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1.
W. O. Soboyejo J. Dipasquale F. Ye C. Mercer T. S. Srivatsan D. G. Konitzer 《Metallurgical and Materials Transactions A》1999,30(4):1025-1038
This article presents the results of a study of the fatigue and fracture behavior of a damage-tolerant Nb-12Al-44Ti-1.5Mo
alloy. This partially ordered B2 + orthorhombic intermetallic alloy is shown to have attractive combinations of room-temperature
ductility (11 to 14 pct), fracture toughness (60 to 92 MPa√m), and comparable fatigue crack growth resistance to IN718, Ti-6Al-4V,
and pure Nb at room temperature. The studies show that tensile deformation in the Nb-12Al-44Ti-1.5Mo alloy involves localized
plastic deformation (microplasticity via slip-band formation) which initiates at stress levels that are significantly below the uniaxial yield stress (∼9.6 pct of
the 0.2 pct offset yield strength (YS)). The onset of bulk yielding is shown to correspond to the spread of microplasticity
completely across the gage sections of the tensile specimen. Fatigue crack initiation is also postulated to occur by the accumulation
of microplasticity (coarsening of slip bands). Subsequent fatigue crack growth then occurs by the “unzipping” of cracks along
slip bands that form ahead of the dominant crack tip. The proposed mechanism of fatigue crack growth is analogous to the unzipping
crack growth mechanism that was suggested originally by Neumann for crack growth in single-crystal copper. Slower near-threshold
fatigue crack growth rates at 750 °C are attributed to the shielding effects of oxide-induced crack closure. The fatigue and
fracture behavior are also compared to those of pure Nb and emerging high-temperature niobium-based intermetallics. 相似文献
2.
D. L. Davidson K. S. Chan R. Loloee M. A. Crimp 《Metallurgical and Materials Transactions A》2000,31(4):1075-1084
The fatigue and fracture resistance of a commercially made, single-phase Nb-base alloy with 35 at. pct Ti, 5 at. pct Cr, 6
at. pct Al, and several elements to increase solid solution strengthening have been investigated. The threshold for fatigue
crack growth was determined to be ≈7 MPa√m and fracture toughness ≈35 MPa√m. Crack growth was intermittent and sporadic; the
fracture path was tortuous, crystallographic, and appeared to favor the {100} and {112} planes. Fatigue crack closure was
measured directly at the crack tip. The fatigue and fracture properties of the commercial alloy are compared against those
of Nb-Cr-Ti and Nb-Cr-Ti-Al alloys. The comparison indicated that Ti addition is beneficial for, but Al addition is detrimental
to, both fracture toughness and fatigue crack resistance. 相似文献
3.
S. Hariprasad S. M. L. Sastry K. L. Jerina R. J. Lederich 《Metallurgical and Materials Transactions A》1994,25(5):1005-1014
The room-temperature fatigue crack growth rates (FCGR) and fracture toughness were evaluated for different crack plane orientations
of an Al-8.5 Pct Fe-1.2 Pct V-1.7 Pct Si alloy produced by planar flow casting (PFC) and atomized melt deposition (AMD) processes.
For the alloy produced by the PFC process, properties were determined in six different orientations, including the short transverse
directions S-T and S-L. Diffusion bonding and adhesive bonding methods were used to prepare specimens for determining FCGR
and fracture toughness in the short transverse direction. Interparticle boundaries control fracture properties in the alloy
produced by PFC. Fracture toughness of the PFC alloy varies from 13.4 MPa√m to 30.8 MPa√m, depending on the orientation of
the crack plane relative to the interparticle boundaries. Fatigue crack growth resistance and fracture toughness are greater
in the L-T, L-S, and T-S directions than in the T-L, S-T, and S-L orientations. The alloy produced by AMD does not exhibit
anisotropy in fracture toughness and fatigue crack growth resistance in the as-deposited condition or in the extruded condition.
The fracture toughness varies from 17.2 MPa√m to 18.5 MPa√m for the as-deposited condition and from 19.8 MPa√m to 21.0 MPa√m
for the extruded condition. Fracture properties are controlled by intrinsic factors in the alloy produced by AMD. Fatigue
crack growth rates of the AMD alloy are comparable to those of the PFC alloy in the L-T orientation. The crack propagation
modes were studied by optical metallographic examination of crack-microstructure interactions and scanning electron microscopy
of the fracture surfaces. 相似文献
4.
Toughness and strength characteristics of Nb-W-Si ternary alloys prepared by Arc melting 总被引:2,自引:0,他引:2
Jiangbo Sha Hisatoshi Hirai Hidetoshi Ueno Tatsuo Tabaru Akira Kitahara Shuji Hanada 《Metallurgical and Materials Transactions A》2003,34(12):2861-2871
This article describes the room-temperature and high-temperature mechanical properties and failure modes of series Nb-W-Si
alloys—Nb-10W, Nb-10Si, Nb-10Si-5W, Nb-10W-5Si, and Nb-10W-10Si—prepared by arc melting. For the Nb-10W alloy, the microstructure
was a monolithic Nb solid solution (Nb
ss
) with a grain size up to a few hundred microns, while the other four alloys consisted of primary Nb
ss
and a eutectic of Nb
ss
/Nb5Si3 (5-3 silicide) as a result of replacing Nb with Si. Among all alloys, the Nb-10W showed the highest fracture toughness of
about 15.3 MPa√m1/2 and the lowest 0.2 pct yield compressive strength of 90 MPa at 1670 K. Conversely, the Nb-10Si-10W had the highest 0.2 pct
yield strength of about 330 MPa at 1670 K and the lowest fracture toughness of 8.2 MPa√m1/2. It is suggested that toughness is supplied by the metallic Nb
ss
phase, while high-temperature strength is mainly provided by the brittle silicide phase. For the Nb-10W alloy with the monolithic
Nb
ss
, intergranular cleavagelike crack propagation is the fracture mode at room temperature, and dislocation movement within the
grains and grain-boundary sliding are the dominant modes of high-temperature failure. With two-phase Nb
ss
/Nb5Si3 microstructures, the compressive damage of all four alloys at high temperature was dominated by debonding of the interfaces
between the Nb
ss
and the silicide; however, the fracture mode at room temperature is transgranular, controlled by the primary Nb
ss
cleavage. 相似文献
5.
This article presents the results of a combined experimental and theoretical study of the effects of loading rate (1, 10,
and 100 MPa√m · s−1) on the resistance-curve behavior and toughening in cast lamellar gamma-based titanium aluminides (Ti-48Al-2Cr-2Nb, Ti-45Al-2Mn-2Nb
+ 0.8 vol pct TiB2, and Ti-47Al-2Mn-2Nb + 0.8 vol pct TiB2). Note that compositions are quoted in at. pct unless stated otherwise. The fracture-initiation toughness and resistance-curve
behavior in Ti-48Al-2Cr-2Nb are shown to be similar at the three loading rates examined. In the case of the Mn-containing
alloys, stronger resistance-curve behavior is observed as the loading rate increases from 1 to 10 MPa√m · s−1. However, the fracture-initiation toughness and resistance-curve behavior of the Mn-containing alloys are similar at loading
rates of 10 and 100 MPa√m · s−1. The observed resistance-curve behavior is attributed largely to the role of ligament bridging and, to a lesser extent, to
the effects of cracktip plasticity. Small- and large-scale bridging models are also shown to predict the measured resistance
curves when the observed/measured bridging parameters and material properties are used in the micromechanical modeling of
crack bridging. The implications of the results are also discussed for the design of damage-tolerant gamma alloys and microstructures. 相似文献
6.
J. J. Kruzic J. H. Schneibel R. O. Ritchie 《Metallurgical and Materials Transactions A》2005,36(9):2393-2402
Ambient- to elevated-temperature fracture and fatigue-crack growth results are presented for five Mo-Mo3Si-Mo5SiB2-containing α-Mo matrix (17 to 49 vol pct) alloys, which are compared to results for intermetallic-matrix alloys with similar compositions.
By increasing the α-Mo volume fraction, ductility, or microstructural coarseness, or by using a continuous α-Mo matrix, it was found that improved fracture and fatigue properties are achieved by promoting the active toughening mechanisms,
specifically crack trapping and crack bridging by the α-Mo phase. Crack-initiation fracture toughness values increased from 5 to 12 MPa√m with increasing α-Mo content from 17 to 49 vol pct, and fracture toughness values rose with crack extension, ranging from 8.5 to 21 MPa√m at
ambient temperatures. Fatigue thresholds benefited similarly from more α-Mo phase, and the fracture and fatigue resistance was improved for all alloys tested at 1300 °C, the latter effects being
attributed to improved ductility of the α-Mo phase at elevated temperatures. 相似文献
7.
Chongmin Kim A. Richard Johnson William F. Hosford 《Metallurgical and Materials Transactions A》1982,13(9):1595-1605
The influence of microstructural variations on the fracture toughness of two tool steels with compositions 6 pct W-5 pct Mo-4
pct Cr-2 pct V-0.8 pct C (AISI M2 high-speed steel) and 2 pct W-2.75 pct Mo-4.5 pct Cr-1 pct V-0.5 pct C (VASCO-MA) was investigated.
In the as-hardened condition, the M2 steel has a higher fracture toughness than the MA steel, although the latter steel is
softer. In the tempered condition, MA is softer and has a higher fracture toughness than M2. When the hardening temperature
is below 1095 °C (2000 °F), tempering of both steels causes embrittlement,i.e., a reduction of fracture toughness as well as hardness. The fracture toughness of both steels was enhanced by increasing
the grain size. The steel samples with intercept grain size of 5 (average grain diameter of 30 microns) or coarser exhibit
2 to 3 MPa√m (2 to 3 ksi√in.) higher fracture toughness than samples with intercept grain size of 10 (average grain diameter
of 15 microns) or finer. Tempering temperature has no effect on the fracture toughness of M2 and MA steels as long as the
final tempered hardness of the steels is constant. Retained austenite has no influence on the fracture toughness of as-hardened
MA steel, but a high content of retained austenite appears to raise the fracture toughness of as-hardened M2 steel. There
is a temperature of austenitization for each tool steel at which the retained austenite content in the as-quenched samples
is a maximum. The above described results were explained through changes in the microstructure and the fracture modes.
CHONGMIN KIM, formerly with Climax Molybdenum Company of Michigan, Ann Arbor, MI. 相似文献
8.
H. Choe J. H. Schneibel R. O. Ritchie 《Metallurgical and Materials Transactions A》2003,34(2):225-239
The need for structural materials with high-temperature strength and oxidation resistance coupled with adequate lower-temperature
toughness for potential use at temperatures above ∼1000 °C has remained a persistent challenge in materials science. In this
work, one promising class of intermetallic alloys is examined, namely, boron-containing molybdenum silicides, with compositions
in the range Mo (bal), 12 to 17 at. pct Si, 8.5 at. pct B, processed using both ingot (I/M) and powder (P/M) metallurgy methods.
Specifically, the oxidation (“pesting”), fracture toughness, and fatigue-crack propagation resistance of four such alloys,
which consisted of ∼21 to 38 vol. pct α-Mo phase in an intermetallic matrix of Mo3Si and Mo5SiB2 (T2), were characterized at temperatures between 25 °C and 1300 °C. The boron additions were found to confer improved “pest”
resistance (at 400 °C to 900 °C) as compared to unmodified molybdenum silicides, such as Mo5Si3. Moreover, although the fracture and fatigue properties of the finer-scale P/M alloys were only marginally better than those
of MoSi2, for the I/M processed microstructures with coarse distributions of the α-Mo phase, fracture toughness properties were far superior, rising from values above 7 MPa √m at ambient temperatures to almost
12 MPa √m at 1300 °C. Similarly, the fatigue-crack propagation resistance was significantly better than that of MoSi2, with fatigue threshold values roughly 70 pct of the toughness, i.e., rising from over 5 MPa √m at 25 °C to ∼8 MPa √m at 1300 °C. These results, in particular, that the toughness and cyclic
crack-growth resistance actually increased with increasing temperature, are discussed in terms of the salient mechanisms of
toughening in Mo-Si-B alloys and the specific role of microstructure. 相似文献
9.
B. V. Cockeram 《Metallurgical and Materials Transactions A》2005,36(7):1777-1791
The high-temperature strength and creep resistance of low carbon arc cast (LCAC) unalloyed molybdenum, oxide dispersion strengthened
(ODS) molybdenum, and molybdenum-0.5 pct titanium-0.1 pct zirconium (TZM) molybdenum have attracted interest in these alloys
for various high-temperature structural applications. Fracture toughness testing of wrought plate stock over a temperature
range of −150 °C to 1000 °C using bend, flexure, and compact tension (CT) specimens has shown that consistent fracture toughness
results and transition temperatures are obtained using subsized 0.5T bend and 0.18T disc-CT specimens. Although the fracture
toughness values are not strictly valid in accordance with all ASTM requirements, these values are considered to be a reasonable
measure of fracture toughness. Ductile-to-brittle transition temperature (DBTT) values were determined in the transverse and
longitudinal orientations for LCAC (200 °C and 150 °C, respectively), ODS (<room temperature and −150 °C), and TZM (150 °C
and 100 °C). At test temperatures > DBTT, the fracture toughness values for LCAC ranged from 45 to 175 MPa√m, TZM ranged from
74 to 215 MPa√m, and the values for ODS ranged from 56 to 149 MPa√m. No temperature dependence was resolved within the data
scatter for fracture toughness values between the DBTT and 1000 °C. Thin sheet toughening is shown to be the dominant toughening
mechanism, where crack initiation/propagation along grain boundaries leaves ligaments of sheetlike grains that are pulled
to failure by plastic necking. Specimen-to-specimen variation in the fraction of the microstructure that splits into thin
sheets is proposed to be responsible for the large scatter in toughness values at test temperatures > DBTT. A finer grain
size is shown to result in a higher fraction of thin sheet ligament features at the fracture surface. As a result finer grain
size materials such as ODS molybdenum have a lower DBTT. 相似文献
10.
The fracture behavior of an Fe-12 Ni-0.25 Ti alloy, grain refined through thermal cycling was studied down to liquid helium
temperature using a simple method of cryogenic fracture toughness testing. Comparison tests were also made with two other
common cryogenic alloys. Ultrafine grained Fe-12 Ni-0.25 Ti alloy, which is 100 pct ferritic, behaved in a ductile manner
similar to 304 austenitic steel. It was shown that the ductile-brittle transition temperature of the ferritic steel specimen
can be suppressed below liquid helium temperature by grain refinement even in the presence of a sharp crack. Yield strength
of 149 ksi with fracture toughness of 307 ksi√in. at liquid nitrogen temperature, and yield strength of 195 ksi with fracture
toughness of 232 ksi√in. at liquid helium temperature were obtained. 相似文献
11.
The fatigue and fracture resistance of a TiAl alloy, Ti-47Al-2Nb-2Cr, with 0.2 at. pct boron addition was studied by performing
tensile, fracture toughness, and fatigue crack growth tests. The material was heat treated to exhibit a fine-grained, fully
lamellar microstructure with approximately 150-μm grain size and 1-μm lamellae spacing. Conventional tensile tests were conducted as a function of temperature to define the brittle-to-ductile
transition temperature (BDTT), while fracture and fatigue tests were performed at 25 °C and 815 °C. Fracture toughness tests
were performed inside a scanning electron microscope (SEM) equipped with a high-temperature loading stage, as well as using
ASTM standard techniques. Fatigue crack growth of large and small cracks was studied in air using conventional methods and
by testing inside the SEM. Fatigue and fracture mechanisms in the fine-grained, fully lamellar microstructure were identified
and correlated with the corresponding properties. The results showed that the lamellar TiAl alloy exhibited moderate fracture
toughness and fatigue crack growth resistance, despite low tensile ductility. The sources of ductility, fracture toughness,
and fatigue resistance were identified and related to pertinent microstructural variables. 相似文献
12.
The temperature dependence of fatigue crack propagation is considered in an Fe-1 pct Cr-0.5 pct Mo alloy steel. This material
was tested at temperatures between 425 and 550 °C, a frequency of 1 Hz, and anR-ratio of 0.1. It is shown that the effect of temperature can be explained in terms of a thermal activation energy for fatigue.
The magnitude of this activation energy is a function of ΔK and varies from more than 150 kJ/mole at 15 MPa√m to 30 kJ/mole
above 30 MPa√m. The magnitude of these activation energies supports the idea that oxidation, and not creep, is the rate-controlling
time-dependent process for the test conditions studied. 相似文献
13.
S. Ashok K. Kain J. M. Tartaglia N. S. Stoloff 《Metallurgical and Materials Transactions A》1983,14(10):1997-2003
High cycle fatigue tests in vacuum have been performed on ordered (Fe, Co, Ni)3V alloys between 25 °C and 850 °C. Heat-to-heat variations in fatigue properties of a Co-16.5 wtpct Fe-25 pct alloy, LRO-1, appeared to be due to differing quantities of grain boundary precipitates. Modification of this alloy with 0.4 pct Ti, to produce an alloy designated LRO-23, reduced the density of grain boundary precipitates and increased ductility, resulting in superior fatigue strength at high temperatures. The fatigue lives of LRO-1 and LRO-23 decreased rapidly above 650 °C, and increased intergranular failure was noted. The fatigue resistance of a cobalt-free alloy, Fe-29 pct Ni-22 pct V-0.4 pct Ti (LRO-37), was examined at 25 °C, 400 °C, and 600 °C; there was little evidence for intergranular fracture at any of these temperatures. Fatigue behavior of the LRO alloys is compared to that of conventional high temperature alloys. 相似文献
14.
Fatigue crack growth rate behavior in CORONA 5, an alloy developed for applications requiring high fracture toughness, has
been examined for eight material conditions. These conditions were designed to give differences in microstructure, strength
level (825 to 1100 MPa [120 to 160 ksi]), and oxygen content (0.100 to 0.174 wt pct), in such a manner that the separate effects
of these variables could be defined. For all eight conditions, fatigue crack growth rates (da/dN) are virtually indistinguishable
over the full spectrum of stress-intensity range (ΔK) examined,viz., 8 to 40 MPa√m (7 to 36 ksi√in). Concomitantly, it is noted that over the sizable solution annealing range studied (830°
to 915 °C [1525° to 1675 °F]), the primary α-phase morphology was substantially invariant. Eachda/dN curve exhibits a bilinear form with a transition point (ΔKT) between 16 and 19 MPa√m (15 and 17 ksi√in). A change in microfractographic appearance occurs at ΔKT, as extensive secondary cracking along α/β interfaces is observed at all hypertransitional levels ofAK, but not for AK < ΔKT. For each material condition, the mean length of primary α platelets is approximately the same as the cyclic plastic zone
size at ΔKT. Accordingly, locations ofAKT (and their similarity for the different material conditions) are rationalized in conformance with a cyclic plastic zone model
of fatigue crack growth. Finally, the difference in behavior of CORONA 5, as compared to conventional α/β alloys such as Ti-6A1-4V,
is rationalized in terms of crack path behavior. 相似文献
15.
K. T. Venkateswara Rao J. C. McNulty R. O. Ritchie 《Metallurgical and Materials Transactions A》1993,24(10):2233-2245
Aluminum-lithium alloys are currently being considered for applications at moderately elevated temperatures; accordingly,
a study has been made on the effects of prolonged (100 and 1000 hours overaging) thermal exposure at 149 °C and 260 °C on
the mechanical properties of a peakaged Al-Li-Cu-Mg-Zr alloy 8090-T8771. In the as-received T8771 temper, the alloy exhibits
an excellent combination of strength (˜500 MPa) and toughness (35 MPa√m) with moderate tensile elongation (4 pct). Overaging
at 149 °C results in a ˜50 pct reduction in ductility and toughness, primarily associated with the growth of equilibrium phases
along grain/subgrain boundaries, resulting in formation of solute-depleted precipitate-free zones and coarsening of matrix8' andS precipitates; strength levels and fatigue-crack growth rates, however, remain largely unchanged. Thermal exposures at 260
°C, conversely, lead to dramatic reductions in strength (by ˜50 to 80 pct), toughness (by ˜30 pct) and fatigue-crack propagation
resistance; crack-growth rates at all ΔK levels above ~5 MPa√m are 2 to 3 orders of magnitude faster. Microstructurally, this was associated with complete dissolution
of δ′, severe coarsening ofS andT
2
precipitates in the matrix, and formation of equilibrium Cu- and Mg-rich intermetallic phases in the matrix and along grain
boundaries. The resulting lack of planar-slip deformation and low yield strength of 8090 following overaging exposures at
260 °C increase the cumulative crack-tip damage per cycle and reduce the tendency for crack-path deflection, thereby accelerating
fatigue-crack growth rates. Despite this degradation in properties, the 8090-T8771 alloy has better strength retention and
generally superior fatigue-crack growth properties compared to similarly overaged Al-Li-Cu-Zr 2090 and Al-Cu-Zn-Mg 7150 alloys.
formerly with the University of California,
formerly with the University of California, 相似文献
16.
A comparative study has been made of the room- and elevated-temperature properties, room-temperature fracture toughness, fatigue-crack
propagation rates, and 650 °C creep properties of Ti-24Al-14Nb-3V-0.5Mo with and without 0.9 at. pct Si. Both alloys have
microstructures consisting of the α
2, B2, and the orthorhombic O phase, with different proportions of the α
2 phase relative to the (O + B2) mixtures, depending on solution-treatment temperature. The alloy with a Si addition contains
additional primary ζ-Ti5Si3 particles distributed in the (O + B2) matrix. Tests of mechanical properties showed that the incorporation of a small fraction
(about 0.03 by volume) of the Ti5Si3 phase leads to greater room-temperature and elevated-temperature strengths, but lower room-temperature elongations and fracture
toughness as compared with the base alloy. Alloys containing greater volume fractions of the α
2 phase exhibited better tensile ductility, and this was attributed to the concurrent stabilization of the B2 phase. Examination
of tensile-tested and fatigued specimens indicates that the primary failure mode of the alloys, regardless of Si addition,
was due to the brittleness of the α
2 phase; the silicide particles that debonded from the matrix also contribute to cracking in the monotonic loading mode. Up
to a 20 pct improvement in creep-rupture life was observed in the Si-containing alloys, and this was interpreted in terms
of the solute-strengthening effect of Si. While the incorporated Ti5Si3 phase has an unfavorable effect on ductility and room-temperature fracture toughness, the difference in fatigue-crack propagation
rates between the alloys with and without Si is minimal. It is concluded that the controlling factor for the fatigue failure
in orthorhombic alloys is related to the (α
2 + O + B2) microstructure, instead of the Ti5Si3 particles. 相似文献
17.
Sunghak Lee Je Won Rhyu Kyung-Mox Cho Jacques Duffy 《Metallurgical and Materials Transactions A》1993,24(4):901-912
An investigation was conducted into the effects of test temperature and loading rate on the initiation of plane strain fracture
of an HY-100 steel. Fracture toughness tests were conducted using fatigue precracked round bars loaded in tension to produce
a quasi-static stress intensity rate of ·K1
= 1 MPa√m/s and a dynamic rate of ·K1 = 2 × 106 MPa√m/s. Testing temperatures covered the range from -150 °C to 200 °C, which encompasses fracture initiation modes involving
quasi-cleavage to fully ductile fracture. The results of toughness tests show that the lower-shelf values of fracture toughness
were substantially independent of loading rate, while the dynamic values exceeded the quasi-static values by about 50 pct
on the upper shelf. In analyzing these results, phenomenological fracture initiation models were adopted based on the requirement
that, for fracture to occur, a critical strain or stress must be achieved over a critical distance. In separate tests, the
observation of microfracture processes was investigated using fractography and anin situ scanning electron microscope (SEM) fracture technique. The layered ppearance of the fracture surfaces was found to be associated
with a banded structure which generally contains many MnS inclusions, probably resulting in a reduction of the fracture toughness
values. 相似文献
18.
The present study compares the fatigue and fracture properties of the high-strength β titanium alloy β-Cez with the conventional α+β titanium alloy Ti-6Al-4V, because of increasing interest in replacing α+β titanium alloys with β titanium alloys for highly stressed airframe and jet engine components. This comparison study includes the Ti-6Al-4V alloy
in an α+ β-processed condition (for a typical turbine blade application) and the β-Cez alloy in two distinctly different α+β-processed and β-processed conditions (optimized for a combination of superior strength, ductility, and fracture toughness). The comparison
principally showed a much lower yield stress for Ti-6Al-4V (915 MPa) than for both β-Cez conditions (1200 MPa). The Ti-6Al-4V material also showed the significantly lower high-cycle fatigue strength (resistance
against crack initiation) of 375 MPa (R=−1) as compared to the β-Cez alloy (∼600 MPa, R=−1). Particularly in the presence of large cracks (>5 mm), the fatigue crack growth resistance and fracture toughness of
the Ti-6Al-4V material is superior when compared to both β-Cez conditions. However, for small crack sizes, the conditions of both the alloys under study show equivalent resistance
against fatigue crack growth. For the β-Cez material, where microstructures were optimized for high fracture toughness (conventional large crack sizes) by thermomechanical
processing, maximum K
Ic-values of 68 MPa√m of the β-processed β-Cez condition (tested in the longitudinal direction) decreased by ∼50 pct in the presence of small cracks (1 mm). A similar
decrease in fracture toughness was obtained by loading the β-processed β-Cez condition perpendicular to the flat surfaces of the pancake-shaped β grain structure (tested in the short transverse direction). These results were discussed in terms of the effectiveness of
the crack front geometry in hindering crack propagation. Further, the results of this study were considered for alloy selection
and optimized microstructures for fatigue and fracture critical applications. Finally, the advantage of the α+β-processed β-Cez condition in highly stressed engineering components is pointed out because of its overall superior combination of fatigue
crack initiation and propagation resistance (especially against small fatigue cracks). 相似文献
19.
Design of quaternary Ir-Nb-Ni-Al refractory superalloys 总被引:2,自引:0,他引:2
X. H. Yu Y. Yamabe-Mitarai Y. Ro H. Harada 《Metallurgical and Materials Transactions A》2000,31(1):173-178
We propose a method for developing new quaternary Ir-Nb-Ni-Al refractory superalloys for ultra-high-temperature uses, by mixing
two types of binary alloys, Ir-20 at. pct Nb and Ni-16.8 at. pct Al, which contain fcc/L12 two-phase coherent structures. For alloys of various Ir-Nb/Ni-Al compositions, we analyzed the microstructure and measured
the compressive strengths. Phase analysis indicated that three-phase equilibria—fcc, Ir3Nb-L12, and Ni3Al-L12—existed in Ir-5Nb-62.4Ni-12.6Al (at. pct) (alloy A), Ir-10Nb-41.6Ni-8.4Al (at. pct) (alloy B), and Ir-15Nb-20.8Ni-4.2Al (at.
pct) (alloy C) at 1400 °C; at 1300 °C, three phase equilibria—fcc, Ir3Nb, and Ni3Al—existed in alloys A and C and four-phase equilibria—fcc, Ir3Nb, Ni3Al, and IrAl-B2—existed in alloy B. The fcc/L12 coherent structure was examined by using transmission electron microscopy (TEM). At a temperature of 1200 °C, the compressive
strength of these quaternary alloys was between 130 and 350 MPa, which was higher than that of commercial Ni-based superalloys,
such as MarM247 (50 MPa), and lower than that of Ir-based binary alloys (500 MPa). Compared to Ir-based alloys, the compressive
strain of these quaternary alloys was greatly improved. The potential of the quaternary alloys for ultra-high-temperature
use is also discussed. 相似文献
20.
Michael J. Haynes Richard P. Gangloff 《Metallurgical and Materials Transactions A》1997,28(9):1815-1829
The plane-strain initiation fracture toughness (K
JICi
) and plane-stress crack growth resistance of two Al-Cu-Mg-Ag alloy sheets are characterized as a function of temperature
by a J-integral method. For AA2519 +Mg+Ag, K
JICi
decreases from 32.5 MPa√m at 25 °C to 28.5 MPa√m at 175 °C, while K
JICi
for a lower Cu variant increases from 34.2 MPa√m at 25 °C to 36.0 MPa√m at 150 °C. Crack-tip damage in AA2519+Mg+Ag evolves
by nucleation and growth of voids from large undissolved Al2Cu particles, but fracture resistance is controlled by void sheeting coalescence associated with dispersoids. Quantitative
fractography, three-dimensional (3-D) reconstruction of fracture surfaces, and metallographic crack profiles indicate that
void sheeting is retarded as temperature increases from 25 °C to 150°C, consistent with a rising fracture resistance. Primary
microvoids nucleate from smaller constituent particles in the low Cu alloy, and fracture strain increases. A strain-controlled
micromechanical model accurately predicts K
JICi
as a function of temperature, but includes a critical distance parameter (l*) that is not definable a priori. Nearly constant initiation toughness for AA2519+Mg+Ag is due to rising fracture strain with temperature, which balances
the effects of decreasing flow strength, work hardening, and elastic modulus on the crack-tip strain distribution. Ambient
temperature toughnesses of the low Cu variant are comparable to those of AA2519+Mg+Ag, despite increased fracture strain,
because of reduced constituent spacing and l*. 相似文献