US3320099A - Method of processing steel - Google Patents

Method of processing steel Download PDF

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US3320099A
US3320099A US389212A US38921264A US3320099A US 3320099 A US3320099 A US 3320099A US 389212 A US389212 A US 389212A US 38921264 A US38921264 A US 38921264A US 3320099 A US3320099 A US 3320099A
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steel
nitrogen
grains
aluminum
cold
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US389212A
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Anthony P Weber
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United States Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling

Definitions

  • This invention relates to a method of processing steel to produce a substantially non-aging ductile product. More particularly, the invention is directed to a treatment which produces a ductile steel having a fine-grained structure, i.e. a structure with a grain size not larger than ASTM No. 7, and which has a high yield strength.
  • Steel produced according to the invention possesses non-aging properties which permit long-term storage prior to usage without significant change in mechanical properties.
  • the steel is a cold reduced product and possesses a uniformity of thickness significantly better than hot rolled material.
  • the surface quality of the steel processed by my invention is very good and the surface is free of minute cracks or coil breaks such as are norm-ally found in hot rolled material. This steel is particularly useful as bumper stock material for automobiles.
  • Steel is processed according to my invention by adding a nitrogen-bearing compound to a melt of aluminumkilled, low carbon steel which has a carbon content of at least about 0.08%.
  • the nitrogen-bearing compound is added in an amount to provide a final nitrogen content in the steel of from 0.008 to 0.015% by weight, and the nitrogenized steel is then solidified.
  • Nitrogen in the steel is substantially completely dissolved by maintaining the steel at nitrogen dissolution temperature, preferably about 2200 F. or higher.
  • the steel is then hot rolled at a temperature above 1520 F. to achieve a partial reduction in thickness to the desired final gauge. After hot rolling, the steel is rapidly cooled to a temperature below 1100" F. to minimize precipitation of aluminum-nitride.
  • the steel may be pickled if desired and is then cold reduced to finishing thickness less the reduction to be accomplished in final temper rolling. Following cold reduction, the steel is annealed for a time sutficient to obtain a recrystallized elongated grain structure wherein the grains are not larger than ASTM No. 7 and to precipitate aluminum-nitride around the grains. The precipitated aluminum-nitride forms an envelope surrounding the grains and restricts growth of the grains during annealing. After annealing, the steel is temper rolled to increase the yield strength and produce the desired final mechanical properties.
  • a low carbon steel having 0.080.2% carbon, 0.6% manganese max. and 0.02% silicon max. is killed by adding aluminum to the steel melt while in the ladle.
  • the term killed refers to deoxidation of the metal until gas evolution is completed and the melt is quiescent.
  • Nitrogen is added to the steel for grain refinement and to improve the strength of the steel. It also has the efiect of increasing the work hardening rate so that the desired strength level, e.g. at least 35,000 p.s.i. yield strength, can be achieved with a small final reduction on the cold rolling mill (i.e. a small extension during temper rolling).
  • Nitrogen is preferably introduced to the steel by a nitrogenbearing compound, such as calcium cyanamide, which is added to the steel in an amount sufiicient to provide a final nitrogen content of between 0.008% to 0.015% by weight.
  • a nitrogenbearing compound such as calcium cyanamide
  • the amount of nitrogen in the steel is important since if too little is present, there will be insufiicient improvement in strength, and unduly large amounts of nitrogen will adversely affect the steels ductility.
  • the steel is subjected to a suflicient temperature to accomplish substantially complete dissolution of the nitrogen.
  • Significant nitrogen dissolution can occur above about 1500 F., but higher temperatures, e.g. above about 2200 F., are preferred because the dissolution rate is greater and substantially complete dissolution can be accomplished in a shorter time.
  • the steel is hot rolled to achieve a part of the total reduction in thickness required; however, hot rolling must be performed above about 1520 F. so that hot rolling can be completed without significant nitrogen precipitation. Following the fin-al hot rolling, the steel must be rapidly cooled from above the 1520 F. minimum hot working temperature to below about 1100 F. to retain the maximum amount of nitrogen in solution. It is necessary to cool quickly to below about 1100 F.
  • the steel is usually descaled by pickling to prepare it for subsequent cold reduction. After cleaning as desired, the steel is cold rolled to the finishing gauge, i.e. desired final thickness, less the reduction due to extension in temper rolling. Cold working the aluminum-killed steel elongates the grains and produces a typically flat, pancake-like, grain structure.
  • Cold rolling also fractures the grain structure formed during hot rolling and develops strain in the steel.
  • the steel is annealed following cold rolling to relieve the strains and to provide an elongated grain structure wherein the grains are not larger than ASTM No. 7.
  • aluminum nitride is precipitated at the grain boundaries and forms an envelope surrounding the grains which restricts grain growth during annealing so that the desirable small-grained structure is produced.
  • Grain size is usually determined by viewing a polished planar section which has been prepared in such a way as to delineate the grain boundaries.
  • the American Society for Testing Materials has established a standard grain size chart used in industry to standardize grain size descriptions.
  • the designation in the ASTM Chart range from 3 to 10 with the negative and smaller numbers referring to larger sizes.
  • the size of the grains is denoted by three measurements: (1) the number of grains/ in. of image at x magnification, (2) the number of grains/mmfi, and (3) the number of grains per cubic millimeter.
  • the designation of the coarsest grains in the chart, -3 refers to a structure in which there are 0.06 grains/in. of image at 100x magnification, one grain/mm. and/ or 0.7 grains per cubic millimeter.
  • the grain structure having ASTM No. 1 contains one grain/ in. of image at 100x magnification, 16 grains/mm. and 45 grains per cubic millimeter.
  • the grain structure of steel produced by my invention must have the grain size of not larger than ASTM No. 7, that is to say the grain structure must have an ASTM number of 7, 8, 9 or 10.
  • ASTM No. 7 that is to say the grain structure must have an ASTM number of 7, 8, 9 or 10.
  • This designation refers to a grain structure in which there are at least '64 grains/in. of image at 100x magnification, 1024 grains/mmF, and/ or 23,000 grains per cubic millimeter.
  • Annealing is preferably conducted "at above about 1200 F. to accomplish complete nitride precipitation relatively quickly.
  • the maximum aluminum-nitride precipitation occurs at approximately 1300 to 0 F. and at these temperatures only a few minutes is required for substantially complete precipitation Whereas above and below this temperature range more time is required to achieve complete precipitation.
  • the final processing step of my treatment is cold rolling f the steel to increase its yield strength and obtain the esired physical and mechanical properties.
  • Cold reduc- .on, i.e. temper rolling, to about a 2% extension of the teel beyond its original length is generally adequate to chieve a yield strength of at least about 35,000 p.s.i. he product produced as described above will have a uctility sufficiently high to enable obtaining a 32% miniium elongation in two inches.
  • the steel was rough olled to slabs.
  • the slabs were heated to a temperature etween 2200 to 2250 F. for two hours in which time 1e nitrogen was substantially completely dissolved.
  • the labs were then hot rolled on a continuous hot strip mill 3 a finishing temperature of 1560 F. In hot rolling, the lab thickness was reduced from 5.50 inches to a thickness f 0.187 inch.
  • the steel was then continuously pickled to :move hot rolling scale and rapidly cooled through the itrogen precipitation range to 1020 F. It was then cold :duced from 0.187 inch thick to 0.125 inch thick and oiled for box annealing.
  • the cold rolled steel was box nnealed at a minimum temperature of 1260 F.
  • the steel coil was removed from 1e box annealing furnace and after cooling to about 115 temper rolled to a 2% extension.
  • the product prouced had a yield strength greater than 35,000 p.s.i., and grain structure such that the grains were not larger than tSTM No, 7.
  • the material was ductile and was capable f a 35% elongation in two inches.
  • a method of processing steel to produce a substanally non-aging, ductile product comprising:

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Description

United States Patent Ofiice 3,320,099 Patented May 16, 1967 3,320,099 METHOD OF PROCESSENG STEEL Anthony P. Weber, Grifith, Ind, assignor to United States Steel Corporation, a corporation of Delaware No Drawing. Filed Aug. 12, 1%4, Ser. No. 389,212 4 Ciairns. (Cl. 1482) This invention relates to a method of processing steel to produce a substantially non-aging ductile product. More particularly, the invention is directed to a treatment which produces a ductile steel having a fine-grained structure, i.e. a structure with a grain size not larger than ASTM No. 7, and which has a high yield strength.
Steel produced according to the invention possesses non-aging properties which permit long-term storage prior to usage without significant change in mechanical properties. The steel is a cold reduced product and possesses a uniformity of thickness significantly better than hot rolled material. The surface quality of the steel processed by my invention is very good and the surface is free of minute cracks or coil breaks such as are norm-ally found in hot rolled material. This steel is particularly useful as bumper stock material for automobiles.
Steel is processed according to my invention by adding a nitrogen-bearing compound to a melt of aluminumkilled, low carbon steel which has a carbon content of at least about 0.08%. The nitrogen-bearing compound is added in an amount to provide a final nitrogen content in the steel of from 0.008 to 0.015% by weight, and the nitrogenized steel is then solidified. Nitrogen in the steel is substantially completely dissolved by maintaining the steel at nitrogen dissolution temperature, preferably about 2200 F. or higher. The steel is then hot rolled at a temperature above 1520 F. to achieve a partial reduction in thickness to the desired final gauge. After hot rolling, the steel is rapidly cooled to a temperature below 1100" F. to minimize precipitation of aluminum-nitride. The steel may be pickled if desired and is then cold reduced to finishing thickness less the reduction to be accomplished in final temper rolling. Following cold reduction, the steel is annealed for a time sutficient to obtain a recrystallized elongated grain structure wherein the grains are not larger than ASTM No. 7 and to precipitate aluminum-nitride around the grains. The precipitated aluminum-nitride forms an envelope surrounding the grains and restricts growth of the grains during annealing. After annealing, the steel is temper rolled to increase the yield strength and produce the desired final mechanical properties.
In the preferred practice of my process, a low carbon steel having 0.080.2% carbon, 0.6% manganese max. and 0.02% silicon max. is killed by adding aluminum to the steel melt while in the ladle. The term killed refers to deoxidation of the metal until gas evolution is completed and the melt is quiescent. Nitrogen is added to the steel for grain refinement and to improve the strength of the steel. It also has the efiect of increasing the work hardening rate so that the desired strength level, e.g. at least 35,000 p.s.i. yield strength, can be achieved with a small final reduction on the cold rolling mill (i.e. a small extension during temper rolling). Nitrogen is preferably introduced to the steel by a nitrogenbearing compound, such as calcium cyanamide, which is added to the steel in an amount sufiicient to provide a final nitrogen content of between 0.008% to 0.015% by weight. The amount of nitrogen in the steel is important since if too little is present, there will be insufiicient improvement in strength, and unduly large amounts of nitrogen will adversely affect the steels ductility.
After nitrogenizing and solidification, the steel is subjected to a suflicient temperature to accomplish substantially complete dissolution of the nitrogen. Significant nitrogen dissolution can occur above about 1500 F., but higher temperatures, e.g. above about 2200 F., are preferred because the dissolution rate is greater and substantially complete dissolution can be accomplished in a shorter time. The steel is hot rolled to achieve a part of the total reduction in thickness required; however, hot rolling must be performed above about 1520 F. so that hot rolling can be completed without significant nitrogen precipitation. Following the fin-al hot rolling, the steel must be rapidly cooled from above the 1520 F. minimum hot working temperature to below about 1100 F. to retain the maximum amount of nitrogen in solution. It is necessary to cool quickly to below about 1100 F. to preclude any significant precipitation of nitrogen. If the steel is not rapidly cooled, excessive precipitation of nitrogen will occur which will reduce the ductility. The steel is usually descaled by pickling to prepare it for subsequent cold reduction. After cleaning as desired, the steel is cold rolled to the finishing gauge, i.e. desired final thickness, less the reduction due to extension in temper rolling. Cold working the aluminum-killed steel elongates the grains and produces a typically flat, pancake-like, grain structure.
Cold rolling also fractures the grain structure formed during hot rolling and develops strain in the steel. The steel is annealed following cold rolling to relieve the strains and to provide an elongated grain structure wherein the grains are not larger than ASTM No. 7. During annealing, aluminum nitride is precipitated at the grain boundaries and forms an envelope surrounding the grains which restricts grain growth during annealing so that the desirable small-grained structure is produced.
Grain size is usually determined by viewing a polished planar section which has been prepared in such a way as to delineate the grain boundaries. The American Society for Testing Materials has established a standard grain size chart used in industry to standardize grain size descriptions. The designation in the ASTM Chart range from 3 to 10 with the negative and smaller numbers referring to larger sizes. The size of the grains is denoted by three measurements: (1) the number of grains/ in. of image at x magnification, (2) the number of grains/mmfi, and (3) the number of grains per cubic millimeter. The designation of the coarsest grains in the chart, -3, refers to a structure in which there are 0.06 grains/in. of image at 100x magnification, one grain/mm. and/ or 0.7 grains per cubic millimeter. The grain structure having ASTM No. 1 contains one grain/ in. of image at 100x magnification, 16 grains/mm. and 45 grains per cubic millimeter.
The grain structure of steel produced by my invention must have the grain size of not larger than ASTM No. 7, that is to say the grain structure must have an ASTM number of 7, 8, 9 or 10. This designation refers to a grain structure in which there are at least '64 grains/in. of image at 100x magnification, 1024 grains/mmF, and/ or 23,000 grains per cubic millimeter.
At annealing temperatures, there is a tendency for grains to increase in size. By effecting the nitride precipitation during annealing, the growth of the grains can be controlled and limited. Thus, whereas precipitation of nitrogen must be restricted during hot rolling, it is required subsequent to cold reduction to obtain the desired grain structure. Annealing is preferably conducted "at above about 1200 F. to accomplish complete nitride precipitation relatively quickly. The maximum aluminum-nitride precipitation occurs at approximately 1300 to 0 F. and at these temperatures only a few minutes is required for substantially complete precipitation Whereas above and below this temperature range more time is required to achieve complete precipitation.
The final processing step of my treatment is cold rolling f the steel to increase its yield strength and obtain the esired physical and mechanical properties. Cold reduc- .on, i.e. temper rolling, to about a 2% extension of the teel beyond its original length is generally adequate to chieve a yield strength of at least about 35,000 p.s.i. he product produced as described above will have a uctility sufficiently high to enable obtaining a 32% miniium elongation in two inches.
The following example illustrates the practice of the lvention to produce steel strip useful for many applica- .ons.
An aluminum-killed steel melt was nitrogenized by the ddition of sufiicient calcium cyanamide to produce a nal nitrogen content of 0.012% by weight. The steel .ad the following composition:
Percent f .10 In .48 .010 .020 1 .014 Iu .06 Ii .02 Zr .03 k1 .05 I .012
After solidification into ingots, the steel was rough olled to slabs. The slabs were heated to a temperature etween 2200 to 2250 F. for two hours in which time 1e nitrogen was substantially completely dissolved. The labs were then hot rolled on a continuous hot strip mill 3 a finishing temperature of 1560 F. In hot rolling, the lab thickness was reduced from 5.50 inches to a thickness f 0.187 inch. The steel was then continuously pickled to :move hot rolling scale and rapidly cooled through the itrogen precipitation range to 1020 F. It was then cold :duced from 0.187 inch thick to 0.125 inch thick and oiled for box annealing. The cold rolled steel was box nnealed at a minimum temperature of 1260 F. and naked for 20 hours. The steel coil was removed from 1e box annealing furnace and after cooling to about 115 temper rolled to a 2% extension. The product prouced had a yield strength greater than 35,000 p.s.i., and grain structure such that the grains were not larger than tSTM No, 7. The material was ductile and was capable f a 35% elongation in two inches.
I claim:
1. A method of processing steel to produce a substanally non-aging, ductile product comprising:
(A) adding to a melt of aluminum-killed steel which has a carbon content of at least 0.08%, not more than 0.6% manganese and not more than 0.02% silicon, a nitrogen-bearing compound in an amount to provide a final nitrogen content in the steel of from 0.008 to 0.015% by weight and then solidifying said melt,
(B) substantially completely dissolving said nitrogen in said steel by maintaining said steel at nitrogen-dissolution temperature,
(C) hot rolling said steel at a temperature above about (D) rapidly cooling the hot rolled steel to a temperature below about 1100" F. to minimize precipitation of aluminum-nitride and thereafter cold reducing said steel,
(E) annealing said cold reduced steel for a time sufficient to obtain a recrystallized, elongated grain structure wherein the grains are not larger than ASTM No. 7 and to precipitate aluminum-nitride around said grains whereby the growth of said grains during annealing is restricted by said aluminumnitride, and
(F) temper rolling to increase the yield strength of the steel.
2. A method according to claim 1 wherein said nitrogen is dissolved in said steel at a temperature of at least about 2200 F.
3. A method according to claim 1 wherein the cold reduced steel is annealed at a temperature in the range of about 1200 F, to 1300 F.
4. Amethod according to claim 1 wherein said steel is temper rolled to about a 2% extension to provide a yield strength of at least about 35,000 p.s.i. and an elongation of over 32% in 2 inches.
References Cited by the Examiner UNITED STATES PATENTS 2,444,788 7/ 1948 Reichenbach 148-2 3,028,270 4/1962 Morita et al 148143 3,163,565 12/1964 Wada 148143 3,178,279 4/1965 Nakamura -124 3,178,318 4/1965 Shimizu et a1 14812 X 3,180,726 4/1965 Nakamura 14812 X 3,239,390 3/1966 Matsukura et al. 14812 X 3,259,488 7/1966 Nakamura 14836 X FOREIGN PATENTS 808,556 2/1959 Great, Britain.
DAVID L. RECK, Primary Examiner,
CHARLES N. LQVELL, Examiner.

Claims (1)

1. A METHOD OF PROCESSING STEEL TO PRODUCE A SUBSTANTIALLY NON-AGING,DUCTILE PRODUCE COMPRISING: (A) ADDING TO A MELT OF ALUMINUM-KILLED STEEL WHICH HAS A CARBON CONTENT OF AT LEAST 0.08%, NOT MORE THAN 0.6% MANGANESE AND NOT MORE THAN 0.02% SILICON, A NITROGEN-BEARING COMPOUND IN AN AMOUNT TO PROVIDE A FINAL NITROGEN CONTENT IN THE STEEL OF FROM 0.00, TO 0.015% BY WEIGHT AND THEN SOLIDIFYING SAID MELT, (B) SUBSTANTIALLY COMPLETELY DISSOLVING SAID NITROGEN IN SAID STEEL BY MAINTAINING SAID STEEL AT NITROGEN-DISSOLUTION TEMPERATURE, (C) HOT ROLLING SAID STEEL AT A TEMPERATURE ABOVE ABOUT 1520*F., (D) RAPIDLY COOLING THE HOT ROLLED STEEL TO A TEMPERATURE BELOW ABOUT 1100*F. TO MINIMIZE PRECIPITATION OF ALUMINUM-NITRIDE AND THEREAFTER COLD REDUCING SAID STEEL, (E) ANNEALING SAID COLD REDUCED STEEL FOR A TIME SUFFICIENT TO OBTAIN A RECRYSTALLIZED, ELONGATED GRAIN STRUCTURE WHEREIN THE GRAINS ARE NOT LARGER THAN ASTM NO. 7 AND TO PRECIPITATE ALUMINUM-NITRIDE AROUND SAID GRAINS WHEREBY THE GROWTH OF SAID GRAINS DURING ANNEALING IS RESTRICTED BY SAID ALUMINUMNITRIDE, AND (F) TEMPER ROLLING TO INCREASE THE YIELD STRENGTH OF THE STEEL.
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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3513036A (en) * 1967-05-02 1970-05-19 Inland Steel Co Process for producing coiled,hotrolled,pickled steel strip
US3839095A (en) * 1971-03-27 1974-10-01 Nippon Kokan Kk Method of making a drawing steel sheet by continuous annealing process including shelf treatment therein
US3939013A (en) * 1969-02-03 1976-02-17 Youngstown Sheet And Tube Company Process for producing rimmed enameling steel

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2444788A (en) * 1945-02-21 1948-07-06 Carnegie Illinois Steel Corp Steel strip tempering
GB808556A (en) * 1954-05-17 1959-02-04 Mannesmann Ag A process for the heat treatment of an unalloyed or low-alloy structural steel containing from 0.03% to 0.12% of aluminium nitride
US3028270A (en) * 1958-08-25 1962-04-03 Yawata Iron & Steel Co Production of high tensile strength, high notch toughness steel by low temperature anneal
US3163565A (en) * 1961-06-22 1964-12-29 Yawata Iron & Steel Co Process for producing a tough steel for low temperatures
US3178279A (en) * 1961-05-16 1965-04-13 Ishikawajima Harima Heavy Ind Nitride bearing low-manganese ductile steel
US3178318A (en) * 1962-10-22 1965-04-13 Yawata Iron & Steel Co Process for producing nonageing super deep-drawing steel sheets
US3180726A (en) * 1960-03-31 1965-04-27 Ishikawajima Harima Heavy Ind Method for producing nitride-bearing low-carbon ductile steel
US3239390A (en) * 1961-04-12 1966-03-08 Yawata Iron & Steel Co Method of producing non-ageing special low carbon iron sheets
US3259488A (en) * 1960-03-31 1966-07-05 Ishikawajima Harima Heavy Ind Nitride-bearing low carbon ductile steels

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2444788A (en) * 1945-02-21 1948-07-06 Carnegie Illinois Steel Corp Steel strip tempering
GB808556A (en) * 1954-05-17 1959-02-04 Mannesmann Ag A process for the heat treatment of an unalloyed or low-alloy structural steel containing from 0.03% to 0.12% of aluminium nitride
US3028270A (en) * 1958-08-25 1962-04-03 Yawata Iron & Steel Co Production of high tensile strength, high notch toughness steel by low temperature anneal
US3180726A (en) * 1960-03-31 1965-04-27 Ishikawajima Harima Heavy Ind Method for producing nitride-bearing low-carbon ductile steel
US3259488A (en) * 1960-03-31 1966-07-05 Ishikawajima Harima Heavy Ind Nitride-bearing low carbon ductile steels
US3239390A (en) * 1961-04-12 1966-03-08 Yawata Iron & Steel Co Method of producing non-ageing special low carbon iron sheets
US3178279A (en) * 1961-05-16 1965-04-13 Ishikawajima Harima Heavy Ind Nitride bearing low-manganese ductile steel
US3163565A (en) * 1961-06-22 1964-12-29 Yawata Iron & Steel Co Process for producing a tough steel for low temperatures
US3178318A (en) * 1962-10-22 1965-04-13 Yawata Iron & Steel Co Process for producing nonageing super deep-drawing steel sheets

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3513036A (en) * 1967-05-02 1970-05-19 Inland Steel Co Process for producing coiled,hotrolled,pickled steel strip
US3939013A (en) * 1969-02-03 1976-02-17 Youngstown Sheet And Tube Company Process for producing rimmed enameling steel
US3839095A (en) * 1971-03-27 1974-10-01 Nippon Kokan Kk Method of making a drawing steel sheet by continuous annealing process including shelf treatment therein

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