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US3926687A - Method for producing a killed steel wire rod - Google Patents

Method for producing a killed steel wire rod Download PDF

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Publication number
US3926687A
US3926687A US504270A US50427074A US3926687A US 3926687 A US3926687 A US 3926687A US 504270 A US504270 A US 504270A US 50427074 A US50427074 A US 50427074A US 3926687 A US3926687 A US 3926687A
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percent
rolling
temperature
finish
steel
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Hisashi Gondo
Naoki Eguchi
Takafumi Yoshimura
Masaki Araki
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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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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

Definitions

  • the balance being the iron and unavoidable impurities, which comprises heating a steel having the above composition at a temperature not lower than 1,- l50C, conducting an intermediate rolling and/or finish rolling at a temperature between 700 and l,050C, controlling the colling rate from the end of the hot rolling to a coiling to 40 to 350C/sec., and controlling the cooling rate from the coiling to gathering to 1 to l5"C/sec. to obtain hot rolled steel wire rods and bars having excellent workability and spot weldability and having a tensile strength not lower than 50 kg/mm and a reduction of area not lower than 50 percent.
  • the present invention relates to a method for producing a killed steel wire rod (including bar) having a tensile strength of 50 kg/mm to H kg/mm as hot rolled and having excellent workability especially coldworking cold-forging and drawability and spot weldability. Descriptions will be made for steel wire rods and bars all together.
  • One of the objects of the present invention is to provide a method for producing a high-strength steel wire rod having a structure of good workability by controlling the temperature of the rolled steel material and also controlling the cooling rate after the finish rolling, and the steel material obtained by the present invention is useful for high-strength bolts, PC wire, metal networks, umbrella ribs, spring washers and springs.
  • the steel wire rod according to the present invention shows both high strength and excellent toughness, so that it is possible to obtain a product having a similar or better quality than that of a conventional product obtained by a secondary working (mainly of heat treatment) even when the secondary working of the wire rod is considerably omitted.
  • the conventional practice is as follows.
  • a high-carbon steel wire rod such as a plain carbon steel containing 0.45 percent C is subjected to cold wire drawing to a required size, then to a spheroidizing annealing so as to facilitate cold-forgeability to skin-pass working to heading and threading works into bolt shape, to water or oil quenching and lastly 'to tempering to obtain 80 to l 10 kg/mm strength.
  • the wire rod as hot rolled is subjected only to slight skin-pass drawing into a required size, and then to heading and threading works, thereby a bolt having to kg/mm of tensile strength without any defect can be obtained, and heat treatments such as spheroidizing annealing, quenching and tempering can be omitted and thus a high level of economy is assured.
  • the present invention when the present invention is applied to production of PC wires (prestressed concrete wires) it is sufficient that the wire rod of the present invention is subjected only to slight skin-pass drawing and shape working including indent work for application is prestressed concrete products for example, and thus the patenting heat treatment which is conventionally done can be omitted. Yet a wire having high tensile strength and very excellent spot weldability can be obtained.
  • the chemical composition of the wire rod according to the present invention contains as basic elements 0.02 to 0.20 percent C, 0.03 to 0.90 percent Si and 1.00 to 1.85 percent Mn together with one or more of not more than 0.05 percent Nb, not more than 0.08 percent V, not more than 0.25 percent Ti, not more than 0.30 percent Zr, not more than 0.005 percent B andnot more than 0.40 percent Cr, and contains Al in an amount as contained in an ordinary killed-steel with the balance being iron and unavoidable impurities.
  • the lower limit of 0.002 percent for carbon has been set for the reason that if the carbon content is less than 0.02 percent strength is lowered and desired results can not be obtained, while if the carbon content is beyond 0.20 percent workability and spot weldability lower and thus the upper limit set at 0.20 percent.
  • Si is a deoxidizing element and also is effective to increase strength by solid solution hardening. For this purpose it is added up to 0.90 percent, beyond which the workability lowers and the addition is uneconomical.
  • the lower limit is set at 0.03 percent which is necessary for deoxidation.
  • Mn is an element effective to improve hardenability and contributes to facilitate the bainite hardening during cooling after the finish rolling and to convert and refine a bainite structure of the steel matrix, and to improve toughness.
  • the lower limit of Mn is set at 1.00 percent because below this limit the above effects can not be obtained and the upper limit is set at 1.85 percent from the consideration for minimizing adverse effect by the manganese segregation as well as economy.
  • Nb, V, Ti and Zr are added for the purpose of forming their carbides and nitrides and precipitating them finely during the rolling to suppress recrystallization of austenite grains of the wire rod during the hot rolling so as to refine the ferritepearlite or bainite structure produced during the cooling step, as well as for the purpose of increasing strength by precipitating the carbides and nitrides in a super-fine condition.
  • the carbides and nitrides of these elements must be dissolved in solid solution into the steel matrix during the billet heating prior to the rolling of the wire rod and for this purpose, it is necessary to heat the billet at a temperature higher than 1150C.
  • the upper limits of these elements are set in view of the contents of C and N in the steel and from the economical point.
  • Cr is added in a small amount for improving hardenability, but as shown in the examples Cr needs not be added in case of a wire rod of small diameter. However, it is desirable to add Cr in an amount not more than 0.40 percent in case of a wire rod of diameter more than about 8 mm.
  • the upper limit of 0.40 percent in this case is set from the reason that Cr addition beyond this limit will not produce any remarkable effect and result only in uneconomy.
  • B is also added for the purpose of improving hardenability, and its addition is defined to the minimum amount necessary for this purpose.
  • Ti is necessary to attain fully the effect of B, but Ti is added in the present invention for attaining precipitation hardening by precipitation of fine titanium carbide and nitride, increasing strength through refinement of the grains and improving weldability.
  • the upper limit of Ti is set at 0.25 percent from the limitation in the heating temperature prior to the wire rod rolling as well as from the economical point.
  • the billet heating temperature for the wire rod rolling is lower than that for the rolling of other products, and is usually between 1,050 and 1,150C.
  • the billet heating temperature should be not lower than 1 150C, preferably not lower than 1200C in order to assure complete solid solution of the precipitates so as to fully attain the precipitation hardening due to the carbides and nitrides of Nb, V, Ti, Zr and B.
  • the rolling temperature is controlled as under.
  • a cooling device is not generally used during the rolling and the rolled material is cooled gradually by a small amount of cooling water used to cool the rolls, but in the step of finish rolling, the temperature of the rolled material is raised by the heat of plastic working due to increased rolling speed.
  • This ordinary rolling method is referred to as OR hereinafter.
  • One of the features of the present invention lies in that the temperature of the steel material during the rolling is controlled by a suitable cooling device. (This method is referred to as CR hereinafter).
  • the cooling device must have a cooling capacity large enough to cool the steel to a prescribed temperature in a short time because the rolling speed is high, and must be capable to adjust to cooling in association with a thermometer.
  • FIG. 1 shows the temperature control during the wire rod (8 mm diameter) rolling.
  • FIG. 2 shows relations between tensile strength and reduction of area of the wire rod as rolled.
  • FIG. 3 shows relations between the finish outlet temperature and tensile strength, yield point and reduction of area.
  • FIG. 4 shows similarly relations between yield point and relaxation-loss.
  • FIG. 5 is a microphotograph X200 of the wire rod obtained by the present invention.
  • FIG. 6 is a graph showing transition curves of impact values.
  • the rolling apparatus includes a rough rolling mill of 7 stands, a first intermediate rolling mill of 6 stands, a second intermediate rolling mill of 2 stands, and a finish rolling mill of 10 stands.
  • the finish rolling mill 8 stands are used for production of wire rods of 8 mm diameter, and four stands are used for production of wire rods of 13 mm diameter.
  • the billet size is l 15 mm square, and 18 m length.
  • the size of the intermediate products is 24 mm diameter at the stand No. 13 and 20 mm diameter at the stand No. 15.
  • No. 3 shows the ordinary rolling (OR) in which the heating temperature is set at 1200C, and the temperature of the rolled material gradually lowers from the rough rolling to the second intermediate rolling and gets about 930C at the finish inlet, but increases when the rolled material enters the finish rolling mill group and gets a finish temperature of about l0O5C.
  • No. 21 is an example of OR in which the heating temperature is 1085C, and relatively lower than in No. 3, but almost the same tendencies take place.
  • No. 2 is an example of the controlled rolling (CR) in which the heating temperature is 1 C and a cooling device is provided between the first intermediate rolling mill stand group and the second intermediate rolling mill stand group and between the second intermediate rolling mill stand group and the finish rolling mill stand group to adjust the cooling and cool the rolled material to a prescribed temperature. Namely the same procedures are taken until the rolled material passes the first intermediate rolling mill stand group as in case of OR, but after the stand No. 13, the rolled material is cooled to 910C and rolled by the second intermediate rolling mill, cooled to 810C after the stand No. 15, enters between the finish rolls and finished at 860C.
  • CR controlled rolling
  • No. 20 is an example of CR in which the temperature of the rolled material is further lowered and the material enters the finished rolling mill stand group at 750C. The results obtained by the example will be described hereinafter.
  • the heating temperature should be not lower than ll50C and is desirably as high as possible.
  • the upper limit of the heating temperature is set at 1200C in this example, because an excessively high temperature is not economical.
  • the above mentioned nitrides and carbides being to precipitate as the temperature lowers but not too much around 1000C.
  • the austenite phase of the steel mate rial is converted into a deformed structure by the rolling, but immediately recrystallizes because the temperature is high enough and is converted in the worked structure by the next rolling and then recrystallizes.
  • the present inventors have studied the above structural changes by investigating the intermediate material having a frozen structure caused by quenching in the course of a rolling, and have found that the carbide and nitride forming elements, such as Nb, delays the recrystallization, and that the recrystallization proceeds immediately at a rolling temperature above about 910C, but the structure remains as a non-recrystallized phase below 910C. It is predicted that this temperature varies depending on the rolling speed, namely the passing time between the stands. However, the recrystallization is not caused during the pass time (about6 seconds) between the stand No. 13 and the stand No. 14 and between the stand No. 15 and'the stand No. 16, and the boundry temperature for the recrystallization and the non-recrystallization at the pass time of 6 to 6.5 m/sec. over the stand No. 15 is about 910C.
  • this boundary temperature is considered to be higher than 910C, but it is difficult to confirm by experiments whether the recrystallized austenite grains are formed or not.
  • the present inventors classified the finish rolled wire rods into the structure in which the worked structure remains and the structure in which the worked structure is not retained through observation of their microstructures, and investigated them in connection with the finish inlet temperature, and found the worked structure is retained when the finish inlet temperature is not higher than 910C even if the finish temperature is higher than 910C, and thus discovered that if an adjustment is made in the preceding stands so as to maintain the temperature at the stand No. 16, namely the finish inlet temperature not higher than 910C, the rolling is regarded to be within the non-recrystallization zone.
  • This technical thought provides means which are applicable to other type of rolling mills. For this purpose, the rolling degrees in this example are shown as under.
  • the rolling degree from the billet of 115 mm square to the intermediate rod of mm diameter (finish inlet) is about 97 percent in the reduction of area
  • the rolling degree from the intermediate rod of 20 mm diameter to the final product of 8 mm diameter is 84 percent
  • the degree from the intermediate rod of 20 mm diameter to the final product of 13 mm diameter is 60 percent
  • the pass times in the finish rolling mill stand group is 8 passes for the rolling from the 20 mm diameter to the 8 mm diameter
  • the cooling of the wire rod after the finish rolling is divided into two steps; in the first step the surface temperature is cooled by about 100 to 300C within a few seconds using a leading and cooling device equipped with pipes filled with water as used in the wire rolling mill and the wire rod is coiled to a desired temperature between 850 and 600C. In the second step, the cooling is done at an adequate rate between 1 and 15C/sec. using a uniform cooling device such as disclosed in the Japanese patent publications Sho 42-15463 and Sho 42-18894 and the coil is gathered. Thus, the cooling rate after the finish rolling is 2 to 15C/sec. in average through the first and second steps.
  • the fine austenite grains are obtained by the controlled rolling as above, and yet in the course of transformation of the austenite into a ferrite-pearlite or bainite structure, the structure gets finer if the cooling rate is increased. thus improving the strength and toughness. Meanwhile the nitrides and carbides precipitated on the dislocation, which is induced in the hot rolling are coherent with the 'ferritic matrix and these precipitates harden the ferritephase remarkably. This precipitation varies depending on the cooling rate and thus it is very important to adjust the cooling rate. Namely, the adjustment of cooling has two distinctive metallurgical significances as above.
  • Table l l (2), and Table .2 show chemical compositions, the relation between the rolling method and temperature and mechanical properties.
  • FIGS. 2 and 3 show, respectively, the relation between tensile strength and reduction of area, between tensile strength and yield point, and between tensile strength and the finish outlet temperature.
  • All of the steels of the present invention were prepared in LD convertor, but there is no special limitation in the steel-making method.
  • the steel of the present invention has considerably high strength and high ductility even when rolled by the ordinary rolling method.
  • the steels No. 1, No. 21, No. 25 and No. 27 show tensile strength of about 55 to kg/mm and reduction of area of 77 to 70 percent as comparedwith tensile strength of 55 to 70 kg/mm and drawability of 65 to 55 percent of an ordinary carbon steel and thus these steels show relatively high reduction of area in comparison with the tensile strength.
  • the CR materials are related by the arrow mark to the OR materials.
  • the steel No. 2 shows only slight effect of CR due to the low heating temperature of 1150C, but shows improvement of yield point as shown in FIG. 3.
  • Steels No. 4 and No. 5 show remarkable increase of reduction of area, and these steels show remarkable improvement of workability instead of slight increase of yield point (see Table 3). This is due to the fact that the intermediate rolling temperature was set in the order of 700C and the finish temperature was lowered as shown in Table 'l-(2).
  • FIG. 3 shows effects of the finish outlet temperature.
  • the finish outlet temperature: of the OR material is about 1000C and that of the CR material is about 950 to 780C.
  • tensile strength and yield point lower and reduction of area increases when the finish outlet temperature is below 850C. It is between about 850 and 950C that tensile strength and yield point increase while reduction of area does not change.
  • the fact that the steel of the present invention has always higher reduction of area than the ordinary material having the same level of strength is mainly due to the effect by the refinement of the ferrite-pearlite structure as shown in FIG. 5.
  • the ferrite grain size obtained by the controlled rolling temperature is a very fige grain having a grain size number larger than No. 1
  • FIG. 6 shows the transition curves of Charpy impact values, and it is clearly shown by this figure that the transition temperature is lowered remarkably by the controlled rolling temperature.
  • Fatigue limil determined after 10 times.
  • a method for producing high tensile strength steel wire rods and bars having a basic composition compris- C 0.02 to 0.20 percent Si 0.03 to 0.90 percent Mn 1.00 to 1.85 percent together with one or more selected from the group consisting of Nb 5 0.05 percent V 0.08 percent 0.25 percent Zr 0.30 percent Cr 0.40 percent B 5 0.005 percent with the balance being the iron and unavoidable impurities, which comprises heating a steel having above composition at a temperature not lower than 1,150C. conducting intermediate rolling and/or finish rolling at a temperature between 700 and 1050C. controlling the cooling rate from finish of the hot rolling to a coiling to 40 to 350C/sec., and controlling the cooling rate from the coiling to gathering to 1 to 15C/sec. to obtain hot rolled steel wire rods and bars having excellent workability and spot weldability and having a tensile strength not lower than 50 kg/mm and a reduction of area not lower than 50 percent.
  • the steel wire rods and bars contain one or more of not more than 0.05 percent Nb, not more than 0.08 percent V, not more than 0.25% Ti and not more than 0.30 percent Zr, in addition to the basic composition.

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  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
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  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
US504270A 1973-09-10 1974-09-09 Method for producing a killed steel wire rod Expired - Lifetime US3926687A (en)

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Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2913584A1 (de) * 1978-04-05 1979-10-11 Nippon Steel Corp Verfahren zur herstellung von bainitischem stahlblech
US4279646A (en) * 1978-12-25 1981-07-21 Daido Tokushuko Kabushiki Kaisha Free cutting steel containing sulfide inclusion particles with controlled aspect, size and distribution
EP0058016A1 (de) * 1981-01-27 1982-08-18 Kabushiki Kaisha Kobe Seiko Sho Verfahren zur Herstellung von Stahldraht oder Stabstahl mit hoher Dehnbarkeit und Festigkeit
US4474627A (en) * 1982-04-22 1984-10-02 Ugine Aciers Method of manufacturing steel bars and tubes with good mechanical characteristics
FR2558174A1 (fr) * 1984-01-13 1985-07-19 Sumitomo Metal Ind Procede pour la production de barres ou fils d'acier ayant une structure spheroidale de cementite amelioree
WO1986001231A1 (en) * 1984-08-06 1986-02-27 The Regents Of The University Of California Controlled rolling process for dual phase steels and application to rod, wire, sheet and other shapes
US4584032A (en) * 1982-12-10 1986-04-22 Daido Steel Company Limited Bolting bar material and a method of producing the same
US4594113A (en) * 1984-05-30 1986-06-10 Von Roll Ag. Process for producing reinforcing steel in the form of rods or rod wire
US4604146A (en) * 1980-11-08 1986-08-05 Sumitomo Metal Industries, Ltd. Process for manufacturing high tensile steel wire
US4605449A (en) * 1981-05-19 1986-08-12 Arbed S.A. Process for producing a rolled steel product having high weldability, a high yield strength and a good notch impact toughness at very low temperatures
US5252153A (en) * 1991-06-14 1993-10-12 Nippon Steel Corporation Process for producing steel bar wire rod for cold working
US5554233A (en) * 1994-05-26 1996-09-10 Inland Steel Company Cold deformable, high strength, hot rolled bar and method for producing same
US6017274A (en) * 1997-09-02 2000-01-25 Automotive Racing Products, Inc. Method of forming a fastener
US6682613B2 (en) 2002-03-26 2004-01-27 Ipsco Enterprises Inc. Process for making high strength micro-alloy steel
US20040101432A1 (en) * 2002-04-03 2004-05-27 Ipsco Enterprises Inc. High-strength micro-alloy steel
CN102978362A (zh) * 2012-11-27 2013-03-20 南京钢铁股份有限公司 一种超低碳纤维钢的控热控冷工艺
PL424691A1 (pl) * 2018-02-27 2019-09-09 Solvera Gawel Technology Spółka Akcyjna Sposób wytwarzania drutu ciągniętego, zwłaszcza do zastosowania jako materiał wsadowy do kucia na zimno elementów złącznych
CN111235466A (zh) * 2020-02-26 2020-06-05 江苏省沙钢钢铁研究院有限公司 一种TiC弥散强化复相钢筋及其生产方法
CN113151653A (zh) * 2021-02-26 2021-07-23 邢台钢铁有限责任公司 一种大规格中碳钢盘条的生产方法

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5734333B2 (de) * 1974-06-21 1982-07-22
JPS5215407A (en) * 1975-07-29 1977-02-05 Nippon Steel Corp Continuous heat treatment method for wire rods
JPS5286919A (en) * 1976-01-13 1977-07-20 Kobe Steel Ltd High strength steel superior in workability and weldability and its pr eparation
JPS5921369B2 (ja) * 1976-10-25 1984-05-19 新日本製鐵株式会社 伸線加工性が優れた高張力高炭素鋼線材の製造法
JPS5476421A (en) * 1977-12-01 1979-06-19 Nippon Steel Welding Prod Eng Intermediate annealing method for welding steel wire
JPS5910415B2 (ja) * 1978-12-27 1984-03-08 新日本製鐵株式会社 耐応力腐食割れ性の優れた高張力線材及び棒鋼の製造法
JP2802155B2 (ja) * 1990-09-21 1998-09-24 株式会社神戸製鋼所 耐疲労性および耐摩耗性に優れた熱処理省略型高張力鋼線材の製造方法
KR100435468B1 (ko) * 1999-12-21 2004-06-10 주식회사 포스코 송전선 보강용 선재의 제조방법

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US3231432A (en) * 1964-10-08 1966-01-25 Morgan Construction Co Process for the quenching of hot rolled rods in direct sequence with rod mill
US3574000A (en) * 1968-02-15 1971-04-06 Huettenwerk Oberhausen Ag High flexibility steel wire and method of treating same
US3584494A (en) * 1968-05-21 1971-06-15 Huettenwerk Oberhausen Ag High-flexibility steel wire and method of treating same
US3711338A (en) * 1970-10-16 1973-01-16 Morgan Construction Co Method for cooling and spheroidizing steel rod
US3783043A (en) * 1967-07-21 1974-01-01 Templeborough Rolling Mills Lt Treatment of hot-rolled steel rod

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DE2133744B2 (de) * 1971-07-07 1973-07-12 August Thyssen-Hütte AG, 4100 Duisburg Die verwendung eines vollberuhigten stahles fuer gegenstaende aus warmgewalztem band

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3231432A (en) * 1964-10-08 1966-01-25 Morgan Construction Co Process for the quenching of hot rolled rods in direct sequence with rod mill
US3783043A (en) * 1967-07-21 1974-01-01 Templeborough Rolling Mills Lt Treatment of hot-rolled steel rod
US3574000A (en) * 1968-02-15 1971-04-06 Huettenwerk Oberhausen Ag High flexibility steel wire and method of treating same
US3584494A (en) * 1968-05-21 1971-06-15 Huettenwerk Oberhausen Ag High-flexibility steel wire and method of treating same
US3711338A (en) * 1970-10-16 1973-01-16 Morgan Construction Co Method for cooling and spheroidizing steel rod

Cited By (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2913584A1 (de) * 1978-04-05 1979-10-11 Nippon Steel Corp Verfahren zur herstellung von bainitischem stahlblech
US4279646A (en) * 1978-12-25 1981-07-21 Daido Tokushuko Kabushiki Kaisha Free cutting steel containing sulfide inclusion particles with controlled aspect, size and distribution
US4604146A (en) * 1980-11-08 1986-08-05 Sumitomo Metal Industries, Ltd. Process for manufacturing high tensile steel wire
EP0058016A1 (de) * 1981-01-27 1982-08-18 Kabushiki Kaisha Kobe Seiko Sho Verfahren zur Herstellung von Stahldraht oder Stabstahl mit hoher Dehnbarkeit und Festigkeit
US4605449A (en) * 1981-05-19 1986-08-12 Arbed S.A. Process for producing a rolled steel product having high weldability, a high yield strength and a good notch impact toughness at very low temperatures
US4474627A (en) * 1982-04-22 1984-10-02 Ugine Aciers Method of manufacturing steel bars and tubes with good mechanical characteristics
US4584032A (en) * 1982-12-10 1986-04-22 Daido Steel Company Limited Bolting bar material and a method of producing the same
FR2558174A1 (fr) * 1984-01-13 1985-07-19 Sumitomo Metal Ind Procede pour la production de barres ou fils d'acier ayant une structure spheroidale de cementite amelioree
US4604145A (en) * 1984-01-13 1986-08-05 Sumitomo Metal Industries, Ltd. Process for production of steel bar or steel wire having an improved spheroidal structure of cementite
US4594113A (en) * 1984-05-30 1986-06-10 Von Roll Ag. Process for producing reinforcing steel in the form of rods or rod wire
AU590212B2 (en) * 1984-08-06 1989-11-02 Regents Of The University Of California, The Controlled rolling process for dual phase steels and application to rod, wire, sheet and other shapes
US4619714A (en) * 1984-08-06 1986-10-28 The Regents Of The University Of California Controlled rolling process for dual phase steels and application to rod, wire, sheet and other shapes
WO1986001231A1 (en) * 1984-08-06 1986-02-27 The Regents Of The University Of California Controlled rolling process for dual phase steels and application to rod, wire, sheet and other shapes
US5252153A (en) * 1991-06-14 1993-10-12 Nippon Steel Corporation Process for producing steel bar wire rod for cold working
US5554233A (en) * 1994-05-26 1996-09-10 Inland Steel Company Cold deformable, high strength, hot rolled bar and method for producing same
US6017274A (en) * 1997-09-02 2000-01-25 Automotive Racing Products, Inc. Method of forming a fastener
US6682613B2 (en) 2002-03-26 2004-01-27 Ipsco Enterprises Inc. Process for making high strength micro-alloy steel
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JPS5051920A (de) 1975-05-09
JPS5420931B2 (de) 1979-07-26

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