US3698963A - Ultrahigh strength steels - Google Patents

Ultrahigh strength steels Download PDF

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Publication number
US3698963A
US3698963A US73962A US3698963DA US3698963A US 3698963 A US3698963 A US 3698963A US 73962 A US73962 A US 73962A US 3698963D A US3698963D A US 3698963DA US 3698963 A US3698963 A US 3698963A
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composite
stainless steel
cold
strength
core
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Expired - Lifetime
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US73962A
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English (en)
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John Nunes
Albert D Martin
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Brunswick Corp
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Brunswick 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12486—Laterally noncoextensive components [e.g., embedded, etc.]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12903—Cu-base component
    • Y10T428/12917—Next to Fe-base component
    • Y10T428/12924—Fe-base has 0.01-1.7% carbon [i.e., steel]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12937—Co- or Ni-base component next to Fe-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
    • Y10T428/12979—Containing more than 10% nonferrous elements [e.g., high alloy, stainless]

Definitions

  • An ultrahigh strength material made from ordinary 18- 8 stainless steel has a tensile strength in excess of 400,000 p.s.i.
  • the method of producing the ultrahigh strength is accomplished by thermo-mechanical operations.
  • the material can have any desired geometric cross section contiguration and is adaptable for use as a spring material.
  • This invention is in the iield of high strength steels and, more particularly, in the field of ultrahigh strength 18-8 stainless steel materials.
  • Type 302 stainless exhibits an austenitic structure and cannot be readily or appreciably transformed by heat treatment only into a substantially martensitic structure.
  • many attempts have been tried to make type 302 stainless steel stronger and harder primarily by exotic heat treatments without altering the oxidation and corrosion resistance thereof. In retrospect, it was not expected that such attempts would work and in essence they have not worked.
  • type 302 stainless steel and special compositions thereof have been strengthened by cold work with achievable results indicating strength up to a maximum of 355,000 p.s.i. for standard type 302 stainless and 380,000 p.s.i. for special compositions thereof. These special compositions constituting small chemical changes do not significantly alter the structure of the material.
  • This invention relates to oxidation and corrosion resistant steels, and is concerned with new and improved characteristics 0f 18-8 stainless steel alloys that provide ultrahigh strength levels from over 400,000 p.s.i. to over 600,000 p.s.i. This invention also relates to a new and improved thermo-mechanical method of treating such 18-8 stainless steels to achieve these ultrahigh strength levels.
  • an 18-8 stainless steel material is subjected to a series of deformation hardening operations always performed below the recrystallization temperature for the material with intermediate anneals. Subsequently, the material is deformation hardened to a very high level of cold work, over The material is further processed by being subjected to an intermediate heat treatment to inhibit dynamic recovery, and to obtain an aging response thereby enhancing the strength already achieved from the deformation hardening.
  • the material can be further deformation hardened with intermediate heat treatments to again increase the strength to higher levels, yet still exhibiting excellent oxidation resistance at temperatures in the 500 degree F. rangeL
  • such materials will provide excellent spring characteristics and oxidation resistance hitherto unknown in 18-8 stainless steel spring materials.
  • Still another feature of the invention is to provide an ultrahigh strength 18-8 stainless steel material in an operating range up to about 500 degrees F. yet retaining good oxidation resistance.
  • Yet another feature of the invention is to provide a plurality of 18-8 stainless steel filaments, each having a tensile strength in excess of 400,000 p.s.i.
  • Another feature of the invention is to provide a composite material having the plurality of 18-8 stainless steel filaments surrounded by metal matrix material, said composite exhibiting a tensile strength in excess of 400,000 p.s.i.
  • Another feature of the invention is to provide an 18-8 stainless steel Wire having an ultra-high strength with a. corrosion resistant covering superior to the core stainless steel.
  • FIG. l is a cross sectional View of a circular tube surrounding a circular wire
  • FIG. 2 is a cross sectional view of a sheathing material having a circular external configuration surrounding a core material having a square external configuration;
  • FIG. 3 is a cross sectional view of a sheathing material having a circular external configuration Surrounding a core material having a rectangular external configuration;
  • FIG. 4 is a cross sectional view of a sheathing material having a circular external configuration surrounding a core material having an hexagonal external configuration;
  • FIG. 5 is a cross sectional view of a sheathing material having a circular external configuration surrounding a core material having an I-shaped external configuration;
  • FIG. 6 is a cross sectional view of a sheathing material having a circular external coniiguration surrounding a core material having an elongated external configuration
  • FIG. 7 is a cross sectional view of the configuration of FIG. 1 wherein the sheath is drawn down tightly on the core material and having an interface designated therebetween;
  • FIG. 8 is a schematic ilow chart of the process utilized in producing the high strength stainless steel material.
  • an 18-8 stainless steel core material having a cross-sectional configuration such as a circle, a square, a rectangle, a hexagon, an I-shaped, an elongated rectilinear shape, etc.
  • a metal such as a nickel-copper alloy, type 310 stainless steel nickel base superalloys, cobalt base superalloys, nickel-cobalt alloys, copper base alloys, lead, titanium and its alloys, to form a composite.
  • the composite is then reduced in cross section so that the sheath tightly adheres to the core.
  • the interior of the sheath should conform to the exterior of the core.
  • the cold deformation may be performed by drawing, swaging, rolling, pressing, squeezing, etc., or any desired combination thereof.
  • type 302 stainless steel (18-8 stainless steel) has the following approximate chemical analysis by weight:
  • FIG. 1 The substantially cvircular exterior cross section 8 of such a composite 7 configuration is shown in FIG. 1 wherein the core 10 is surrounded by a sheath 12 and the exterior surface 11 of the core 10 is substantially circular and adjacent the interior surface 13 of the sheath 12.
  • FIGS. 2 through 6 the cross-sectional composite configurations for a square 10A, a rectangle 10B, a hexagon 10C, an I-shape 4 10D, and an elongated rectangle 10E, are shown in FIGS. 2 through 6.
  • the sheath 12 is reduced in size tightly on the core to prevent any relative movement between the core 10 and the sheath 12 with an interface 15 provided to promote equal reduction of the core 10 and the sheath 12, as shown in FIG. 7.
  • the ratio of the sheath material to the core material depends upon the types of materials and configuration. Approximately a 5 to 10% reduction in area is required to provide the initial tight mechanical bond between the, sheath 12 and the core 10.
  • the core 10 is made of a material such as type 302 stainless steel
  • the sheath is made of the material such as a nickel-copper alloy
  • the composite' is yannealed in ⁇ a heat treating furnace at a nate of approximately two seconds -per mil of diameter of the composite.
  • the annealing or recrystallization temperature must ⁇ be suliiciently high to .provide la complete solution anneal of the' core.
  • the composite is then subjected to a series of cold reducing steps with intermediate anneals wherein the composites area is reduced at least 75% by cold deformation and preferably by cold deformation after the last anneal.
  • Each of the intermediate anneals is performed above the recrystallization temperature of the core material. However, this temperature should be kept as low as possible to prevent extensive diffusion between the core and sheathing materials. It is believed that the extreme amount of cold deformation is enhanced because the sheathing supports the core material, provides a protective coating and functions as a lubricant.
  • This particular step in the process is extremely important, and heretofore has not been recognized as one of the primary steps necessary to provide the ultrahigh strength material having complicated geometric cross sectional configurations. It is believed that for simple geometric shapes, such as an elongated rectangle, a square, a circle, etc., that the cladded sheath is not required; however, it can be used, if desired.
  • the 75-84% cold deformed composite is heated for approximately four hours (with the permissable time ranging from about one half hour to about sixteen hours or more) at a temperature well below the lowest recrystallization or transformation temperature of the core material; for type 302 stainless material, the range would be about 700 degrees F. to 825 degrees F., and preferably in a narrower range of about 775 degrees F. to 800 degrees F.
  • the sub-transformation temperature of the core material refers to a temperature at which substantially no recrystallization of the microstructure will occur. This sub-transformation temperature is also called a stress relieving temperature.
  • the 84% cold deformed composite is additionally cold deformed to as much as 97%, wherein the core material has a tensile strength in excess of 500,000 p.s.i.
  • the sheath can be removed from the core such as by chemical dissolution and other methods well known in the art. When the sheath is a nickel-copper alloy, chemical dissolution in nitric acid is quite satisfactory. If the sub-transformation heat treatment is omitted, then the material at a 97% cold deformed state would exhibit a tensile strength in excess of 400,000 p.s.i.
  • the 84% cold deformed composite is further cold deformed to approximately 93% to 94%.
  • the composite is heat treated at the sub-transformation temperature range of 700 degrees to 825 degrees F. for an approximate period of time such as four hours.
  • the composite is subsequently cold deformed to 98% and again heat treated at the subtransformation temperature range of 700 degrees F. to 825 degrees F. for an approximate period of time, such as four hours.
  • the sheath can be removed as described above, with the core having a resulting tensile strength ranging from approximately 500,000 p.s.i. to approximately 580,000 p.s.i.
  • the 84% cold deformed composite was further drawn to a 97.6% cold deformation state.
  • the composite is heat-treated at the sub-transformation temperature of about 700 degrees F. to 825 degrees F. for approximately four hours.
  • the composite is then additionally cold deformed to a 98.7% state.
  • the core material exhibited a tensile strength of about 575,000 p.s.i. to 600,000 p.s.i.
  • This composite is then heat-treated a second time at a sub-transformation temperature, the same as above, for approximately about 4'1/2 hours.
  • the core material then exhibited a tensile strength in excess of 600,000 p.s.i.
  • the 84% cold deformed composite is further cold deformed to approximately 97% or more.
  • the composite is then heat treated at the sub-transformation temperature ranging from 700 degrees F. to 825 degrees F. After the sheath is removed similar to the manner described above, the core has a resultant tensile strength varying from 475,000 p.s.i. to 525,000 p.s.i.
  • EXAMPLE I A type of 302 stainless steel rod having a 0.080 inch diameter and an approximate chemical analysis by weight of:
  • the rod-sheath composite was drawn through a 0.091 inch diameter wire drawing die.
  • the composite was solution annealed at 1950 degrees F. at a rate of two seconds per mil of diameter of the composite and rapidly quenched.
  • the composite was cold drawn through a series of dies with intermediate anneals to a 97.6% cold worked state.
  • the composite was then heat treated at a sub-transformation temperature of about 795 degrees F. for approximately four hours.
  • the sheathing material was removed and the resulting stainless wire exhibited a tensile strength of 540,100 p.s.i.
  • EXAMPLE II Same as Example I except that after the sub-transformation heat treatment of the composite, the composite was further cold drawn from the 97.6% state to a 98.7% state of cold work. The sheathing material was then stripped from the composite and the resultant stainless steel rod exhibited a tensile strength of 592,000 p.s.i. Prior to removing the sheathing the tensile strength was 472,- 800 p.s.i. with the Monel acting as corrosion resistance coating.
  • EXAMPLE III Same as Example II except that a final heat treatment at a sub-transformation temperature of 795 degrees F. for approximately 41/2 hours was employed. The sheathing material was then removed from the composite, and the stainless steel wire exhibited a tensile strength of 608,000 pounds per square inch.
  • EXAMPLE IV A type 302 stainless steel rod having a 0.080 diameter and an approximate chemical analysis by weight of and was surrounded by a Monel K sheath having a 0.115 inch outside diameter, 0.100 inch inside diameter, and a chemical analysis of nickel, 66%; copper, 29%; and aluminum, 3%.
  • the rod-sheath composite was drawn through a 0.091 inch diameter wire drawing die.
  • the composite was solution annealed at 1950 degrees F. at a rate of two seconds per mil of diameter of the composite and rapidly quenched.
  • the composite was cold drawn through a series of dies with intermediate anneals prior to achieving a 99.4% cold worked state.
  • the composite was then stripped of its sheathing material and exhibited a tensile strength of 535,500 p.s.i.
  • EXAMPLE V The same as Example IV except that after the subtransformation heat treatment of the composite, the composite was further cold Worked from a 99.4% cold work state to a 99.6% cold work state. The sheathing material was removed therefrom, with the final stainless steel wire exhibiting a tensile strength of 619,000 pounds per square inch.
  • EXAMPLE VI Ninety-one (91) type 302 stainless steel rods, each having a diameter of 0.080 inch were placed in Monel 400 tubes, each having a 0.115 inch outside diameter and a .100 inch inside diameter.
  • the chemical composition of the 302 stainless steel by weight was:
  • the rod-tube combinations were packed in a mild steel billet, heated, evacuated to about l"5 torr and sealed. The billet was heated and extruded at 1800 degrees F. with a 16 times reduction forming a composite. The composite was then reduced by cold reduction with intermediate anneals. The composite was fully annealed at a rate of two seconds per mil diameter of the composite. The composite was then cold drawn to a linal diameter of 16.8 mils with each of the individual rods (now filaments) having an effective cross section diameter of about 1.13 mils. The filaments were at a 93.8% cold worked state.
  • the strength of the 302 stainless steel laments was found to be 393,200 p.s.i.
  • the composite was then heat treated at a sub-transformation temperature of about 700 degrees F. for about 16 hours.
  • the final strength of the 302 stainless steel filaments was then found to be 427,500 p.s.i.
  • EXAMPLE VII Same as Example VI except that the composite was d cold drawn to a 98.5% cold worked state.
  • the iinal composite diameter was 16.8 mils with each of the individual filaments having an effective cross section dimension of about 1.13 mils.
  • the strength of the 302 stainless filaments was found to be 453,700 p.s.i.
  • the composite was then heat treated at a sub-transformation temperature of about 700 degrees F. for approximately 16 hours.
  • the final strength of the laments was found to be 512,200 p.s.i.
  • the austenite that originally existed in the core material transformed intoy at least 50% martensite by a diffusionless phase transformation.
  • the sheathing material is preselected to have a cold deformation rate that is compatible with the cold deformation rate of the core material. It is believed that the additional treatment at the sub-transformation temperature range further inhibits dynamic recovery and obtains an aging response thereby enhancing the strength already achieved from the deformation hardening.
  • the ultra-high strength core material may be subjected to a final sizing operation to obtain a uniform cross sectional geometry.
  • the general processing steps or operations are graphically depicted in FIG. 8.
  • the ordinate denotes the heat treatment range in temperature and the abscissa depicts the cycle of operations or steps.
  • Operations A and C indicate cold deforming operations with B indicating an intermediate anneal.
  • Operations indicated as A, B and C are size reducing operations and can be repeated any number of times.
  • D indicates the solution anneal of the core material.
  • E indicates the amount of cold work reduction measured in percentage.
  • F indicates the flrst sub-transformation anneal with G indicating subsequent cold reduction.
  • H indicates the iinal sub-transformation anneal.
  • ultrahigh strength materials can be coiled for use in springs, either as tension or compression springs.
  • spiral type watch springs, leaf springs, etc. can also be made from this material exhibiting such high tensile strength.
  • a high strength stainless steel material having a composition by weight consisting essentially of .15% maximum carbon, 1.5% maximum silicon, 2% maximum manganese, about 17% to about 19% chromium, about 7% to about 10% nickel, minor amounts of other metals, and the balance constituent iron, and characterized in that said material has a tensile strength in excess of 400,000 p.s.i.
  • the material of claim 1 further including a tightly adhering sheath material.
  • a method of obtaining a tensile strength of at least 400,000 p.s.i. from an 18-8 stainless steel material closely controlling the steps comprising:
  • a method of obtaining a tensile strength of at least 400,000 p.s.i. from an 18-8 stainless steel material comprising the steps of:

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
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US73962A 1970-09-21 1970-09-21 Ultrahigh strength steels Expired - Lifetime US3698963A (en)

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Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3871925A (en) * 1972-11-29 1975-03-18 Brunswick Corp Method of conditioning 18{14 8 stainless steel
US3883371A (en) * 1973-02-21 1975-05-13 Brunswick Corp Twist drawn wire
US3917492A (en) * 1973-06-08 1975-11-04 Sandvik Ab Method of making stainless steel
US4217399A (en) * 1975-11-05 1980-08-12 Monsanto Company Sintered bi-metallic conjugate filaments and their preparation
US4287254A (en) * 1978-02-13 1981-09-01 Monsanto Company Conjugate filaments and films
EP0222166A1 (de) * 1985-10-11 1987-05-20 Sumitomo Electric Industries Limited Hochfester elektrischer Leiter und Verfahren zum Herstellen dieses Leiters
US4818634A (en) * 1986-12-24 1989-04-04 Texas Instruments Incorporated Composite metal spring material, method of making, and spring members formed therefrom
US4909002A (en) * 1987-04-27 1990-03-20 Cliffston Products Limited Concrete screed rails
US20040265576A1 (en) * 2001-07-20 2004-12-30 Stefaan De Bondt Bundle drawn stainless steel fibers
US20070051080A1 (en) * 2002-12-20 2007-03-08 Applied Materials, Inc. In-line filter in a diffusion bonded layered substrate
EP2402051B1 (de) * 2010-06-30 2019-10-02 Asahi Intecc Co., Ltd. Medizinischer Führungsdraht
US10818411B2 (en) * 2017-03-09 2020-10-27 Sumitomo Wiring Systems, Limited Wire conductor, insulated wire, and wiring harness, and method for manufacturing wire conductor
CN113477712A (zh) * 2021-07-30 2021-10-08 安徽工业大学 一种多层金属复合带的制备工艺

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0031399A3 (en) * 1979-07-30 1981-11-25 Consultronic (Int.)Ltd. Material for the production of stainless alpine ski edges

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3871925A (en) * 1972-11-29 1975-03-18 Brunswick Corp Method of conditioning 18{14 8 stainless steel
US3883371A (en) * 1973-02-21 1975-05-13 Brunswick Corp Twist drawn wire
US3917492A (en) * 1973-06-08 1975-11-04 Sandvik Ab Method of making stainless steel
US4217399A (en) * 1975-11-05 1980-08-12 Monsanto Company Sintered bi-metallic conjugate filaments and their preparation
US4287254A (en) * 1978-02-13 1981-09-01 Monsanto Company Conjugate filaments and films
EP0222166A1 (de) * 1985-10-11 1987-05-20 Sumitomo Electric Industries Limited Hochfester elektrischer Leiter und Verfahren zum Herstellen dieses Leiters
US4818634A (en) * 1986-12-24 1989-04-04 Texas Instruments Incorporated Composite metal spring material, method of making, and spring members formed therefrom
US4909002A (en) * 1987-04-27 1990-03-20 Cliffston Products Limited Concrete screed rails
US20040265576A1 (en) * 2001-07-20 2004-12-30 Stefaan De Bondt Bundle drawn stainless steel fibers
US7166174B2 (en) * 2001-07-20 2007-01-23 Nv Bekaert Sa Bundle drawn stainless steel fibers
US20070051080A1 (en) * 2002-12-20 2007-03-08 Applied Materials, Inc. In-line filter in a diffusion bonded layered substrate
US7459003B2 (en) * 2002-12-20 2008-12-02 Applied Materials, Inc. In-line filter in a diffusion bonded layered substrate
EP2402051B1 (de) * 2010-06-30 2019-10-02 Asahi Intecc Co., Ltd. Medizinischer Führungsdraht
US10818411B2 (en) * 2017-03-09 2020-10-27 Sumitomo Wiring Systems, Limited Wire conductor, insulated wire, and wiring harness, and method for manufacturing wire conductor
CN113477712A (zh) * 2021-07-30 2021-10-08 安徽工业大学 一种多层金属复合带的制备工艺
CN113477712B (zh) * 2021-07-30 2023-12-05 安徽工业大学 一种多层金属复合带的制备工艺

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DE2138195C3 (de) 1979-11-08
GB1352403A (en) 1974-05-08
BE772880A (fr) 1972-01-17
DE2138195B2 (de) 1979-03-15
DE2138195A1 (de) 1972-03-23
JPS5538409B1 (de) 1980-10-03

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