lean can mean sinter-hard and cost-effective
TRANSCRIPT
40 MPR July/August 2008 0026-0657/08 ©2008 Elsevier Ltd. All rights reserved.
technical trends
Lean can meansinter-hard andcost-effectiveWhen sinter-hardenable steels were first brought to market the cost of alloying elements was not a major issue. But times change, and economics with them, as any production engineer can attest. However, some aspects of the challenges raised by soaring commodity prices can be tackled by technology. The wider inclusion of improved cooling zones by furnace manufacturers in their products means that lower-cost, low-alloy steels can be successfully sinter-hardened…
The first sinter-hardenable alloys
introduced into the marketplace
relied on high concentrations of
alloying elements in the steel. As
sinter hardening has become more common,
sinter furnace producers have improved the
cooling zones in the furnace. The increase in
obtainable cooling rates allows lower alloyed
steels to be used to obtain sinter-hardened
parts. This is especially important in relation
to small parts, where higher cooling rates can
be achieved. This indicates the need for an
alloy with a composition that optimises the
levels of price sensitive elements while main-
taining the ability to sinter-harden in current
belt furnaces.
Traditional sinter-hardening PM steel
compositions utilise high levels of molyb-
denum (Mo), nickel (Ni) and copper (Cu)
along with high carbon (C) contents to
achieve martensitic microstructures in the
as-sintered condition. Historically, high
cooling rates could not be achieved in
the sintering furnace, leading to only the
most highly alloyed materials being used
for sinter hardening. With the advent of
accelerated cooling zones and the adop-
tion of these technologies, lower alloy
contents can be used. When alloy prices
are low, it is easier to use heavily alloyed
materials to ensure a martensitic micro-
structure forms regardless of section size
and cooling rate in the part. As price
pressures force a re-assessment of alloy
selection, it may be more cost effective to
invest in additional processing to reduce
the content of high priced alloying ele-
ments. The added processing may include
longer sintering times to fully utilise
admixed ingredients, accelerated cooling,
and an analysis of the actual cooling rate
in each part to determine the lowest alloy
content necessary for sinter hardening.
There are several approaches that can
be taken to address raw material costs.
The first is to introduce lower cost alloying
elements, such as chromium (Cr) and/or
manganese (Mn). These oxygen-sensi-
tive elements provide excellent harden-
ability, but may lead to higher processing
costs associated with powder production
and sintering. One benefit of these more
effective alloying elements is that lower
carbon levels can be used while maintain-
ing a martensitic microstructure. These
lower carbon martensitic alloys provide
lower dimensional variation and enhanced
mechanical properties [1]. The chro-
mium-containing Ancorsteel® 4300 and
Ancorsteel 4300L (0.3% Mo) are examples
of such alloys, where as-sintered marten-
sitic microstructures are common with
sintered carbon contents less than or equal
to 0.6 % (wt%) [2].
Another approach to lower cost sinter
hardening is the development of alloys
that have intermediate levels of alloying
elements. Earlier alloys used high levels of
molybdenum and nickel as powder costs
were relatively low compared with secondary
heat-treating steps. Ancorsteel 737 SH (MPIF
FL-4800 [3]) has the combination of good
Table I. Nominal composition (in wt%) of the base alloys studied.
Alloy Fe Mo Ni Mn
Ancorsteel 721 SH Bal. 0.9 0.5 0.4
Ancorsteel 737 SH (FL-4800) Bal. 1.2 1.4 0.4
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compressibility and excellent hardenability,
but at current price levels, the 1.25% Mo and
1.4% Ni prealloyed in the powder make it
somewhat less attractive. Nevertheless, when
processing larger parts or where accelerated
cooling is not an option, slow cooling rates
within the part require these high levels of
alloying for sinter hardening. The diffusion
alloyed materials containing 4% nickel and
either 0.5% or 1.5% molybdenum also have
relatively high cost, and given that the nickel
is not prealloyed, do not take full advantage
of the alloying elements present. Those parts
producers that have the ability to
cool components at higher rates than
Table II. Comparison of the new alloy Ancorsteel 721 SH and FL-4800 at cooling rates of 0.7-2.2°C/s with 1 wt% Copper and
0.9 % Graphite.
Base
Alloy
Copper
(wt%)
Graphite
(wt%)
Cooling
Rate (°C/s)
Compaction
(MPa)
Density
(g/cm3)
DC
(%)
Hardness
(HRA)
YS
(MPa)
UTS
(MPa)
Elong.
(%)
721 SH 1 0.7 0.7 550 6.96 0.21 52 449 559 1.2
721 SH 1 0.7 0.7 690 7.11 0.23 54 540 644 1.3
FL-4800 1 0.7 0.7 550 6.83 0.31 65 726 783 1.0
FL-4800 1 0.7 0.7 690 6.98 0.33 67 777 875 1.0
721 SH 1 0.7 1.6 550 6.94 0.29 66 770 884 1.1
721 SH 1 0.7 1.6 690 7.10 0.31 68 858 955 1.1
FL-4800 1 0.7 1.6 550 6.83 0.33 67 767 785 0.8
FL-4800 1 0.7 1.6 690 6.99 0.35 69 849 906 0.9
721 SH 1 0.7 2.2 550 6.87 0.30 71 804 903 1.0
721 SH 1 0.7 2.2 690 7.03 0.33 71 873 963 0.9
FL-4800 1 0.7 2.2 550 6.83 0.34 67 732 823 0.8
FL-4800 1 0.7 2.2 690 6.99 0.37 69 891 945 0.8
Table III. Comparison of the new alloy Ancorsteel 721 SH and FL-4800 at cooling rates of 0.7-2.2°C/s
with 2 wt% Copper and 0.9 wt% Graphite.
Base
Alloy
Copper
(wt%)
Graphite
(wt%)
Cooling
Rate (°C/s)
Compaction
(MPa)
Density
(g/cm3)
DC
(%)
Hardness
(HRA)
YS
(MPa)
UTS
(MPa)
Elong.
(%)
721 SH 2 0.9 0.7 550 6.95 0.23 63 679 840 1.2
721 SH 2 0.9 0.7 690 7.09 0.27 66 733 912 1.2
FL-4800 2 0.9 0.7 550 6.85 0.15 68 654 818 1.2
FL-4800 2 0.9 0.7 690 7.00 0.22 69 693 996 1.4
721 SH 2 0.9 1.6 550 6.93 0.27 68 637 849 1.1
721 SH 2 0.9 1.6 690 7.08 0.31 71 701 954 1.2
FL-4800 2 0.9 1.6 550 6.85 0.16 69 634 829 1.2
FL-4800 2 0.9 1.6 690 7.00 0.22 70 685 983 1.4
721 SH 2 0.9 2.2 550 6.87 0.29 73 706 902 1.1
721 SH 2 0.9 2.2 690 7.00 0.32 74 759 919 1.0
FL-4800 2 0.9 2.2 550 6.85 0.18 69 618 944 1.3
FL-4800 2 0.9 2.2 690 6.99 0.23 70 649 914 1.1
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conventional cooling need not pay for extra
alloying when a leaner alloy would suffice.
With that in mind, a new alloy, Ancorsteel
721 SH, has been developed by Hoeganaes
Corporation for lower cost sinter hardening.
The nominal compositions of
Ancorsteel 721 SH and Ancorsteel 737
SH (FL-4800) are given in Table I. The
new alloy, Ancorsteel 721 SH, contains the
same prealloyed constituents as FL-4800,
however with 0.3% less Mo and 0.9% less
Ni. All mixes for this study were prepared
with 0.75% EBS wax (Acrawax® C) as the
lubricant and varying amounts of Asbury
type 3203H graphite. Admixed copper was
used to produce alloys with 1% and 2%
Cu. Transverse rupture strength, dogbone
tensile, and impact bars were pressed at 415
MPa (30 tsi), 550 MPa (40 tsi) and 690 MPa
(50 tsi) and sintered in 90% N2- 10% H2
(vol%) atmosphere at 1120°C (2050°F) for
15 minutes in an Abbott continuous-belt fur-
nace with an accelerated cooling system.
Jominy evaluation
Three average cooling rates were
chosen for study: 0.7°C/s (1.3°F/s),
1.6°C/s (2.8°F/s) and 2.2°C/s (4.0°F/s).
The cooling rate was measured in the
sample between 650°C (1200°F) and
315°C (600°F). All samples were tem-
pered at 205°C (400°F) for one hour
in a nitrogen (N2) atmosphere prior to
testing. Measurements were performed
in accordance with the relative MPIF
standards [4].
Hardenability of the new alloy was
evaluated using the Jominy end-quench
method. Cylindrical test specimens were
machined to a length of 100 mm (4 in.)
and 25 mm (1 in.) diameter from blocks
compacted to a green density of approxi-
mately 7.0 g/cm3. All bars were initially
sintered in 90% N2 – 10% H2 (vol%)
atmosphere at 1120°C (2050°F) for 15
minutes in a continuous-belt furnace.
These samples were austenitised at 900°C
(1650°F) for 30 minutes in 90% N2 – 10%
H2 (vol%) atmosphere prior to end-
quenching. The Jominy end-quench test
method and hardness measurements were
carried out according to ASTM standard
A 255 [5] and MPIF standard 65 [4].
Figure 1 demonstrates the compress-
ibility of Ancorsteel 721 SH in compari-
son to the more heavily alloyed version,
FL-4800. It is apparent that the new alloy
has an improved compressibility with the
capability of achieving a green density of
7.1 g/cm3 or better at a compaction pres-
sure of 690 MPa. The increase in density
at similar compaction pressures, in part,
plays a significant role in the new alloy’s
capacity to achieve and even surpass
the mechanical properties of FL-4800.
Processing considerations (ie accelerated
cooling zones) strongly dictate the effec-
tiveness of the new alloy in providing the
necessary mechanical properties attrib-
uted to a viable sinter-hardening alloy.
Mixes of Ancorsteel 721 SH and FL-4800
were prepared with additions of 1% Cu
with 0.7% graphite (Table II) and 2% Cu
with 0.9% graphite (Table III). Compaction
pressures of 550 MPa and 690 MPa are pre-
sented which allow for an easy comparison
of mechanical properties as a function of
sintered density. The hardness and tensile
data are arranged according to conventional
(0.7°C/s) and accelerated cooling (1.6-
2.2°C/s) conditions within a continuous-belt
furnace. FL-4800 clearly displays superior
mechanical properties over Ancorsteel 721
SH at conventional cooling rates when only
1% Cu and 0.7% graphite is added. This
demonstrates the capability for a fully
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44 MPR July/August 2008 metal-powder.net
hardening FL-4800 under even the most dif-
ficult processing conditions. However, if the
cooling rate can be increased beyond 0.7°C/s
during processing, Ancorsteel 721 SH is
capable of exhibiting comparable values to
FL-4800 at a lower alloy cost. Though not
presented in this study, the new alloy even
offers a sufficient hardenability with no
admixed copper, similar to that of FL-4800,
given an increased cooling rate [6].
Section size and belt speed are increas-
ingly more important factors when con-
sidering the usefulness of accelerated
cooling with a lean sinter-hardening alloy.
Therefore, careful consideration as to the
amount of admixed constituents should be
explored to fully utilise the alloy. With the
addition of 2% copper and 0.9% graph-
ite to Ancorsteel 721 SH, the mechanical
properties appear to be less sensitive to
cooling rate, although reduced levels are still
Figure 2. Apparent hardness of Ancorsteel 721 SH and FL-4800.Figure 1. Compressibility of Ancorsteel 721 SH and FL-4800.
Figure 3. Dimensional change of Ancorsteel 721 SH and FL-4800. Figure 4. Elongation of Ancorsteel 721 SH and FL-4800.
Figure 5. Ultimate Tensile Strength of Ancorsteel 721 SH and FL-4800. Figure 6. Yield Strength of Ancorsteel 721 SH and FL-4800.
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apparent at conventional cooling rates when
compared with FL-4800. Beyond conven-
tional cooling, Ancorsteel 721 SH with 2%
Cu notably achieves the same, if not greater
properties over FL-4800.
Figures 2-6 highlight the mechanical
properties of the alloys studied at a com-
paction pressure of 690 MPa over the range
of cooling rates tested. With the addition
of 2% copper and 0.9% graphite, the two
alloys perform similarly. Both alloys have
sufficient hardenability, over the three
cooling rates, to achieve 30 HRC and above,
as shown in Figure 2. A major difference
between Ancorsteel 721 SH and FL-4800
is the dimensional change after sintering.
Current die dimensions would require
modification to account for the increase in
part expansion beyond that which is cur-
rently seen with FL-4800. However, one
benefit of the lower alloy content (especially
nickel) in Ancorsteel 721 SH is less retained
austenite in the as-sintered microstructure.
The lower retained austenite content will
lead to better dimensional consistency in
parts. Additionally, elongation, ultimate
tensile strength, and yield strength are com-
parable in level and observed trend for parts
admixed with 2% copper and 0.9% graph-
ite for both alloys. These results suggest
that Ancorsteel 721 SH is a feasible sinter-
hardening alternative to FL-4800.
At 1% copper and 0.7% graphite, the
new alloy exhibits a reduced level of hard-
ness than that of FL-4800 at the lower
cooling rates as a result of diminished
hardenability. Nevertheless, Ancorsteel
721 SH is capable of demonstrating an
improved hardness at the highest cooling
rate, 41 HRC, exceeding FL-4800. Under
conventional cooling rates, Ancorsteel
721 SH is clearly inferior to FL-4800 in
hardenability and therefore mechanical
properties. Accelerated cooling in con-
junction with enhanced compressibility of
the alloy does, however, provide the capa-
bility to greatly enhance these properties
to comparable values.
Microstructure revealed
The microstructure of Ancorsteel 721 SH
admixed with 1% Cu and 0.7% graphite
is increasingly martensitic when proc-
essed at higher cooling rates, Figure 7.
When slow cooled at 0.7°C/s, this new
alloy largely transforms into a pearlitic
(with some bainite) microstructure, which
agrees well with the lower mechanical
properties already presented. At increased
cooling rates however, the microstructure
almost fully transforms into martensite;
increasing from approximately (a) 15%
martensite, 85% bainite/pearlite, to (b)
72% martensite, 28% bainite/pearlite,
and (c) 87%martensite, 13% bainite/
pearlite at the highest cooling rate; based
on a point-count method [7]. This clearly
displays the significance and necessity of
using accelerated cooling rates in order
to take full advantage of this lean sinter-
hardening alloy.
When admixed with 2% copper and
0.9% graphite, the microstructural develop-
ment of Ancorsteel 721 SH follows a simi-
lar trend when processed with increasing
cooling rates (Figure 8). With the increased
amount of admixed constituents, the
slow-cooled microstructure transforms to
a greater fraction of martensite compared
with the 1% copper version; starting at
approximately (a) 45% martensite, 55%
bainite/pearlite for a cooling rate of 0.7°C/s,
to (b) and (c) 97% martensite, 3% bainite/
pearlite for cooling rates of 1.6 to 2.2°C/s,
Figure 7. Microstructures of Ancorsteel 721 SH with 1% Cu and 0.7% graphite compacted at 690 MPa, sintered at 1120 °C for 15 minutes, and cooled at (a) 0.7 °C/s (b) 1.6 °C/s and (c) 2.2 °C/s.
Figure 8. Microstructures of Ancorsteel 721 SH with 2% Cu and 0.9% graphite compacted at 690 MPa, sintered at 1120 °C for 15 minutes, and cooled at (a) 0.7 °C/s (b) 1.6 °C/s and (c) 2.2 °C/s.
Figure 9. Jominy end-quench hardenability of Ancorsteel 721 SH and Ancorsteel 4600V.
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respectively. A small amount of retained
austenite was observed in the martensitic
microstructure. As mentioned previously,
the increase in copper and graphite content
generally leads to the formation of retained
austenite, typically around the prior particle
boundaries [7], potentially generating a
negative impact on properties. The amount
of retained austenite appeared to be lower
in the Ancorsteel 721 SH alloy compared
with FL-4800. This alloy is most effective
when sintering furnaces are equipped with
accelerated cooling zones.
References1. B Lindsley and T F Murphy,
“Effect of post sintering thermal
treatments on dimensional preci-
sion and mechanical properties
in sinter-hardening PM steels”,
Advances in Powder Metallurgy
& Particulate Materials, MPIF,
Princeton, NJ, 2007.
2. P King and B Lindsley,
“Performance Capabilities Of
High Strength Powder Metallurgy
Chromium Steels With Two
Different Molybdenum Contents”
Advances in Powder Metallurgy
& Particulate Materials, MPIF,
Princeton, NJ, 2006.
3. MPIF Standard 35, Materials
Standards for PM Structural Parts,
2007 Edition.
4. MPIF Standard Test Methods
for Metal Powders and Powder
Metallurgy Products, 2007 Edition.
5. ASTM A 255, Standard Method of
End-quench test for Hardenability
of Steel.
6. B Lindsley, “Alloy Development of
Sinter-Hardenable Compositions”,
EuroPM Proceedings, 2007.
7. T F Murphy, M Baran, “An
Investigation Into the Effect of
Copper and Graphite Additions
to Sinter Hardening Steels”,
Advances in Powder Metallurgy
& Particulate Materials – 2004,
compiled by W B James and R
A Chernenkoff, Metal Powder
Industries Federation, Princeton,
NJ, Part 10, pp. 266-274.
8. W B James, “What is Sinter-
Hardening?” Presented at PM2TEC
1998.
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48 MPR July/August 2008 metal-powder.net
The hardenability of ferrous alloys has
been well documented using the Jominy
end-quench test. This method is used as
an indicator of the depth, or thickness to
which an alloy is capable of being trans-
formed to martensite. Figure 9 compares the
hardness profiles along the length of water
end-quenched bars of Ancorsteel 721 SH to
another commonly used sinter-hardenable
alloy, Ancorsteel 4600V (MPIF FL-4600 [3]),
which has 0.5% molybdenum, 1.8% nickel,
and 0.2% manganese. Notably, Ancorsteel
721 SH with 2% copper and 0.9% graphite
through-hardens in excess of 75 mm
(3 in.), maintaining a hardness above
45 HRC throughout the majority of the
bar length. The higher content of carbon in
solution is generally a significant contribut-
ing factor in maximum attainable harden-
ability [8].
Nevertheless, the difference between
the two alloys is clearly a result of other
alloy additions and their relative alloy-
ing behavior [2]. It is well known that the
hardenability factors for manganese and
molybdenum are greater than that of nickel,
and as Ancorsteel 721 SH contains more
manganese and molybdenum than FL-4600,
the Jominy results represent the expected
performance of the alloy constituents. This
material feature, in connection with acceler-
ated cooling, should allow for parts with
thick cross-sections to be constructed from
this new alloy. Even with a reduced level
of admixed copper and graphite, the alloy
retains an appreciable level of hardenability,
not dropping below the J Depth (65 HRA)
until approximately 57 mm (36/16 in.). In
comparison with FL-4600, Ancorsteel 721
SH is a superior sinter-hardening grade at
similar levels of admixed copper and graph-
ite. The amount of admixing can be tailored
to meet customer specific requirements
based on part dimension, sinter furnace
design, and required mechanical constraints.
To summarise: A new sinter-hardening
alloy, Ancorsteel 721 SH, has been devel-
oped by Hoeganaes Corporation as a viable
alternative to address the continuing trend
in metal price volatility. The reduced level of
alloying, in comparison with its predecessor
Ancorsteel 737 SH (FL-4800), can lead to
insufficient hardening under conventional
cooling parameters (~ 0.7°C/s). Nonetheless,
with the incorporation of advanced cool-
ing systems in modern sintering furnaces,
accelerated cooling rates of 1.6 to 2.2°C/s are
capable of yielding almost fully martensitic
microstructures within the new alloy. The rel-
ative amount of martensitic transformation
under accelerated cooling, of Ancorsteel 721
SH, provides suitable mechanical properties
rivalling those of FL-4800 at a reduced cost.
In the event part manufacturers are willing
to utilise elevated cooling systems along with
judicious tailoring of the premix, Ancorsteel
721 SH provides the appropriate level of
strength and mechanical response required
for selective components.
The AuthorsTHIS article was adapted from
Introduction of a new sinter-harden-
ing PM steel, a paper given at the
Washington World Congress, by Peter
Sokolowski, Bruce Lindsley and Francis
Hanejko, who work for Hoeganaes
Corporation. The authors thanked
Gerard Golin for his assistance in provid-
ing microstructures and analysis as well
as Andrew Chan and Paul Fallis for col-
lecting the data found within this paper.
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