Fatigue deformation of copper single crystals containing noncoherent cobalt particles
- PDF / 1,399,049 Bytes
- 3 Pages / 612 x 792 pts (letter) Page_size
- 4 Downloads / 252 Views
crease in flow s t r e s s from the first cycle to saturation, is 12.1 MN.m -~ for copper-cobalt as compared to 28.4 MN. m -z for the copper single crystals. The cumulative strain at which the saturation s t r e s s is reached is l a r g e r for copper-cobalt than for pure copper. The effect of orientation on fatigue hardening of copper-cobalt single c r y s t a l s is quite marked as shown in Fig. 1. The fatigue hardening is 35.1 MN 9m -2 for the copper-cobalt single crystals of duplexslip orientation as compared to 12.1 MN. m -2 for the crystals of single-slip orientation. The cumulative strain at which the saturation s t r e s s is reached is an order of magnitude smaller for copper-cobalt single crystals of duplex-slip orientation as compared to that for crystals of single-slip orientation. An examination of the surface of the fatigued specimens by optical m i c r o s c o p y revealed uniformly spaced fine slip lines on all the surfaces within the gage length. While crystals of single-slip orientation r e vealed only the p r i m a r y slip traces, crystals of duplexslip orientation showed a c r i s s - c r o s s pattern of prim a r y and conjugate slip. The spatial and Burgers vector distribution of the dislocations was studied after fatigue deformation into the saturation stage. The dislocation m i c r o s t r u c t u r e was studied on sections parallel to the p r i m a r y and conjugate planes, i.e., (111) and (111) planes r e s p e c tively. Single-slip orientation: The dislocation m i c r o s t r u c ture in the saturation stage of fatigue deformation of copper-cobalt single crystals is shown in Fig. 2. A detailed study of the Burgers vector of dislocations showed that almost all the dislocations were in the r t
7.0
101
102
70
Cu-Co Duplex
Stip)
6.0
50
5.0
50 =•
~
~o~
~" 4.0 E E
z 7
03
@
3.0
2.0
_~0
/ Pure Cu' / //(Duplex slip) ./'Pure Cut' / ." (Single slip) /
/
11
I0
1.0 t""
r K e m s t e y & P o t e r s o n (6 ) t~ K u p c i s et al (2)
"" i,,
t
|11t111
......1
I
I
I 1
101 102 N (Cycles)
|
0 ,103
I ! !
Fig. l--Fatigue hardening curve. VOLUME6A, OCTOBER 1975-1957
p r i m a r y plane and had either the p r i m a r y Burgers vector, a/2 [I01] or the coplanar Burgers vectors a/2 [0~1] and a/2 [lI0]. There were v e r y few forest dislocations. A prominent feature is the alignment of p r i m a r y edge dipoles in the trace directions of the conjugate and critical planes on the p r i m a r y plane.
Duplex-slip orientation. The dislocation m i c r o structure in the saturation stage of fatigue d e f o r m a tion of copper-cobalt single crystals oriented for duplex-slip is shown in Figs. 3 and 4. The cell s t r u c ture is well-developed and an equiaxed closed-cell distribution is seen on the (111) or primary plane.
Fig. 2--Single-slip orientation: Dislocation microstructure on the (111) plane.
Fig. 3--Duplex-slip orientation: Dislocation microstructure on the primary plane.
1958-VOLUME 6A, OCTOBER 1975
METALLURGICALTRANSACTIONSA
m i n a p a r t i c l e s . 1 The p r
Data Loading...
