Patent Application
20140255719
1. Field of the Technology
The present disclosure relates to methods of processing high strength, non-magnetic corrosion resistant alloys. The present methods may find application in, for example, and without limitation, the processing of alloys for use in the chemical, mining, oil, and gas industries. The present invention also relates to alloys made by methods including the processing discussed herein.
2. Description of the Background of the Technology
Metal alloy parts used in chemical processing facilities may be in contact with highly corrosive and/or erosive compounds under demanding conditions. These conditions may subject metal alloy parts to high stresses and aggressively promote corrosion and erosion, for example. If it is necessary to replace damaged, worn, or corroded metallic parts of chemical processing equipment, it may be necessary to suspend facility operations for a period of time. Therefore, extending the useful service life of metal alloy parts used in chemical processing facilities can reduce product cost. Service life may be extended, for example, by improving mechanical properties and/or corrosion resistance of the alloys.
Similarly, in oil and gas drilling operations, drill string components may degrade due to mechanical, chemical, and/or environmental conditions. The drill string components may be subject to impact, abrasion, friction, heat, wear, erosion, corrosion, and/or deposits. Conventional alloys may suffer from one or more limitations that negatively impact their performance as drill string components. For example, conventional materials may lack sufficient mechanical properties (for example, yield strength, tensile strength, and/or fatigue strength), possess insufficient corrosion resistance (for example, pitting resistance and/or stress corrosion cracking), or lack necessary non-magnetic properties to operate for extended periods in the down-hole environment. Also, the properties of conventional alloys may limit the possible size and shape of the drill string components made from the alloys. These limitations may reduce the service life of the components, complicating and increasing the cost of oil and gas drilling.
It has been discovered that during warm working radial forging of some high strength, non-magnetic materials to develop a preferred strength, there may be an uneven deformation or an uneven amount of strain in the cross-section of the workpiece. The uneven deformation may be manifest, for example, as a difference in hardness and/or tensile properties between the surface and the center of the forging. For example, observed hardness, yield strength, and tensile strength may be greater at the surface than at the center of the forging. These differences are believed to be consistent with differences in the amount of strain developed in different regions of the cross-section of the workpiece during radial forging.
One method for promoting consistent hardness through the cross-section of a forged bar is to use an age hardenable material such as, for example, the nickel-base superalloy Alloy 718 (UNS N07718) in the direct aged or solution treated and aged condition. Other techniques have involved using cold or warm working to impart hardness to the alloy. This particular technique has been used to harden ATI Datalloy 2® alloy (UNS unassigned), which is a high strength, non-magnetic austenitic stainless steel available from Allegheny Technologies Incorporated, Pittsburgh, Pa. USA. The final thermomechanical processing step used to harden ATI Datalloy 2® alloy involves warm working the material at 1075° F. to an approximately 30 percent reduction in cross-sectional area on a radial forge. Another process, which utilizes a high grade alloy steel referred to as “P-750 alloy” (UNS unassigned), sourced from Schoeller-Bleckmann Oilfield Technology, Houston, Tex., is generally disclosed in U.S. Pat. No. 6,764,647, the entire disclosure of which is hereby incorporated by reference. The P-750 alloy is cold worked to about a 6-19 percent reduction in cross-sectional area at temperatures of 680-1094° F. to obtain relatively even hardness through the cross-section of a final 8-inch billet.
Another method for producing a consistent hardness across the cross-section of a worked workpiece is to increase the amount of cold or warm work used to produce a bar from the workpiece. This, however, becomes impractical with bars having finished diameters equal to or greater than 10 inches because the starting size can exceed the practical limits of ingots that can be melted without imparting problematic melt-related defects. It is noted that if the diameter of the starting workpiece is sufficiently small, then the strain gradient can be eliminated, resulting in consistent mechanical properties and hardness profiles across the cross-section of the finished bar.
It would be desirable to develop a thermomechanical process that could be used on high strength, non-magnetic alloy ingots or workpiece of any starting size that produces a relatively consistent amount of strain through the cross-section of a bar or other mill product produced by the process. Producing a relatively constant strain profile across the cross-section of the worked bar also may result in generally consistent mechanical properties across the bar's cross-section.
According to a non-limiting aspect of the present disclosure, a method of processing a non-magnetic alloy workpiece comprises: heating the workpiece to a temperature in a warm working temperature range; open die press forging the workpiece to impart a desired strain to a central region of the workpiece; and radial forging the workpiece to impart a desired strain to a surface region of the workpiece. In certain non-limiting embodiments, the warm working temperature range is a range spanning a temperature that is one-third of the incipient melting temperature of the non-magnetic alloy up to a temperature that is two-thirds of the incipient melting temperature of the non-magnetic alloy. In a non-limiting embodiment, the warm working temperature is any temperature up to the highest temperature at which recrystallization (dynamic or static) does not occur in the non-magnetic alloy.
In certain non-limiting embodiments of the method of processing a non-magnetic alloy workpiece according to the present disclosure, the open die press forging step of the method precedes the radial forging step. In still other non-limiting embodiments of the method of processing a non-magnetic alloy workpiece according to the present disclosure, the radial forging step precedes the open die press forging step.
Non-limiting examples of non-magnetic alloys that may be processed by embodiments of methods according to the present disclosure include non-magnetic stainless steel alloys, nickel alloys, cobalt alloys, and iron alloys. In certain non-limiting embodiments, a non-magnetic austenitic stainless steel alloy is processed using embodiments of methods according to the present disclosure.
In certain non-limiting embodiments of a method according to the present disclosure, after the steps of open die press forging and radial forging, the central region strain and the surface region strain are each in a final range of from 0.3 inch/inch up to 1.0 inch/inch, with a difference in strain from the central region to the surface region of not more than 0.5 inch/inch. In a certain non-limiting embodiment of a method according to the present disclosure, after the steps of open die press forging and radial forging, the central region strain and the surface region strain are each in a final range of from 0.3 inch/inch to 0.8 inch/inch. In other non-limiting embodiments, after the steps of open die press forging and radial forging, the surface region strain is substantially equivalent to the central region strain and the workpiece exhibits at least one substantially uniform mechanical property throughout the workpiece cross-section.
According to another aspect of the present disclosure, certain non-limiting embodiments of a method of processing a non-magnetic austenitic stainless steel alloy workpiece comprise: heating the workpiece to a temperature in the range of from 950° F. to 1150° F.; open die press forging the workpiece to impart a final strain in the range of from 0.3 inch/inch up to 1.0 inch/inch to a central region of the workpiece; and radial forging the workpiece to impart a final strain in the range of from 0.3 inch/inch up to 1.0 inch/inch to a surface region of the workpiece, with a difference in strain from the central region to the surface region of not more than 0.5 inch/inch. In a certain non-limiting embodiment, the method includes: open die press forging the workpiece to impart a final strain in the range of from 0.3 inch/inch to 0.8 inch/inch.
In a non-limiting embodiment, the open die press forging step precedes the radial forging step. In another non-limiting embodiment, the radial forging step precedes the open die press forging step.
Another aspect according to the present disclosure is directed to non-magnetic alloy forgings. In certain non-limiting embodiments according to the present disclosure, a non-magnetic alloy forging comprises a circular cross-section having a diameter greater than 5.25 inches, and wherein at least one mechanical property of the non-magnetic alloy forging is substantially uniform throughout the cross-section of the forging. In certain non-limiting embodiments, the mechanical property that is substantially uniform throughout the cross-section of the forging is at least one of hardness, ultimate tensile strength, yield strength, percent elongation, and percent reduction in area.
In certain non-limiting embodiments, a non-magnetic alloy forging according to the present disclosure comprises one of a non-magnetic stainless steel alloy, a nickel alloy, a cobalt alloy, and an iron alloy. In certain non-limiting embodiments, a non-magnetic alloy forging according to the present disclosure comprises a non-magnetic austenitic stainless steel alloy forging.
The features and advantages of apparatus and methods described herein may be better understood by reference to the accompanying drawings in which:
The reader will appreciate the foregoing details, as well as others, upon considering the following detailed description of certain non-limiting embodiments according to the present disclosure.
It is to be understood that certain descriptions of the embodiments described herein have been simplified to illustrate only those elements, features, and aspects that are relevant to a clear understanding of the disclosed embodiments, while eliminating, for purposes of clarity, other elements, features, and aspects. Persons having ordinary skill in the art, upon considering the present description of the disclosed embodiments, will recognize that other elements and/or features may be desirable in a particular implementation or application of the disclosed embodiments. However, because such other elements and/or features may be readily ascertained and implemented by persons having ordinary skill in the art upon considering the present description of the disclosed embodiments, and are therefore not necessary for a complete understanding of the disclosed embodiments, a description of such elements and/or features is not provided herein. As such, it is to be understood that the description set forth herein is merely exemplary and illustrative of the disclosed embodiments and is not intended to limit the scope of the invention as defined solely by the claims.
Any numerical range recited herein is intended to include all sub-ranges subsumed therein. For example, a range of “1 to 10” or “from 1 to 10” is intended to include all sub-ranges between (and including) the recited minimum value of 1 and the recited maximum value of 10, that is, having a minimum value equal to or greater than 1 and a maximum value of equal to or less than 10. Any maximum numerical limitation recited herein is intended to include all lower numerical limitations subsumed therein and any minimum numerical limitation recited herein is intended to include all higher numerical limitations subsumed therein. Accordingly, Applicants reserve the right to amend the present disclosure, including the claims, to expressly recite any sub-range subsumed within the ranges expressly recited herein. All such ranges are intended to be inherently disclosed herein such that amending to expressly recite any such sub-ranges would comply with the requirements of 35 U.S.C. §112, first paragraph, and 35 U.S.C. §132(a).
The grammatical articles “one”, “a”, “an”, and “the”, as used herein, are intended to include “at least one” or “one or more”, unless otherwise indicated. Thus, the articles are used herein to refer to one or more than one (i.e., to at least one) of the grammatical objects of the article. By way of example, “a component” means one or more components, and thus, possibly, more than one component is contemplated and may be employed or used in an implementation of the described embodiments.
All percentages and ratios are calculated based on the total weight of the alloy composition, unless otherwise indicated.
Any patent, publication, or other disclosure material that is said to be incorporated, in whole or in part, by reference herein is incorporated herein only to the extent that the incorporated material does not conflict with existing definitions, statements, or other disclosure material set forth in this disclosure. As such, and to the extent necessary, the disclosure as set forth herein supersedes any conflicting material incorporated herein by reference. Any material, or portion thereof, that is said to be incorporated by reference herein, but which conflicts with existing definitions, statements, or other disclosure material set forth herein is only incorporated to the extent that no conflict arises between that incorporated material and the existing disclosure material.
The present disclosure includes descriptions of various embodiments. It is to be understood that all embodiments described herein are exemplary, illustrative, and non-limiting. Thus, the invention is not limited by the description of the various exemplary, illustrative, and non-limiting embodiments. Rather, the invention is defined solely by the claims, which may be amended to recite any features expressly or inherently described in or otherwise expressly or inherently supported by the present disclosure.
As used herein, the terms “forming”, “forging”, “open die press forging”, and “radial forging” refer to forms of thermomechanical processing (“TMP”), which also may be referred to herein as “thermomechanical working”. “Thermomechanical working” is defined herein as generally covering a variety of metal forming processes combining controlled thermal and deformation treatments to obtain synergistic effects, such as, for example, and without limitation, improvement in strength, without loss of toughness. This definition of thermomechanical working is consistent with the meaning ascribed in, for example, ASM Materials Engineering Dictionary, J. R. Davis, ed., ASM International (1992), p. 480. “Open die press forging” is defined herein as the forging of metal or metal alloy between dies, in which the material flow is not completely restricted, by mechanical or hydraulic pressure, accompanied with a single work stroke of the press for each die session. This definition of open press die forging is consistent with the meaning ascribed in, for example, ASM Materials Engineering Dictionary, J. R. Davis, ed., ASM International (1992), pp. 298 and 343. “Radial forging” is defined herein as a process using two or more moving anvils or dies for producing forgings with constant or varying diameters along their length. This definition of radial forging is consistent with the meaning ascribed in, for example, ASM Materials Engineering Dictionary, J. R. Davis, ed., ASM International (1992), p. 354. Those having ordinary skill in the metallurgical arts will readily understand the meanings of these several terms.
Conventional alloys used in chemical processing, mining, and/or oil and gas applications may lack an optimal level of corrosion resistance and/or an optimal level of one or more mechanical properties. Various embodiments of alloys processed as described herein may have certain advantages including, but not limited to, improved corrosion resistance and/or mechanical properties over conventionally processed alloys. Certain embodiments of alloys processed as described herein may exhibit one or more improved mechanical properties without any reduction in corrosion resistance, for example. Certain embodiments of alloys processed as described herein may exhibit improved impact properties, weldability, resistance to corrosion fatigue, galling resistance, and/or hydrogen embrittlement resistance relative to certain conventionally processed alloys.
In various embodiments, alloys processed as described herein may exhibit enhanced corrosion resistance and/or advantageous mechanical properties suitable for use in certain demanding applications. Without wishing to be bound to any particular theory, it is believed that certain of the alloys processed as described herein may exhibit higher tensile strength, for example, due to an improved response to strain hardening from deformation, while also retaining high corrosion resistance. Strain hardening or cold or warm working may be used to harden materials that do not generally respond well to heat treatment. However, the exact nature of the cold or warm worked structure may depend on the material, applied strain, strain rate, and/or temperature of the deformation.
The current manufacturing practice for making non-magnetic materials for exploration and drilling applications is to impart a specific amount of warm work into the product as one of the last thermomechanical processing steps. The term “non-magnetic” refers to a material that is not or is only negligibly affected by a magnetic field. Certain non-limiting embodiments of non-magnetic alloys processed as described herein may be characterized by a magnetic permeability value (μr) within a particular range. In various non-limiting embodiments, the magnetic permeability value of an alloy processed according to the present disclosure may be less than 1.01, less than 1.005, and/or less than 1.001. In various embodiments, the alloy may be substantially free from ferrite.
The terms “warm working” and “warm work” as used herein refer to thermomechanical working and deformation of a metal or metal alloy by forging at temperatures that are below the lowest temperature at which recrystallization (dynamic or static) occurs in the material. In a non-limiting embodiment, warm working is accomplished in a warm working temperature range that spans a temperature that is one-third of the incipient melting temperature of the alloy up to a temperature that is two-thirds of the incipient melting temperature of the alloy. It will be recognized that the lower limit of the warm working temperature range is only limited to the capabilities of the open die press forge and rotary forge equipment to deform the non-magnetic alloy workpiece at the desired forging temperature. In a non-limiting embodiment, the warm working temperature is any temperature up to the highest temperature at which recrystallization (dynamic or static) does not occur in the non-magnetic alloy. In this embodiment, the term warm working, as-used herein, encompasses and includes working at temperatures that are less than one-third of the incipient melting temperature of the material, including room or ambient temperature and temperatures lower than ambient temperatures. In a non-limiting embodiment, warm working, as used herein, comprises forging a workpiece at a temperature in a range that spans a temperature that is one-third of the incipient melting temperature of the alloy up to a temperature that is two-thirds of the incipient melting temperature of the alloy. In another non-limiting embodiment, the warm working temperature comprises any temperature up to the highest temperature at which recrystallization (dynamic or static) does not occur in the non-magnetic alloy. In this embodiment, the term warm working, as-used herein, encompasses and includes forging at temperatures that are less than one-third of the incipient melting temperature of the material, including room or ambient temperature and temperatures lower than ambient temperatures. The warm working step imparts strength to the alloy workpiece sufficient for the intended application. In the current manufacturing practice, the warm working thermomechanical processing of the alloy is carried out on a radial forge in a single step. In the single radial forging step, the workpiece is warm worked from an initial size to a final forged size using multiple passes on the radial forge, without removing the workpiece from the forging apparatus, and without annealing treatments intermediate the forging passes of the single step.
The present inventors have discovered that during warm work radial forging of high strength non-magnetic austenitic materials to develop a desired strength, it is often the case that the workpiece is deformed unevenly and/or the amount of strain imparted to the workpiece is not uniform across the workpiece cross-section. The uneven deformation may be observed as a difference in hardness and tensile properties between the surface and the center of the workpiece. Hardness, yield strength, and tensile strength were generally observed to be greater at the workpiece surface than at the workpiece center. These differences are believed to be consistent with differences in the amount of strain developed in different regions of the cross-section of the workpiece during radial forging. Differences in mechanical properties and hardness between the surface and central regions of warm worked radial forged-only alloy workpieces may be seen in the test data presented in Table 1. All test samples were non-magnetic austenitic stainless steels, and the chemical composition of each heat is provided in Table 2 below. All test samples listed in Table 1 were warm worked radial forged at 1025° F. as the last thermomechanical processing step applied to the samples before measuring the properties listed in Table 1.
An aspect of the present disclosure is directed to modifying a conventional method of processing a non-magnetic alloy workpiece including warm work radial forging as the last thermomechanical step, so as to include a warm working open die press forging step.
Referring to
The workpiece is then radial forged 46 to impart a desired strain to a surface region of the workpiece. In a non-limiting embodiment, the workpiece is radial forged to impart a desired strain in the surface region in a range of 0.3 inch/inch to 1.0 inch per inch. In another non-limiting embodiment, the workpiece is radial forged to impart a desired strain in the surface region in a range of 0.3 inch/inch to 0.8 inch per inch.
In a non-limiting embodiment, after open die press forging and radial forging, the strain imparted to the central region and the strain imparted to the surface region are each in a range of from 0.3 inch/inch to 1.0 inch/inch, and the difference in strain from the central region to the surface region is not more than 0.5 inch/inch. In another non-limiting embodiment after the steps of open die press forging and radial forging, the strain imparted to the central region and the strain imparted to the surface region are each in a range of from 0.3 inch/inch to 0.8 inch/inch. Ordinary skilled practitioners know or will be able to easily determine open die press forging and radial forging parameters required to achieve the desired respective strains, and operating parameters of individual forging steps need not be discussed herein.
In certain non-limiting embodiments, a “surface region” of a workpiece includes a volume of material between the surface of the workpiece to a depth of about 30 percent of the distance from the surface to the workpiece center. In certain other non-limiting embodiments, a “surface region” of a workpiece includes a volume of material between the surface of the workpiece to a depth of about 40 percent, or in certain embodiments about 50 percent, of the distance from the surface to the workpiece center. It will be apparent to those having ordinary skill as to what constitutes the “center” of a workpiece having a particular shape for purposes of identifying a “surface region”. For example, an elongate cylindrical workpiece will have a central longitudinal axis, and the surface region of the workpiece will extend from the outer peripheral curved surface of the workpiece in the direction of the central longitudinal axis. Also for example, an elongate workpiece having a square or rectangular cross-section taken transverse to a longitudinal axis of the workpiece will have four distinct peripheral “faces” a central longitudinal axis, and the surface region of each face will extend from the surface of the face into the workpiece in the general direction of the central axis and the opposing face. Also, for example, a slab-shaped workpiece will have two large primary opposed faces generally equidistant from an intermediate plane within the workpiece, and the surface region of each primary face will extend from the surface of the face into the workpiece toward the intermediate plane and the opposed primary face.
In certain non-limiting embodiments, a “central region” of a workpiece includes a centrally located volume of material that makes up about 70 percent by volume of material of the workpiece. In certain other non-limiting embodiments, a “central region” of a workpiece includes a centrally located volume of material that makes up about 60 percent, or about 50 percent, by volume of the material of the workpiece.
In another non-limiting embodiment of the method, after the open die press forging and radial forging steps, strain within a surface region of the workpiece is substantially equivalent to strain within a central region of the workpiece. As used herein, strain within a surface region of the workpiece is “substantially equivalent” to strain within a central region of the workpiece when strain between the regions differs by less than 20%, or by less than 15%, or less than 5%. The combined use of open die press forging and radial forging in embodiments of the method according to the present disclosure can produce a workpiece with strain that is substantially equivalent throughout the cross-section of a final forged workpiece. A consequence of the strain distribution in such forged workpieces is that the workpieces may have one or more mechanical properties that are substantially uniform, through the workpiece cross-section and/or as between a surface region and a central region of the workpiece. As used herein, one or more mechanical properties within a surface region of the workpiece are “substantially uniform” to one or more properties within a central region of the workpiece when one or more mechanical properties between the regions differs by less than 20%, or by less than 15%, or less than 5%.
It is not believed to be critical to the strain distribution and subsequent mechanical properties whether the warm work open die press forging step 44 or the warm work radial forging step 46 is conducted first. In certain non-limiting embodiments, the open die press forging 44 step precedes the radial forging 46 step. In other non-limiting embodiments, the radial forging 46 step precedes the open die press forging 44 step. It will be understood that multiple cycles consisting of an open die press forging step 44 and a radial forging step 46 may be utilized to achieve the desired strain distribution and desired one or more mechanical properties across the cross-section of the final forged article. Multiple cycles, however, involve additional expense. It is believed that it is generally unnecessary to conduct multiple cycles of radial forging and open die press forging steps to achieve an substantially equivalent strain distribution across the cross-section of the workpiece.
In certain non-limiting embodiments of the method according to the present disclosure, the workpiece may be transferred from the first forging apparatus, i.e., one of a radial forge and an open die press forge, directly to the second forging apparatus, i.e., the other of the radial forge and open die press forge. In certain non-limiting embodiments, after the first warm work forging step (i.e., either radial forging or open die press forging), the workpiece may be cooled to room temperature and then reheated to a warm working temperature prior to the second warm work forging step, or alternatively, the workpiece could be directly transferred from the first forging apparatus to a reheat furnace to be reheated for the second warm work forging step.
In non-limiting embodiments, the non-magnetic alloy processed using the method of the present disclosure is a non-magnetic stainless steel alloy. In a certain non-limiting embodiments, the non-magnetic stainless steel alloy processed using the method of the present disclosure is a non-magnetic austenitic stainless steel alloy. In certain non-limiting embodiments, when the method is applied to processing a non-magnetic austenitic stainless steel alloy, the temperature range in which the radial forging and open die press forging steps are conducted is from 950° F. to 1150° F.
In certain non-limiting embodiments, prior to heating the workpiece to the warm working temperature, the workpiece may be annealed or homogenized to facilitate the warm work forging steps. In a non-limiting embodiment, when the workpiece comprises a non-magnetic austenitic stainless steel alloy, the workpiece is annealed at a temperature in the range of 1850° F. to 2300° F., and is heated at the annealing temperature for 1 minute to 10 hours. In certain non-limiting embodiments, heating the workpiece to the warm working temperature comprises allowing the workpiece to cool from the annealing temperature to the warm working temperature. As will be readily apparent to those having ordinary skill, the annealing time necessary to dissolve deleterious sigma precipitates that could form in a particular workpiece during hot working will be dependent on annealing temperature; the higher the annealing temp, the shorter the time needed to dissolve any deleterious sigma precipitate that formed. Ordinarily skilled practitioners will be able to determine suitable annealing temperatures and times for a particular workpiece without undue effort.
It has been noted that when the diameter of a workpiece that has been warm work forged according to the method of the present disclosure is on the order of 5.25 inches or less, a significant difference may not be observed in strain and certain consequent mechanical properties between material in a central region and material in a surface region of the forged workpiece (see Table 1). In certain non-limiting embodiments according to the present disclosure, the forged workpiece that has been processed using the present method is generally cylindrical and comprises a generally circular cross-section. In certain non-limiting embodiments, the forged workpiece that has been processed using the present method is generally cylindrical and comprises a circular cross-section having a diameter that is no greater than 5.25 inches. In certain non-limiting embodiments, the forged workpiece that has been processed using the present method is generally cylindrical and comprises a circular cross-section having a diameter that is greater than 5.25 inches, or is at least 7.25 inches, or is 7.25 inches to 12.0 inches after warm work forging according to the present disclosure.
Another aspect of the present disclosure is directed to a method of processing a non-magnetic austenitic stainless steel alloy workpiece, the method comprising: heating the workpiece to a warm working temperature in a temperature range from 950° F. to 1150° F.; open die press forging the workpiece to impart a final strain of between 0.3 inch/inch to 1.0 inch/inch, or 0.3 inch/inch to 0.8 inch/inch to a central region of the workpiece; and radial forging the workpiece to impart a final strain of between 0.3 inch/inch to 1.0 inch/inch, or 0.3 inch/inch to 0.8 inch/inch to a surface region of the workpiece. In a non-limiting embodiment, after open press die forging and radial forging the workpiece a difference in final strain in the central region and the surface region is no more than 0.5 inch/inch. In other non-limiting embodiment, strain between the regions differs by less than 20%, or by less than 15%, or less than 5%. In non-limiting embodiments of the method, the open die press forging step precedes the radial forging step. In other non-limiting embodiments of the method, the radial forging step precedes the open die press forging step.
The method of processing a non-magnetic austenitic stainless steel alloy workpiece according to the present disclosure may further comprise annealing the workpiece prior to heating the workpiece to the warm working temperature. In a non-limiting embodiment, the non-magnetic austenitic stainless steel alloy workpiece may be annealed at an annealing temperature in a temperature range of 1850° F. to 2300° F., and an annealing time may be in the range of 1 minute to 10 hours. In still another non-limiting embodiment, the step of heating the non-magnetic austenitic stainless steel alloy workpiece to the warm working temperature may comprise allowing the workpiece to cool from the annealing temperature to the warm working temperature.
As discussed above, it has been noted that when the diameter of a workpiece that has been warm work forged according to the method of the present disclosure is on the order of, for example, 5.25 inches or less, a significant difference may not be observed in strain and certain consequent mechanical properties between material in a central region and material in a surface region of the forged workpiece. In certain non-limiting embodiments according to the present disclosure, the forged workpiece that has been processed using the present method is a generally cylindrical non-magnetic austenitic stainless steel alloy workpiece and comprises a generally circular cross-section. In certain non-limiting embodiments, the forged workpiece that has been processed using the present method is a generally cylindrical non-magnetic austenitic stainless steel alloy workpiece and comprises a circular cross-section having a diameter that is no greater than 5.25 inches. In certain non-limiting embodiments, the forged workpiece that has been processed using the present method is a generally cylindrical non-magnetic austenitic stainless steel alloy workpiece and comprises a circular cross-section having a diameter that is greater than 5.25 inches, or is at least 7.25 inches, or is 7.25 inches to 12.0 inches after warm work forging according to the present disclosure.
Still another aspect according to the present disclosure is directed to a non-magnetic alloy forging. In a non-limiting embodiment, a non-magnetic alloy forging according to the present disclosure comprises a circular cross-section with a diameter greater than 5.25 inches. At least one mechanical property of the non-magnetic alloy forging is substantially uniform throughout the cross-section of the forging. In non-limiting embodiments, the substantially uniform mechanical property comprises one or more of a hardness, an ultimate tensile strength, a yield strength, a percent elongation, and a percent reduction in area.
It will be recognized that while non-limiting embodiments of the present disclosure are directed to a method for providing substantially equivalent strain and at least one substantially uniform mechanical property across a cross-section of a forged workpiece, the practice of radial forging combined with open press die forging may be used as to impart strain in a central region of a workpiece that differs to a desired degree from strain imparted by the method in a surface region of the workpiece. For example, with reference to
In various non-limiting embodiments, a non-magnetic alloy forging according to the present disclosure may be selected from a non-magnetic stainless steel alloy, a nickel alloy, a cobalt alloy, and an iron alloy. In certain non-limiting embodiments, a non-magnetic alloy forging according to the present disclosure comprises a non-magnetic austenitic stainless steel alloy.
A broad chemical composition of one high strength non-magnetic austenitic stainless steel intended for exploration and production drilling applications in the oil and gas industry that may be processed by a method and embodied in a forged article according to the present disclosure is disclosed in co-pending U.S. patent application Ser. No. 13/331,135, filed on Dec. 20, 2011, which is incorporated by reference herein in its entirety.
One specific example of a highly corrosion resistant, high strength material for exploration and discovery applications in the oil and gas industry that may be processed by a method and embodied in a forged article according to the present disclosure is AL-6XN® alloy (UNS N08367), which is an iron-base austenitic stainless steel alloy available from Allegheny Technologies Incorporated, Pittsburgh, Pa. USA. A two-step warm work forging process according to the present disclosure can be used for AL-6XN® alloy to impart high strength to the material.
Another specific example of a highly corrosion resistant, high strength material for exploration and discovery applications in the oil and gas industry that may be processed by a method and embodied in a forged article according to the present disclosure is ATI Datalloy 2® alloy (no UNS assigned), a high strength, non-magnetic austenitic stainless steel, which is available from Allegheny Technologies Incorporated, Pittsburgh, Pa. USA. A nominal composition of ATI Datalloy 2® alloy in weight percentages based on the total alloy weight is 0.03 carbon, 0.30 silicon, 15.1 manganese, 15.3 chromium, 2.1 molybdenum, 2.3 nickel, 0.4 nitrogen, remainder iron and incidental impurities.
In certain non-limiting embodiments, an alloy that may be processed by a method and embodied in a forged article according to the present disclosure is an austenitic alloy that comprises, consists essentially of, or consists of chromium, cobalt, copper, iron, manganese, molybdenum, nickel, carbon, nitrogen, tungsten, and incidental impurities. In certain non-limiting embodiments, the austenitic alloy optionally further includes one or more of aluminum, silicon, titanium, boron, phosphorus, sulfur, niobium, tantalum, ruthenium, vanadium, and zirconium, either as trace elements or as incidental impurities.
Also, according to various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises, consists essentially of, or consists of, in weight percentages based on total alloy weight, up to 0.2 carbon, up to 20 manganese, 0.1 to 1.0 silicon, 14.0 to 28.0 chromium, 15.0 to 38.0 nickel, 2.0 to 9.0 molybdenum, 0.1 to 3.0 copper, 0.08 to 0.9 nitrogen, 0.1 to 5.0 tungsten, 0.5 to 5.0 cobalt, up to 1.0 titanium, up to 0.05 boron, up to 0.05 phosphorus, up to 0.05 sulfur, iron, and incidental impurities.
In addition, according to various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises, consists essentially of, or consists of, in weight percentages based on total alloy weight, up to 0.05 carbon, 1.0 to 9.0 manganese, 0.1 to 1.0 silicon, 18.0 to 26.0 chromium, 19.0 to 37.0 nickel, 3.0 to 7.0 molybdenum, 0.4 to 2.5 copper, 0.1 to 0.55 nitrogen, 0.2 to 3.0 tungsten, 0.8 to 3.5 cobalt, up to 0.6 titanium, a combined weight percentage of columbium and tantalum no greater than 0.3, up to 0.2 vanadium, up to 0.1 aluminum, up to 0.05 boron, up to 0.05 phosphorus, up to 0.05 sulfur, iron, and incidental impurities.
Also, according to various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure may comprise, consist essentially of, or consist of, in weight percentages based on total alloy weight, up to 0.05 carbon, 2.0 to 8.0 manganese, 0.1 to 0.5 silicon, 19.0 to 25.0 chromium, 20.0 to 35.0 nickel, 3.0 to 6.5 molybdenum, 0.5 to 2.0 copper, 0.2 to 0.5 nitrogen, 0.3 to 2.5 tungsten, 1.0 to 3.5 cobalt, up to 0.6 titanium, a combined weight percentage of columbium and tantalum no greater than 0.3, up to 0.2 vanadium, up to 0.1 aluminum, up to 0.05 boron, up to 0.05 phosphorus, up to 0.05 sulfur, iron, and incidental impurities.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises carbon in any of the following weight percentage ranges: up to 2.0; up to 0.8; up to 0.2; up to 0.08; up to 0.05; up to 0.03; 0.005 to 2.0; 0.01 to 2.0; 0.01 to 1.0; 0.01 to 0.8; 0.01 to 0.08; 0.01 to 0.05; and 0.005 to 0.01.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises manganese in any of the following weight percentages: up to 20.0; up to 10.0; 1.0 to 20.0; 1.0 to 10; 1.0 to 9.0; 2.0 to 8.0; 2.0 to 7.0; 2.0 to 6.0; 3.5 to 6.5; and 4.0 to 6.0.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises silicon in any of the following weight percentages: up to 1.0; 0.1 to 1.0; 0.5 to 1.0; and 0.1 to 0.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises chromium in any of the following weight percentage ranges: 14.0 to 28.0; 16.0 to 25.0; 18.0 to 26; 19.0 to 25.0; 20.0 to 24.0; 20.0 to 22.0; 21.0 to 23.0; and 17.0 to 21.0.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises nickel in any of the following weight percentage ranges: 15.0 to 38.0; 19.0 to 37.0; 20.0 to 35.0; and 21.0 to 32.0.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises molybdenum in any of the following weight percentage ranges: 2.0 to 9.0; 3.0 to 7.0; 3.0 to 6.5; 5.5 to 6.5; and 6.0 to 6.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises copper in any of the following weight percentage ranges: 0.1 to 3.0; 0.4 to 2.5; 0.5 to 2.0; and 1.0 to 1.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises nitrogen in any of the following weight percentage ranges: 0.08 to 0.9; 0.08 to 0.3; 0.1 to 0.55; 0.2 to 0.5; and 0.2 to 0.3. In certain embodiments, the nitrogen content in the austenitic alloy may be limited to 0.35 weight percent or 0.3 weight percent to address its limited solubility in the alloy.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises tungsten in any of the following weight percentage ranges: 0.1 to 5.0; 0.1 to 1.0; 0.2 to 3.0; 0.2 to 0.8; and 0.3 to 2.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises cobalt in any of the following weight percentages: up to 5.0; 0.5 to 5.0; 0.5 to 1.0; 0.8 to 3.5; 1.0 to 4.0; 1.0 to 3.5; and 1.0 to 3.0. In certain embodiments of alloys processed by a method and embodied in a forged article according to the present disclosure, cobalt unexpectedly improved mechanical properties of the alloy. For example, in certain embodiments of the alloy, additions of cobalt may provide up to a 20% increase in toughness, up to a 20% increase in elongation, and/or improved corrosion resistance. Without wishing to be bound to any particular theory, it is believed that replacing iron with cobalt may increase the resistance to detrimental sigma phase precipitation in the alloy relative to non-cobalt bearing variants which exhibited higher levels of sigma phase at the grain boundaries after hot working.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises cobalt and tungsten in a cobalt/tungsten weight percentage ratio of from 2:1 to 5:1, or from 2:1 to 4:1. In certain embodiments, for example, the cobalt/tungsten weight percentage ratio may be about 4:1. The use of cobalt and tungsten may impart improved solid solution strengthening to the alloy.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises titanium in any of the following weight percentages: up to 1.0; up to 0.6; up to 0.1; up to 0.01; 0.005 to 1.0; and 0.1 to 0.6.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises zirconium in any of the following weight percentages: up to 1.0; up to 0.6; up to 0.1; up to 0.01; 0.005 to 1.0; and 0.1 to 0.6.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises niobium and/or tantalum in any of the following weight percentages: up to 1.0; up to 0.5; up to 0.3; 0.01 to 1.0; 0.01 to 0.5; 0.01 to 0.1; and 0.1 to 0.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises a combined weight percentage of columbium and tantalum in any of the following ranges: up to 1.0; up to 0.5; up to 0.3; 0.01 to 1.0; 0.01 to 0.5; 0.01 to 0.1; and 0.1 to 0.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises vanadium in any of the following weight percentages: up to 1.0; up to 0.5; up to 0.2; 0.01 to 1.0; 0.01 to 0.5; 0.05 to 0.2; and 0.1 to 0.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises aluminum in any of the following weight percentage ranges: up to 1.0; up to 0.5; up to 0.1; up to 0.01; 0.01 to 1.0; 0.1 to 0.5; and 0.05 to 0.1.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises boron in any of the following weight percentage ranges: up to 0.05; up to 0.01; up to 0.008; up to 0.001; up to 0.0005.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises phosphorus in any of the following weight percentage ranges: up to 0.05; up to 0.025; up to 0.01; and up to 0.005.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises sulfur in any of the following weight percentage ranges: up to 0.05; up to 0.025; up to 0.01; and up to 0.005.
In various non-limiting embodiments, the balance of an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure may comprise, consist essentially of, or consist of iron and incidental impurities. In various non-limiting embodiments, In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises iron in any of the following weight percentage ranges: up to 60; up to 50; 20 to 60; 20 to 50; 20 to 45; to 45; 30 to 50; 40 to 60; 40 to 50; 40 to 45; and 50 to 60.
In various non-limiting embodiments, an austenitic alloy processed by a method according to the present disclosure comprises one or more trace elements. As used herein, “trace elements” refers to elements that may be present in the alloy as a result of the composition of the raw materials and/or the melting method employed and which are present in concentrations that do not significantly negatively affect important properties of the alloy, as those properties are generally described herein. Trace elements may include, for example, one or more of titanium, zirconium, columbium (niobium), tantalum, vanadium, aluminum, and boron in any of the concentrations described herein. In certain non-limiting embodiments, trace elements may not be present in alloys according to the present disclosure. As is known in the art, in producing alloys, trace elements typically may be largely or wholly eliminated by selection of particular starting materials and/or use of particular processing techniques. In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises a total concentration of trace elements in any of the following weight percentage ranges: up to 5.0; up to 1.0; up to 0.5; up to 0.1; 0.1 to 5.0; 0.1 to 1.0; and 0.1 to 0.5.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises a total concentration of incidental impurities in any of the following weight percentage ranges: up to 5.0; up to 1.0; up to 0.5; up to 0.1; 0.1 to 5.0; 0.1 to 1.0; and 0.1 to 0.5. As generally used herein, the term “incidental impurities” refers elements present in the alloy in minor concentrations. Such elements may include one or more of bismuth, calcium, cerium, lanthanum, lead, oxygen, phosphorus, ruthenium, silver, selenium, sulfur, tellurium, tin and zirconium. In various non-limiting embodiments, individual incidental impurities in an alloy that may be processed by a method and embodied in a forged article according to the present disclosure do not exceed the following maximum weight percentages: 0.0005 bismuth; 0.1 calcium; 0.1 cerium; 0.1 lanthanum; 0.001 lead; 0.01 tin, 0.01 oxygen; 0.5 ruthenium; 0.0005 silver; 0.0005 selenium; and 0.0005 tellurium. In various non-limiting embodiments, an alloy that may be processed by a method and embodied in a forged article according to the present disclosure, the combined weight percentage of cerium, lanthanum, and calcium present in the alloy (if any is present) may be up to 0.1. In various non-limiting embodiments, the combined weight percentage of cerium and/or lanthanum present in the alloy may be up to 0.1. Other elements that may be present as incidental impurities in alloys that may be processed by a method and embodied in a forged article according to the present disclosure will be apparent to those having ordinary skill in the art upon considering the present disclosure. In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure comprises a total concentration of trace elements and incidental impurities in any of the following weight percentage ranges: up to 10.0; up to 5.0; up to 1.0; up to 0.5; up to 0.1; 0.1 to 10.0; 0.1 to 5.0; 0.1 to 1.0; and 0.1 to 0.5.
In various non-limiting embodiments, an alloy that may be processed by a method and embodied in a forged article according to the present disclosure may be non-magnetic. This characteristic may facilitate use of the alloy in applications in which non-magnetic properties are important including, for example, certain oil and gas drill string component applications. Certain non-limiting embodiments of an austenitic alloy that may be processed by the methods and embodied in the forged articles described herein may be characterized by a magnetic permeability value GO within a particular range. In various non-limiting embodiments, the magnetic permeability value is less than 1.01, less than 1.005, and/or less than 1.001. In various embodiments, the alloy may be substantially free from ferrite.
In various non-limiting embodiments, an alloy that may be processed by a method and embodied in a forged article according to the present disclosure may be characterized by a pitting resistance equivalence number (PREN) within a particular range. As is understood, the PREN ascribes a relative value to an alloy's expected resistance to pitting corrosion in a chloride-containing environment. Generally, alloys having a higher PREN are expected to have better corrosion resistance than alloys having a lower PREN. One particular PREN calculation provides a PREN16 value using the following formula, wherein the percentages are weight percentages based on total alloy weight:
PREN16=% Cr+3.3(% Mo)+16(% N)+1.65(% W)
In various non-limiting embodiments, an alloy that may be processed by a method and embodied in a forged article according to the present disclosure may have a PREN16 value in any of the following ranges: up to 60; up to 58; greater than 30; greater than 40; greater than 45; greater than 48; 30 to 60; 30 to 58; 30 to 50; 40 to 60; 40 to 58; 40 to 50; and 48 to 51. Without wishing to be bound to any particular theory, it is believed that a higher PREN16 value may indicate a higher likelihood that an alloy will exhibit sufficient corrosion resistance in environments such as, for example, highly corrosive environments, high temperature environments, and low temperature environments. Aggressively corrosive environments may exist in, for example, chemical processing equipment and the down-hole environment to which a drill string is subjected in oil and gas drilling applications. Aggressively corrosive environments may subject an alloy to, for example, alkaline compounds, acidified chloride solutions, acidified sulfide solutions, peroxides, and/or CO2, along with extreme temperatures.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure may be characterized by a coefficient of sensitivity to avoid precipitations value (CP) within a particular range. The concept of a CP value is described in, for example, U.S. Pat. No. 5,494,636, entitled “Austenitic Stainless Steel Having High Properties”. In general, the CP value is a relative indication of the kinetics of precipitation of intermetallic phases in an alloy. A CP value may be calculated using the following formula, wherein the percentages are weight percentages based on total alloy weight:
CP=20(% Cr)+0.3(% Ni)+30(% Mo)+5(% W)+10(% Mn)+50(% C)−200(% N)
Without wishing to be bound to any particular theory, it is believed that alloys having a CP value less than 710 will exhibit advantageous austenite stability which helps to minimize HAZ (heat affected zone) sensitization from intermetallic phases during welding. In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure may have a CP in any of the following ranges: up to 800; up to 750; less than 750; up to 710; less than 710; up to 680; and 660-750.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure may be characterized by a Critical Pitting Temperature (CPT) and/or a Critical Crevice Corrosion Temperature (CCCT) within particular ranges. In certain applications, CPT and CCCT values may more accurately indicate corrosion resistance of an alloy than the alloy's PREN value. CPT and CCCT may be measured according to ASTM G48-11, entitled “Standard Test Methods for Pitting and Crevice Corrosion Resistance of Stainless Steels and Related Alloys by Use of Ferric Chloride Solution”. In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure has a CPT that is at least 45° C., or more preferably is at least 50° C., and has a CCCT that is at least 25° C., or more preferably is at least 30° C.
In various non-limiting embodiments, an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure may be characterized by a Chloride Stress Corrosion Cracking Resistance (SCC) value within a particular range. The concept of an SCC value is described in, for example, A. J. Sedricks, Corrosion of Stainless Steels (J. Wiley and Sons 1979). In various non-limiting embodiments, the SCC value of an alloy according to the present disclosure may be determined for particular applications according to one or more of the following: ASTM G30-97 (2009), entitled “Standard Practice for Making and Using U-Bend Stress-Corrosion Test Specimens”; ASTM G36-94 (2006), entitled “Standard Practice for Evaluating Stress-Corrosion-Cracking Resistance of Metals and Alloys in a Boiling Magnesium Chloride Solution”; ASTM G39-99 (2011), “Standard Practice for Preparation and Use of Bent-Beam Stress-Corrosion Test Specimens”; ASTM G49-85 (2011), “Standard Practice for Preparation and Use of Direct Tension Stress-Corrosion Test Specimens”; and ASTM G123-00 (2011), “Standard Test Method for Evaluating Stress-Corrosion Cracking of Stainless Alloys with Different Nickel Content in Boiling Acidified Sodium Chloride Solution.” In various non-limiting embodiments, the SCC value of an austenitic alloy that may be processed by a method and embodied in a forged article according to the present disclosure is high enough to indicate that the alloy can suitably withstand boiling acidified sodium chloride solution for 1000 hours without experiencing unacceptable stress corrosion cracking, pursuant to evaluation under ASTM G123-00 (2011).
The examples that follow are intended to further describe certain non-limiting embodiments, without restricting the scope of the present invention. Persons having ordinary skill in the art will appreciate that variations of the following examples are possible within the scope of the invention, which is defined solely by the claims.
The ESR ingot 64 was homogenized at 2225° F. for 48 hours, followed by ingot breakdown to about a 14-inch diameter workpiece 66 on a radial forge machine. The 14-inch diameter workpiece 66 was cut into a first workpiece 68 and a second workpiece 70 and processed as follows.
Samples of the 14-inch diameter second workpiece 70 were processed according to an embodiment of a method according to the present disclosure. Samples of the second workpiece 70 were reheated at 2225° F. for 6 to 12 hours and radial forged to a 9.84-inch diameter bar including step shaft 72 with a long end 74, and then water quenched. Step shaft 72 was produced during this radial forging operation to provide an end region on each forging 72,74 having a size that could be gripped by the workpiece manipulator for the open die press forge. Samples of the 9.84-inch diameter forgings 72,74 were annealed at 2150° F. for 1 to 2 hours and cooled to room temperature. Samples of the 9.84-inch diameter forgings 72,74 were reheated to 1025° F. for between 10 and 24 hours, followed by open die press forging to produce forgings 76. The forgings 76 were step shaft forgings, with the majority of each forgings 76 having a diameter of approximately 8.7 inches. Subsequent to open die press forging, the forgings were air cooled. Samples of the forgings 76 were reheated for between 3 to 9 hours at 1025° F. and radial forged to bars 78 having a diameter of approximately 7.25 inches. Test samples were taken from surface regions and central regions of the bars 78, in a middle section of the bars 78 between the bars' distal ends, and were evaluated for mechanical properties and hardness.
Samples of the 14-inch diameter first workpiece 68 were processed by a comparative method that is not encompassed by the present invention. Samples of the first workpiece 68 were reheated at 2225° F. for 6 to 12 hours, radial forged to 9.84-inch diameter workpieces 80, and water quenched. The 9.84-inch diameter forgings 80 were annealed at 2150° F. for 1 to 2 hours, and cooled to room temperature. The annealed and cooled 9.84-inch forgings 80 were reheated for 10 to 24 hours at 1025° F. or 1075° F. and radial forged to approximately 7.25-inch diameter forgings 82. Surface region and central region test samples for mechanical property evaluation and hardness evaluation were taken from the middle of each forging 82, between the distal ends of each forging 82.
Processing of other ingot heats were similar to those for Heat Number 49FJ-1,2, described above, except for the degree of warm working. The percent deformation and type of warm working used for other heats are shown in Table 3. Table 3 also compares the hardness profile across the 7.25-inch diameter forging 82 with that of the 7.25-inch diameter forging 78. As described above, the forgings 82 received only warm work radial forging at temperatures of 1025° F. or 1075° F. as a final processing step. In contrast, forgings 78 were processed using steps of warm work open press die forging at 1025° F., followed by warm work radial forging at 1025° F.
From Table 3, it is apparent that the difference in hardness from the surface to the center is significantly greater for the comparative samples than for the inventive samples. These results are consistent with the results shown in
Table 1, hereinabove, shows the room temperature tensile properties for the comparative heats having the hardness values disclosed in Table 3. Table 4 provides a direct comparison of room temperature tensile properties for Heat No. 49-FJ-4 for a comparative sample that was warm worked by press forging only, and for an inventive sample that was warm worked by press forging followed by radial forging.
The yield and ultimate tensile strengths at the surface of the comparative samples are greater than at the center. However, the ultimate tensile and yield strengths for the material processed according to the present disclosure (inventive sample) not only show that strength at the center of the billet and at the surface of the billet is substantially uniform, but also show that the inventive samples are considerably stronger than the comparative samples.
It will be understood that the present description illustrates those aspects of the invention relevant to a clear understanding of the invention. Certain aspects that would be apparent to those of ordinary skill in the art and that, therefore, would not facilitate a better understanding of the invention have not been presented in order to simplify the present description. Although only a limited number of embodiments of the present invention are necessarily described herein, one of ordinary skill in the art will, upon considering the foregoing description, recognize that many modifications and variations of the invention may be employed. All such variations and modifications of the invention are intended to be covered by the foregoing description and the following claims.
