US3865645A - Cold-rolled steel sheet for press-forming - Google Patents

Cold-rolled steel sheet for press-forming Download PDF

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Publication number
US3865645A
US3865645A US319017A US31901772A US3865645A US 3865645 A US3865645 A US 3865645A US 319017 A US319017 A US 319017A US 31901772 A US31901772 A US 31901772A US 3865645 A US3865645 A US 3865645A
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steel sheet
percent
cold
temperature
steel
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Expired - Lifetime
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US319017A
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English (en)
Inventor
Nobuyuki Takahashi
Kenitiro Suemune
Shuji Nagata
Tatumi Tomozoe
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Nippon Steel Corp
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Nippon 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling

Definitions

  • the present invention relates to a cold-rolled steel sheet for press-forming, manufactured by a continuous annealing.
  • cold-rolled steel sheets are used as such parts of automobiles as cold-formed by a drawing working, for instance, rear fendemfront fender and door inner, for which an excellent drawing workability is required.
  • cold-rolled steel sheets having such an excel lent drawing workability there are used at present an aluminum-killed low carbon steel containing 0.03 to 0.07 wt. percent carbon and 0.02 to 0.08 wt. percent acid-soluble aluminum and further a cold-rolled titani um-added extremely low carbon steel sheet, in which the drawing workability is not influenced by a rate of heating of an annealing and is superior to the aluminum-killed low carbon steel sheet, due to the fixation of carbon and nitrogen by titanium.
  • this aluminum-killed low carbon steel sheet is almost annealed in the state of a tight coil or of an open coil by using a box annealing furnace.
  • a box annealing has following disadvantages: a long time is required for annealing, the productivity is low and a uniform heating of the whole coil or of the interior of the furnace is not obtainable for a constructional reason, whereby a uniform material quality over the whole length of coil can not be achieved.
  • a titanium-added extremely low carbon steel sheet has a disadvantage that its production cost becomes higher than that of an aluminum-killed low carbon steel, because the former contains about 0.1 wt. percent titanium.
  • a continuous annealing to be conducted in a continuous annealing furnace.
  • a continuous annealing has following advantages: the productivity is high for reason of construction; a uniformity of material qualities through one coil and that between coils are obtained; and a uniform contact between the surface of a steel sheet and atmosphere gas within the furnace is secured.
  • the continuous annealing can not be freed from disadvantages: that is, on account of a rapid heating and a short soaking time crystal grains are refined in general, and on account of a high rate of cooling subsequent to the annealing carbon contained in the steel can not sufficiently precipitate as carbide so that the continuously annealed steel is high in yield stress and tensile strength, but low in breaking elongation and n-value and great in aging property as compared with a boxannealed steel material. Therefore, the former is inferior to the latter in the press-formability. Therefore, the continuous annealing treatment is usually not applied to the production of a cold-rolled steel sheet for pressforming, but iiiahiyfor' the production of steel sheet to be used as material for producing tin plate.
  • the object of the present invention is to produce a cold-rolled steel sheet having an excellent pressformability when subjected to a continuous annealing.
  • Another object of the present invention is to provide a cold-rolled steel sheet having an excellent press-formability by the application of an overaging treatment of a continuous annealing system.
  • a still another object of the present invention is to provide a cold-rolled steel having always an excellent drawing workability without being influenced by a rate of cooling subsequent to a hot-rolling and a coiling temperature by subjecting the said steel to a vacuum degassing treatment to reduce the C content to 0.001 to 0.009 percent.
  • the attached drawing shows influences of silicon contents on changes in properties of steel materials, when subjecting aluminum-killed low carbon steel sheets having different silicon contents to an overaging treatment of the continuous annealing.
  • the steel sheet of the present invention is a coldrolled steel sheet having an excellent press-formability, said steel consisting of less than 0.08 wt. percent carbon, 0.05 to 0.4 wt. percent manganese, 0.015 to 0.10 wt. percent silicon, 0.01 to 0.1 wt. percent acid-soluble aluminum, 0.003 to 0.015 wt. percent nitrogen and the rest being iron and unavoidable impurities.
  • the carbon content of the steel sheet of the present invention is the same as that of a cold-rolled low carbon steel of the SPCC class (cold-rolled steel sheet in general) or the SPCD class (cold-rolled steel sheet for drawing) prescribed by G 3141 of the 11s. It is not particularly necessary to reduce the carbon content for mitigating the hardening aging. However, in case properties of the same degree as of a titanium-added extremely low carbon steel sheet is required for the steel sheet of the present invention its carbon content is reduced to 0.001 to 0.009 wt. percent by subjecting the steel to a vacuum degassing treatment.
  • Manganese Mangan must be contained for the purpose of preventing a brittle rupture caused by sulfur at the time of hot-rolling.
  • an aluminum-killed steel prepared by melting in a converter contains usually sulfur in an amount of more than 0.005 percent
  • the manganese content must be more than 0.05 percent in order to fix the above-mentioned amount of sulfur.
  • the upper limit thereof is made 0.4
  • Silicon is contained usually in an amount of less than 0.01 percent in a cold-rolled steel sheet refined in a steel making furnace prescribed in G 3141 of the HS.
  • the silicon content is necessary to be in an amount of more than 0.015 percent, preferably more than 0.02 percent, in order to obtain properties of a steel sheet for pressforming (of SPCD class of HS) by a continuous annealing comprising an overaging treatment, without being influenced by conditions of production steps (for instance, hot-rolling condition) prior to the cold-rolling.
  • the silicon content exceeds 0.1 percent, the strength of the steel sheet is increased to a degree more than required, whereby the workability is deteriorated. Therefore, the upper limit thereof is made 0.1 percent.
  • the F-value can not be liberated from the dependency on the heating rate of annealing, even if the carbon content is in the range of from 0.001 to 0.009 percent, as specified by the present invention.
  • the object of the present invention it is necessary to contain an acid-soluble aluminum in an amount of more than 0.01 percent.
  • the lower limit of the acid-soluble aluminum desirable to prevent the occurance of stretcher strain caused by oxides contained in the steel is defined to be 0.02 percent.
  • the upper limit thereof is made 0.1 percent.
  • the co-presence of three components that is, silicon, aluminum and nitrogen
  • nitrogen is necessary to be contained in an amount of more than 0.003 percent.
  • the upper limit thereof is made 0.015 percent.
  • the prerequisite conditions for achieving the object of the present invention is the limitation of four basic chemical components: carbon, silicon, aluminum and nitrogen, for reasons asabove-mentioned.
  • the steel sheet of the present invention is manufactured by the steps of refining a molten steel in a steelmaking furnace such as converter, open hearth furnace, electric furnace, an ingot-making, a slab-making by blooming or a continuous casting and subsequent hot-rolling.
  • the finishing temperature of the hot-rolling is preferable to be higher than 800C.
  • a coiling temperature is not limited. That is, in the case of an aluminumkilled low carbon steel the drawing workability of the steel can not be obtained, unless the steel is heated to a grain coarsening point as a finishing temperature of hot-rolling and rapidly cooled after the hot-rolling, for reason that the drawability will be deteriorated on account of AlN precipitating at grain boundaries or coiled at a temperature near the A, transformation point.
  • the finishing temperature of the hot-rolling nor coiling temperature has influence on the effects of components of the steel of the present invention for promoting the overaging.
  • the thus obtained hot-rolled coil is then subjected to a cold-rolling after it was sealed.
  • the reduction percentage of the cold-rolling must be more than 30 percent, preferably 60 to percent, from the view point of the drawing workability.
  • the cold-rolled coil is then annealed in a continuous annealing furnace with an adequate heating system.
  • the annealing temperature is higher than 680C, but lower than 900C., and the time required for the soaking is less than 10 minutes.
  • the annealed coil is then subjected to an overaging treatment in a apparatus for overaging treatment under conditions of a temperature of 300 to 500C, and a time of less than minutes, preferably 2 to 5 minutes. Further, in the case of the steel of the present invention the rate of cooling from the annealing temperature to the overaging treatment EXAMPLE 1 Table 1 shows chemical components of steel materials of various kinds for explaining examples of the present invention.
  • the steel materials were annealed at 700C. for 3 min-' utes in a continuous annealing furnace after up to 700C. in a minute. After the annealing the steel materials were cooled down to 370C. by any of cooling rates shown in Table 3 and then were subjected to an overaging treatment at 430C. for 5 minutes. Further, each of the steel materials was subjected to a refining rolling with a reduction percentage of 1.5 percent. Mechanical properties of the cold-rolled steel sheets obtained through the above-mentioned process steps are shown in Table 4.
  • tents were subjected to a continuous annealing. Then, a part of them were subjected to the overaging treatment, while another part of them were not.
  • the mechanical properties of the steels were investigated in comparison of both cases, and the results of the investigations are shown in Figure.
  • composition of steel samples subjected to the investigations and the treatment conditions are as follows:
  • Coiling temperature 630 i l0"C.
  • Reduction percentage 1.5 percent As is seen from the attached drawing, if steel sheets contain silicon in an amount of more than 0.01 percent, a remarkable softening of the steel materials under the same overaging treatment conditions is obtained, whereby a press-formability is so strikingly improved that the material qualities obtained thereby are closely allied to those of SPCD class of the HS which are subjected to a box annealing.
  • Cold-rolled steel sheets containing acid-soluble alu- Table 2 minum, nitrogen and silicon in amounts within the ranges specified by the present invention are in general softer than those containing these components in Rolling record amounts out of the satd respective ranges and are ex- H cellent in all of the breaking elongation, n-value and r- C l f f 5?- O1 lnlS ing 01mg re uCIlOl'l value. Therefore, it 1s clear that the steel sheets of the N0 temperamre temperature percentage present tnventlon have very good press-formab1l1ty.
  • Table 5 shows steel samples prepared by sub ecting E 850 570 70 the steels having chemical compositions shown in Ex- 2 888 228 32 amples 1 and 2 to a vacuum degassing treatment to re- Table 7 L
  • Mechanical properties of annealed steel materials Mechanical properties Yield*4
  • present invention an artificial aging which is aimed at the softening of steel material.
  • the present invention has succeeded in economically overcoming the greatest problem, the steel material becoming hard due to a hardening aging, encountered in producing a cold-rolled low carbon steel sheet by a continuous annealing according to any conventional methods.
  • Example 3 teaches that even without subjecting the steel of the present invention to the overaging treatment at the end of the continuous annealing treatment the press-formability may be improved, when the carbon content is reduced to a range of from 0.001 to 0.009 percent to soften the steel by subjecting the molten steel to a vacuum degassing treatment.
  • the F-value may be also liberated from its dependency on a heating rate of annealing.
  • the dependency of the F-value on the heating rate of annealing varies depending upon the carbon content of the steel, as is special for an aluminum-killed coldrolled steel sheet. Therefore, by reducing the carbon content of the steel of the present invention to less than 0.09 percent by subjecting the same to a vacuum degassing treatment, as above-mentioned, said dependency of the F-value disappears.
  • recrystallization structure of the aluminum-killed cold-rolled steel sheet undergoes a change from a certain line of carbon content, while making the carbon content of 0.01 percent a boundary line, from which it is understood that the recrystallization structure of the aluminum-killed cold-rolled steel sheet having a carbon content of less than 0.01 percent is suited to an annealing process, in which rapid heating is to be conducted.
  • a process for preparing a cold-rolled steel sheet for a press forming which process comprises heating a cold-rolled steel sheet consisting essentially of less than 0.08 wt. percent carbon 0.05 to 0.4 wt. percent manganese 0.015 to 0.10 wt. percent silicon 0.003 to 0.015 wt. percent nitrogen 0.01 to 0.10 wt. percent acid-soluble aluminum the remainder being iron and unavoidable impurities, to
  • a temperature in a range from 680 to 900C and holding the same at this temperature for less than 10 minutes subsequently cooling the steel sheet from the said temperature with a cooling rate of 5 to 54C/sec. to the temperature of an overaging treatment, then subjecting the steel sheet to said overaging treatment, in which the steel sheet is held at a temperature of 300 to 500C for less than 10 minutes and thereafter subjecting the steel sheet to a continuous annealing treatment, in which the steel sheet is quenched to room temperature.
  • a process for preparing a cold-rolled steel sheet for press forming which includes vacuum degassing, whereby prior to cold rolling, the initial carbon content of a molten steel of 0.02 to 0.08 wt. percent is reduced to range of 0.001 to 0.009 wt. percent, which process comprises heating a cold-rolled steel sheet consisting essentially of less than 0.08 wt. percent carbon 0.05 to 0.4 wt. percent manganese 0.015 to 0.10 wt. percent silicon 0.003 to 0.015 wt. percent nitrogen 0.01 to 0.10 wt.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
US319017A 1971-12-27 1972-12-27 Cold-rolled steel sheet for press-forming Expired - Lifetime US3865645A (en)

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JP10537671A JPS5322052B2 (enrdf_load_stackoverflow) 1971-12-27 1971-12-27

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JP (1) JPS5322052B2 (enrdf_load_stackoverflow)
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BR (1) BR7209158D0 (enrdf_load_stackoverflow)
ZA (1) ZA729117B (enrdf_load_stackoverflow)

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4040873A (en) * 1975-08-23 1977-08-09 Nippon Kokan Kabushiki Kaisha Method of making low yield point cold-reduced steel sheet by continuous annealing process
US4050959A (en) * 1974-11-18 1977-09-27 Nippon Kokan Kabushiki Kaisha Process of making a high strength cold reduced steel sheet having high bake-hardenability and excellent non-aging property
US4066474A (en) * 1974-01-31 1978-01-03 Nippon Kokan Kabushiki Kaisha Method of making high strength cold reduced steel by continuous annealing process
US4113523A (en) * 1973-07-25 1978-09-12 Nippon Kokan Kabushiki Kaisha Process of making high tension cold-reduced al-killed steel excellent in accelerated aging property
US4191600A (en) * 1977-05-02 1980-03-04 Centre De Recherches Metallurgiques-Centrum Voor Research In De Metallurgie Method of continuously heat-treating steel sheet or strip
US4292097A (en) * 1978-08-22 1981-09-29 Kawasaki Steel Corporation High tensile strength steel sheets having high press-formability and a process for producing the same
FR2694024A1 (fr) * 1992-07-23 1994-01-28 Lorraine Laminage Tôle améliorée pour emboutissage en rétreint et procédé de fabrication d'une telle tôle.
US5750222A (en) * 1994-05-02 1998-05-12 Toyo Seikan Kaisya, Ltd. Seamless can with necked-in portion
RU2212469C1 (ru) * 2002-02-01 2003-09-20 Акционерное общество закрытого типа "Радонеж" Низколегированная сталь и изделие, выполненное из нее
US20040094247A1 (en) * 1999-07-01 2004-05-20 Sollac Aluminum-killed medium-carbon steel sheet for containers and process for its prepration

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5522533B2 (enrdf_load_stackoverflow) * 1973-10-01 1980-06-17
JPS50108120A (enrdf_load_stackoverflow) * 1974-02-04 1975-08-26
JPS50142417A (enrdf_load_stackoverflow) * 1974-04-25 1975-11-17
JPS50137815A (enrdf_load_stackoverflow) * 1974-04-25 1975-11-01
JPS50139013A (enrdf_load_stackoverflow) * 1974-04-27 1975-11-06
JPS54107415A (en) * 1978-02-09 1979-08-23 Nippon Kokan Kk <Nkk> Cold rolled steel plate with baking hardenability for deep drawing
JPS5531182A (en) * 1978-08-28 1980-03-05 Sumitomo Metal Ind Ltd High strength cold rolled steel plate with superior workability and manufacture thereof
JPS566708A (en) * 1979-06-28 1981-01-23 Sumitomo Metal Ind Ltd Gold rolled steel sheet possessing excellent press formability and baking hardenability and its manufacture
US4473411A (en) * 1983-07-20 1984-09-25 Armco Inc. Process of making aluminum killed low manganese deep drawing steel

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2109271A (en) * 1936-10-05 1938-02-22 Monsanto Chemicals Vitreous enameled products
US2125128A (en) * 1936-10-30 1938-07-26 Westinghouse Electric & Mfg Co Process of heat treating steel
US2319655A (en) * 1939-06-24 1943-05-18 A E Feragen Inc Wheel balancing apparatus
US2986403A (en) * 1958-12-03 1961-05-30 William B Jaspert Fluid suspension systems for automobiles
US3117897A (en) * 1961-11-07 1964-01-14 British Iron Steel Research Process for hardening steel steet and strips by over-aging
US3239389A (en) * 1962-07-11 1966-03-08 Kawasaki Steel Co Deep drawing cold rolled rimmed steel sheet and strip and production of the same
US3323953A (en) * 1964-09-15 1967-06-06 United States Steel Corp Method of treating steel and novel product
US3357822A (en) * 1964-06-26 1967-12-12 Sumitomo Metal Ind Low-carbon aluminum killed steel for high temperature applications

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2109271A (en) * 1936-10-05 1938-02-22 Monsanto Chemicals Vitreous enameled products
US2125128A (en) * 1936-10-30 1938-07-26 Westinghouse Electric & Mfg Co Process of heat treating steel
US2319655A (en) * 1939-06-24 1943-05-18 A E Feragen Inc Wheel balancing apparatus
US2986403A (en) * 1958-12-03 1961-05-30 William B Jaspert Fluid suspension systems for automobiles
US3117897A (en) * 1961-11-07 1964-01-14 British Iron Steel Research Process for hardening steel steet and strips by over-aging
US3239389A (en) * 1962-07-11 1966-03-08 Kawasaki Steel Co Deep drawing cold rolled rimmed steel sheet and strip and production of the same
US3357822A (en) * 1964-06-26 1967-12-12 Sumitomo Metal Ind Low-carbon aluminum killed steel for high temperature applications
US3323953A (en) * 1964-09-15 1967-06-06 United States Steel Corp Method of treating steel and novel product

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4113523A (en) * 1973-07-25 1978-09-12 Nippon Kokan Kabushiki Kaisha Process of making high tension cold-reduced al-killed steel excellent in accelerated aging property
US4066474A (en) * 1974-01-31 1978-01-03 Nippon Kokan Kabushiki Kaisha Method of making high strength cold reduced steel by continuous annealing process
US4050959A (en) * 1974-11-18 1977-09-27 Nippon Kokan Kabushiki Kaisha Process of making a high strength cold reduced steel sheet having high bake-hardenability and excellent non-aging property
US4040873A (en) * 1975-08-23 1977-08-09 Nippon Kokan Kabushiki Kaisha Method of making low yield point cold-reduced steel sheet by continuous annealing process
US4191600A (en) * 1977-05-02 1980-03-04 Centre De Recherches Metallurgiques-Centrum Voor Research In De Metallurgie Method of continuously heat-treating steel sheet or strip
US4292097A (en) * 1978-08-22 1981-09-29 Kawasaki Steel Corporation High tensile strength steel sheets having high press-formability and a process for producing the same
FR2694024A1 (fr) * 1992-07-23 1994-01-28 Lorraine Laminage Tôle améliorée pour emboutissage en rétreint et procédé de fabrication d'une telle tôle.
EP0581629A1 (fr) * 1992-07-23 1994-02-02 Sollac Tôle pour emboutissage en rétreint et procédé pour la fabrication d'une telle tôle
US5750222A (en) * 1994-05-02 1998-05-12 Toyo Seikan Kaisya, Ltd. Seamless can with necked-in portion
US20040094247A1 (en) * 1999-07-01 2004-05-20 Sollac Aluminum-killed medium-carbon steel sheet for containers and process for its prepration
US6776856B2 (en) * 1999-07-01 2004-08-17 Sollac Aluminum-killed medium-carbon steel sheet for containers
US20040221928A1 (en) * 1999-07-01 2004-11-11 Sollac Aluminum-killed medium-carbon steel sheet for containers and process for its preparation
US7169243B2 (en) 1999-07-01 2007-01-30 Sollac Aluminum-killed medium-carbon steel sheet for containers and process for its preparation
RU2212469C1 (ru) * 2002-02-01 2003-09-20 Акционерное общество закрытого типа "Радонеж" Низколегированная сталь и изделие, выполненное из нее

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BR7209158D0 (pt) 1973-09-18
ZA729117B (en) 1973-11-28
JPS4870611A (enrdf_load_stackoverflow) 1973-09-25
JPS5322052B2 (enrdf_load_stackoverflow) 1978-07-06
AU470367B2 (en) 1974-07-04
AU5056272A (en) 1974-07-04

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