US3532560A - Cold-working process - Google Patents

Cold-working process Download PDF

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US3532560A
US3532560A US677507A US67750767A US3532560A US 3532560 A US3532560 A US 3532560A US 677507 A US677507 A US 677507A US 67750767 A US67750767 A US 67750767A US 3532560 A US3532560 A US 3532560A
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Prior art keywords
steel wire
cold
steel
wire
bolts
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US677507A
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Mitsuo Tomioka
Koichi Urakawa
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Kobe Steel Ltd
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Kobe Steel Ltd
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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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K1/00—Making machine elements
    • B21K1/44—Making machine elements bolts, studs, or the like
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a process for producing cold-shaped or forged products having excellent mechanical properties and high fatigue limits from a length of a continuous elongated shaped steel article such as steel wire, rods, bars and the like (hereafter it should be recognized that although the discussion is directed to steel wire, other continuous elongate shapes could be used) which has been previously tempered under particular conditions.
  • the above enumerated machine parts may also be produced by a conventional cold-shaping process which usually comprises selecting a length of coiled steel wire (this material will be merely referred to as steel wire hereinafter) as the starting material to be processed and then cold shaping the steel Wire in a cold shaping machine in a continuous operation.
  • a conventional cold-shaping process which usually comprises selecting a length of coiled steel wire (this material will be merely referred to as steel wire hereinafter) as the starting material to be processed and then cold shaping the steel Wire in a cold shaping machine in a continuous operation.
  • the steel wire material contains carbon in excess of 0.3% by weight or has an excessively high degree of hardness, the steel wire may break or fissure during the cold shaping operation or the thus obtained product may have insufficient tensile strength.
  • the cold-shaping processes of the prior art frequently use the so-called spherically annealed steel wire as the starting material to be cold-shaped.
  • the annealed steel wire is then cold shaped and subjected to a further tempering treatment so as to obtain a machine part or product having a high tensile strength and predetermined mechanical properties. Therefore, in order for conventional steel wire to be suitably employed as the starting material to be cold-shaped into a machine part, the steel Wire must be first subjected to an annealing or spherical annealing treatment in order to reduce the hardness of such a steel wire to a level suitable for the cold shaping operation. However, since such annealing treatments are carried out at a high temperature ranging from 700 to 900 C. for a rather long period of time covering 5 to 10 hours, the steel wire is liable to form a deoxidized layer or layers during the annealing treatment.
  • the tempering treatment since the tempering treatment is the last stage in a series of stages involved in the cold shaping of a machine part, the tempering treatment has to be carried out in a non-oxidizing atmosphere furnace or salt bath soaking pit; otherwise it is quite difficult to obtain a product having satisfactory quality.
  • the patenting process comprises the steps of heating steel wire to a temperature about its A3 transition point and quenching the steel wire in a lead bath soaking pit heated to 400 to 600 C. so as to temper the steel material.
  • the patenting treatment primarily has been developed as a pre-treatment step in the coldstretching operation of hard steel wires having high carbon contents such as piano wires for example, the patenting treatment is not applicable as a pre-treatment process in the cold-forging of steel wires having carbon contents less than 0.6% by weight for producing machine parts. That is, it is possible to obtain fine grain structures for high carbon steel wires having carbon content above 0.6% by weight, but in case of carbon steel wires having a carbon content of less than 0.6% by weight, the wires treated by the patenting process will have uneven grain structures due to insuflicient quenching.
  • novel process of our invention makes it possible so obtain uniform fine grain sorbite structures for steel wires and this process can be clearly distinguished from the conventional patenting treatment process.
  • the present invention does not represent a merely mechanical combination of heat treatment and soldshaping steps for steel wires, but rather is a novel process which has been developed on the basis of findings of the workabilities of materials to be cold-forged or shaped.
  • a improved cold-forging process for producing cold-shaped products which comprises the steps of rapidly heating a running length of carbon steel wire or steel alloy wire to a temperature above the A3 transition point of the steel material while continuously reeling out of a roll of coiled wire; quenching said heated steel wire by means of cooling agent such as water or oil so as to harden the wire; rapidly heating said quenched steel wire to a temperature 300 to 700 C.; cooling said heated wire to room temperature by means of cooling agent such as water or compressed air so as to temper the wire whereby a length of tempered wire having a uniform fine grain sorbite structure is obtained; and cold-forging said tempered steel wire into products having prescribed shape and dimention by a cold-forging machine.
  • the steel wires suitably employed as the starting material in carrying out the novel process by the present invention include carbon steel wire containing carbon in an amount of 0.2 to 0.6% by weight and alloy steel wire containing one or more of silicon, manganese, nickel, chromium, molybdenum, vanadium and boron in an amount less than 3% 'by Weight respectively in addition to carbon in the above prescribed content range. That the amount of carbon be within the aforementioned range is particularly critical; this criticality will be explained in greater detail below in the preferred embodiment.
  • FIG. 1 shows a block flow sheet for a conventional cold-shaping process and for the process of our invention
  • FIG. 2 graphically shows the relationship between micro-structures and percentage of break or crack occurrence for various types of steel wires
  • FIG. 3 graphically shows the relationship between critical cold compressive amounts and percent reductions in area on various cold-forged steel wires
  • FIG. 4 is a graph of load-number cycle curves for bolts produced by our process and bolts prepared by conventional processes-as discussed in Example I.
  • FIG. 1 shows a flow sheet comparison between a conventional prior art process and the novel process of our invention.
  • our process as well as producing a superior product, results in the elimination of several costly and time-consuming steps required in the prior art process. Further advantages of our process and the products produced thereby are enumerated as follows:
  • the steel wire used as the starting material is continuously subjected to the tempering treatment in its wire form as it was produced, the thus tempered steel material has uniform mechanical properties and microstructure throughout its length, and, accordingly, disparity in quality of products processed from such a tempered material is quite rare.
  • the obtained products have various excellent mechanical properties, especially an excellent resistance to repetitive fatigue.
  • FIGS. 2 and 3 are particularly useful in considering the workability of materials to be cold-forged, especially since as to the workabilities of materials to be coldforged, there has been no established definition up to date.
  • the cold workabilities of various materials we have concluded that the cold workabilities of steel materials are essentially determined depending upon the chemical compositions and heat treatment processes, and expressed in the terms of mechanical properties and microstructures of such materials.
  • we are convinced that even some steel materials having high tensile strengths can be properly cold-forged without difficulty provided that they satisfy certain specific requirements. This point will be explained in detail referring to FIGS. 2 and 3 of the accompanying drawings.
  • FIG. 2 graphically shows relations between microstructures of various types of steel wires produced under different heat treatment conditions, such as 835C (AISI 1035), S450 (AISI 1045), SCrZ (A181 5130), SCrR (AISI 5140), SCM3 (AISI4135), SCr21 (AISI 5130) and the subsequent parenthetical terms indicating the standard U.S. nomenclature for the same steel wire; reductions of area of these wires determined through tension tests (horizontal), and percentage of break or crack occurrence during cold-forging with 80% of coldcompression ratio (vertical).
  • 835C AISI 1035
  • S450 AISI 1045
  • SCrZ A181 5130
  • SCrR AISI 5140
  • SCM3 AISI4135
  • SCr21 AISI 5130
  • Curve A designates an annealed coarse grain structure steel Wire
  • Curve B designates an annealed fine grain structure steel wire
  • Curve C designates a spherodized fine grain structure steel wire
  • Curve D designates a tempered fine grain structure steel wire.
  • FIG. 3 shows graphically the relations between critical cold compressive amounts (the point at which a break takes place in steel wires) in cold compression tests and reductions of area percent in tension tests performed on various cold-forged steel wires which were coldstretched under different drawing ratios. From the graph of FIG. 3, it is clear that even the drawing ratio of coldforged steel wires amounts to such great degrees as to Further, if the chemical compositions of steel materials and heat treatment conditions for such materials are so selected that the reductions of area in such materials may be great, the breaking point of such materials can be raised, that is, the cold workability of such materials can be improved.
  • the novel invention utilizes these excellent cold workabilities of tempered steel wires as shown in the graphs of FIGS. 2 and 3. Especially, since D steel wire has a fine grain sorbite microstructure, it is noted that this D wire has a high tensile strength and excellent workability. Therefore, it is mandatory that in order to industrially utilize such properties of these steel wires in producing cold-forged products from such steel wires, the chemical compositions of such steel wires and the treatment conditions for such materials should be properly combined depending upon the properties, strength and shape called for in the cold-forged products prepared from such materials. This novel combination of chemical compositions and heat treatment conditions can be achieved only by the present invention.
  • an alloying component such as silicon, manganese, nickel, chromium, molybdenum, vanadium, and boron, and preferably containing not more than 3% by weight of any given alloying metal
  • the reason for which the amount of carbon to be contained in carbon steel wire as the starting material is specified as the range 0.2 to 0.6% by weight is that if the carbon content of the steel material is less than 0.2% by weight, the carbon content during the tempering treatment is insufficient to impart the prescribed mechanical strength, which will be called for by the desired product or machine part; and, if the carbon content of the steel wire is in excess of 0.6% by weight, a cold-forged product prepared from such steel material will not possess sufficient tensile strength to meet requirements for the desired cold-forged product.
  • alloy steel is employed as the starting material to be cold-forged
  • the reason that that content for each of the alloying elements is specified as less than 3% by weight is that if one or more of these elements in the prescribed amount are properly incorporated into the base steel material, a product having excellent mechanical properties can be easily obtained through the tempering treatment.
  • these alloying elements in excess of the prescribed amount, there may be no notable improvements in mechanical properties of the product over those of a product prepared from alloy steel wire containing the allowing elements in the prescribed amounts respectively, and, accordingly, the use of these alloying elements which are exepnsive in excess of 3% respectively is uneconomical.
  • the incorporation of from 0.0007 to 0.003% by weight of boron into the steel will improve the heat treatment capability of the alloy steel wire and, accordingly, economy of the other alloying element or elements which are greater in amount than that of the boron additive.
  • Steel wire or alloy steel having the above-mentioned chemical compositions may be used as the starting material for our process in the form of unstretched wire as it is produced or these steel materials may be stretched prior to being subjected to our tempering treatment.
  • stretcihng the amount of stretching is usually such as to effect a 13% reduction in cross-sectional area.
  • a tempered intermediate product having mechanical properties and uniform fine grain sorbite structure suitable for continuous cold-forging will be obtained.
  • the selected plain carbon steel wire or alloy steel wire having the required composition is rapidly heated to a temperature above the A3 transition point of the steel material of the steel wire.
  • This heating may be effected by continuously passing the steel rod, preferably at a rate of 2 to 6 in. per minute, through a suitable conventional high temperature heating means, such as for example a high frequency heating furnace, flame heating furnace, electric resistance heating furnace, electric furnace, heavy oil furnace, salt bath soaking pit or lead bath soaking pit, so that the steel wire may be maintained at a temperature range of 850 to 950 C. for l to 3 minutes.
  • a suitable conventional high temperature heating means such as for example a high frequency heating furnace, flame heating furnace, electric resistance heating furnace, electric furnace, heavy oil furnace, salt bath soaking pit or lead bath soaking pit, so that the steel wire may be maintained at a temperature range of 850 to 950 C. for l to 3 minutes.
  • the purpose of the rapid heating of the steel wire is to obtain a uniform austenite structure of the steel wire.
  • heating of the steel wire to a temperature below 850 C. is insufficient to obtain a uniform austenite structure of the steel wire, and, accordingly, the insufficiently heated steel wire
  • the steel wire is heated to a temperature above 950 C.
  • the steel wire will be overheated, resulting in deoxidation layer and/or rough surface formation which leads to a poor surface quality or coarsely hardened structure. Therefore, the rapid heating of the steel wire within the temperature range of 850 to 950 C. for a time space of 1 to 3 minutes is critical in order that the steel wire may be properly treated in the heat treatment step of the present process.
  • the heated steel wire After having been rapidly heated to the temperature range of 850 to 950 C., the heated steel wire is passed to a quenching device, which is preferably directly connected to the preceding heating surface, where the heated steel wire is quenched by means of any suitable cooling agent, such as water or oil, until the innermost portion of the interior structure of the steel wire is cooled to a temperature below about 200 C.
  • any suitable cooling agent such as water or oil
  • the type of cooling agent may be suitably selected depending upon the chemical compositon and diameter of the steel wire to be processed. When the diameter of the steel wire is smaller than 11 mm., oil is employed as the quenching or hardening agent whereas steel wire having a diameter greater than 11 mm.
  • the steel wire is quenched or hardened by means of water.
  • the steel material be quenched until the interior structure of the steel material will also have a uniformly quenched structure as well as the exterior thereof.
  • the quenching is effected at an extremely rapid rate, breaks may occur in the steel wire. Therefore, it is preferable that the steel wire be quenched until the innermost portion of the interior structure of the steel material is cooled to 200 C., and thereafter the steel material is gradually cooled.
  • the steel wire now having a uniformly hardened structure, is then passed through a second heating furnace which is preferably connected to the above-mentioned quenching device and is maintained at 300 to 700 C- where the steel wire is evenly heated for a period of 2 to 10 minutes.
  • the heated steel wire is then passed to a second cooling device which is preferably connected to the second heating surface where the steel material is cooled or tempered to room temperature by means of water or compressed air.
  • a heating temperature for tempering in the range mentioned above is that such a temperature range is necessary to impart mechanical properties suitable for cold-forging i the specific type of steel wires to be processed by the process of the present invention, and especially for obtaining a desired area reduction value for the steel wires in a tension test and a fine grain sorbite micro-structure suitable for cold-forging the steel wires.
  • the heating temperature for tempering is below 300 C.
  • decomposition of the martensite structure of the steel Wire in the hardened state into the fine grain sorbite structure thereof is insufficient and, although the tempered steel wire will have a high strength, its tenacity will be too low, and the steel wire will be unfit for cold-forging.
  • the tempering heating temperature is in excess of 700 C.
  • the decomposition of the martensite structure of the steel wire into the sorbite structure is too rapid, resulting in a coarse grain sorbite structure or a 2 pearlite structure which reduces the tensile strength of the steel wire to a value below 70 kg./mm. Therefore, a tempering heating temperature in excess of 700 C.
  • the heating temperature for tempering is an important factor and the heating or tempering temperature should be suitably selected within the specified temperature range of 300 to 700 C. depending upon the tesile strength desired in the final product, the diameter of the steel wire employed as the starting material, and the processing rate of the steel wire material.
  • the cooling of the steel wire material from the tempering temperature to room temperature need not be rapid.
  • an intermediate steel product having a uniform fine grain sorbite structure and a tensile strength of 70120 kg./ mm. can be easily produced in a short space of time.
  • the intermediate or tempered wire product is then subjected to a surface treatment such as pickling, lime and phosphoric acid film formation in the conventional manner so as to obtain a so-called tempered steel wire which may then be suitably cold-forged by conventional coldforging machine into desired final products or machine parts.
  • the tempered steel wire is stretched by an amount less than reduction in area (usually about 13%) so as to ad just its diameter and tensile strength.
  • the thus obtained tempered steel wire of uniform fine grain sorbite structure is then continuously cold-forged through a cold-forging or shaping machine so as to produce machine parts having a tensile strength of 70 to 120 kg./mm. a high hardness and a high tenacity. Since the steps in the process of the present invention are carried out in succession, production efiiciency is quite high; further, the shaped or forged products do not require any heat treatment after production, and products of precise dimensions can be easily obtained.
  • Example I This example illustrates our inventive process using a steel wire as the starting material having the following chemical composition:
  • a length of coiled steel wire having the above chemical composition (11 mm. in diameter and 350 kgs. in weight per roll) was first cold stretched to a diameter of 10.2 mm. and then passed through a Muflie type heavy oil furnace at a rate of 5 m./min. so as to heat the steel wire to a temperature below about 900 C.
  • the thus heated wire was then quenched in an oil bath so as to reduce the temperature of the wire to a temperature below 200 C.
  • the quenched wire was then tempered by being passed through a lead bath maintained at 600 C. at the same rate as that at which the wire was passing through the heavy oil furnace.
  • the diameter of the wire was reduced to 9.45 mm. by cold finish stretching to obtain a length of tempered steel wire which was suitable for producing bolts of diameter by cold forging.
  • the thus treated steel had a uniform fine grain sorbite microstructure and the following mechanical properties:
  • this tempered steel wire was cold-shaped or forged by a cold shaping machine so as to form hexagon headed bolts of /8 diameter.
  • the shaping machine produced six hexagon headed bolts per minute.
  • the obtained bolts were further subjected to a screw-thread forming step while they were turned round to produce complete /s" x mm. hexagon headed bolts.
  • the bolts were tested in accordance with the 118 bolt test procedure to determine their mechanical properties and the determined mechanical properties were compared with those of comparable bolts produced by the conventional processes.
  • the bolt test procedure is the same as the SAE Standard for Mechanical and Quality Requirements for Threaded Fasteners--SAE 1429C.
  • the 30 wedge test refers to a tension test which was performed by placing a 30 angle wedge between the bottom surface of the head of the bolt and the supporting surface of a supporting seat. Further, in accordance with the standard DIN procedure (i.e., DIN 267Bolt Screws, Nuts and Similar Threaded and Formed Parts Technical Condition of Delivery), bolt head impact tests were performed on the above three types of bolts and good results were obtained on all of these bolts.
  • a length of coiled steel wire having the above chemical composition (11 mm. in diameter and 360 kg. in weight per roll), from a roll of such a wire was first coldstretched to a diameter of 8.5 mm. and then passed through a lead bath soaking pit maintained at 880 C., which used light oil as its fuel, at a rate of 2 m./rnin. so as to heat the steel wire to 880 C. in three minutes.
  • the wire was then cooled to 200 C. by being passed through an oil bath whereby the steel wire was hardened to have a uniformly hardened structure.
  • the tensile strength of the hardened steel wire was above 150 kg./mm.
  • the hardened steel wire was then passed through a tempering lead bath soaking pit maintained at 630 C., at the same rate as that at which the steel wire was passed through the first lead bath soaking pit.
  • the steel wire maintained in this bath at a temperature of the steel wire at 630 C. for five minutes.
  • the steel wire was then cooled to room temperature by means of compressed air.
  • the abovementioned series of treatments were consecutively performed throughout the entire length of the steel wire and the resulting steel wire had a uniform fine grain sorbite structure and a tensile strength of 85 kg./mm.
  • the thus treated steel wire was subjected to pickling and phosphate film forming treatment and then cold-stretched to reduce its diameter to 7.93 mm. so as to obtain a length of tempered steel wire to be suitably employed to produce I IS 8 mm. diameter bolts.
  • the tempered steel wire had a uniform fine grain sorbite structure and the following mechanical properties:
  • the tempered steel was cold forged into /8" diameter hexagon headed bolts by a 78" bolt former (a three stage-transfer header) and then screwthreads were provided on the stems of the bolts while the bolts were being turned about the longitudinal axes thereof so as to produce complete 118 8 mm. diameter (M X 35 mm.) hexagon headed bolts.
  • the formation of cold-forged bolts from a length of tempered steel wire requires considerable mechanical working and specifically the steps of shearing, rolling, heading, trimming, and thread-cutting of the tempered steel wire.
  • the tempered wire of Example II was subjected to these steps during the formation of the bolts and found to have, in spite of its high tensile strength, the same degree of cold-workability as that of the conventional annealed steel wire. Further, there were no breaks or cracks, flaws, etc., formed during the cold-forging operation.
  • a process for producing a cold-forged product which comprises the steps of:
  • metal wire from a continuously unwinding coil
  • said metal selected from the group consisting of carbon steel containing about 0.2 to 0.6% and an alloy steel containing about 0.2 to 0.6% carbon, up to 3% manganese, up to 3% silicon and 0.0007 to 0.003% boron and at least one element selected from the group consisting of up to 3% chromium, up to 3% nickel and up to 3% molybdenum;
  • cooling agent 25 of the quenching step is selected from the group consisting of water and oil.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
US677507A 1963-04-18 1967-10-20 Cold-working process Expired - Lifetime US3532560A (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP2039563 1963-04-18
GB14791/65A GB1077994A (en) 1963-04-18 1965-11-22 Process for producing cold-forged products from tempered steel wire
DEK0059377 1966-05-27
NL6611433A NL6611433A (nl) 1963-04-18 1966-08-15 Werkwijze voor het vervaardigen van koudsmeedbaarstaaldraad en produkten verkregen door middel van deze werkwijze
LU51833A LU51833A1 (de) 1963-04-18 1966-08-26

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US (1) US3532560A (de)
DE (1) DE1508416C3 (de)
GB (1) GB1077994A (de)
LU (1) LU51833A1 (de)
NL (1) NL6611433A (de)

Cited By (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3877281A (en) * 1972-10-27 1975-04-15 Kobe Steel Ltd Method for producing a high strength bolt
US3900347A (en) * 1974-08-27 1975-08-19 Armco Steel Corp Cold-drawn, straightened and stress relieved steel wire for prestressed concrete and method for production thereof
US4046600A (en) * 1973-12-17 1977-09-06 Kobe Steel Ltd. Method of producing large diameter steel rods
US4123296A (en) * 1973-12-17 1978-10-31 Kobe Steel, Ltd. High strength steel rod of large gauge
US4170499A (en) * 1977-08-24 1979-10-09 The Regents Of The University Of California Method of making high strength, tough alloy steel
US4170497A (en) * 1977-08-24 1979-10-09 The Regents Of The University Of California High strength, tough alloy steel
US4404047A (en) * 1980-12-10 1983-09-13 Lasalle Steel Company Process for the improved heat treatment of steels using direct electrical resistance heating
FR2531998A1 (fr) * 1982-08-18 1984-02-24 Skf Steel Eng Ab Tiges resistant a l'acide hydrosulfurique
US4540447A (en) * 1983-06-09 1985-09-10 Huck Manufacturing Company Method of making a multigrip fastener and fastener made thereby
US4563222A (en) * 1983-06-29 1986-01-07 Sugita Wire Mfg. Co., Ltd. High strength bolt and method of producing same
FR2594142A1 (fr) * 1986-02-11 1987-08-14 Avdel Ltd Tige brisable pour dispositif de fixation, et son procede d'obtention
FR2788997A3 (fr) * 1999-02-02 2000-08-04 Unimetall Sa Procede de fabrication d'un organe de fixation filete de petit diametre par frappe a froid d'un fil trefile en acier a fort durcissement par ecrouissage
EP1293578A2 (de) * 2001-09-14 2003-03-19 Samhwa Steel Co., Ltd. Vergüteter Stahldraht mit ausgezeichneten Kaltverformungseigenschaften
US20040035506A1 (en) * 2000-11-09 2004-02-26 Keith Denham Method of manufacturing a blind threaded insert
US20040108027A1 (en) * 2002-10-10 2004-06-10 Norbert Siebenlist Method of making a hardened steel part, especially a roll load-bearing steel part
US20040261918A1 (en) * 1999-05-20 2004-12-30 Honda Giken Kogyo Kabushiki Kaisha Billet for cold forging, method of manufacturing billet for cold forging, method of continuously cold-forging billet, method of cold-forging
EP1697552A1 (de) * 2003-12-18 2006-09-06 Samhwa Steel Co., Ltd. Stahldraht zum kaltschmieden mit hervorragenden kälteschlageigenschaften und herstellungsverfahren dafür
US20060234800A1 (en) * 2005-03-30 2006-10-19 Honda Motor Co., Ltd. Titanium alloy bolt and its manufacturing process
US20070178469A1 (en) * 2003-10-24 2007-08-02 Selexis S.A. High efficiency gene transfer and expression in mammalian cells by a multiple transfection procedure fo mar sequences
US20080264524A1 (en) * 2005-10-31 2008-10-30 Keiichi Maruta High-Strength Steel and Metal Bolt Excellent In Character of Delayed Fracture
WO2012119764A1 (en) 2011-03-08 2012-09-13 Società Bulloneria Europea S.B.E. Spa A high load flanged fastener to be installed by tensioning tools
WO2017015202A1 (en) * 2015-07-17 2017-01-26 Felix Sorkin Compact anchor for post-tensioned concrete segment
US10941799B2 (en) 2014-10-13 2021-03-09 Monogram Aerospace Fasterners, Inc. Deformable sleeve nut and a method of manufacturing

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DE102007022487B3 (de) * 2007-05-14 2008-10-09 FWU Kuang Enterprises Co., Ltd., Jen-Te Hsiang Verfahren zum Herstellen von Schmiedestücken mit einer exzellenten Zugfestigkeit und Bruchdehnung aus Stahldrahtstangen
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US3877281A (en) * 1972-10-27 1975-04-15 Kobe Steel Ltd Method for producing a high strength bolt
US4046600A (en) * 1973-12-17 1977-09-06 Kobe Steel Ltd. Method of producing large diameter steel rods
US4123296A (en) * 1973-12-17 1978-10-31 Kobe Steel, Ltd. High strength steel rod of large gauge
US3900347A (en) * 1974-08-27 1975-08-19 Armco Steel Corp Cold-drawn, straightened and stress relieved steel wire for prestressed concrete and method for production thereof
US4170499A (en) * 1977-08-24 1979-10-09 The Regents Of The University Of California Method of making high strength, tough alloy steel
US4170497A (en) * 1977-08-24 1979-10-09 The Regents Of The University Of California High strength, tough alloy steel
US4404047A (en) * 1980-12-10 1983-09-13 Lasalle Steel Company Process for the improved heat treatment of steels using direct electrical resistance heating
FR2531998A1 (fr) * 1982-08-18 1984-02-24 Skf Steel Eng Ab Tiges resistant a l'acide hydrosulfurique
US4540447A (en) * 1983-06-09 1985-09-10 Huck Manufacturing Company Method of making a multigrip fastener and fastener made thereby
US4563222A (en) * 1983-06-29 1986-01-07 Sugita Wire Mfg. Co., Ltd. High strength bolt and method of producing same
FR2594142A1 (fr) * 1986-02-11 1987-08-14 Avdel Ltd Tige brisable pour dispositif de fixation, et son procede d'obtention
US4717300A (en) * 1986-02-11 1988-01-05 Avdel Limited Pin for a fastener, and method of making same
FR2788997A3 (fr) * 1999-02-02 2000-08-04 Unimetall Sa Procede de fabrication d'un organe de fixation filete de petit diametre par frappe a froid d'un fil trefile en acier a fort durcissement par ecrouissage
US20040261918A1 (en) * 1999-05-20 2004-12-30 Honda Giken Kogyo Kabushiki Kaisha Billet for cold forging, method of manufacturing billet for cold forging, method of continuously cold-forging billet, method of cold-forging
US7438773B2 (en) * 2000-11-09 2008-10-21 Avdel Uk Limited Method of manufacturing a blind threaded insert
US20040035506A1 (en) * 2000-11-09 2004-02-26 Keith Denham Method of manufacturing a blind threaded insert
EP1293578A3 (de) * 2001-09-14 2004-10-06 Samhwa Steel Co., Ltd. Vergüteter Stahldraht mit ausgezeichneten Kaltverformungseigenschaften
US20040206426A1 (en) * 2001-09-14 2004-10-21 Samhwa Steel Co., Ltd. Quenched and tempered steel wire with excellent cold forging properties
EP1293578A2 (de) * 2001-09-14 2003-03-19 Samhwa Steel Co., Ltd. Vergüteter Stahldraht mit ausgezeichneten Kaltverformungseigenschaften
US7387694B2 (en) * 2002-10-10 2008-06-17 Rexroth Star Gmbh Method of making a hardened steel part, especially a roll load-bearing steel part
US20040108027A1 (en) * 2002-10-10 2004-06-10 Norbert Siebenlist Method of making a hardened steel part, especially a roll load-bearing steel part
US10669562B2 (en) 2003-10-24 2020-06-02 Selexis S.A. High efficiency gene transfer and expression in mammalian cells by a multiple transfection procedure of MAR sequences
US9879297B2 (en) 2003-10-24 2018-01-30 Selexis Sa High efficiency gene transfer and expression in mammalian cells by amultiple transfection procedure of MAR sequences
US20070178469A1 (en) * 2003-10-24 2007-08-02 Selexis S.A. High efficiency gene transfer and expression in mammalian cells by a multiple transfection procedure fo mar sequences
US20070006947A1 (en) * 2003-12-18 2007-01-11 Soon-Tae Ahn Steel wire for cold forging having excellent low temperature impact properties and method of producing the same
US20070256767A1 (en) * 2003-12-18 2007-11-08 Samhwa Steel Co., Ltd. Steel Wire for Cold Forging Having Excellent Low Temperature Impact Properties and Method of Producing the Same
EP1697552A4 (de) * 2003-12-18 2011-01-12 Samhwa Steel Co Ltd Stahldraht zum kaltschmieden mit hervorragenden kälteschlageigenschaften und herstellungsverfahren dafür
EP1697552A1 (de) * 2003-12-18 2006-09-06 Samhwa Steel Co., Ltd. Stahldraht zum kaltschmieden mit hervorragenden kälteschlageigenschaften und herstellungsverfahren dafür
US8293032B2 (en) * 2005-03-30 2012-10-23 Honda Motor Co., Ltd. Titanium alloy bolt and its manufacturing process
US20060234800A1 (en) * 2005-03-30 2006-10-19 Honda Motor Co., Ltd. Titanium alloy bolt and its manufacturing process
US20080264524A1 (en) * 2005-10-31 2008-10-30 Keiichi Maruta High-Strength Steel and Metal Bolt Excellent In Character of Delayed Fracture
WO2012119764A1 (en) 2011-03-08 2012-09-13 Società Bulloneria Europea S.B.E. Spa A high load flanged fastener to be installed by tensioning tools
US10941799B2 (en) 2014-10-13 2021-03-09 Monogram Aerospace Fasterners, Inc. Deformable sleeve nut and a method of manufacturing
WO2017015202A1 (en) * 2015-07-17 2017-01-26 Felix Sorkin Compact anchor for post-tensioned concrete segment

Also Published As

Publication number Publication date
DE1508416A1 (de) 1969-10-23
DE1508416B2 (de) 1975-11-06
GB1077994A (en) 1967-08-02
DE1508416C3 (de) 1976-06-10
LU51833A1 (de) 1966-10-26
NL6611433A (nl) 1968-02-16

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