLEMENTARY NOTES 12. SPONSORING MILITARY ACTIVITY
Army Materials & Mechanics ResearchCenter, Watertown, Mass. 02172
13. ABSTRACT
This project was concerned with determining the influence ofmicrostructural refinement on the mechanical properties of cast highstrength 4335 steel. It was determined that the addition of approx-imately 0.10% Ti to the steel subsequent to deoxidation provided con-siderable structural refinement. Such refinement was accompanied byimprovements in the tensile ductility and impact resistance of thesteel. This improvement in properties was particularly marked onspecimens located with their long axis perpendicular to the directiorof heat flow. Studies of the microstructure of the cast steel deter-mined that nonmetallic inclusions were the primary factor (in theabsence of microshrinkage) in determining the level of ductility.Improved ductility was also obtained with the final secondary den-drite arm spacing that is obtained by rapid solidification rates andby grain refinement with titanium.
F D ORM 17DD Casfcto1473
Security Classification
Security Classification14. "LINK A LINK 8 LINK C
KEY WORDS ROLE WT ROLE WT ROLE WT
Steel Castings
Grain Size Effects
Mechanical Properties
INSTRUCTIONS1. ORIGINATING ACTIVITY: Enter the name and address imposed by security classification, using standard statementsof the contractor, subcontractor, grantee, Department of De- such as:fense activity or other organization (corporate author) issuing (1) "Qualified requesters may obtain copies of thisthe report. report from DDC."
2a. REPORT SECURITY CLASSIFICATION: Enter the over- (2) "Foreign announcement and dissemination of thisall security classification of the report. Indicate wHether report anno t andhdized.""Restricted Data" is included. Marking is to be in accord- report by DDC is not authorized."ance with appropriate security regulations. (3) "U. S. Government agencies may obtain copies of
this report directly from DDC. 'Other qualified DDC2b. GROUP: Automatic downgrading is specified in DoD Di- users shall request throughrective 5200. 10 and Armed Forces Industrial Manual. Enterthe group number. Also, when applicable, show that optionalma;'kings have been used for Group 3 and Group 4 'as author- (4) "U. S. military agencies may obtain copies ofthisized. report directly from DDC. Other qualified users
3. REPORT TITLE: Enter the complete report title in all shall request throughn-pitnI letters. Titles in all cases should be unclassified.
I ', tm,. ani'wful title cannot be selected without classifica-lion, shoow title classification in all capitals in parenthesis (5) "All distribution of this report is controlled. Qual-immed'iatety following the title. ified DDC users shall request through
4. DESCRIPTIVE NOTES: If appropriate, enter the type of __00
report, e.g., interim, progress, summary, annual, or final. If the report has beert furnished to the Office of TechnicalGive the inclusive dates when a specific reporting period is Services, Department of Commerce, for sale to the public, indi-covered, cate this fact and enter the price, if known.5. AUTHOR(S): Enter the name(s) of author(s) as shown on IL SUPPLEMENTARY NOTES: Use for additional explana-or in the report. Enter last name, first name, middle initial, tory notes.If military, show rank and branch of service. The name ofthe P1rincipal a;.thor is an absolute minimum requirement. 12. SPONSORING MILITARY ACTIVITY: Enter the name of
the departmental project office or laboratory sponsoring (pay-6. REPORT DATL_• Enter the date of the report as day, irng for) the research and development. Include address.
month, year; or month, year. If more than one date appearson the report, use date of publication. 13. ABSTRACT: Enter an abstract giving a brief and factual
summary of the document indicative of the report, even though7a. TOTAL NUMBER OF PAGES: The total page count it may also appear elsewhere in the body of the technical re-suldr ofo pagesnormalnipination poeus.ieport. If additional space is required, a continuation sheet shallnumber of pages containing information, be attached.7b. NUMBER OF REFERENCES: Enter the total number of It is highly desirable that the abstract of classified reportsreferences cited in the report., be Unclassified. Each paragraph of the abstract shall end with8&. CONTRACT OR GRANT NUMBER: If appropriate, enter an indication of the military security classification of the in-the applicable number of the contract or grant under which formation in the paragraph, represented as (TS). (S), (C), or (U).the report was written. There is no limitation on the length of the. abstract. How-
8b, 8c, & 8d. PROJECT NUMBER: Enter the appropriate ever, the suggested length is from 150 to 225 words.military department identification, such as project number,subproject number, system numbers, task number, etc. 14. KEY WORDS: Key words are technically meaningful terms
or short phrases that characterize a report and may be used as9a. ORIGINATOR'S REPORT NUMBER(S): Enter the offi- index entries for cataloging the report. Key words must becial report number by which the document will be identified selected so that no security classification is required. Identi-and controlled by the originating activity. This number must fiers, such as equipment model designation, trade name, militarybe unique to this report. project code name, geographic location, may be used as key
9b. OTHER REPORT NUMBER(S): If the report has been words but will be followed by an indication of technical con-assigned any other report numbers (either by the originator text. The assignment of links, rales, and weights is optional.or by the sponsor), also enter this number(s).
10. AVAILABILITY/LIMITATION NOTICES: Enter any frm-itotions on further dissemination of the report, other than those
DFORMDD JAN 61473 (BACK)Security Classification
0 0ý
0 40 1 0 0 4
o 34 W4.3 u4 O' 0to 0 U 4334 .44 ix '4 0 -4 0
-4.Or r 00 v34 -r .4 4 v 0
3 o30 00 . 0 w N M0 -a c30 k J 0-041 0N0, C.03 14 r4 C! NO M3 3 ' 0
03~~. 003 ,33 43 30 .' 3
3. 43.
03 . 43 re A 43 0 03 43 a303 30 0 - 434 >0. A3 . af>V0.. 433 a)c 0.
0 c 0> 43 V .. w4 43 >34A04,3 004 3- 0 v3* v 0003v-
03 43 9043v.0 o .4 430 v3 -A43 0043.0 '-4~v043op.0
-. 4 4-4431.5. 433344 ao. M- - )43 43 .4-1zr 1o l.v
.00 0 %4 0V.40
w-M. 30, ox3 43.4 00.4.Ov M43. Q m. w 43 01 '0,0 ~~~ 0 0443 34>3 o30 0 0 04w3 'd433 430
2~ ~ 0 w .4303 43.40 A 43 0 -40343 4.0 4
I34 r43.ýo or 0 Nk o -a040 3 40 4 4 434 a3 01 N l 430 0. w0.4 4 o
0 . 4 . . -A '. -4 . 30. 00 k3 -4ý e4 43 0 4.4 0m43.04 3 43 r4 04 0 04 0 @3 40 w3. E3 w3 4W 04 0004300034
43 '4 >. 43.4 43.W 43 '4 4
0 4 0 0-4 043434300430434343r u 0 a44 0 0' 0444 003 4310434
04 03 '434 4030 0' '. 3-4 43 A m' 4 'd3 o 33 4304 A'044 4 4r a,- 11k v a 43 -. 4434303 c0.44 43-443 c603 4 .433343403.4
43440 . 4 c 43 434 I404 04 M4 0 a. V4 43 434 04.c3 4..434.4 r04334 1"A~ c43 4 A 4
43034 ..0 344 0 4 43 . . '0 4 x3 3 3 .x a m .0 43c '0u3 -.40au44~ - -o 11 uE
.343 u 3 4) A v w w 043 V H. e 3v443 -r43 ' 0D4 'H 3
:3 0 0 43 o3 -4 30 34 . c 0 0 n 43 . 4 04 ., . 1 a a
4 u4 43. 043. 44 r - a
4
I * 4- ý 1 1 V 430.043. .4443 >.044 '0 v44" .>4o0v 3.33 43 Q, 044 '0 ,a 4340 s4 o o, w c-343
4304 0. r44-40 .. 43> 34 4304 0. .44030 40
43.w o43 v4 .4431 a oI" w44431 o; 3443.ý -4 -43, -. 44w
0, 0 ,0 43, 43o t- . 4 0'
I0 a, o 0 0o 0V
43 Q. 434 'O c3 43 44 434 '0N w 3M - ou)>0R o 34 .4431, '4 0-o 4 00 0 034 44 '-410 : 0-4 00
4z 03 'a ,4 o.03 .1 34W1 d Q4m~~~~~ ~. 00 4343 w4 w"w.Zý
'do 00 43434 wwf.43~ . 4t 4 S.. v m 43. ' * , .a4)avo
4t3 433 0 N 3 3 403 0 N
43.1
H 41' 44ý . u43 11' H 01ý o1
4)~~0 4)'A0 N
o4 043404
34 W4 M 44440 434 4344 V4 v3 4.4 4444404334 00433.4 4 03*4 00V4
43~ ~ 3444 -043 43 so -o 43 344443 33 430
'0 v4 43 34043. 43 43
43 r vw '.4 .530~0.44~~~4 43 134333 433434
I-3 w V,303 43.4 43 43 V . 4 0) 43 4340 4LI) a 03 3 4 00 3 0 . -. ' 44 0 c3433 '004 '.tl.4v
430u w 2 , r ' 0cl N L30 430 o0 .44w
o0 w Q.. '0.4 .41 > 00 r '0.0. .430>04-304 433p 44 v0 43 R.; 3 44333 .
c3 um 0 o3' 3 4 3 3 4 3 3 a 4 3 E43) " r 0 V 0 ' 3040 3 3 4 - 4
w43oo 1 Uo >,' r W .4 1.034330443 3 4 U ... 3400 .0 43 434304434
43~ 43 0 0 430344.04 63 43 00 4304433w v~0 0 ' 43 > 4 0 o.4.oz3 c o.4Z 30V3w
04" ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ E c3 '43 I>4'40'043' 43 43. '4V404'400'3 4 4
w30 V Q, q3'4 43M3 4 43 43M
§a 4~ 4W .I4 Z~ I334 0 34 43 o >04
o3 43. v3 0 43 -4 34 434300 A-434v43a0o34'a..3 3 0a 004303o-.04
.c443: . 43 43 3 0 4 3 . 04 H 3 3 .44 a34 3 44 4 03 43 4 . - 34 4 4 3 4 V 3 4o' 0 g '0 4 3Hw
03 . '4 4 3 4 3 4 3 4 3 0 m 'o v v 2u " 4 c4g34 4 3 3 0 .34 4 3 3 3 4 3 3
430.434 ~ ~ ~ ~ ~ ~ m 430 6349304 re>43 0u c ' 4043433N.43'~'0434 0. -43V34 0 43.43
43043u 0. .4143w4V300404w . - 431. 343 4304 '03.
w z c -0' 0. uv. . 1 w I .r ka 41 o0.0~. 4 0 -'44 .0 v v v~ 43. .40 44 w.0o3.Z3 43 4 3 3 0 3 43430430~~~~~. 43 434 4433330404000 c4Q.3 -4 0330404330