Wrought chromium-containing cobalt-based alloys with improved resistance to galling and chloride-induced crevice corrosion.

Abstract

A chromium-containing cobalt-base alloy suitable for wrought processing has improved resistance to both chloride-induced crevice corrosion and galling. The alloy contains up to 3.545 wt.% nickel, 0.242-0.298 wt.% nitrogen, 22.0-30.0 wt.% chromium, 3.0-10.0 wt.% molybdenum, up to 5.0 wt.% tungsten, up to 7 wt.% iron, 0.5-2.0 wt.% manganese, 0.5-2.0 wt.% silicon, 0.02-0.11 wt.% carbon, and 0.005-0.205 wt.% aluminum, the balance being cobalt and impurities.

Description

[Technical Field]

[0001] The present invention relates to corrosion- and wear-resistant cobalt-based alloys. [Background technology]

[0002] Cobalt-based alloys containing chromium have been used in industry for over a century to solve wear problems under harsh conditions (i.e., in corrosive liquids and gases).

[0003] During this time, two main (wear-resistant) types evolved: one containing tungsten and a significant amount of carbon (about 1-3% by weight), and the other containing molybdenum but with a much lower carbon content. The former alloys have a significant amount of carbides in the microstructure, high bulk hardness, and excellent resistance to low-stress (abrasive) wear, but low ductility. The latter alloys have only small amounts, if any, of carbides. As a result, they are not as hard, but are more ductile and corrosion-resistant.

[0004] A related group of chromium-containing cobalt-based alloys, designed primarily for high strength at high temperatures and for use in flight gas turbine engines, deserves mention, as they have also evolved from the aforementioned materials.

[0005] Despite common belief, bulk hardness is not necessarily a good measure of general wear resistance. In fact, there are modes of wear that are controlled more by the properties of the cobalt-rich matrix (rather than by the presence of carbides in the microstructure); these modes include galling (high load / low velocity metal-to-metal sliding), cavitation erosion (caused by bubble collapse near the surface in turbulent liquids), and droplet erosion.

[0006] Regarding the patent history of chromium-containing cobalt-base alloys, the first such alloy was described in U.S. Pat. No. 6,269,492 (December 17, 1907) by Elwood Haynes. U.S. Pat. No. 6,269,492 (April 1, 1913) by the same inventor claimed an alloy of cobalt, chromium, and tungsten, paving the way for the evolution of the first major type (associated with the STELLITE trademark). The earliest U.S. patent disclosing the second major type of chromium-containing cobalt-base alloy was U.S. Pat. No. 6,269,492 (May 15, 1934) by Charles H. Prange, which describes such an alloy for use as a cast denture.

[0007] These early alloys were typically used in cast or welded overlay form. Wrought and powder metallurgy (P / M) versions of some alloys became available in the mid-20th century.

[0008] To understand the role of various alloying elements in cobalt-based alloys, it is important to have knowledge of the changes that can occur in the atomic structure of pure cobalt and its many alloys. At temperatures below approximately 420°C / 788°F, the stable atomic structure of pure cobalt is hexagonal close-packed (HCP). At higher temperatures (up to the melting point), it is face-centered cubic (FCC). Elements such as nickel, iron, and carbon (within their limited solubility ranges) are known to lower the transition (or transformation) temperature, i.e., extend the temperature range of the FCC structure. Conversely, elements such as chromium, molybdenum, and tungsten increase the transition temperature (TT), i.e., extend the temperature range of the HCP structure.

[0009] The thermal transformation of cobalt and its alloys from HCP to FCC and vice versa is slow; therefore, these materials tend to exhibit a metastable FCC morphology at or near room temperature upon cooling from the molten state or after periods exceeding the TT. However, application of mechanical stress at temperatures below the TT can rapidly form HCP regions within the metastable FCC structure. These regions have the appearance of platelets (during metallographic examination) and are believed to arise from the coalescence of stacking faults within the metastable FCC structure. The driving force behind this stress-induced metastable FCC to HCP transformation at a given temperature is governed by the TT (i.e., the higher the TT, the greater the tendency).

[0010] It is known that the TT has a significant effect on the wear behavior of cobalt and its alloys. This is due to the rapid work hardening that occurs when HCP platelets are formed under mechanical stress, which is an important attribute for resistance to plastic deformation. Chromium, molybdenum, and tungsten are therefore known to be beneficial to wear resistance (especially resistance to galling, cavitation erosion, and droplet erosion). Conversely, nickel, iron, and (at low levels within their solubility range) carbon would ostensibly be detrimental to wear resistance.

[0011] Chromium, molybdenum, and tungsten also contribute to the resistance of such materials to aqueous corrosion. As with stainless steels and nickel-based alloys, chromium forms a passive film (a protective surface film) in oxidizing acidic solutions, while molybdenum and tungsten make cobalt and its alloys noble in reducing solutions where the cathodic reaction is hydrogen evolution.

[0012] The most relevant prior art to the present invention is U.S. Patent No. 5,629,499 (March 26, 1991), inventors of which are Paul Crook, Aziz I. Asphahani, and Steven J. Matthews. The commercial embodiment of this patent is known as ULTIMET alloy. U.S. Patent No. 5,629,499 (March 26, 1991) discloses a cobalt-based alloy containing significant amounts of chromium, nickel, iron, molybdenum, tungsten, silicon, manganese, carbon, and nitrogen. The unexpected benefits of carbon (enhanced by the presence of similar amounts of nitrogen) were found with respect to both cavitation erosion resistance and corrosion resistance. Furthermore, the effect of nickel on cavitation erosion was found to be insignificant, at least in the 5.3-9.8 wt.% content range. The experimental wrought materials used in Crook et al.'s findings were produced by vacuum induction melting, electroslag remelting, hot forging and hot rolling (to sheet and plate), and subsequent solution treatment. Interestingly, a maximum nitrogen content of 0.12 wt. % was claimed due to the fact that a higher content of 0.19 wt. % caused cracking problems during wrought processing.

[0013] A study of the relevant prior art revealed chromium-containing cobalt-based alloys specifically designed for use in powder metallurgy processing and biomedical applications. One example, described in U.S. Patent No. 5,623,666, has chromium and molybdenum contents similar to those of the ULTIMET alloy (a commercial embodiment of U.S. Patent No. 5,623,666) and the alloys of the present invention. However, tungsten is not included, and a special relationship between carbon and nitrogen is required. More importantly, U.S. Patent No. 5,623,666 requires that aluminum (along with other oxide-forming metals such as magnesium, calcium, yttrium, lanthanum, titanium, and zirconium) be kept at very low levels (i.e., these elements combined should not exceed approximately 0.01% by weight). [Prior art documents] [Patent documents]

[0014] [Patent Document 1] U.S. Patent No. 873,745 [Patent Document 2] U.S. Patent No. 1,057,423 [Patent Document 3] U.S. Patent No. 1,958,446 [Patent Document 4] U.S. Patent No. 5,002,731 [Patent Document 5] U.S. Patent No. 5,462,575 Summary of the Invention [Problem to be solved by the invention]

[0015] The material properties to which this discovery pertains are resistance to galling and crevice corrosion. Galling is a term used for damage caused by metal-on-metal sliding under very heavy loads and without lubrication. It is characterized by gross plastic deformation of one or both surfaces, bonding between the surfaces, and (in most cases) the transfer of material from one surface to the other. Most stainless steels are particularly susceptible to this form of wear and tend to seize completely under galling test conditions.

[0016] Chloride-induced crevice corrosion occurs in crevices or narrow gaps between structural components, or under surface deposits, in the presence of chloride-containing solutions. Attack is associated with the local buildup of positive charge and the attraction of negatively charged chloride ions into the crevice, followed by the formation of hydrochloric acid. This acid accelerates the attack, and the process becomes autocatalytic. Crevice corrosion testing is also a good indicator of chloride-induced pitting corrosion resistance. [Means for solving the problem]

[0017] We have discovered that the combination of a relatively low nickel content and a relatively high nitrogen content significantly enhances the galling and chloride-induced crevice corrosion resistance of a chromium-bearing cobalt-base wrought alloy containing nickel, iron, molybdenum, tungsten, silicon, manganese, aluminum, carbon, and nitrogen. The positive effect on crevice corrosion resistance of reducing the nickel content to 3.17 wt.% and further to 1.07 wt.% was completely unexpected, as was the fact that alloys with nitrogen contents up to 0.278 wt.% could be readily hot-forged and hot-rolled into wrought products at these lower nickel contents. [Brief explanation of the drawings]

[0018] [Figure 1] Graph of crevice corrosion and galling test results reported in Table 2. DETAILED DESCRIPTION OF THE INVENTION

[0019] The experimental alloys relevant to this discovery were prepared by vacuum induction melting (VIM) followed by electroslag remelting (ESR) to produce ingots of material suitable for hot working. Prior to hot working (i.e., hot forging and hot rolling), the ingots were homogenized at 1204°C / 2200°F. Based on previous experience with this class of alloys, a hot working start temperature of 1204°C / 2200°F was used for all experimental alloys. Annealing tests indicated that a solution annealing temperature of 1121°C / 2050°F was suitable for this class of materials, followed by rapid cooling / quenching (to produce a metastable FCC solid solution structure at room temperature). Annealed sheets 3.2 mm / 0.125 in. thick were produced to enable the fabrication of crevice corrosion test samples. Annealed plates 25.4 mm / 1 in. thick were produced to enable the fabrication of galling test pins and blocks. Two batches of alloy 1 and two batches of alloy 3 were produced because one batch had insufficient material for both types of testing.

[0020] The actual (analyzed) compositions of the experimental alloys are shown in Table 1. [Table 1]

[0021] The experimental procedures performed during this study were as follows. 1. An experimental version of the commercial embodiment of the '481 patent (Alloy 1) is melted and tested using the same melting, hot working, and testing procedures intended for all other experimental alloys. Two batches were required to produce all the required samples. 2. Melt and test a reduced nickel (approximately 3 wt%) version (Alloy 2) with all other elements at Alloy 1 levels. 3. A version (Alloy 3) with increased nitrogen (about 0.25 wt%), about 3 wt% nickel, and all other elements at Alloy 1 level was melted and tested. Two batches were required to produce all the required samples. 4. A version (Alloy 4) with further reduced nickel (approximately 1 wt%), nitrogen at approximately 0.25 wt%, and all other elements at Alloy 1 level is melted and tested. 5. Melt and test a version (Alloy 5) with intermediate nickel (about 5 wt%), nitrogen about 0.25 wt%, and all other elements at Alloy 1 level. 6. A version (Alloy 6) with more nitrogen (about 0.35 wt%), about 3 wt% nickel, and all other elements at Alloy 1 level is melted and tested. 7. Also, a melted version (Alloy 7) with more nitrogen (about 0.40 wt%), about 3 wt% nickel, and all other elements at Alloy 1 level is tested. 8. Melt and test a version (Alloy 8) in which all elements except nickel (about 3 wt%) and nitrogen (about 0.10 wt%) are at the lower end of the range of the commercial embodiment of the '661 patent. A version (Alloy 9) in which all elements except nickel (about 3 wt%) and nitrogen (about 0.40 wt%) are at the upper end of the ranges of the commercial embodiments of the '661 patent is melted and tested.

[0022] It should be noted that the higher the nitrogen content of the experimental alloys, the higher their chromium content. This was not intentional, but is likely due to the higher recovery of chromium during melting of the material. This may be related to the use of a "chromium nitride" charge material as a means of adding nitrogen.

[0023] It was also found that the actual nitrogen contents were generally higher than the target nitrogen contents during this study. For example, the target nitrogen content for Alloy 1 and Alloy 2 was 0.08 wt%, while the actual contents were 0.114 (Alloy 1, Batch A), 0.127 (Alloy 1, Batch B), and 0.109 wt% (Alloy 2). These variations are due to unexpectedly higher nitrogen recovery rates during VIM / ESR melting and remelting of the alloys.

[0024] Aluminum was added to the experimental alloys to react with and remove oxygen during primary melting (in a laboratory VIM furnace). In addition to its function as a deoxidizer, aluminum is very important in production-scale air melting, where it is used to maintain the very high temperatures required during argon oxygen decarburization (AOD). Manganese was added to aid in the removal of sulfur during melting, at levels suggested in U.S. Patent No. 6,229,949. The silicon and carbon contents used in the alloys of this invention are similar to those claimed in U.S. Patent No. 6,229,949. Such contents have provided excellent weldability over the intervening years. The benefits of carbon addition at these contents, namely, excellent cavitation erosion and corrosion resistance, are described in U.S. Patent No. 6,229,949. The two benefits of chromium, molybdenum, and tungsten with respect to resistance to certain forms of wear and corrosion are discussed in the Background section of this specification, and all three of these elements were kept (during this study) within the same approximate ranges claimed in U.S. Patent No. 6,229,949. Iron is also added to the alloys of the present invention within the ranges claimed in the '661 patent, the main advantage of which is the tolerance of iron-contaminated scrap material in the furnace charge, with significant economic benefits.

[0025] The key additions to the wrought cobalt-base alloys described herein are nickel and nitrogen. As previously noted, the most significant and surprising finding of this work was the strong positive impact on chloride-induced crevice corrosion resistance of reducing the nickel content to 3.17 wt.% or less in the commercial embodiments of the '660 patent. Furthermore, in view of the prior art (particularly the '660 patent), it was unexpected that alloys having nitrogen contents greater than about 0.12 wt.% could be readily processed into wrought products. This suggests that lower nickel contents may have a positive impact on the wrought properties of these high-nitrogen alloys.

[0026] The fact that the three alloys (6, 7, and 9) with the highest nitrogen contents (0.367, 0.415, and 0.413 wt.%, respectively) cracked during forging may imply that the solubility of nitrogen was exceeded, resulting in the presence of one or more additional phases within the microstructure of the hot ingot. If the nitrogen content of these alloys were reduced to a content within the range of 0.262–0.278 wt.% for Alloys 3(A), 3(B), and 4 (plus or minus the normal manufacturing tolerance of nitrogen of 0.02 wt.%), these modified Alloys 6, 7, and 9 would likely not crack.

[0027] Regarding the effects of decreasing nickel content on galling resistance, these appear to be non-linear (not predicted by current wear theory), and indeed only at nickel contents up to 3.17 wt. % did the galling resistance exceed that of Alloy 1 (the commercial embodiment of US Pat. No. 5,629,999, but with a slightly increased nitrogen content due to the melting variations mentioned above).

[0028] Melting these alloys under large-scale production conditions requires not only a target content for each element, but also a practical range, given variations due to elemental segregation in cast (real-time) analytical samples, variations due to secondary melting (e.g., ESR), and variations due to chemical analysis. To accommodate these variations, the "plus or minus" tolerances during melting for each intentional addition in the commercial embodiment of the '661 patent are as follows: chromium: ±1.5 wt.%, nickel: ±1.25 wt.%, molybdenum: ±0.5 wt.%, tungsten: ±0.5 wt.%, iron: ±1 wt.%, manganese: ±0.25 wt.%, silicon: ±0.2 wt.%, aluminum: ±0.075 wt.%, carbon: ±0.02 wt.%, and nitrogen: ±0.02 wt.%. The balance, cobalt, does not require such tolerances. For cobalt-based alloys with lower nickel content than the commercial embodiment of the '661 patent (eg, HAYNES 6B alloy), the nickel tolerance is plus or minus 0.375 wt. %.

[0029] Although testing was performed on the wrought form of the composition, improved resistance to chloride-induced crevice corrosion and galling is also present in other product forms, including cast, welded, and powdered products (for powder metallurgy processing, additive manufacturing, thermal spraying, and welding).

[0030] Test results The crevice corrosion test used in this study was that described in ASTM Standard G48, Method D. It included sheet samples with dimensions of 50.8 x 25.4 x 3.2 mm / 2 x 1 x 0.125 in. and fitted with a TEFLON® crevice assembly. Method D allows for the determination of a material's critical crevice temperature (CCT), i.e., the lowest temperature at which crevice attack is observed over a (continuous) 72-hour period in a solution of 6 wt.% ferric chloride and 1 wt.% hydrochloric acid. The ASTM standard does not address the equipment (i.e., autoclave) required for testing at higher temperatures, so the test temperature in this study was limited to 100°C / 212°F.

[0031] To differentiate the experimental alloys under conditions conducive to galling, a modern laser-based 3D surface measurement system was employed to study the wear scars, along with galling test hardware and procedures established in 1980. These procedures involved rotating a pin (15.9 mm / 0.625 in diameter) ten times through a 121° arc against a fixed block (12.7 mm / 0.5 in thick) using a hand-cranked back and forth motion. A load of 2722 kg / 6000 lb was applied by a tension unit (compression mode) and a (greased) ball bearing seated in a female cone machined into the top of the pin.

[0032] Galling tests included self-matching samples (i.e., pin and block made of the same material) and laser-based high-precision measurements of the root-mean-square (RMS) roughness of the block scratches.

[0033] All tests associated with this study were repeated under identical conditions. The RMS values ​​shown in Table 2 are the average of two galling tests. The CCT values ​​shown in Table 2 are the lowest temperatures at which crevice attack was observed, regardless of whether one or both samples showed attack at that temperature.

[0034] A higher CCT indicates better resistance to chloride-induced crevice corrosion, while a lower RMS indicates better resistance to galling during (self-bonding) high-load / low-speed metal-to-metal sliding. [Table 2]

[0035] The results in Table 2 are presented in graphical form in Figure 1.

[0036] Table 3 includes broad and preferred ranges for chromium, iron, molybdenum, tungsten, silicon, manganese, and carbon in the alloys disclosed in U.S. Patent No. 6,223,269. Because the alloys of the present invention are derived from commercial embodiments of U.S. Patent No. 6,223,269, any alloy having amounts of chromium, iron, molybdenum, tungsten, silicon, manganese, and carbon within the ranges disclosed in U.S. Patent No. 6,223,269, along with up to 3.17 wt. % (plus a normal manufacturing tolerance of 0.375 wt. %) nickel, 0.262-0.278 wt. % nitrogen (plus or minus a normal manufacturing tolerance of 0.02 wt. %), and 0.08-0.13 wt. % (plus or minus a normal manufacturing tolerance of 0.075 wt. %) aluminum, would be expected to have the same improved resistance to galling and chloride-induced crevice attack as the test alloys disclosed herein. [Table 3]

[0037] The above manufacturing tolerances / tolerances can be applied to the amounts of chromium, iron, molybdenum, tungsten, silicon, manganese, carbon, and aluminum in the test alloys of the present invention to determine the acceptable ranges for these elements in the alloys of the present invention. Also, alloys having up to 3.545 wt.% nickel and 0.242-0.298 wt.% nitrogen are expected to have similar improved resistance to galling and chloride-induced crevice attack when the chromium, iron, molybdenum, tungsten, silicon, manganese, and carbon contents are the same as those claimed in U.S. Patent No. 5,002,731.

[0038] While presently preferred embodiments of the alloys of the present invention have been described, it is to be understood that the invention is not so limited and can be variously embodied within the scope of the following claims.

Claims

1. 1. A chromium-containing cobalt-based alloy suitable for wrought processing, having improved resistance to both chloride-induced crevice corrosion and galling, comprising: Nickel present in an amount up to 3.545 wt.%; 0.242 to 0.298 wt. % nitrogen; 22.0 to 30.0 wt. % chromium; 3.0 to 10 wt. % molybdenum; tungsten present in an amount up to 5.0 wt. %; 1.71 to 7 wt. % iron; 0.05 to 2.0 wt. % manganese; 0.05 to 2.0 wt. % silicon; 0.02 to 0.11 wt. % carbon; 0.005 to 0.205 wt. % aluminum; A chromium-containing cobalt-based alloy, the balance being cobalt and impurities.

2. 1.07 to 3.17 wt. % nickel; 27.96 to 28.12 wt. % chromium; 4.90 to 6.84 wt. % molybdenum; 2.04 to 2.26 wt. % tungsten; 2.71 to 2.92 wt. % iron; 0.77 to 0.90 wt. % manganese; 0.24 to 0.29 wt. % silicon; 0.058 to 0.067 wt. % carbon; 0.262 to 0.278 wt. % nitrogen; 0.08 to 0.13 wt. % aluminum; 2. The chromium-containing cobalt-base alloy of claim 1, wherein the balance consists of cobalt and impurities.

3. 0.695 to 3.545 wt. % nickel; 26.46 to 29.62 wt. % chromium; 4.40 to 7.34 wt. % molybdenum; 1.54 to 2.76 wt. % tungsten; 1.71 to 3.92 wt. % iron; 0.52 to 1.15 wt. % manganese; 0.04 to 0.49 wt. % silicon; 0.038 to 0.087 wt. % carbon; 0.242 to 0.298 wt. % nitrogen; 0.005 to 0.205 wt. % aluminum; 2. The chromium-containing cobalt-base alloy of claim 1, wherein the balance consists of cobalt and impurities.

4. Nickel present in an amount up to 3.545 wt.%; 0.242 to 0.298 wt. % nitrogen; 24.0 to 27.0 wt. % chromium; 4.5 to 5.5 wt. % molybdenum; 1.5 to 2.50 wt. % tungsten; 2.0 to 4.0 wt. % iron; 0.5 to 1.0 wt. % manganese; 0.30 to 0.50 wt. % silicon; 0.04 to 0.08 wt. % carbon; 0.005 to 0.205 wt. % aluminum; 2. The chromium-containing cobalt-base alloy of claim 1, wherein the balance consists of cobalt and impurities.

5. 10. The chromium-containing cobalt-base alloy of claim 1, wherein the alloy is in a form selected from the group consisting of wrought products, castings, weldments, and powder products.

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