Compression-impact testing of aluminum at elevated temperatures

This paper presents and experimental technique for determining compressive stress-strain curves well into the plastic range of relatively soft metals at strain rates from 300 to 2000 sec^?1 at six temperatures from 30 to 550° C. More than 100 curves were obtained on annealed 1100° F aluminum. The strain-rate dependence in these tests could be fitted quite well either by a power function (log-log plot) or by a semilogarithmic plot, but the power function gave a better correlation of the present data with that obtained at lower strain rates by Alder and Phillips.¹     

Strain field associated with brittle-fracture propagation in wide steel plates

The results of an experimental investigation concerned with the study of the strain field surrounding a brittle fracture propagating across a wide steel plate are presented in this paper. The data were obtained from tests of 6-ft wide steel plates that were instrumentated to measure surface strain and crack speed. The plates were tested at an average net applied stress of 19,000 psi, a temperature of about ?5° F, and with the notch-wedgeimpact method for fracture initiation. Several plates were tested under similar conditions and the results were superimposed to give a representative picture of the strain distribution on the surface of a plate in the region of the tip of a propagating fracture. Contours of the maximum principal strain for various lengths of crack are presented. The studies indicate that for this particular specimen geometry and associated test conditions, the strain field surrounding the tip of the advancing fracture remains essentially unchanged after traversing about one-third of the width of a 6-ft wide plate.     

Mechanical behavior of Gamma-Met PX under uniaxial loading at elevated temperatures and high strain rates

Gamma titanium aluminides have received considerable attention over the last decade. These alloys are known to have low density, good high temperature strength retention and good oxidation and corrosion resistance. However, poor ductility and low fracture toughness have been the key limiting factors in the full utilization of these alloys. More recently, a new generation of gamma titanium aluminide alloys, commonly referred to as Gamma-Met PX, has been developed by GKSS, Germany. These alloys have been observed to have superior strength and better oxidation resistance at elevated temperatures when compared with conventional gamma titanium aluminides.The present paper discusses results of a study to understand the uniaxial mechanical behavior in both compression and tension of Gamma-Met PX at elevated temperatures and high strain rates. The compression and tensile tests are conducted using a modified Split-Hopkinson Bar apparatus at test temperatures ranging from room temperature to 900 °C and strain rates of up to 3500 s⁻¹. Under uniaxial compression, in the temperature range from room to 600 °C, the flow stress is observed to be nearly independent of test temperature. However, at temperatures higher than 600 °C thermal softening is observed at all strain rates with the rate of thermal softening increasing dramatically between 800 and 900 °C. The room temperature tensile tests show negligible strain-rate dependence on both yield stress and flow stress. With an increase in test temperature from room to 900 °C, the material shows a drop in both yield and flow stress at all levels of plastic strain. However, the measured flow stress is still higher when compared to nickel based super-alloys and other gamma titanium aluminides under similar test conditions. Also, no anomaly in yield stress is observed up to 900 °C.     

High-temperature test facility for repeated pressure loading of cylinders

A test facility capable of subjecting cylindrical specimens to repeated pressure loadings at high temperatures is described. The loading rates range from 480 to 600 cycles per minute. The test pressures range from 310 to 447 MN/m² and the test temperatures are 260°C, 538°C and 816°C. Testing was performed at two strain rates. A “low” strain rate of about 4 per second and a “high” strain rate of about 9.6 per second. The uniqueness of the facility lies in the choice of a solid loading medium to transmit pressure to the specimen. Some typical results are presented.     

Testing the space-shuttle thermal-protection coating

A light-weight insulation material and its protective glassy coating will protect thespace shuttle from temperatures as high as 1250°C (2300°F). The critical performance characteristics of the brittle coating are investigated using testing techniques developed to accommodate these extreme environments and the delicate material. These include an ultimate-strain test-specimen geometry which circumvents problems created by flawed edges, as well as a tension specimen preparation and loading system with which premature failures due to excessive bending moment are avoided. Additionally, an elevated-temperature mechanical strain transducer—useable at more than 870°C (1600°F)—is described. Potential alterations to this sensor are discussed which would make it functional at up to 1600°C (3000°F).     

Strain-gage installations for adverse environments

Seven projects in which resistance-type bonded strain gages were used in adverse environments are described. The projects involved: (1) force measurements in a 10^?10 torr vacuum, (2) load measurements over a temperature range of 75 to 300° F, (3) displacement measurements in a nonconductive fluid at 500° F, (4) dynamic displacement measurements in an electric field, (5) strain measurements in air at 600° F, (6) dynamic displacement and strain measurements to ?320°F, and (7) strain measurements in water at pressures up to 2500 psi and temperatures up to 300° F. This report provides detailed information about the gage installations, the transducers used and the performance obtained.     

Strain rate effects and temperature history effects for three different tempers of 4340 var steel

A series of experiments is described in which specimens of AISI 4340 VAR steel are deformed in shear at temperatures ranging from −190°C.to 20°C. The tests were performed in a torsional Kolsky (split-Hopkinson) bar at quasistatic and dynamic strain rates. Before testing, all the specimens were normalized, austenitized and tempered to hardnesses of 55, 44 or 33, on the Rockwell C scale. In addition to constant temperature and constant strain rate tests, a number of experiments were performed to study strain rate and temperature history effects in these three tempers. For this purpose a prestrain was imposed at one temperature and strain rate, followed by continued straining at a new temperature or at a new strain rate.Results provide stress-strain curves in shear for the three tempers of this steel. Temperature effects appear greater between −190°C and −50°C than between −50°C and room temperature, particularly for the 200°C temper, while the strain rate sensitivity is about the same as found in mild steel. History effects are quite small for the 600°C and 425°C tempers, even at large strains. However, for the 200°C temper a prestrain at −50°C followed by a temperature change to −190°C requires a higher flow stress than does deformation imposed entirely at the lower temperature. Anomalous history effects of this nature have been seen before in steels, although this is the first evidence for their association with a particular temper.     

Micro Scale Tensile Behaviour of Thin Bitumen Films

The tensile behaviour of two types of viscoelastic bituminous films confined between mineral aggregates or steel as adherends, was investigated in the brittle and ductile regimes. Uniaxial specimens were fabricated employing a prototype set up allowing construction of micro-scale thin films and visualization of failure phenomena. The effect of key parameters, namely, temperature (23°C and −10°C), binder type (straight run and polymer modified), adherend type (stainless steel and mineral aggregate), and water conditioning were investigated sequentially. The results show that water sensitive aggregate-binder combinations in macro (150 mm diameter) and mega (in service) scales also displayed reduced tensile strength in the micro scale when water conditioned. At 23°C ductile failure and at −10°C brittle fracture were observed. At 23°C phenomena, such as formation of striations during tensile mechanical loading, void nucleation and growth, filamentation and large ductile flow before fracture could be witnessed. When using proper surface preparation procedures, in all types of specimen investigated at 23°C only cohesive failure and at −10°C predominantly adhesive-cohesive failure were found.     

The recrystallization technique for local plastic-zone observation in type 304 stainless steel in the temperature range of −196° to 950° C

The recrystallization technique has been extended for direct observation of plastic zone in Type 304 stainless steel in the temperature range of ?196° to 950°C. It can reveal plastic deformation with plastic strain above 0.02 in the range of ?196° to 850° C and that with plastic strain above 0.06 at 950°C. Results of plastic-zone observation in notched specimen in the range of ?196° to 950° C are presented to illustrate the technique's capability.     

Strain-rate history and temperature effects on the torsional-shear behavior of a mild steel

Previous investigations on the effects of strain-rate and temperature histories on the mechanical behavior of steel are briefly reviewed. A study is presented on the influence of strain rate and strain-rate history on the shear behavior of a mild steel, over a wide range of temperature Experiments were performed on thin-walled tubular specimens of short gage length, using a torsional split-Hopkinson-bar apparatus adapted to permit quasi-static as well as dynamic straining at different temperatures. The constant-rate behavior was first measured at nominal strain rates of 10^?3 and 10³ s^?1 for ?150, ?100, ?50, 20, 200 and 400°C. Tests were then carried out, at the same temperatures, in which the strain rate was suddenly increased during deformation from the lower to the higher rate at various large values of plastic strain. The increase in rate occurred in a time of the order of 20 μs so that relatively little change of strain took place during the jump. The low strain-rate results show a well-defined elastic limit but no yield drop, a small yield plateau is found at room temperature. The subsequent strain hardening shows a maximum at 200°C, when serrated flow occurs and the ductility is reduced. The high strain-rate results show a considerable drop of stress at yield. The post-yield flow stress decreases steadily with increasing temperature, throughout the temperature range investigated. At room temperature and below, the strain-hardening rate becomes negative at large strains. The adiabatic temperature rise in the dynamic tests was computed on the assumption that the plastic work is entirely converted to heat. This enabled the isothermal dynamic stress-strain curves to be calculated, and showed that considerable thermal softening took place. The initial response to a strain-rate jump is approximately elastic, and has a magnitude which increases with decrease of testing temperature; it is little affected by the amount of prestrain. At 200 and 400° C, a yield drop occurs after the initial stress increment. The post-jump flow stress is always greater than that for the same strain in a constant-rate dynamic test, the strain-hardening rate becoming negative at large strains or low testing temperature. This observed effect of strain-rate history cannot be explained by the thermal softening accompanying dynamic deformation. These and other results concerning total ductility under various strain-rate and temperature conditions show that strain-rate history strongly affects the mechanical behavior of the mild steel tested and, hence, should be taken into account in the formulation of constitutive equations for that material.     

A Finite Element Analysis of a Tapered Flat Sheet Tensile Specimen

A uniaxial tension sheet metal coupon with a tapered instead of a straight gage section has been used for centering the location of diffuse neck and for measuring sheet stretchability in a non-uniform strain field. A finite element analysis of such a tensile coupon made of automotive steel sheet metals has been carried out to assess the effect of the tapered gage section geometry and material plastic strain hardening characteristics on the development of local plastic deformation pattern and local stress state, especially beyond the onset of diffuse necking but before localized necking. In particular, the finite element analysis was used in this study to evaluate the accuracy and reliability of an experimental data analysis method for estimating the post-necking effective plastic stress-strain curve based on the direct local surface axial plastic strain measurements for base metal, heat-affected zone, and weld metals of a dual-phase steel DP600. It is concluded that the estimated lower and upper bounds of the effective stress-strain curve at large strains are not satisfactory for low strain-hardening materials such as heat-affected zone and weld metals with the tapered tension coupons. A simple correction method utilizing only the additional local surface strain measurement in the transverse direction is proposed and it is shown to be effective in correcting the estimated effective stress-strain curve of dual-phase steel weld metals obtained for two tapered gage section geometries.     

Photoelastic technique to investigate the effect of temperature and strain rate on plastic flow in mild steel

Dynamic photoelastic-coating technique was used to observe successive developments of plastic flow in tension at a temperature ranging from ?157°C to 20°C. A type of plastic flow occurred which was determined by a combination of temperature and strain rate. A correlation was found to exist between photoelastic observations and the equation of thermal activation.     

Modelling of the plastic flow of trip-aided multiphase steel based on an incremental mean-field approach

An incremental mean-field model is developed for the prediction of transformation induced plasticity (TRIP) in multiphase steel. The partitioning of strain between softer and harder constituents is computed based on an elastic-plastic Mori–Tanaka approach that accounts for the progressive transformation of austenite into martensite. The latter transformation is predicted using an energy-balance criterion that is formulated at the level of individual austenite grains. The model has been tested against experimental data. Macroscopic stress-strain curves and rate of martensite formation have been measured on sheet samples subjected to various loading modes: uniaxial tension, simple shear, and (in-plane) uniaxial compression. These experiments were performed at 20 °C and the uniaxial tensile test was repeated at ?30 °C. The mean-field model produces fair predictions of the macroscopic hardening resulting from TRIP on the condition that a sufficient proportion of the load is carried by the very hard martensite inclusions. Such prediction implies that one accounts for the stress heterogeneity across the ferrite-based matrix. At the same time, the model reproduces the elastic lattice strains and the plastic elongation which are measured within the phases by neutron diffraction and by image correlation in a scanning electron microscope, respectively. The model can be used in finite element simulations of forming processes which is illustrated in a study of necking of a cylindrical bar under uniaxial tension.     

Residual stresses in thick electrodeposits of a nickel-cobalt alloy

Some electroplated metals contain residual stresses which can cause warpage or premature failure of parts plated or electrofomed with these materials. Noticeably absent from the literature are residual-stress data for finished parts. Typically for plated or electroformed parts, residual stresses are determined independently on thin strips and then piece parts are plated. This research describes a technique which can be used to measure stress on finished parts. The method involves drilling a hole in the part and measuring the resulting change of strain in the vicinity of the hole. Viability of this technique was demonstrated by measuring the stress in a nickel-cobalt deposit plated on an aluminum cylinder. Two separate runs, one 50 deg removed from the other, provided almost identical results; stress was 160 MN/m² (23,200 psi). Two other runs in a region where plating was somewhat thinner provided slightly lower results probably because all boundary-condition requirements were not met. The computed residual-stress values compared quite favorably with independent rigid-strip measurements of 131 MN/m² (19,000 psi) obtained for the solution before and after plating of the cylinder.     

On modes and criteria of ABS melt failure in extension

Melt failure of a commercial ABS polymer in uniaxial extension over ranges of elongation rate ([(e)\dot] = 0.01 - 1.0 s ^{- 1}\dot \varepsilon = 0.01 - 1.0\,{\rm s}^{ - 1} ) and temperature (140-200 °C) was investigated. Four methods of experimental and numerical calculation for determination of modes and criteria of melt failure in uniaxial extension were investigated: 1) visual observation of necking; 2) visual observation of non-uniform flow during stress relaxation after cessation of steady elongation; 3) calculation of the Considère criterion from the measured elongational stress-strain curve; 4) numerical calculation of inflection point (‘C²/‘)²=0) from the tensile stress-strain curve. In addition, under higher Deborah number conditions the critical Hencky strains at Considère criterion were calculated using PSM model parameters (! and #) and were compared with those obtained from the measured elongational stress-strain curve. The relationship between these failure modes is discussed in terms of rheological properties of the polymer, putting emphasis on the relationship with the thermoforming process. The Considère criterion appears to be the most effective indicator of the non-uniform deformation of ABS melt in uniaxial extension under conditions where cohesive fracture does not occur. The rheological properties such as elongational viscosity, strain hardening and/or strain softening, and their temperature dependence play an important role in determining the growth and transition of melt failure of ABS polymer in uniaxial extension.     

Strain-history effect on isotropic and anisotropic plastic behavior

An experimental investigation was performed to evaluate the effect of strain history on an initially isotropic material. A hot-rolled 2.5-in.-diam bar of SAE 1045 steel provided all the test specimens. Axial and circumferential compression data indicated that the steel was isotropic. Additional tension and torsion data indicated that the steel was an isotropic-hardening von Mises material; this was also confirmed by proportionate loading of thin-walled cylinders such that the ratio of axial to circumferential stresses was either 0, 1/2, 1, 2 or ∞. Two additional sets of cylinders were preloaded either in simple axial tension or as closed-ended cylinders to an effective plastic strain of 0.006 before they were proportionately loaded. The preloading had a pronounced effect on yield surfaces for reloading if the effective plastic strain on reloading was only slightly greater than that for the preloading. The effect of preloading on the yield surfaces was small when the effective plastic strain was three to four times that for the preloading. Hill's anisotropic theory was used to predict stress-strain relations for several of the reloaded cylinders. Good agreement was obtained between theory and experiment.     

超强钢18NiC250在不同加载速率下的断裂韧性

为了揭示国产超强钢18NiC250的强度、断裂韧性随加载速率的变化规律,利用电子万能试验机和Hopkinson压杆,测试其在0.001～2 000 s-1的塑性流动应力应变曲线及在10-1~106 MPam1/2/s的断裂韧性,同时对断裂破坏机理进行了微观分析。结果表明:该材料的强度对加载速率不敏感,即流动应力基本保持在1.9 GPa;而断裂韧性很敏感,当加载速率由10-1 MPam1/2/s增大到106 MPam1/2/s时,断裂韧性降低了38.2%,断裂模式由韧窝断裂转变为解理断裂。     

Synchronous Full-Field Strain and Temperature Measurement in Tensile Tests at Low,Intermediate and High Strain Rates

Tensile tests with simultaneous full-field strain and temperature measurements at the nominal strain rates of 0.01, 0.1, 1, 200 and 3000 s^?1 are presented. Three different testing methods with specimens of the same thin and flat gage-section geometry are utilized. The full-field deformation is measured on one side of the specimen, using the DIC technique with low and high speed visible cameras, and the full-field temperature is measured on the opposite side using an IR camera. Austenitic stainless steel is used as the test material. The results show that a similar deformation pattern evolves at all strain rates with an initial uniform deformation up to the strain of 0.25–0.35, followed by necking with localized deformation with a maximum strain of 0.7–0.95. The strain rate in the necking regions can exceed three times the nominal strain rate. The duration of the tests vary from 57 s at the lowest strain rate to 197 μs at the highest strain rate. The results show temperature rise at all strain rates. The temperature rise increases with strain rate as the test duration shortens and there is less time for the heat to dissipate. At a strain rate of 0.01 s^?1 the temperature rise is small (up to 48 °C) but noticeable. At a strain rate of 0.1 the temperature rises up to 140 °C and at a strain rate of 1 s^?1 up to 260 °C. The temperature increase in the tests at strain rates of 200 s^?1 and 3000 s^?1 is nearly the same with the maximum temperature reaching 375 °C.     

Elevated-temperature creep and relaxation of torsion-tension members

Based on the assumption that each material satisfies the condition for isotropic hardening for a von Mises material, an incremental solution is developed to predict axial-strain creep curves and maximum shearing-strain creep and relaxation curves for solid circular torsion-tension members subjected to proportionate and nonproportionate stepped loading including creep in tension and relaxation in torsion. Test data are obtained from torsion-tension members made either of annealed OFHC copper at 800°F (427°C) or hot-rolled SAE 1045 steel at 950°F (510°C). The loading histories include either four stepped proportionate load changes, four stepped nonproportionate load changes, or torsion-tension loading in which the axial load remains constant and the torsional load is allowed to relax during two loading periods of the test. Each test duration is about 100 h. Good agreement is indicated between the predicted and measured creep and relaxation curves.     

High-temperature tensile and creep tester for wire

To provide test facilities for determining the tension and short-time creep properties of small-diameter tungsten wire at high temperatures, special equipment has been designed and built, employing rf (radio frequency) heating as the means of attaining temperatures up to 2600° C. This paper describes the problems which had to be solved in designing and building the equipment, and gives results to tests made after the equipment was assembled. The equipment had to meet these requirements: it had to be capable of providing tension and short-time creep data on tungsten wire in sizes from 0.001 in. diam to 0.009 in. at temperatures up to 2600° C, it had to provide an autographic stress-strain curve for the tension tests, the loading rate during tension tests had to be constant, and all of this had to be done in good vacuum. Basically the equipment consists of a loading frame which supports a calibrated beam-type load dynamometer, a synchronous electric-clock motor for applying the load, rf equipment for attaining the desired temperature, an X-Y recorder for recording stress-strain curves, and a two-color automatic optical pyrometer for measuring the temperature. The test arrangement is mounted on a vacuum base plate under a bell jar. For creep testing, the flexible beam is replaced by a rigid beam, and load is applied by means of dead weights. Creep strain is measured with a cathetometer or Optron.