HIGH NICKEL CHROMIUM ALLOY

Abstract: An oxidation resistant nickel-chromium based alloy possessing good stress rupture characteristics at elevated temperature and consisting essentially of; 55 to 65% nickel 19 to 28% chromium 0,75 to 2% aluminium 0,2 to 1% titanium 0,035 to 0,1% nitrogen up to about 0,1% carbon up to 1% each of silicon, molybdenum, manganese and niobium up to 0,1% boron the balance essentially iron.

Description: The subject invention is directed to a high nickel-chromium-iron alloy, and more particularly to a Ni-Cr-Fe alloy of special chemistry and micro-structure such that it is capable of affording a desired combination of properties at elevated temperatures upwards of 2000°F (1093°C) under oxidizing conditions. Since at least the early 50's the demand has been incessant for economical materials capable of performing satisfactorily under increasingly severe operating conditions, notably temperature. For example, and by way of illustration, in the ceramic tile industry frit-firing temperatures have been on the increase in an effort to accomodate new frits and higher furnace loads, this to remain competitive in the market-place. Initially, various manufacturers of furnace rollers for this application used an alloy containing roughly 0.04% C, 0.25% Si, 0.25% Mn, 22.75% Cr, 0.4% Ti, 0.01% Nb, 1.35% Al, 59.5% Ni, 0.35% Co, 0.03% N, 0.001% 0₂, balance iron, the alloy being produced from ingots melted in an air induction furnace. The rollers lasted up to roughly 18 months at 2060°F (1127°C), ultimately failing from oxidation-enhanced stress-rupture failure with fracture being intergranular. More recently, the rollers have been produced from electric-arc furnace melted, argon-oxygen decarburized (AOD) refined ingots. The composition used differed somewhat from the above, a typical composition being approximately 0.03%C, 0.3% Si, 0.3% Mn, 22.5% Cr, 0.4% Ti, 0.02% Nb, 1.27% Al, 60.8% Ni, 0.08% Co, 0.29% Mo. 0.015% N, less than 0.001% 0₂, balance iron and impurities. At 2050°F (1121°C) rollers lasted some 12 months and at times longer. However, at 2130°F (1165°C) such rollers manifested failure in 2 months or less. From our investigation of the problem it would appear that failure is caused by a rather dramatic change in microstructure as temperature is increased. This was not initially or readily apparent since our first approach was to increase the levels of aluminum and chromium to enhance oxidation behavior. But this was not a panacea. In any case, extensive experimentation reflects that circa 2150°F (1177°C), and above there is a lack of microstructural control of grain size. It would appear that the M₂₃C₆ carbide, stabilized by silicon and molybdenum, but consisting mainly of chromium, begins to redissolve into the matrix. This frees the grain boundaries to migrate under applied stress and results in coarse or massive grains, e.g., one to three grains across the wall thickness, 0.080 in. (2.0mm), of the rollers. This can be viewed, at least in part, as failure induced by the alternating tensile and compressive stresses set up in the rollers as a consequence of temperature and time. Actually, many grain boundaries appear to be perpendicular to the roller surface and serve as sites for preferential grain boundary oxidation attack which, in turn, leads to premature grain boundary rupture. It has now been found that the oxidation resistance of alloys of the type above-discussed can be improved by a controlled addition and retention of nitrogen as discussed infra. Put another way, it has been discovered that the microstructure of the alloys of the type under consideration, notably grain size, can be controlled or rendered relatively structurally stable over extended periods at elevated temperature through a microalloying addition of nitrogen. Generally speaking and in accordance with the present invention, the alloy contemplated herein contains 19 to 28% chromium, 55 to 65% nickel, 0.75 to 2% aluminum, 0.2 to 1% titanium, from 0.1 to 1% silicon, up to 1% each of molybdenum, manganese and niobium, up to 0.1% carbon, from 0.035 to 0.1% (e.g. 0.04 to 0.08%) nitrogen and up to 0.01% or even 0.1% boron, up to 0.1% calcium and up to 0.1% magnesium, the balance, apart from impurities, being iron. A preferred alloy contains 21 to 25% Cr, 58 to 63% Ni, 1 to 2% Al, 0.3 to 0.7% Ti, 0.1 to 0.6% Si and optionally 0.1 to 0.8% Mo, up to 0.6% Mn, up to 0.4% Nb, 0.02 to 0.1% c, 0.04 to 0.08% N, with iron being the balance. Nitrogen plays a major role in effectively enhancing oxidation resistance. It combines with titanium to form approximately 0.15 to 0.8% of titanium nitride, depending upon the stoichiometry of the nitride. This level of titanium nitride pins the grain size at temperatures as high as 2192°F (1200°C). Put another way, the presence of nitrogen/nitride increases the temperature capability over conventionally used materials by some 135°F (75°C) or more. Below about 0.04% nitrogen (0.17% stoichiometric titanium nitride) there would appear to be insufficient precipitate to pin the grain boundaries. Above about 0.08% (non-stoichiometric titanium nitride) the alloy tends to become gassy, difficult to manufacture and difficult to weld. Apart from the foregoing advantage of this microalloy addition, stress-rupture life is increased, thus permitting furnace operators to increase load-bearing capacity at temperature without a detrimental sacrifice in roller life. In carrying the invention in practice, care should be exercised in achieving proper composition control. Nickel contributes to workability and fabricability as well as imparting strength and other benefits. Aluminum and chromium confer oxidation resistance but if present to the excess lend to undesirable microstructural phases such as sigma. Little is gained with chromium levels much above 28% or aluminum levels exceeding 2%. Carbon need not exceed 0.1% to minimize the formation of excess carbides. A level of about 0.1 to 0.5% Cr₂₃C₆ aids strength to about 2057°F (1125°C). Silicon and molybdenum stabilize the carbide phase. In this regard the presence of 0.1 to 0.6% silicon with or without 0.1 to 0.8% molybdenum is advantageous. Titanium acts as a malleabilizer as well as serving to form the grain boundary pinning titanium nitride phase. Niobium will further stabilize the nitride phase and from 0.05 to 0.4% is beneficial. Manganese is preferably held to low levels, preferably not about 0.6%, since higher percentages detract from oxidation resistance. Up to 0.006% boron may be present to aid malleability. Calcium and/or magnesium in amounts, say up to 0.05 or 0.1%, are useful for deoxidation and malleabilization. Iron comprises essentially the balance of the alloy composition. This allows for the use of standard ferroalloys in melting thus reducing cost. As to other constituents, sulphur and phosphorus present as impurities should be maintained at low levels, e.g., up to 0.015% sulphur and up to 0.02 or 0.03% phosphorus. Copper can be present as an impurity. In terms of processing, conventional air melting procedures may be used, including the employment of induction furnaces. However, vacuum melting and refining can be employed where desired. Preferably the alloy is electric-arc furnace melted, AOD refined and electroslag remelted (ESR) for (a) uniform distribution of the nitrides (b) better nitrogen content control, and (c) to maximize yield. In this connection, the nitrogen can be added to the AOD refined melt by means of a nitrogen blow just prior to pouring the ingot to be ESR melted. The alloy is, as a practical matter, non age-hardenable or substantially non age-hardenable, and is comprised essentially of a stable austenitic matrix virtually free of detrimental quantities of subversive phases. For example, upon heating for prolonged periods, say 300 hours, at temperatures circa 1100°F (593°C) to 1400°F (760°C) metallographic analysis did not reveal the presence of the sigma phase. The following information and data are given to afford those skilled in the art a better perspective as to the nature of the alloy herein abovedescribed: A series of alloys (Table I) were melted in an air induction furnace (Alloys C, E and 2) or in an electric-arc furnace (Alloys A, B and D), then AOD refined and ESR remelted. Ingots were broken down to approximately 70 mm (0.280 inch) hot bands which were then cold rolled in coils to approximately 2 mm (0.080in) thickness with two intermediate anneals at 2050°F (1121°C). Sheet specimens were annealed at about 2150°F (1177°C) prior to test. A metallographic examination was then conducted upon exposing each alloy for either 16 hour increments at 2012°F (1100°C) and 2192°F (1200°C) or 100 hour increments at 2130°F (1165°C) to measure grain growth versus time at various temperatures. The data are reported in Table II. Alloys A through C are low nitrogen compositions with varying carbon content. Although increasing carbon content progressively inhibited grain growth, it was ineffective in controlling grain size for long periods of time above about 1100°C (2010°F). Increasing the nitrogen level resulted in several beneficial attributes, as shown by the titanium-containing Alloy 2 of the invention. The uniform dispersion of nitride resulted in stabilization of the grain size and longer stress rupture lives at elevated temperature. The oxidation resistance of alloys within the invention was also improved (surprisingly) as measured by the reduction of the denuded zone beneath the surface scale. The nitrogen levels of Alloys D and E were also beneficial in comparison with A, B and C, but it is deemed that Alloy D would not perform as well as Alloys E and 2 over prolonged periods, as is indicated by the data in Table II. Alloys A and B were fabricated into 26.9 mm diameter (1.06 in) x 2438.4mm (96 in.) rollers using 2.0 mm (0.08 in.) gauge sheets and then field tested in an actual furnace operating at 1165°C (2130°F). Both alloys failed by stress rupture in a short time. Alloy C was hot worked into a solid bar 26.9 mm (1.06 in.) diameter and in field operation for 6 days. The average grain size was 300 µm. after exposure, with grains as large as 1500 µm. The stress rupture life of an alloy similar to alloy A at 1177°C (2150°F) and 6.89 MPa (1 Ksi) was 308 hours. Alloys E and 2 (and also Alloy D) were fabricated similarly and exposed to the same thermal conditions as alloys A through C. (Alloys D, E and 2 are intermediate carbon content compositions with increasing nitrogen levels). The beneficial effect of increasing nitrogen content on grain size stability is demonstrated by the data in Table II. Rollers were fabricated from Alloy 2 (and also D) as described for Alloys A and B and are currently in field service without incident. Alloy E was fabricated into a solid roller as described for Alloy C. This alloy (1) was tested in field service at 1165°C (2130°F) for 8 days and then metallographically evaluated for grain size. The grain size was 300 µm after exposure and 50 µm prior to exposure. The stress rupture life of an alloy composition similar to Alloy 1 at 1177°C (2150°F) and 6.89 MPa (1Ksi) was 507 hours. This increase in stress rupture life over, for example, alloy A demonstrates a contribution to strength by the nitrogen addition. Likewise alloy D was stress rupture tested at 1090°C (2000°F) and 13.78 MPa (2Ksi) along with an alloy similar to Alloy C. The times to failure were a maximum of 224 and 157 hours, respectively. Again, the contribution to strength by the nitrogen addition was noted. In manufacturing the furnace rollers, all the above alloys were autogeneously welded using tungsten-arc argon-shielded welding procedures. No difficulties in welding were encountered. However, at higher than 0.08% nitrogen welding problems might ensue. As indicated herein, electric-arc furnace melting, AOD refining with a nitrogen blow, followed by ESR remelting of the alloy is the preferred manufacture route over air induction furnace melting of the ingots because of improved yield to final product and because of the better dispersion of the nitrides. An additional and unexpected benefit of the nitrogen additions is a marked reduction of the depth of the denuded zone (depletion of chromium and aluminum contents) as the nitrogen content is increased. Table III shows the depth of the denuded zone for alloys C, D and 2. This dramatic increase in resistance to alloy depletion in the base alloy is attributed to the effect of nitrogen on grain size retention and concomitantly on oxide scale density and tenacity. EFFECT OF NITROGEN ON THE DEPTH OF THE DENUDED ZONE AFTER 600 HOURS AT 1165°C (2130°F) Alloy Depth of Denuded Zone (µm) C 1230 D 300 2 150 Given the foregoing, including the data in Tables I, II and III it will be noted that the subject invention provide nickel chromium alloys which afford a combination of desirable metallurgical properties including (1) good oxidation resistance at elevated temperatures (2) high stress-rupture lives at such temperatures, and (3) a relatively stable microstructure. The alloys are characterized by (4) a substantially uniform distribution of titanium nitrides (TiN) throughout the grains and grain boundaries. The nitrides are stable in the microstructure up to near the melting point provided at least 0.04% nitrogen is present. A nitrogen level down to 0.035% might be satisfactory in certain instances. This is in marked contrast to the M₂₃C₆ type of carbide which tends to go back into solution at around 2125-2150°F (1163-1177°C) whereupon nothing remains to control grain size. It is to advantage that (5) the grain size not exceed about 380 µm, preferably being not more than, 300 µm the size of the grains being uniform outwardly to the alloy surface. While the alloy of the present invention has been described in connection with the behavior of rollers in furnaces for frit production, the alloy is also deemed useful for heating elements, ignition tubes, radiant tubes, combustor components, burners, heat exchangers, furnace fixtures, mufflers, belts, etc. The metal and ceramic process industries, chemical manufactures and the petroleum and petrochemical processing industries are illustrative of industries in which the alloy of the invention is deemed particularly useful. Although the present invention has been described in conjunction with preferred embodiments, it is to be understood that it is not limited thereto.

Claims: A high nickel-chromium alloy characterised by (a) enhanced resistance to oxidation at elevated temperature, (b) good stress rupture life at such temperatures, and (c) a controlled grain size, said alloy consisting of 55 to 65% nickel, 19 to 28% chromium, 0.75 to 2% aluminum, 0.2 to 1% titanium, 0.035% to 0.1% nitrogen, up to 0.1% carbon, from 0.1 to 1% of silicon, up to 1% each of molybdenum, manganese and niobium and up to 0.1% boron, up to 0.1% calcium and up to 0.1% magnesium, the balance, apart from impurities, being iron. An alloy according to claim 1 containing 58 to 63% nickel, 21 to 25% chromium, 1 to 2% aluminum, 0.3 to 0.7% titanium, 0.1 to 0.6% silicon and optionally 0.1 to 0.8% molybdenum, up to 0.6% manganese, up to 0.4% niobium, 0.02 to 0.1% carbon and 0.04 to 0.08% nitrogen. An alloy according to claim 1 or claim 2 containing molybdenum. An alloy according to claim 1 containing 61.17% nickel, 23.89% chromium, 1.51% aluminum, 0.37% titanium, 0.08% nitrogen, 0.04% carbon, 0.32% silicon, 0.23% molybdenum, and 0.29% manganese, the balance, apart from impurities, being iron. An alloy according to any preceding claim containing at least one of calcium and magnesium. A wrought article or part made from an alloy according to any preceding claim, having a relatively stable microstructure having titanium nitrides substantially uniformly distributed throughout the grains and grain boundaries and with the average grain size not exceeding about 380 µm. The use of an alloy according to any one of claims 1 to 5 for articles and parts requiring good resistance to oxidation and rupture under stress for prolonged periods at temperatures exceeding 1093°C. A furnace roller formed from an alloy according to any one of claims 1 to 5.

Inventors: GANESAN, PASUPATHY, SMITH, GAYLORD, TASSEN, CURTIS STEVEN, WHEELER, JACK MILTON
Applicants: INCO ALLOYS INTERNATIONAL, INC.
Application year: 1987
Main classification: C22C19
IPC codes: C22C19