High elastic modulus shafts and method of manufacture

Abstract

High modulus turbine shafts and high modulus cylindrical articles are described as are the process parameters for producing these shafts and cylindrical articles. The shafts/articles have a high Young's modulus as a result of having high modulus <111> crystal texture along the longitudinal axis of the shaft/article. The shafts are produced from directionally solidified seeded <111> single crystal cylinders that are axisymmetrically hot worked before a limited recrystallization process is carried out at a temperature below the recrystallization temperature of the alloy. The disclosed process produces an intense singular <111> texture and results in shaft or cylindrical article with a Young's modulus that is at least 40% greater than that of conventional nickel or iron alloys or conventional steels.

Claims

1. A method of producing a high elastic modulus shaft from an iron based alloy, the method comprising: providing a single crystal cylinder of the alloy, the single crystal cylinder having a longitudinal axis, the single crystal cylinder being seeded so that a high modulus <111> direction is at least substantially parallel to the longitudinal axis; hot working the cylinder to achieve a cylindrically shaped shaft of a desired size; heat treating the shaft after the hot working step in order to subject the shaft to a limited recrystallization process at a temperature below a recrystallization temperature of the alloy in order to produce the a shaft having a desired elastic modulus.

2. The method of claim 1 wherein the alloy is steel.

3. The method of claim 1 wherein the hot working step comprises axisymmetrically hot working the cylinder.

4. The method of claim 1 wherein subsequent to the heat treating a Young's modulus in the <111> direction is greater than about 37 Mpsi (255 GPa).

5. The method of claim 1 wherein subsequent to the heat treating a Young's modulus in the <111> direction ranges from about 37 to about 45 Mpsi (from about 255 to about 310 GPa).

6. The method of claim 1 wherein the cylinder is solid.

7. The method of claim 1 wherein the cylinder is hollow.

8. A method of producing a high elastic modulus shaft from an iron based alloy, the method comprising: casting a single crystal cylinder from the alloy, the single crystal cylinder having a longitudinal axis, the single crystal cylinder being seeded so that a high modulus <111> direction is at least substantially parallel to the longitudinal axis of the cylinder; axisymmetrically hot working the cylinder to achieve a cylindrically shaped shaft of a desired size at a temperature below a recrystallization temperature of the alloy; heat treating the shaft after the hot working step in order to subject the shaft to a limited recrystallization process at a temperature below the recrystallization temperature of the alloy in order to produce a shaft having a desired elastic modulus.

9. The method of claim 8 wherein the alloy is steel.

10. The method of claim 8 wherein subsequent to the heat treating a Young's modulus in the <111> direction is greater than about 37 Mpsi (255 GPa).

11. The method of claim 8 wherein subsequent to the heat treating a Young's modulus in the <111> direction ranges from about 37 to about 45 Mpsi (from about 255 to about 310 GPa).

12. A method of producing a high strength and/or high torque resistant shaft from an iron based alloy, the method comprising: providing a single crystal cylinder of the alloy, the single crystal cylinder having a longitudinal axis, the single crystal cylinder being seeded so that a high modulus <111> direction is at least substantially parallel to the longitudinal axis; hot working the cylinder to achieve a cylindrically shaped shaft of a desired size; heat treating the shaft after the hot working step in order to subject the shaft to a limited recrystallization process at a temperature below or above a recrystallization temperature of the alloy to maximize the strength the shaft to a desired strength.

13. The method of claim 12 wherein the alloy is steel.

14. The method of claim 13, wherein the steel is selected from the group consisting of the following: ferritic, austenitic, martensitic, precipitation strengthened steels, wrought steels suitable for structural applications, and cast steels suitable for structural applications.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 illustrates a typical room temperature Young's modulus surface for nickel and iron base alloys in a single crystal with cubic structure, which may be face centered, body centered, simple cubic or some ordered variation such as B2.

(2) FIG. 2 illustrates how a room temperature Young's modulus varies with crystallographic direction in a typical complex nickel-base alloy represented with reference to a standard stereographic triangle.

(3) FIG. 3 schematically illustrates a highly textured polycrystalline material with majority of the grains oriented along the high modulus <111> direction.

(4) FIG. 4 schematically illustrates a prior art, random grain textured and prior art high modulus <111> grain textured shaft manufacturing process.

(5) FIG. 5 schematically illustrates a disclosed method for producing a high modulus <111> grain textured shaft, based on axisymmetric hot working of a <111> oriented single crystal.

(6) FIG. 6 illustrates a high modulus <111> oriented single crystal successfully swaged with 61% reduction in diameter and confirmed to retain the high modulus <111>.

(7) FIG. 7 illustrate a high modulus <111> oriented IN 718 single crystal ingot successfully extruded with 50% reduction in diameter and confirmed to show 30% improvement in modulus over conventional polycrystalline material.

DETAILED DESCRIPTION

(8) Investment casting is one of the oldest known metal-forming techniques. Beeswax was originally used to form investment castings. Today, high-technology waxes, refractory materials and special alloys are used in investment castings, which provide accuracy, repeatability, versatility and integrity for a variety of metals and high-performance alloys.

(9) The turbofan is a type of jet engine is widely used for aircraft propulsion. The turbofan is basically the combination of two engines, a turbo portion which is a conventional gas turbine engine, and a propeller-like fan enclosed in a duct. The engine produces thrust through a combination of these two portions working in concert. The vast majority of turbofans follow the same basic design with a large fan or compressor at the front of the engine and a relatively small turbine or jet engine behind the large fan. There have been a number of variations on this theme, however, including dual compressors at the front of the engine and dual turbines at the rear of the engine. Other variations include rear-mounted fans which can be easily added to an existing jet engine, or designs that combine a low-pressure turbine and a fan stage in a single rear-mounted unit.

(10) Critical to the efficiency of turbofan engines is the maintenance of minimum clearances between moving and stationary parts. The turbine drive shaft is coupled to disks and blades for rotation and transmits power from the turbine section to the compressor section of the engine. Efficient operation requires accurate location of the blades relative to the casing. Therefore, it is of the utmost importance that the turbine drive shaft be stiff and relatively free from deflection and vibration, although some vibration and deflection is unavoidable. The stresses which produce deflection and vibration of the drive shaft result from the engine operation and from externally applied loads resulting from aircraft motion.

(11) The Young's modulus can be selectively enhanced in one direction, by exploiting the high elastic anisotropy in nickel and iron base alloy single crystals. As depicted by a schematic Young's modulus surface in FIG. 1, a room temperature elastic modulus approaching 44 Mpsi (304 GPa) can be achieved in a single crystal along the crystallographic direction <111>. Referring to FIG. 2, the variation of Young's modulus with all crystallographic directions is described by a plot presented with reference to a stereographic projection triangle. From FIGS. 1 and 2, it is clear that Young's modulus varies by at least a factor of two, with a low value of about 18 Mpsi (124 GPa) in the crystallographic <100> direction to about 44 Mpsi (304 GPa) in the crystallographic <111> direction. This variation is exploited in components such as blades and vanes made out of cast single crystal where low elastic modulus is beneficial for improving thermal mechanical fatigue and high elastic modulus is beneficial in a vibratory environment where high cycle fatigue is a concern.

(12) To enhance Young's modulus, it may be impractical to make the shaft out of cast single crystal with <111> direction parallel to the shaft axis. It is commonly assumed, based on experience, that isotropic fine grained, wrought materials are superior to cast materials from the stand point of toughness and fatigue life. But this effect can also be exploited if a highly textured, polycrystalline, fine grained material can be produced, such that majority of the grains are oriented in <111> direction. Such material, depending on the degrees of the <111> grain texture in the axial direction of the shaft will on an average result in Young's modulus between 35 to 40 Mpsi (241 to 276 GPa) at room temperature as set forth in U.S. Pat. No. 4,702,782. This concept is schematically depicted in FIG. 3.

(13) Referring to FIG. 4, in order to achieve fine grained and wrought structure, conventional shafts 19, 20 are made by starting with a cylindrical ingot 21, either cast or made by hot consolidation of powder of appropriate composition and having a large grain size 22. Such an ingot 21 in solid form or as a hollow cylinder is hot worked at step 23 using any of the axisymmetric methods such as swaging, extrusion, or rotary forge to achieve the final length and diameter and a somewhat smaller grain size 24. The final shaft 20 is then appropriately heat treated at steps 25 or 26 to recrystallize fine grains and achieve desired microstructure 27.

(14) The process of FIG. 4 typically yields a final product 19 or 20 with random grain texture 27 with an isotropic Young's modulus of about 30 Mpsi (207 GPa). Some prior art processes are restricted to specific nickel alloy compositions, where the recrystallized grain texture is not random but preferentially forms the strong <111> texture. Such nickel alloy compositions typically have higher stacking fault energies. The stacking fault energy is not an easily quantifiable parameter; the prior art process of FIG. 4 is restricted to alloys empirically observed to provide a strong high modulus <111> texture such as high molybdenum containing nickel-base alloys or alloys based on precipitation of Ni.sub.3Si.

(15) The disclosed processes differ from the conventional processes of FIG. 4 that provide a random grain texture shaft 19 or the shaft 20 with high modulus <111> grain texture. As schematically shown in FIG. 5, the disclosed process begins a single crystal cylinder 30 specifically cast with the axis 31 parallel to the high modulus <111> direction. This may be achieved by directionally solidifying a nickel or iron base alloy ingot 30 starting with a <111> oriented seed or any other single crystal seed 29 appropriately tilted to obtain <111> direction in the direction of solidification, which is the axis 31 of the cylinder 30. The cast cylinder 30 is then appropriately heat treated at step 32 to soften the material and hot work the cylinder 30 to an appropriate reduction as shown by the intermediate product 33. The hot working step 32 is preferably carried out below the temperature at which recrystallization can be triggered by heavy hot working.

(16) As a result, a heavily worked cylinder 33 with a quasi-single crystal 34 is obtained with a large amount of substructure and without destroying the maintenance of high modulus <111> orientation along the axis 31. The cylinder 33 may not yield a recognizable X-ray or electron diffraction pattern reflecting the crystal symmetry, as it does for a cast single crystal. Nonetheless, the crystallographic nature of the cylinder 33 may be confirmed by running X-ray diffraction intensity vs. Bragg angle scan and the elastic modus can be measured either by sound velocity or mechanical means.

(17) The cylinder 33 is then subjected to a limited recrystallization process and direct age heat treatment at step 36 to produce a rod or cylinder 37 with a Young's modulus in the <111> orientation ranging from about 37 to about 40 Mpsi (255-276 GPa). Again, the process of step 36 is conducted at a temperature below the recrystallization temperature of the alloy.

(18) The feasibility of method illustrated in FIG. 5 using axisymmetric swaging at a sub-scale level is shown in FIG. 6. Similarly the feasibility of the process at a sub-scale production method such as extrusion is shown in FIG. 7. The process of FIG. 5 has been demonstrated to work for several alloys, requiring adjustment of the pre-heat treatment to soften the material and the swaging temperature. Those well versed with nickel and iron base alloys can easily select these temperatures based on differential thermal analysis (DTA) of liquidus, solidus and solvus temperatures for any given alloy. The hot worked high modulus single crystal then can be subsequently heat treated in a controlled manner to minimize recrystallization to restore optimum balance of engineering properties.

(19) It is recognized that depending on the specific alloy composition, the post-hot work heat treatment may be allowed to fully recrystallize the grain structure if it happens to retain the <111> texture. However, this method can only be practiced for limited class of alloys. One disclosed method will be to limit the recrystallization so that high modulus <111> texture is largely retained as a quasi-single crystal with a large amount of dislocation sub-structure and high dislocation density. The heavily worked structure with a high dislocation density coupled with low temperature precipitation in many nickel base superalloys as well as iron base alloys or steel will be sufficient to achieve a balance of other engineering properties such as tensile strength, and fatigue life. Direct aging of IN718 is one example of such behavior, well known to those well versed in the art of making structural components such as discs and shafts in jet engines.

(20) Preliminary 1000 F. tensile test results of some swaged alloys presented in the following table bear out the fact that not only such an hypothesis is correct but hot working single crystal holds even greater potential for improving tensile strength and consequently torsion capability. Almost 30% increase in YS and UTS strength was achieved compared to a typical wrought alloy. Traditionally it is assumed that ultimate torsion strength is 70% of UTS and on that basis, the results reflect the potential for improving torsion strength as well.

(21) TABLE-US-00001 Comparison of 1000 F. Tensile Test Results. Temp (F.) Yield (ksi) UTS (ksi) % EL % RA Modulus (MSI) Hot Worked Waspaloy 1000 147.5 211.6 25.6 20.6 28 As swaged <111> PWA 1484 1000 222.5 256.9 6.5 6.5 40.9 1000 178.7 236.8 8.7 11.8 41.6 Swaged + Aged <111> PWA 1484 1000 230.6 254.5 6.5 5.9 38.8 1000 223.9 226.3 3.3 4.9 42.8 Swaged + Aged <111> Udimet 720 LI 1000 234.4 243.6 3.9 5 38.8 1000 226.6 249.5 8.2 6.3 37.8

(22) Hot working of single crystal presents the added advantage of distributing the hot work homogeneously throughout the body of the material by eliminating the elasto-plastic incompatibility between grains, which is inevitable in polycrystalline material. There is plenty of experimental evidence to suggest that in polycrystalline material some grains owing to their unfavorable orientation and incompatibility with the neighboring grain do not respond to the hot work, thereby bringing down the average enhancement in strength due to work hardening. Coarser the starting grain size, worst is this situation. In case of single crystal this situation is eliminated provided uncontrolled shear along limited slip system is not allowed by well selected hot working strategy.

(23) Furthermore the fact that same level of strengthening was achieved in a single crystal alloy PWA 1484 and a typical wrought alloy Udimet 720 LI, by hot working <111> oriented single crystal, clearly suggests that the strength enhancement was purely due to work hardening or increase in uniform dislocation density.

(24) Those well versed in the art will immediately recognize that the proposed approach could be used to further enhance the strength in solid solution strengthened alloys containing no precipitate structure such as Hastealoy-X, and such an approach may provide a better opportunity to enhance strength without loss of ductility.

(25) Also, if retention of high modulus were not required, then in case of precipitation hardened alloys, additional strength enhancement may be achieved by allowing the material to recrystallize and adding precipitation strengthening as well as fine grain strengthening.

(26) Starting with a highly oriented high modulus (40-44 Mpsi; 276-304 GPa) direction with <111> oriented single crystal cylinder 30 leaves a lot of latitude for retaining the high modulus for alloys including those that tend to form random grain texture. This is distinctly different from prior art approaches where the starting cylinder 21 has intermediate level of elastic modulus (30 Mpsi; 207 GPa), followed by recrystallization of the random texture (see steps 25, 26 of FIG. 4), which works only for certain alloy compositions.

(27) It is realized that for some specific alloys, it may be more advantageous to start with single crystal in different orientation such as <110>, <112>, <100> or <123>, or even columnar grain material, if the recrystallization texture ultimately leads to strong <111> texture. The disclosed process suggests a novel way of starting with directionally solidified single crystal 30 or columnar grain material 30, in contrast to conventional methods for making high modulus shaft that start with a cast or consolidated particle ingot 21. For most classes of nickel and iron base alloys, <111> oriented single crystal may be the practical approach.

(28) In this context it is also recognized that some iron base alloys and steels where strength could be derived from martensitic transformation, the end orientation or grain texture, may systematically shift from the starting orientation owing to habit plane relationship between the parent phase and resulting martensitic phase. In such a situation depending on the combination of strength and modulus desired, deviation from the <111> orientation may be desirable.

(29) It is also recognized that unconventional hot working processes such as twist extrusion and equal channel angular extrusion also may be used to enhance strength, and may present added advantage in terms of selection of starting single crystal orientation. For example a combination of such technique may allow to convert a starting single crystal in <100> orientation to a high modulus <111> textured material, presenting a manufacturing advantage at the casting stage by eliminating seed requirement, as <100> is a natural growth direction.

INDUSTRIAL APPLICABILITY

(30) The disclosed process is a combination of process steps. First, a single crystal casting can be seeded to produce a desirable crystallographic orientation. Large single crystal castings, approaching one foot in diameter and several feet in height can be cast by conventional investment casting or zone melting. Further, hollow single crystal cylinders can also be cast using ceramic or refractory metal cores. Single crystal casting of selected orientation can be axisymmetrically hot worked followed by limited recrystallization or direct age treatment using various techniques to achieve desired grain texture. Optimum processing parameters in all steps may differ from alloy to alloy, but none of the processes are fundamentally expected to be limited to a specific composition of nickel or iron base alloys.

(31) Nickel base and iron base (steel) shafts generally possess high toughness and high ductility. Achieving high elastic modulus in these classes of materials makes their application as a high modulus shaft material much less riskier than high modulus composite shafts. Changing the grain texture has only a secondary influence on the plastic behavior of the material.