Powder flakes prepared from 50 μm thick melt spun ribbons of Markomet 1064 (Ni_(52.5)Mo_(38)Cr_8 B_(1.5) wt%) were shock consolidatedin the unannealed and annealed condition. The unannealed flakes (microhardness 933 kg/mm^2) are amorphous while flakes annealed at 900ºC for 2 hours have an fcc structure with a grain size of 0.3 μm and microhardness of 800 kg/mm^2. The shock consolidated amorphous powder compact (250 kJ/kg shock energy) shows no crystal peaks in an X-ray diffractometer scan. Compacts of annealed powder (400 to 600 kJ/kg shock energies) contain amorphous material (18-21%) which was rapidly quenched from the melt formed at interparticle regions during the consolidation process. The microhardness of the amorphous interparticle material is 1100 kg/mm^2. Wear properties of the compacts measured in low velocity pin on disk tests show low average dynamic friction values (∿0.03). The 60 hour cumulative wear appears to correlate with the energy of shock compaction and surface porosity of the compacts rather than the metallic glass content

Mutz, Andrew H.

Nibert, Roger K.

Thadhani, Naresh N.

Thomas, Susan P.

Vreeland, Thad, Jr.

Caltech Authors - Main

WEAR PROPERTIES OF A SHOCK CONSOLIDATED 
METALLIC GLASS AND GLASS-CRYSTALLINE MIXTURES 
123 
THAD VREELAND, JR., NARESH N. THADHANI, AND ANDREW H. MUTZ, Division of 
Engineering and Applied Science, California Institute of Technology, Pasa-
dena, CA 91125 
SUSAN P. THOMAS AND ROGER K. NIBERT, Roy C. Ingersoll Research Center, Borg-
Warner Corp., Des Plaines, IL 60018 
ABSTRACT 
Powder flakes prepared from 50 ~m thick melt spun ribbons of Markomet 
1064 (Ni Mo Cr B1 wt%) were shock consolidated in the unannealed and anne~f~~ co~§iti§n. "lhe unannealed flakes (microhardness g33 kg/mm2) 
are amorphous while flakes annealed at 900°C for 2 hours have an fcc struc-
ture with a grain size of 0.3 ~m and microhardness of 800 kg/mm2. The shock 
consolidated amorphous powder compact (250 kJ/kg shock energy) shows no crys-
tal peaks in an X-ray diffractometer scan. Compacts of annealed powder (400 
to 600 kJ/kg shock energies) contain amorphous material (18-21 %) which was 
rapidly quenched from the melt formed at interparticle regions during the 
consolidation process. The microhardness of the amorphous interparticle 
material is 1100 kg/mm2. Wear properties of the compacts measured in low 
velocity pin on disk tests show low average dynamic friction values (~.03). 
The 60 hour cumulative wear appears to correlate with the energy of shock 
compaction and surface porosity of the compacts rather than the metallic 
glass content. 
INTRODUCTION 
Metallic glasses, with high metalloid concentration and associated 
hardness, have been observed to show superior wear resistance when used as 
coatings on steel substrates [1]. Shock wave consolidation has been employed 
to produce bulk solids with metastable structures [2-5]. During consolida-
tion, the shock energy is preferentially utilized in heating and melting 
interparticle surfaces [6,7]. The melted regions rapidly solidify and may 
form new metastable structures or retain the metastable structure of the 
starting powder. Shock consolidation is a unique form of thermal and mech-
anical processing and can be used to process metallic glass powders to form 
bulk amorphous solids [8,9], and crystalline powders of glass forming alloys 
to produce a solid mixture of metallic glass and microcrystalline material 
[6,10]. In this paper, we report some wear properties of a shock consoli-
dated glass forming alloy powder containing varying amounts of glass and 
microcrystalline phases. 
SHOCK CONSOLIDATION 
Powder Characterization 
The Markomet 1064 alloy (Ni 5 Mo Cr B 5 wt%) powder was prepared by ball milling melt spun amorphBfis rib~§ns ~~sb·~m thick) . Annealing of 
the powder at 900°C for 2 h produces a fully microcrystalline powder (con-
firmed by x-ray and electron diffraction). Optical microscope observations 
on polished and etched powder particles show that the amorphous phase 
resists attack by the Marbles reagent, while microcrystalline grains in the 
annealed powder are attacked and show a dark etching contrast [10]. 
Mat. Res. Soc. Symp. Proc. Vol. 58. tt- 1986 Materials Research Society 
124 
Powder Consolidation 
Green compacts were prepared by static l oading of the powder in stee l 
containers and the compacts were conso lidated by impact of propel lent driven 
stainless steel flyer plates at velocities from 0. 8 to 1.4 km/s. The con-
solidated powder compacts were recovered as ~20 mm diameter discs ~5 mm 
thick. 
Optical photomicrographs of polished and etched sections of recovered 
compacts (plane of the shock) are shown in Fig. la,b. The dark etching re-
gions in the compact of annea l ed powder in Fig. la are microcrystalline while 
the white nonetching regions are metallic glass (a s confirmed by TEM [10]). 
The compact of amorphous powder, Fig. l b shows etching at amorphous particle 
boundaries which did not melt sufficiently to dissolve surface contaminants. 
The amorphous powder compact shows no crystalline peaks in an X-ray diffrac-
tometer scan . The shock energy, glass content, and microhardness of the 
particles and interparticle amorphous regions are given in Table I for the 
four compacts used in the wear tests . 
Fig. 1. Optical photomicrographs of sections (shock plane) 
of compacts of (a) microcrystalline powder (shot #816), and 
(b) amorphous powder (shot #817). 
The volume fraction of metallic glass formed upon compaction was deter-
mined by measurement of the areal fraction of th e nonetching glass phase in 
optical micrographs, and ranged from 0.18 to 0.21 with increasing shock 
energy. The microhardness of the glass phase formed at microcrystalline 
particle boundaries is greater than the hardness of the melt spun glass and 
the hardness of the microcrystalline particle interiors. Interparticle re-
gions of the amorphous powder compact also exhibit a higher hardness than 
that in the i nterior of the amorphous particles. 
TABLE I - CONSOLIDATION EXPERIMENTS AND RESULTS 
Shock Glass Microhardness(DPH,kg/mm2) 
Shot# Energ.z-(kJ/k:g) Fraction Particle Inteq:!article 
813()Jx+a ) 592 0. 21 792 ± 134 1095 87 
815(Jlx+a) 467 0 . 19 782 ± 99 1060 153 
816(Jlx+a) 419 0.18 801 ± 205 1146 98 
817(a) ~250 1.0 933 ± 131 1144 75 
)JX microcrystalline, a = amorphous 
125 
WEAR TESTS 
A low velocity friction apparatus (LVFA) [ll ,12], employing a three pin 
on disc configuration was used to obtain boundary friction test conditions 
which produce adhesive wear . Test samp l es were made from ~3 mm discs (0.5 mm 
thick) of the compacts bonded to 3 mm pins . The discs were ground to match 
the 3 mm diameter pins with a 45° chamfer and the flat ends of the . discs were 
mechanically polished, finishing with 5 ~m diamond grit. The pins were run 
at 0.3 m/s on a circu l ar track (17.5 mm diameter) on the mechanically po l-
ished surface of a disc (~0 mm thick 52100 steel, microhardness 900 kg/mm2) 
for a 17 h break-in period at ambient temperature prior to making meas ure-
ments of friction and wear. The disc was lubricated with an automotive 
transmission f lu id . Fri ction and wear values at 0.4 m/s and the hi ghest 
temperature and thrust load used in the tests (l49 °C and 19.3 MPa pressure) 
are given in Table II. Wear volume was determined from optical microscope 
measurements of the chamfer diameter of the pins after 60 h of running. 
Values determi~ed using an AISI 1095 steel pin base-line sample (microhard-
ness 700 kg/mm ) are also gi ven i n Table II. 
TABLE II - LOW VELOCITY FRICTION APPARATUS RESULTS (l 49°C, 19.3 MPa) 
Coefficient of Friction 
Surface Porosity ~static ~dynamic ~ave dyn. Cumu lative Pin Wear 
Sam~ l e # Rank ing after 60 hrs. (mm3) 
813 L-M 0.105 0.064 0.02 0.10 
815 M-H 0.111 0.074 0.03 1.03 
816 M 0.092 0.078 0.02 0.1 3 
817 H 0.085 0.082 0.05 2.31 
1095 Stee l L 0.113 0.087 0.10 0.08 
Microscopic examination of the po li shed su rfaces of the compacts re-
vealed some poros i ty due to particle pull-out. Thi s surface porosity was 
observed to decrease for compacts consoli dated with increasing s hock energy. 
Initial stati c and dynamic coefficient of friction values are gi ven in 
Table II. The re i s i nsign i ficant variation in the measurements for the 
sta tic fr iction data. The dynamic s li ding friction increased with increas ing 
load and temperature, and decreased as t he sliding speed was increased. This 
behavior is typical for boundary friction condi ti ons. Under the most severe . 
test conditions (l 49°C, 19. 3 MPa) the dynamic coefficient of friction (after 
the f inal 17 h break-in) values tend to increase with increasing porosity. 
Highest dynamic friction coeffic i ent resulted with the base-line 1095 stee l 
sample because of i ts greater surface roughness. The average dynamic co-
eff i cient of friction values, on the other hand are the average of the values 
obtained af ter break-in at 5 min, l h, and 17 h, and fo ll ow the trend for the 
dynamic values . 
The pin vo lume loss in the wear tests corre l ates with the energy of 
shock compaction and surface porosity, and not with the volume fraction of 
met al li c gl ass in the samples. Wear of sampl es #813 and #816, consoli dated 
at high energies , was less than .that of #815 and #817 . Samples of shot #817 
(all gl ass) and #815( 19% glass) showed maximum wear which is attributed to 
particle pull-out . The increase in dynamic friction during the break-in 
cycl e al so indicates particle pull-out. In samples #813 and #816, the pin 
wear is equa l to that of the base-line 1095 steel sample, wit hin the l imits 
of experimental uncerta i nty . 
In contrast to the pin on disc test, prel imi nary wear test results on 
an al l gl ass Markomet 1064 al l oy compact in the block on disc test (at high 
contact pressures) indicates s i gnificantly lower wear rates than on hardened 
126 
steel base-line samples. The results of the block on disc tests will be re-
ported elsewhere. 
CONCLUSIONS 
1. Shock consolidation of amorphous powder flakes of Markomet 1064 
alloy with a 250 kJ/kg shock energy produces a fully amorphous compact with 
microhardness ranging from 933 to 1100 kg/mm2. The interparticle regions of 
the compact exhibit the highest hardness. 
2. The shock consolidation of annealed Markomet 1064 powder produces 
compacts with metallic glass at microcrystalline particle interfaces. The 
volume fraction of metallic glass increases with increasing shock energy up 
to 600 kJ/kg, and the microhardness of the metallic glass and microcrystal-
line particles is ~1100 and ~00 kg/mm2, respectively. 
3. A porosity is observed on mechanically polished surfaces of the 
shock consolidated compacts which is attributed to particle pull-out. The 
porosity decreases with increasin9 shock energy. 
4. Low velocity wear tests (0.4 m/s) show a dynamic coefficient of 
friction and a 60 h cumulative wear which correlates with the energy of shock 
compaction rather than the metallic glass content of the compact. 
5. The compact with 21 % metallic glass between microcrystalline par-
ticles (consolidated with the maximum shock energy) exhibited the lowest 
dynamic friction, and wear comparable to that of the hardened AISI 1095 steel 
base-line sample. 
ACKNOWLEDGEMENTS 
The shock consolidations were carried out using the facilities of Prof. 
Thomas Ahrens in the Caltech Seismological Laboratories and were supported 
in part by the National Science Foundation under Grant No. DMR-8315214 and 
the Cal tech Program in Advanced Technologies sponsored by Aerojet General, 
General Motors, GTE, and TRW Laboratories. Wear Tests were performed by Mr. 
Marc Yesnik at the Roy C. Ingersoll Research Center. 
REFERENCES 
1. M. Mehra, PhD Dissertation, California Institute of Technology, 1984. 
2. D.G. Morris, Metal Sci. 16, 457 (1982). 
3. D. Raybould, J. Matl. Sc.,.-:- 16, 589 (1981). 
4. D.G. Morris, Mat. Sci. and Eng. 57, 187 (1983). 
5. P. Kasiraj, PhD Dissertation, Callfornia Institute of Technology, 1984. 
6. T. Vreeland, Jr., P. Kasiraj, A. H. Mutz, and N.N. Thadhani, in Proc. of 
Int. Conf. on Metallurgical Applications of Shock-Wave and High-Strain-
Rate Phenomena, edited by L.E. Murr (to be published by Marcel Dekker 
Publishing Company, New York, March 1986). 
7. R. Schwarz, P. Kasiraj and T. Vreeland, Jr., source cited in Ref. 6 (to 
be published). 
8. P. Kasiraj, D. Kostka, T. Vreeland, Jr., and T.J. Ahrens, J. of Non-
Cryst. Sol. 61 and 62, 967 (1984). 
9. T. Vreeland,~r., P~Kasiraj, and T.J. Ahrens, in Proc. of MRS Symposium 
on Ra idl Solidified Metastable Materials, edited by B.H. Kear and B. C. 
Giessen Elsevier Science Publishers, New York, 1984), p. 139. 
10. N.N. Thadhani, A.H. Mutz, P. Kasiraj, T. Vreeland, Jr., source cited in 
Ref. 6 (to be published). 
11. M.L. Haviland and J.T. Rodgers, Lubrication Engr. 17, 110 (1961). 
12. C. Albertson and G. Wolfram, ASLE Trans. 1£, 77 (1969). 


English

Wear Properties of A Shock Consolidated Metallic Glass and Glass-Crystalline Mixtures

WEAR PROPERTIES OF A SHOCK CONSOLIDATED 
METALLIC GLASS AND GLASS-CRYSTALLINE MIXTURES 
123 
THAD VREELAND, JR., NARESH N. THADHANI, AND ANDREW H. MUTZ, Division of 
Engineering and Applied Science, California Institute of Technology, Pasa-
dena, CA 91125 
SUSAN P. THOMAS AND ROGER K. NIBERT, Roy C. Ingersoll Research Center, Borg-
Warner Corp., Des Plaines, IL 60018 
ABSTRACT 
Powder flakes prepared from 50 ~m thick melt spun ribbons of Markomet 
1064 (Ni Mo Cr B1 wt%) were shock consolidated in the unannealed and anne~f~~ co~§iti§n. "lhe unannealed flakes (microhardness g33 kg/mm2) 
are amorphous while flakes annealed at 900°C for 2 hours have an fcc struc-
ture with a grain size of 0.3 ~m and microhardness of 800 kg/mm2. The shock 
consolidated amorphous powder compact (250 kJ/kg shock energy) shows no crys-
tal peaks in an X-ray diffractometer scan. Compacts of annealed powder (400 
to 600 kJ/kg shock energies) contain amorphous material (18-21 %) which was 
rapidly quenched from the melt formed at interparticle regions during the 
consolidation process. The microhardness of the amorphous interparticle 
material is 1100 kg/mm2. Wear properties of the compacts measured in low 
velocity pin on disk tests show low average dynamic friction values (~.03). 
The 60 hour cumulative wear appears to correlate with the energy of shock 
compaction and surface porosity of the compacts rather than the metallic 
glass content. 
INTRODUCTION 
Metallic glasses, with high metalloid concentration and associated 
hardness, have been observed to show superior wear resistance when used as 
coatings on steel substrates [1]. Shock wave consolidation has been employed 
to produce bulk solids with metastable structures [2-5]. During consolida-
tion, the shock energy is preferentially utilized in heating and melting 
interparticle surfaces [6,7]. The melted regions rapidly solidify and may 
form new metastable structures or retain the metastable structure of the 
starting powder. Shock consolidation is a unique form of thermal and mech-
anical processing and can be used to process metallic glass powders to form 
bulk amorphous solids [8,9], and crystalline powders of glass forming alloys 
to produce a solid mixture of metallic glass and microcrystalline material 
[6,10]. In this paper, we report some wear properties of a shock consoli-
dated glass forming alloy powder containing varying amounts of glass and 
microcrystalline phases. 
SHOCK CONSOLIDATION 
Powder Characterization 
The Markomet 1064 alloy (Ni 5 Mo Cr B 5 wt%) powder was prepared by ball milling melt spun amorphBfis rib~§ns ~~sb·~m thick) . Annealing of 
the powder at 900°C for 2 h produces a fully microcrystalline powder (con-
firmed by x-ray and electron diffraction). Optical microscope observations 
on polished and etched powder particles show that the amorphous phase 
resists attack by the Marbles reagent, while microcrystalline grains in the 
annealed powder are attacked and show a dark etching contrast [10]. 
Mat. Res. Soc. Symp. Proc. Vol. 58. tt- 1986 Materials Research Society 
124 
Powder Consolidation 
Green compacts were prepared by static l oading of the powder in stee l 
containers and the compacts were conso lidated by impact of propel lent driven 
stainless steel flyer plates at velocities from 0. 8 to 1.4 km/s. The con-
solidated powder compacts were recovered as ~20 mm diameter discs ~5 mm 
thick. 
Optical photomicrographs of polished and etched sections of recovered 
compacts (plane of the shock) are shown in Fig. la,b. The dark etching re-
gions in the compact of annea l ed powder in Fig. la are microcrystalline while 
the white nonetching regions are metallic glass (a s confirmed by TEM [10]). 
The compact of amorphous powder, Fig. l b shows etching at amorphous particle 
boundaries which did not melt sufficiently to dissolve surface contaminants. 
The amorphous powder compact shows no crystalline peaks in an X-ray diffrac-
tometer scan . The shock energy, glass content, and microhardness of the 
particles and interparticle amorphous regions are given in Table I for the 
four compacts used in the wear tests . 
Fig. 1. Optical photomicrographs of sections (shock plane) 
of compacts of (a) microcrystalline powder (shot #816), and 
(b) amorphous powder (shot #817). 
The volume fraction of metallic glass formed upon compaction was deter-
mined by measurement of the areal fraction of th e nonetching glass phase in 
optical micrographs, and ranged from 0.18 to 0.21 with increasing shock 
energy. The microhardness of the glass phase formed at microcrystalline 
particle boundaries is greater than the hardness of the melt spun glass and 
the hardness of the microcrystalline particle interiors. Interparticle re-
gions of the amorphous powder compact also exhibit a higher hardness than 
that in the i nterior of the amorphous particles. 
TABLE I - CONSOLIDATION EXPERIMENTS AND RESULTS 
Shock Glass Microhardness(DPH,kg/mm2) 
Shot# Energ.z-(kJ/k:g) Fraction Particle Inteq:!article 
813()Jx+a ) 592 0. 21 792 ± 134 1095 87 
815(Jlx+a) 467 0 . 19 782 ± 99 1060 153 
816(Jlx+a) 419 0.18 801 ± 205 1146 98 
817(a) ~250 1.0 933 ± 131 1144 75 
)JX microcrystalline, a = amorphous 
125 
WEAR TESTS 
A low velocity friction apparatus (LVFA) [ll ,12], employing a three pin 
on disc configuration was used to obtain boundary friction test conditions 
which produce adhesive wear . Test samp l es were made from ~3 mm discs (0.5 mm 
thick) of the compacts bonded to 3 mm pins . The discs were ground to match 
the 3 mm diameter pins with a 45° chamfer and the flat ends of the . discs were 
mechanically polished, finishing with 5 ~m diamond grit. The pins were run 
at 0.3 m/s on a circu l ar track (17.5 mm diameter) on the mechanically po l-
ished surface of a disc (~0 mm thick 52100 steel, microhardness 900 kg/mm2) 
for a 17 h break-in period at ambient temperature prior to making meas ure-
ments of friction and wear. The disc was lubricated with an automotive 
transmission f lu id . Fri ction and wear values at 0.4 m/s and the hi ghest 
temperature and thrust load used in the tests (l49 °C and 19.3 MPa pressure) 
are given in Table II. Wear volume was determined from optical microscope 
measurements of the chamfer diameter of the pins after 60 h of running. 
Values determi~ed using an AISI 1095 steel pin base-line sample (microhard-
ness 700 kg/mm ) are also gi ven i n Table II. 
TABLE II - LOW VELOCITY FRICTION APPARATUS RESULTS (l 49°C, 19.3 MPa) 
Coefficient of Friction 
Surface Porosity ~static ~dynamic ~ave dyn. Cumu lative Pin Wear Sam~ l e # Rank ing after 60 hrs. (mm3) 
813 L-M 0.105 0.064 0.02 0.10 
815 M-H 0.111 0.074 0.03 1.03 
816 M 0.092 0.078 0.02 0.1 3 
817 H 0.085 0.082 0.05 2.31 
1095 Stee l L 0.113 0.087 0.10 0.08 
Microscopic examination of the po li shed su rfaces of the compacts re-
vealed some poros i ty due to particle pull-out. Thi s surface porosity was 
observed to decrease for compacts consoli dated with increasing s hock energy. 
Initial stati c and dynamic coefficient of friction values are gi ven in 
Table II. The re i s i nsign i ficant variation in the measurements for the 
sta tic fr iction data. The dynamic s li ding friction increased with increas ing 
load and temperature, and decreased as t he sliding speed was increased. This 
behavior is typical for boundary friction condi ti ons. Under the most severe . 
test conditions (l 49°C, 19. 3 MPa) the dynamic coefficient of friction (after 
the f inal 17 h break-in) values tend to increase with increasing porosity. 
Highest dynamic friction coeffic i ent resulted with the base-line 1095 stee l 
sample because of i ts greater surface roughness. The average dynamic co-
eff i cient of friction values, on the other hand are the average of the values 
obtained af ter break-in at 5 min, l h, and 17 h, and fo ll ow the trend for the 
dynamic values . 
The pin vo lume loss in the wear tests corre l ates with the energy of 
shock compaction and surface porosity, and not with the volume fraction of 
met al li c gl ass in the samples. Wear of sampl es #813 and #816, consoli dated 
at high energies , was less than .that of #815 and #817 . Samples of shot #817 
(all gl ass) and #815( 19% glass) showed maximum wear which is attributed to 
particle pull-out . The increase in dynamic friction during the break-in 
cycl e al so indicates particle pull-out. In samples #813 and #816, the pin 
wear is equa l to that of the base-line 1095 steel sample, wit hin the l imits 
of experimental uncerta i nty . 
In contrast to the pin on disc test, prel imi nary wear test results on 
an al l gl ass Markomet 1064 al l oy compact in the block on disc test (at high 
contact pressures) indicates s i gnificantly lower wear rates than on hardened 
126 
steel base-line samples. The results of the block on disc tests will be re-
ported elsewhere. 
CONCLUSIONS 
1. Shock consolidation of amorphous powder flakes of Markomet 1064 
alloy with a 250 kJ/kg shock energy produces a fully amorphous compact with 
microhardness ranging from 933 to 1100 kg/mm2. The interparticle regions of 
the compact exhibit the highest hardness. 
2. The shock consolidation of annealed Markomet 1064 powder produces 
compacts with metallic glass at microcrystalline particle interfaces. The 
volume fraction of metallic glass increases with increasing shock energy up 
to 600 kJ/kg, and the microhardness of the metallic glass and microcrystal-
line particles is ~1100 and ~00 kg/mm2, respectively. 
3. A porosity is observed on mechanically polished surfaces of the 
shock consolidated compacts which is attributed to particle pull-out. The 
porosity decreases with increasin9 shock energy. 
4. Low velocity wear tests (0.4 m/s) show a dynamic coefficient of 
friction and a 60 h cumulative wear which correlates with the energy of shock 
compaction rather than the metallic glass content of the compact. 
5. The compact with 21 % metallic glass between microcrystalline par-
ticles (consolidated with the maximum shock energy) exhibited the lowest 
dynamic friction, and wear comparable to that of the hardened AISI 1095 steel 
base-line sample. 
ACKNOWLEDGEMENTS 
The shock consolidations were carried out using the facilities of Prof. 
Thomas Ahrens in the Caltech Seismological Laboratories and were supported 
in part by the National Science Foundation under Grant No. DMR-8315214 and 
the Cal tech Program in Advanced Technologies sponsored by Aerojet General, 
General Motors, GTE, and TRW Laboratories. Wear Tests were performed by Mr. 
Marc Yesnik at the Roy C. Ingersoll Research Center. 
REFERENCES 
1. M. Mehra, PhD Dissertation, California Institute of Technology, 1984. 
2. D.G. Morris, Metal Sci. 16, 457 (1982). 
3. D. Raybould, J. Matl. Sc.,.-:- 16, 589 (1981). 
4. D.G. Morris, Mat. Sci. and Eng. 57, 187 (1983). 
5. P. Kasiraj, PhD Dissertation, Callfornia Institute of Technology, 1984. 
6. T. Vreeland, Jr., P. Kasiraj, A. H. Mutz, and N.N. Thadhani, in Proc. of 
Int. Conf. on Metallurgical Applications of Shock-Wave and High-Strain-
Rate Phenomena, edited by L.E. Murr (to be published by Marcel Dekker 
Publishing Company, New York, March 1986). 
7. R. Schwarz, P. Kasiraj and T. Vreeland, Jr., source cited in Ref. 6 (to 
be published). 
8. P. Kasiraj, D. Kostka, T. Vreeland, Jr., and T.J. Ahrens, J. of Non-
Cryst. Sol. 61 and 62, 967 (1984). 
9. T. Vreeland,~r., P~Kasiraj, and T.J. Ahrens, in Proc. of MRS Symposium 
on Ra idl Solidified Metastable Materials, edited by B.H. Kear and B. C. 
Giessen Elsevier Science Publishers, New York, 1984), p. 139. 
10. N.N. Thadhani, A.H. Mutz, P. Kasiraj, T. Vreeland, Jr., source cited in 
Ref. 6 (to be published). 
11. M.L. Haviland and J.T. Rodgers, Lubrication Engr. 17, 110 (1961). 
12. C. Albertson and G. Wolfram, ASLE Trans. 1£, 77 (1969). 


https://authors.library.caltech.edu/54076/1/Wear%20Properties%20of%20a%20Shock%20Consolidated%20Metallic%20Glass.pdf

Wear Properties of A Shock Consolidated Metallic Glass and Glass-Crystalline Mixtures

Abstract

Similar works

Full text

Available Versions

Caltech Authors - Main

Caltech Authors - Main