Abstract: A crackable forging steel with excellent machinability and low ductility consisting of (by weight percent): 0.6-0.75 carbon, 0.25-0.5 manganese, 0.04-0.12 sulfur, and the remainder essentially iron except for up to about 1.2% residual impurities selected from the group consisting of phosphorous, silicon, nickel, vanadium, copper, chromium, and molybdenum, the manganese/sulfur ratio being greater than 3.0 and the microstructure of said alloy being substantially 100% pearlite with a grain size grade between 3-8 according to ASTM Specification E112-88.A method of making a connecting rod with such steel comprising: (a) forging a rod of such steel; (b) cooling the forging to ensure essentially a 100% pearlitic microstructure and a grain size of 3-8 ASTM per Specification E112-88; (c) fracturing the rod into cap and body portions; (d) reassembling by use of bolts which have a clearance no greater than 0.04 inch to guide the fractured surfaces to within 0.

Abstract: A method of cracking bearing assembles including the steps of (a) forming a ductile metal (steel, aluminum or titanium) connecting rod in one piece (e.g., by hot forging) having an annular wall defining a crankshaft opening with preformed surface crevices for guiding the initiation of a cracking plane that extends across the crank opening; (b) charging (i.e., for about 40 seconds) the region of such wall along at least one portion of the cracking plane with hydrogen by means of an electrolytic cell or by means of reacting the metal rod with a strong acid (e.g., concentrated sulfuric) to cause hydrogen to dissolve in the metal to facilitate hydrogen stress cracking thereat, with or without the imposition of static mechanical tensile loading at such crevices (i.e., for about 40 seconds) of a magnitude insufficient to cause yielding of the metal; and (c) prolonging, increasing, or imposing the static mechanical loading (i.e.

Abstract: An alloy steel composition is disclosed which has characteristics of (a) enhanced resistance to hardness degradation under high temperatures and/or enhanced resistance to sliding wear and contact fatigue under conditions of poor lubrication, (b) ease of softening for formability and machinability, and (c) ease of heat treating for hardening with austenitizing (or carburizing) at a temperature of 950.degree.-960.degree. C. and tempering at a temperature at or below 600.degree. C. The composition comprises essentially, by weight, carbon--0.15-0.30%, Mo--2.0-3.5%, V--0-0.45%, Cr--0-0.75%, Mn--0.25-0.50%, Si--0.15-0.35%, and remainder Fe.

Abstract: A method of making ductile cast iron with a matrix of acicular ferrite and bainite is disclosed. A melt by weight of 3.0-3.6% carbon, 3.5-5.0% silicon, 0.7-5.0% nickel, 0-0.3% Mo, >0.015% S, >0.06% P (remainder Fe) is subjected to a nodularizing agent and solidified. The iron is then heat treated by heating to 1575.degree.-1650.degree. F. for 1-3 hours, quenched to 400.degree.-775.degree. F. at a rate of at least 275.degree. F./min., held for 0.5-4 hours, and cooled to room temperature. The resulting ductile iron exhibits a yield strength of at least 80 ksi, a tensile strength of at least 140 ksi, elongation of at least 6%, and a hardness of at least 270 BHN.

Abstract: A method of strengthening ferritic ductile iron castings while maintaining ductility at a high level is disclosed. An iron alloy melt is cast consisting essentially of by weight 3.9-6.0% Si, 3.0-3.5% C, 0.1-0.3% Mn, 0-0.35% Mo, at least 1.25% Ni, no greater than 0.015% S and 0.6% P, the remainder Fe, the melt having been subjected to a nodularizing agent to form graphite nodules upon solidification. The cast alloy is heat treated to provide a fully ferritic microstructure with 9-14% by volume graphite, a yield strength of at least 75,000 psi, a tensile strength of at least 95,000 psi, and an elongation of at least 17%.

Abstract: A method of developing compressive residual stresses in the surface region of a high carbon steel alloy article is disclosed. The article is made of an alloy having 0.8-1.6% C, 0.2-5% Cr, 0-20% ingredients selected from the group consisting of M.sub.N, V, Mo, W, Si, and the remainder Fe. The article is heated in a carburizing atmosphere at 800.degree.-950.degree. C. for 1-2.5 hours, and then quenched to cool the central core of the article at a rate sufficiently fast to suppress the formation of non-martensitic austenite decomposition products, thereby establishing a residual compressive stress gradient proceeding from the surface to a depth of 0.007-0.03 inches.

Abstract: A method of nitriding metal parts is disclosed. A preferred mode requires burying the metal part to be treated in a body of vermiculite or other porous media containing urea or other suitable nitriding agent. Prior to burying, a controlled amount of an aqueous solution of the nitriding agent is absorbed into dry vermiculite; the water of the solution is removed by evaporation leaving a pasty substance coating or impregnating the grains of the vermiculite. The pasty substance coating each vermiculite grain physically forms a thin film on the external particle surface and on the surfaces of its internal porosity; the average film thickness is less than 0.001 inch. The vermiculite bearing the nitriding agent and buried part are heated in a closed container to a temperature at which the agent decomposes at a predetermined slow rate and releases gases bearing nitrogen. Heating is continued for about 4-8 hours at 700.degree.-1300.degree. F (preferably 925.degree.-1050.degree.

Abstract: A method (and resulting product) for preparing bearing components is disclosed. Utilizing a low alloy steel shape containing carbon in the range of 0.6-1.5% and containing alloying ingredients in the range of 1-2% selected from the group consisting of Cr, Mn, Ni, Cu and Mo (and preferably the ingredients of SAE 52100 steel), the steel shape is subjected sequentially to a spheroidizing-anneal heat treatment, a rough forming treatment, and a hardening-heat treatment. Immediately prior to the hardening-heat treatment, a fine bainitic or preferably pearlitic microstructure is established having relatively thin carbide films at prior austenite grain boundaries. Austenitizing of said pearlitic or bainitic microstructure is carried out at a temperature in the range of 1625.degree.-1675.degree. F for a period of time preferably between 15 seconds and one-half hour, but operationally for a period of time as short as 5 seconds and as long as 1 hour.