effect of shot peening on the fatigue performance of ductile iron castings · · 2013-04-30effect...
TRANSCRIPT
1
Effect of shot peening on the fatigue performance of ductile iron castings
S. Ji, K. Roberts, Z. Fan
Department of Materials Engineering
Brunel University
Uxbridge, Middlesex, UB8 3PH
UK
Abstract
Ductile iron is a commonly used structural material. However the unsatisfactory fatigue
performance has limited its application for some dynamic loads. Shot peening is a mechanical
surface modification process, which can extend the fatigue life of materials by introduction of
working hardening and compressive layer on surface and removal of the surface
irregularities. Results of the influence of shot peening treatment on ductile iron castings with
as-cast surface and machined surface are presented. The results showed that the shot peening
on ductile iron could double the fatigue life for as-cast surface and increase by 4 times for
machined surface. It is believed that shot peening affects fatigue life through the reduction of
the density and the length of the cracks formed on the surface of specimens of ductile iron.
Keywords: ductile iron, fatigue, surface treatment, shot peening, micro-cracks
2
1. Introduction
Ductile iron is one of the most commonly used structural materials in the world because of its
good combination of low cost, design flexibility, good strength-to-weight ratio, toughness,
wear resistance and fatigue performance [1,2]. It offers this good combination of properties
with the excellent castability, thus possessing unique production advantages [3]. However,
the fatigue performance of ductile iron is not sufficiently good in some applications for
dynamic loads. A lot of trials have been undertaken to improve the fatigue life of ductile iron
in the last few decades [1], but the industrially applicable processes are still rare because of
the limitation of the gains in properties and operation flexibility. However, little is known
about its fatigue in response to shot peening surface treatment, especially for the directly
shot-peened as-cast surface, even though some results have been found on the austempered
ductile iron with other processes [4,5,6,7]. As it involves blasting specimen surface with high
velocity steel or glass particles, shot peening puts the specimen’s interior in a state of tension
while the surface, including a thin layer of sub-surface material, is in compression [8]. This is
considered to be an effective life enhancement process because of the compressive residual
stress and its effect, which is to delay surface cracking [9, 10]. Therefore, this paper aims to
introduce the effect of shot peening on the fatigue life of ductile iron. Four different kinds of
surface conditions, as-cast, shot-peened as-cast, machined, machined and shot-peened were
used to examine the fatigue life, microstructural and fracture features.
2. Experimental
The ductile iron castings were produced in a foundry for the current project. A medium
frequency coreless induction furnace was used to melt the alloys and superheat to 1500oC.
The melt was taped into a preheated shank ladle of 20kg capacity, containing the nodulising
alloys and inoculation alloys with sandwich techniques. Another kind of inoculating granular
additive of ferrosilicon alloys was added as stream inoculation during pouring the treated
melt into the mould. The pouring temperature of the melt was controlled at 1450oC. A plate
type casting with a dimension of 225×150×40 mm were produced in the moulds
manufactured by silica sand with 1% furan resin binder and 0.40% hardener (based on sand).
The typical chemical composition of the produced casting was 3.54wt.%C, 2.41wt.%Si,
0.53wt.%Mn, <0.02wt.%P, <0.01wt.%S and 0.03wt.% of retained magnesium. The numbers
3
and the nodularity of graphite nodules in casting section were >200mm-2 and >0.90,
respectively. The main mechanical properties of the ductile iron include tensile strength of
500MPa, 2% proof stress of 320MPa, elongation of 7% and typical hardness from HB170 to
HB230.
The produced castings were treated with blasting in a foundry, following the industrial
castings. Then the castings were randomly classified into four groups for specimen
production. One group of castings was retained without further surface treatment, which was
defined as as-cast surface (AC). The specimens, as schematically shown in Fig. 1, were
machined from the bottom of the castings. Only one specimen was cut off from one casting.
The bottom surface of the specimens was retained for surface treatment and other surfaces
were machined to a same quality. Three types of further surface treatments used in this study
were shot peened as-cast surface (PC), machined surface (MS), and machined and shot
peened surface (MP). For the machined surface, 1.5mm of metal was cut off at the bottom of
the casting surface.
Shot peening was performed by means of an injector-type system. Peening intensity was
measured using an A Almen strip. The main parameters of shot peening are summarised in
Table 1. The surface roughness was used to define the surface condition, which was
measured by a profilometer. The measured Ra values for different surface conditions were
17.0 µm for AC, 7.3µm for PC, 4.3µm MS and 3.7 for MP, respectively.
The specimens were fatigued to failure in a bending machine at a frequency of 25Hz using
10-20 specimens for S-N curves and the laboratory temperature was 20oC. The
microstructural observations were taken for tested specimens by means of optical microscope
and scanning electron microscope (SEM). SEM also observed the fracture characteristics of
specimens after failure.
3. Results
The relationship between the bending stress and the number of cycles to failure is shown in
Fig. 2. It is evident that the shot peening treatment can significantly improve the fatigue life
of the ductile iron. The numbers of fatigue life of the specimens with shot-peened surface
4
were obviously higher than that of the surface without shot peening treatment, including
machined surface and as-cast surface, even though the roughness of shot-peened as-cast
surface is higher than that of machined surface. The average increasing range of the fatigue
life of the specimens was double between as-cast surface and shot-peened as-cast surface and
4 times between machined surface and shot-peened and machined surface. The fatigue life of
the specimens with shot-peened as-cast surface was higher than those with machined surface.
At low stresses, the fatigue life of the specimens with shot-peened as-cast surface was close
to those with machined surface. Both of them were much higher that the specimens with as-
cast surface and lower than the specimens with machined and shot-peened surface.
Fig. 3 shows the crack developed after bending test on the unetched section of ductile iron
with different surface conditions. The results illustrated that shot peening can drastically
reduce the number and penetrating depth of the micro-cracks on the casting surface and sub-
surface. For the specimens with as-cast surface, as shown in Fig. 3a, a lot of deeply
penetrated cracks were found on and near the surface. The graphite nodules on and near the
casting surface were also apparently distorted, which were prolonged along the crack
direction. After shot peening treatment, as shown in Fig. 3b, the numbers of the cracks on the
surface of the specimens were considerably reduced. The depth and the length of the cracks
penetrating into the specimens were also smaller than those with as-cast surface. Meanwhile,
the distortion of graphite nodules near the surface of specimen was pronouncedly reduced.
The smaller distortion of the graphite nodules and reduced micro-cracks indicated that the
matrix was hardened by shot peening. For the machined surface, as shown in Fig. 3c, small
and short cracks were found to distribute randomly on the surface and sub-surface of the
specimens and the graphite nodule distortion was quite small. For the machined and shot-
peened surface, as shown in Fig. 3d, the numbers of the cracks were further reduced and the
distortion of graphite nodules was not pronounced in the micrograph.
Fig. 4 shows the microstructures of ductile iron with different surface conditions, which
illustrated the variation of the deformation of ferrite and pearlite in the matrix after the
bending fatigue life test. Both ferrite and pearlite in the matrix were apparently distorted near
the as-cast surface in the specimens, as shown in Fig. 4a. The distortion of the ferrite and
pearlite in the matrix was reduced for the specimens with shot-peened as-cast surface
(Fig.4b). This could further indicate the existence of the harden layer on the shot-peened
surface. The distortion of ferrite and pearlite in the matrix of specimens with machined
5
surface (Fig. 4c) and shot-peened and machined surface (Fig. 4d) was not apparent. The
results in Fig. 4 revealed that the distortion of the ferrite and pearlite near the shot peened
surface is different to those with as-cast surface.
Fig. 5 shows the fractographical micrographs of ductile iron with different surface conditions.
For specimens with as-cast surface, the fracture surface contains mainly the faceted brittle
areas. The cleavage cracks were visible on the fracture surface of the specimens (Fig. 5a).
The fracture surface of shot-peened as-cast specimens had less cleavage cracks and more
dimpled ductile areas (Fig. 5b). The similar tendency could be found in Fig. 5c and Fig. 5d,
corresponding to the machined surface and machined and shot-peened surface, respectively.
The faceted brittle fracture was also clearly visible in the shot peened layer near the surface in
both Fig. 5b and 5d.
4. Discussion
The results illustrated that shot peening on the surface of ductile iron castings improves their
fatigue life significantly. The fatigue life of the specimens with shot peening can be doubled
for as-cast surface and increased by 4 times for machined surface. The experimental
observations also found that the increase of the fatigue life can be attributed the reduction of
the cracks on the surface and sub-surface of the specimens. These can be further intercepted
by the existence of surface hardening and compressive stresses and the removal of
irregularities on the casting surface introduced by shot peening.
Numbers of cycles to failure of thin specimens (4mm) are governed by the initiation and
growth of small cracks, and residual stresses. The crack density developed in the early stage
of fatigue life increases with cycling due to the nucleation of additional cracks. Because of
this and the growth of some existing cracks, the cracks spacing is presumed to decrease
continuously and approach its steady value when material attains its saturation. Subsequently,
a few of the cracks could link up to form a critical crack that in turn can propagate to failure
in negligible cycles. As cracks start at the surface, a concern of course is its condition of
surface. Being in as-cast state, the surface is rough and usually contains some inclusions.
There are many graphite nodules distributed in the matrix. These lead the development of
stress concentration and further promote crack nucleation and propagation across the
specimen section. As a result, it has a lower fatigue life at all stresses (Fig. 2&3a). The
6
machined surface cut off the rough layer, which gives rise to an improved feature. So the
fatigue life is longer than those of as-cast surface (Fig.2). But the existence of graphite
nodules can be the source of crack nucleation, as shown in Fig. 3 and 4. So the fatigue life is
still limited.
The improvement of shot peening on the fatigue life can be attributed to three aspects, surface
hardening, and the removal of irregularities on the casting surface and the existence of
compressive residual stress. Shot peening is a classic method known to bring about working
hardening in the surface region of materials, which could considerably improve the fatigue
strength [11]. The working hardening can explained by the dislocation mechanism of crystal-
lattice transformation, which responds to the low-temperature phase transformation of ferrite
and pearlite to influence the mechanical properties. The significantly increased hardness near
the surface region of materials has been found in different materials [12, 13].
It is also conceivable that the removal of irregularities on the casting surface can improve the
fatigue life because most cracks start at surface (Fig. 3), especially for the as-cast surface.
The shot peening on as-cast surface can drastically reduce its surface roughness Ra from 17.0
µm to 7.3µm. Some irregularities and inclusions on the casting surface are peened off. So the
opportunities of crack nucleation from these surface irregularities and inclusions is reduced.
The fatigue performance is therefore improved. Similar behaviours have been noted for other
alloys during shot peening treatment [14].
Another important factor to improve the fatigue life is the existence of compressive residual
stress developed in the ductile iron by shot peening. A high-level compressive residual stress
exists up to the depths of 400-500µm with a maximum values of –450MPa at the surface
layer [15]. When applying a higher level fatigue stress, the compressive residual stress on the
surface is rapidly decreased and the tensile stress occurs through the concentration of stress at
dents or irregularities on the surface or at graphite nodules existing immediately below the
surface. As a result, the cracks can be nucleated and propagate from the surface. In this case,
the fatigue life is mainly determined by the value of the stress concentration. The role of the
existed compressive residual stress on the surface of ductile iron is thus limited. When
applying a lower level fatigue stress, the compressive residual stress at the surface area does
not decrease significantly or can last for a longer cycling time, which could prevent the
7
nucleation and propagation of the cracks. With the increase of cycling, the cracks can be
nucleated from the internal defects such as graphite nodules and inclusions in the matrix and
the irregularities on the surface of castings [15,16]. In this case, the compressive residual
stress is expected to play an important role to extend the fatigue life.
It is difficult to exactly define the role of three aspects, the working hardening on surface, the
removal of surface irregularities and the existence of compressive residual stress on surface
and sub-surface on the improvement of the fatigue performance of the shot-peened casting
surface.
5. Summary
Shot peening on the surface of ductile iron castings can significantly extend their fatigue life.
Compared to conventional as-cast surface and machined surface of castings, numbers of
cycles to failure of thin specimens are doubly increased for shot-peened as-cast surface and
increased by 4 times for shot-peened and machined surface, respectively. It is believed that
shot peening affects fatigue life through the retardation of crack nucleation and growth
because of the introduction of working hardening and compressive stresses on the surface and
sub-surface and removal surface irregularities of the ductile iron castings.
8
Table 1. The parameters of shot peening treatment for ductile iron castings
Pressure Shot size Distance Vertical speed Rotating speed Coverage Intensity
3.0kg/cm2 0.80mm
(S330)
200mm 240 mm/min 30 rpm > 85% 0.30 A
30m
m
φ7mm
90mm
10mm
R32mm
δ=4mm
Fig. 1. The schematic diagram of the specimen for fatigue life tests.
9
150
200
250
300
350
400
450
1.E+04 1.E+05 1.E+06 1.E+07
Number of cycles to failure
Stre
ss (M
Pa)
ACPCMSMP
Fig. 2. S-N curves of ductile iron with as-cast surface (AC), shot-peened as-cast surface (PC),
machined surface (MS), and machined and shot-peened surface (MP).
104 105 106 107
10
11
Fig. 3. The Un-etched optical micrographs showing the cracks and the distortion of graphite
nodules in failed ductile iron specimens at a fatigue stress of 360MPa with different surface
qualities. (a) as-cast surface (AC), (b) shot-peened as-cast surface (PC), (c) machined surface
(MS), and (d) machined and shot-peened surface (MP).
12
13
Fig. 4. The optical micrographs etched with 1% nital showing the microstructures of in failed
ductile iron specimens at a fatigue stress of 360MPa with different surface qualities. (a) as-
cast surface (AC), (b) shot-peened as-cast surface (PC), (c) machined surface (MS), and (d)
machined and shot-peened surface (MP).
14
15
Fig.5. The SEM micrographs showing the fracture surface after fatigue failure of ductile iron
specimens at a fatigue stress of 360MPa with different surface qualities. (a) as-cast surface
(AC), (b) shot-peened as-cast surface (PC), (c) machined surface (MS), and (d) machined
and shot-peened surface (MP).
16
References
[1] M. JOHANSSON: AFS Trans., 1977, 85, 117.
[2] RIO TINTO IRON & TITANIUM, INC.: ‘Ductile Iron Data for Design Engineers’, 1990,
Rio Tinto Iron & Titanium, Inc., USA.
[3] CAST METALS DEVELOPEMNT LTD.: Materials & Design, 1992,13, 285.
[4] S. K. PUTATUNDA, L BARTOSIEWICZ, R. J. HULL, et al: Materials Manufacturing
Process, 1997, 12,137.
[5] N. R. TAO, M. L. SUI, J. LU and K. LUA: Nanostructured Materials, 1999,11, 433.
[6] A. ROY and I. MANNA: Materials Science and Engineering A, 2001,A297, 85.
[7] H. P. FENG, S. C. LEE, C. H. HSU and J. M. HO: Materials Chemistry and Physics,
1999, 59, 154.
[8] G. E. DIETER: ‘Mechanical Metallurgy’, 409; 1986, McGraw-Hill.
[9] F. V. LAWRENCE and P. K. MAZUMDAR: in ‘Low Cycle fatigue Strength and Elasto-
plastic behaviour of Materials (ed. K. T. Rie and E. Haibach )’, 469-475; Stuttgart, 1979.
[10] K. E. THELNING: ‘Steel and its heat treatment’, 2nd edn, 1984, Butterworths.
[11] M. HASHIMOTO, M. SHIRATORI, M. ITO, J. HIRAI: Transaction of Japan Society of
Mechanical Engineering, Series A, 1995,61, 889.
[12] V. O. ABRAMOV, O. V. ABRAMOV, F. SOMMER, O. M. GRADOV and O. M.
SMIRNOV. Ultrasonics, 1998, 36, 1013.
[13] A. DRECHSLER, T. DÖRR and L. WAGNER: Materials Science and Engineering A,
1998, A243, 217.
[14] A. EFTEKHARI, J. E. TALIA, and P. K. MAZUMDAR: Materials Science and
Engineering A, 1995, A199, L3.
[15] Y. OCHI, K. MASAKI, T. MATSUMURA and T. SEKINO: International Journal of
Fatigue, 2001, 23, 441.
[16] K. ASAMI, M. HIRONAGA. Journal of the Society of Material Science of Japan. 1994,
43, 12.