Patent Application
20100230015
The invention relates to steel alloys, and more particularly, to steel alloys having ultra-high strength and high toughness with acceptable cost of production.
AerMet® 100, disclosed in U.S. Pat. Nos. 5,087,415 and 5,268,044, which are incorporated by reference herein and made part hereof, is a commercial ultra-high-strength, non-stainless steel which does not require case hardening. The nominal composition of AerMet 100 is 13.4 Co, 11.1 Ni, 3.1 Cr, 1.2 Mo, 0.23 C, and balance Fe, in wt %. AerMet 100 shows a suitable combination of high strength and fracture toughness for aircraft parts and ordnance. Additionally, AerMet 100 shows an ambient 0.2% yield stress of 1720 MPa and a Rockwell C-scale hardness of 53.0-54.0, with KIc of 126 MPa√m. However, the alloying elements Co and Ni are rather costly, increasing the overall steel cost and constraining applications. Thus, there has developed a need for a steel with similar mechanical properties as AerMet 100 at a significantly lower cost.
HY180, disclosed in U.S. Pat. No. 3,502,462, which is incorporated by reference herein and made part hereof, is a commercial high-strength, non-stainless steel which does not require case hardening. The nominal composition of HY180 is 10 Ni, 8 Co, 2 Cr, 1 Mo, 0.13 C, 0.1 Mn, 0.05 Si, and balance Fe, in wt %. While the material cost of HY180 is lower than AerMet 100, due to the lower Co addition, the ambient 0.2% yield stress of HY180 is limited to 1240 MPa.
U.S. Pat. No. 5,358,577, which is incorporated by reference herein and made part hereof, discloses a high strength, high toughness stainless steel with a nominal composition of 12-21 Co, 11-15 Cr, 0.5-3.0 Mo, 0-2.0 Ni, 0-2.0 Si, 0-1.0 Mn, 0.16-0.25 C, at least one element selected from the group consisting of 0.1-0.5 V and 0-0.1 Nb, and balance Fe, in wt %. This alloy shows an ambient Ultimate Tensile Strength (UTS) of 1720 MPa or greater and an ambient 0.2% yield stress of 1190 MPa or greater. However, the ambient 0.2% yield stress of this alloy is limited to about 1450 MPa, and furthermore, the material cost is high due to the high Co addition.
Alloys disclosed in U.S. Pat. Nos. 7,160,399 and 7,235,212, which are incorporated by reference herein and made part hereof, display ultra-high-strength, corrosion-resistant steels which do not require case hardening. The nominal composition of one alloy taught by the patents, branded as Ferrium S53®, is 14.0 Co, 10.0 Cr, 5.5 Ni, 2.0 Mo, 1.0 W, 0.30V, 0.21 C, and balance Fe, in wt %. Ferrium S53® exhibits an ambient UTS of about 1980 MPa and an ambient 0.2% yield stress of about 1560 MPa. The Kic of Ferrium S53® is limited to about 72 MPa√m, and the material cost is high due to the high Co addition.
U.S. Pat. No. 6,176,946, which is incorporated by reference herein and made part hereof, discloses a class of steel alloys comprising a case hardened mixture with a core composition of 15-28 Co, 1.5-9.5 Ni, 0.05-0.25 C, and one or more additives selected from 3.5-9 Cr, less than 2.5 Mo, and less than 0.2 V and the balance Fe, in wt %. The mixture taught by the patent is case hardened in the range of surface hardness greater than a Rockwell C-scale hardness of 60. The class of steel alloys taught by the patent is thus distinct from AerMet 100, in that it requires case hardening and also targets a much higher surface hardness. In addition, the material cost for the class of steel alloys taught by the patent is high due to the high Co addition.
The present alloy provides advantages such as ultra-high strength coupled with lower amounts of certain elements to thereby achieve lower cost. A full discussion of the features and advantages of the present invention is deferred to the following detailed description, which proceeds with reference to the accompanying drawings.
Aspects of the invention relate to a steel alloy that includes, in combination by weight: about 0.20% to about 0.33% carbon, about 4.0% to about 8.0% cobalt, about 7.0 to about 11.0% nickel, about 0.8% to about 3.0% chromium, about 0.5% to about 2.5% molybdenum, about 0.5% to about 5.9% tungsten, about 0.05% to about 0.20% vanadium, and up to about 0.02% titanium, the balance essentially iron and incidental elements and impurities.
According to one aspect, the alloy includes, in combination by weight, about 0.25% to about 0.31% carbon, about 6.8% to about 8.0% cobalt, about 9.3 to about 10.5% nickel, about 0.8% to about 2.6% chromium, about 0.9% to about 2.1% molybdenum, about 0.7% to about 2.0% tungsten, about 0.05% to about 0.12% vanadium, and up to about 0.015% titanium, the balance essentially iron and incidental elements and impurities. In another aspect, the alloy includes, in combination by weight, about 0.29% to about 0.31% carbon, about 6.8% to about 7.2% cobalt, about 9.8 to about 10.2% nickel, about 0.8% to about 2.6% chromium, about 0.9% to about 2.1% molybdenum, about 0.7% to about 1.4% tungsten, about 0.05% to about 0.12% vanadium, and up to about 0.015% titanium, the balance essentially iron and incidental elements and impurities.
According to another aspect, the alloy is strengthened at least in part by M2C carbide precipitates, where M includes one or more elements selected from the group consisting of: Cr, Mo, W, and V.
According to a further aspect, the alloy has a predominately lath martensite microstructure.
According to a still further aspect, the alloy has an ultimate tensile strength of at least about 1900 MPa, and a KIC fracture toughness of at least about 110 MPa√m.
Additional aspects of the invention relate to a method for processing a steel alloy that includes, in combination by weight, about 0.20% to about 0.33% carbon, about 4.0% to about 8.0% cobalt, about 7.0 to about 11.0% nickel, about 0.8% to about 3.0% chromium, about 0.5% to about 2.5% molybdenum, about 0.5% to about 5.9% tungsten, about 0.05% to about 0.20% vanadium, and up to about 0.02% titanium, the balance essentially iron and incidental elements and impurities. The method includes subjecting the alloy to a solutionizing heat treatment at 950° C. to 1100° C. for 60-90 minutes and then to a tempering heat treatment at 465° C. to 550° C. for 4-32 hours.
According to one aspect, the alloy includes, in combination by weight, about 0.25% to about 0.31% carbon, about 6.8% to about 8.0% cobalt, about 9.3 to about 10.5% nickel, about 0.8% to about 2.6% chromium, about 0.9% to about 2.1% molybdenum, about 0.7% to about 2.0% tungsten, about 0.05% to about 0.12% vanadium, and up to about 0.015% titanium, the balance essentially iron and incidental elements and impurities. In another aspect, the alloy includes, in combination by weight, about 0.29% to about 0.31% carbon, about 6.8% to about 7.2% cobalt, about 9.8 to about 10.2% nickel, about 0.8% to about 2.6% chromium, about 0.9% to about 2.1% molybdenum, about 0.7% to about 1.4% tungsten, about 0.05% to about 0.12% vanadium, and up to about 0.015% titanium, the balance essentially iron and incidental elements and impurities.
According to another aspect, the method includes quenching the alloy after the solutionizing heat treatment, and air cooling the alloy after the tempering heat treatment.
According to a further aspect, the method further includes subjecting the alloy to a cryogenic treatment between the solutionizing heat treatment and the tempering heat treatment.
According to a still further aspect, the alloy has a resultant predominately lath martensite microstructure and includes M2C carbide precipitates, where M includes one or more elements selected from the group consisting of: Cr, Mo, W, and V.
Other features and advantages of the invention will be apparent from the following specification taken in conjunction with the following drawings.
In the detailed description which follows, reference will be made to the drawings comprised of the following figures:
While this invention is susceptible of embodiments in many different forms, exemplary embodiments of the invention are referenced in the drawings and will herein be described in detail with the understanding that the present disclosure is to be considered as an exemplification of the principles of the invention and is not intended to limit the broad aspect of the invention to the embodiments illustrated.
According to embodiments of the present invention, a steel alloy is provided that includes an alloying addition of Co that is lower than that of AerMet 100 and other alloying additions that include W and V. The lower Co content of the invented steel can reduce the thermodynamic driving force of M2C formation. However, the M2C formation during tempering assists in obtaining increased strength. The addition of elements such as W and V can assist in achieving a sufficient driving force of M2C formation to obtain the desired strength. Embodiments of the alloy can be processed so that the alloy comprises a predominantly lath martensitic matrix and is strengthened by a fine-scale distribution of M2C carbides. In one embodiment, the M2C carbides measure less than about 20 nm in the longest dimension and comprise the alloying elements of Mo, Cr, W, and V.
In the embodiment described in
In one example embodiment, an alloy is provided that includes (in wt. %) about 0.20% to about 0.33% carbon (C), about 4.0% to about 8.0% cobalt (Co), about 7.0 to about 11.0% nickel (Ni), about 0.8% to about 3.0% chromium (Cr), about 0.5% to about 2.5% molybdenum (Mo), about 0.5% to about 5.9% tungsten (W), about 0.05% to about 0.20% vanadium (V), and up to about 0.02% titanium (Ti), the balance being essentially iron (Fe) and incidental elements and impurities.
In another embodiment, the alloy includes, in combination by weight, about 0.25% to about 0.31% carbon, about 6.8% to about 8.0% cobalt, about 9.3 to about 10.5% nickel, about 0.8% to about 2.6% chromium, about 0.9% to about 2.1% molybdenum, about 0.7% to about 2.0% tungsten, about 0.05% to about 0.12% vanadium, and up to about 0.015% titanium, the balance essentially iron and incidental elements and impurities.
In yet another embodiment, the alloy comprises, in combination by weight, about 0.29% to about 0.31% carbon, about 6.8% to about 7.2% cobalt, about 9.8 to about 10.2% nickel, about 0.8% to about 2.6% chromium, about 0.9% to about 2.1% molybdenum, about 0.7% to about 1.4% tungsten, about 0.05% to about 0.12% vanadium, and up to about 0.015% titanium, the balance essentially iron and incidental elements and impurities.
As stated above, the alloy is strengthened at least in part by M2C metal carbides. In various embodiments, the alloy may contain metal carbides where M is one or more elements selected from the group consisting of Mo, Cr, W, and V, and may have amounts of each element (if present) decreasing in the order listed, i.e., Mo in the largest concentration, followed by Cr, W, and/or V. In other embodiments, the alloy may contain different amounts of these elements.
Alloys as described herein can be processed in a variety of different manners. In one embodiment, illustrated in
Several example embodiments of alloys according to the invention are described below. Table I lists the measured compositions of each alloy embodiment discussed in the Examples below, along with the nominal composition of commercial steel AerMet 100.
Each of the alloy embodiments in Table I was subjected to processing steps such as those described in
A 300-lb vacuum induction melt of alloy A was prepared from high purity materials. The melt was converted to a 3-inch-round-corner-square bar. The alloy was subjected to a solutionizing heat treatment at 1025° C. for 90 minutes, quenched with oil, immersed in liquid nitrogen for 2 hours, warmed in air to room temperature, and then the samples were each subjected to one of several different tempering heat treatments identified in Table II below and cooled in air. The amounts of Ni and C of alloy A served to place the martensite start temperature (Ms) above about 200° C., and Ms was confirmed for this alloy as 222° C., using dilatometry. Transmission electron microscopy and atom probe tomography verified the presence of M2C, along with grain refining carbides in specimens tempered at 525° C. for 12 hours or 550° C. for 4 hours. The Charpy V-Notch (CVN) impact energy at −40° C. and tensile strength at room temperature were measured for various tempering conditions, using two samples per each condition. These results are also shown in Table II.
The ultimate tensile strength (UTS), KIC fracture toughness, and Rockwell-C hardness were also measured for samples of alloy A.
Additionally, samples of alloy A were tested for stress corrosion cracking resistance (KISCC) at various applied electrical potentials, using the ASTM F1624/F1940 Standard Test Method for Measurement of Hydrogen Embrittlement in Steel by Incremental Loading Technique. Twelve specimens of alloy A were compared to twelve specimens of AerMet 100, and the results of such testing are shown in
A 300-lb vacuum induction melt of alloy B was prepared from high purity materials. The melt was converted to a 3-inch-round-corner-square bar. The alloy was subjected to a solutionizing heat treatment at 1025° C. for 90 minutes, quenched with oil, immersed in liquid nitrogen for 2 hours, and warmed in air to room temperature, and then the samples were each subjected to one of several different tempering heat treatments identified in Table IV below and cooled in air. The amounts of Ni and C of alloy B served to place Ms above about 200° C., and Ms was confirmed for this alloy as 286° C. using dilatometry. The CVN impact energy at −40° C. and tensile strength at room temperature were measured for various tempering conditions, using two samples per each condition. These results are also listed in Table IV.
The ultimate tensile strength (UTS) and KIC fracture toughness were also measured for samples of alloy B, as indicated in
A 300-lb vacuum induction melt of alloy C was prepared from high purity materials. The melt was converted to a 3-inch-round-corner-square bar. The alloy was subjected to a solutionizing heat treatment at 1025° C. for 90 minutes, quenched with oil, immersed in liquid nitrogen for 2 hours, and warmed in air to room temperature, and then the samples were each subjected to one of several different tempering heat treatments identified in Table V below, and cooled in air. The amounts of Ni and C of alloy C served to place Ms above about 200° C., and Ms was confirmed for this alloy as 247° C. using dilatometry. The CVN impact energy at −40° C. and tensile strength at room temperature were measured for various tempering conditions, using two samples per each condition. These results are also listed in Table V.
Alloy C was found to have mechanical characteristics comparable to those of AerMet 100, and the optimum tempering heat treatment in this experiment was found to be 510° C. for 16 hours, although other heat treatments were found to produce positive results.
A 300-lb vacuum induction melt of alloy A was prepared from high purity materials. The melt was converted to a 3-inch-round-corner-square bar. The alloy was subjected to a solutionizing heat treatment at 950° C. for 60 minutes, quenched with oil, immersed in liquid nitrogen for 1 hour, and warmed in air to room temperature, and then subjected to a tempering heat treatment at 468° C. for 32 hours or at 482° C. for 16 hours and cooled in air. The CVN impact energy at −40° C., fracture toughness KIC at room temperature, and tensile strength at room temperature were measured for various tempering conditions. The results of this testing are listed in Table VI below.
Alloy D was found to have mechanical characteristics comparable to those of AerMet 100, and neither of the tempering heat treatments in this experiment were found to be comparatively optimum, as both heat treatments were found to produce positive results.
The various embodiments of alloys described herein, processed in the manners described herein, were found to have a comparable or even superior physical properties compared to existing alloys, such as AerMet 100. In particular, the alloy was found to be capable of providing a desirable combination of high tensile strength and high fracture toughness, a robust design which tolerates slight variations in tempering conditions, and the unexpected benefit of enhanced stress corrosion cracking resistance. Additionally, the comparatively smaller alloying additions of Co and Ni reduce the cost of the alloy as compared to existing alloys, such as AerMet 100. It is understood that further benefits and advantages are readily recognizable to those skilled in the art.
Several alternative embodiments and examples have been described and illustrated herein. A person of ordinary skill in the art would appreciate the features of the individual embodiments, and the possible combinations and variations of the components. A person of ordinary skill in the art would further appreciate that any of the embodiments could be provided in any combination with the other embodiments disclosed herein. It is understood that the invention may be embodied in other specific forms without departing from the spirit or central characteristics thereof. The present examples and embodiments, therefore, are to be considered in all respects as illustrative and not restrictive, and the invention is not to be limited to the details given herein. Accordingly, while the specific embodiments have been illustrated and described, numerous modifications come to mind without significantly departing from the spirit of the invention and the scope of protection is only limited by the scope of the accompanying claims.
This application claims priority to and the benefit of U.S. Provisional Application Ser. No. 61/029,970, filed Feb. 20, 2008, entitled “High Strength and Tough Structural Steel With Secondary Hardening Strengthening Carbides,” and U.S. Provisional Application Ser. No. 61/098,037, filed Sep. 18, 2008, entitled “High Strength and Tough Structural Steel With Secondary Hardening Strengthening Carbides,” each of which is incorporated herein by reference and made part hereof.
Activities relating to the development of the subject matter of this invention were funded at least in part by United States Government, Picatinny Arsenal Contract Number DAAE30-01-9-0800-00 and the Naval Air Warfare Center Contract Number N68335-07-C-0302, and thus may be subject to license rights and other rights in the United States.
| Number | Date | Country | |
|---|---|---|---|
| 61029970 | Feb 2008 | US | |
| 61098037 | Sep 2008 | US |
