US3844848A - Production of low alloy steel wire - Google Patents
Production of low alloy steel wire Download PDFInfo
- Publication number
- US3844848A US3844848A US00416203A US41620373A US3844848A US 3844848 A US3844848 A US 3844848A US 00416203 A US00416203 A US 00416203A US 41620373 A US41620373 A US 41620373A US 3844848 A US3844848 A US 3844848A
- Authority
- US
- United States
- Prior art keywords
- rod
- wire
- low alloy
- alloy steel
- drawn
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title description 4
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 11
- 238000005482 strain hardening Methods 0.000 claims abstract description 6
- 238000010438 heat treatment Methods 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 12
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 238000005275 alloying Methods 0.000 claims description 4
- 238000010622 cold drawing Methods 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 238000005096 rolling process Methods 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 description 10
- 239000010959 steel Substances 0.000 description 10
- 230000035882 stress Effects 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 229910000975 Carbon steel Inorganic materials 0.000 description 4
- 229910019582 Cr V Inorganic materials 0.000 description 4
- 229910008458 Si—Cr Inorganic materials 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 239000010962 carbon steel Substances 0.000 description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000003921 oil Substances 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 239000011651 chromium Substances 0.000 description 2
- 239000010955 niobium Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- HBXWYZMULLEJSG-UHFFFAOYSA-N chromium vanadium Chemical compound [V][Cr][V][Cr] HBXWYZMULLEJSG-UHFFFAOYSA-N 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 125000004433 nitrogen atom Chemical group N* 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
Definitions
- the present invention relates to low alloy steel wire.
- the mechanical properties of drawn carbon-steel wire can be manipulated and controlled by subjecting the wire to oil quench hardening and tempering. It would be desirable to be able to treat low alloy steel so as to'produce wire which has better mechanical'properties than oil quench hardened and tempered wire, espe- 2 (preferably 28 percent); heating the wire leaving the die to 300450C (preferably 420C and forcibly cooling the wire.
- the heat treatment to produce the pearlite structure lower relaxation- 10 preferably comprises heating above the AC point
- Great Britain Pat. No. 748,357 describes a method ofli to d h ldi t a temperature b tw 550 treating cold drawn wire, in which the wire is drawn to d 700C h preferred temperature b i 50C f its final Size in a die and, as 1631/65 the 118,15 heated lowed by cooling in air.
- the material is first given a heat treatment involving heating to a temperature 50-150C above the AC point, air cooling to just above the Ms point, and reheating to 450-650C, followed by air cooling. Then follows multi-hole cold drawing to the finished size, with a reduction in area of at least 40 percent.
- the finished wire is tempered, preferably at 440C or higher, without tensile stress or quenching.
- the steel has a high silicon content.
- the present invention provides a method of producing low alloy steel wire from low alloy steel rod, the method comprising heat treating the rod to produce a pearlite structure; cold drawing the rod to initiate work hardening and thereby raise the tensile strength; drawing the part-drawn rod through a drawing die to reduce As-rolled rod (5 mm diameter) of each steel composition was initially austenitised, cooled to 650C and held at this temperature, and then allowed to cool in air; this provided a pearlite structure. The rod was cleaned, provided with a drawing coat, and drawn to a diameter of 4.4 mm; this initiated work hardening and raised the tensile strength.
- the part-drawn rod was then further drawn, during which operation it was subjected to a reduction in area of 25 percent, to finish at 3.85 mm diameter. As soon as the wire emerged from the die, it was heated to 420C and then quenched from this temperature by forcible cooling using an air blast or water spray.
- the resulting wire had a tensile strength ranging from 158 to 175 kgf/mm
- the mechanical properties of the wire obtained from each steel composition are shown in Table 11.
- the properties of the as drawn wire (not the cross-sectional area by between 10 and 40 percent heated after drawing) are shown for comparison.
- low temperature heat treatment under tension may promote a dislocation locking mechanism involving interstitial carbon and nitrogen atoms, creating a condition similar to strain ageing.
- Additions of such alloying elements as chromium, silicon, and vanadium may promote an interaction between dislocations and alloy carbides, resulting in a further increase in flow stress.
- the rod can be given the pearlite structure by a heat treatment comprising controlled cooling of the rod as it leaves the hot rolling mill.
- a method of producing low alloy steel wire from low alloy steel rod comprising heat treating the rod to produce a pearlite structure; cold drawing the rod to initiate work hardening and thereby raise the tensile strength; drawing the part-drawn rod through a drawing die to reduce the cross-sectional area by between 10 and 40 percent; heating the wire leaving the die to 300450C; and forcibly cooling the wire.
- a method as claimed in claim 1, in which the heat treatment to produce a pearlite structure comprises heating above the AC point, cooling to and holding at a temperature between 550 and 700C, and then cooling in air.
- alloying elements selected from the following elements in the following ranges: Mn 0.20-l.50%, Si 0.l0-4.00%, Cr 0.l04.00%, S 0.050% maximum, P 0.050% maximum, Mo 0.l02.00%, Cu 0.l0-3.00%, Ni 0.l0-5.00%, Ti
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Metal Extraction Processes (AREA)
Abstract
Low alloy steel rod is given a pearlite structure and is then cold-drawn to initiate work hardening. The rod is then drawn through a die producing a reduction in area of between 10 and 40 percent. The wire leaving the die is heated to 300*-450*C and then forcibly cooled.
Description
United States Patent 11 1 Stacey Oct. 29, 1974 1 PRODUCTION OF LOW ALLOY STEEL 3,011,928 12/1961 Kopec et al l48/l56 WIRE 3,574,000 4/1971 Geipel et al 148/12 B 3,584,494 6/l97l Giepel et al 148/12 B Inventor: Andrew Gordon y, Norton, 3,645,805 2/1972 Hoffman et al..... 148/124 near Doncaster, England 3,711,338 1/1973 Vitelli 148/12.4
[73] Assignee: British Ropes Limited, Doncaster,
ng Primary Examiner-W. Stallard Attorney, Agent, or FirmJohnson, Dienner, Emrich, 22 F l d. N l 1 16 0v 1973 Verbeck & Wagner [21] Appl. No.: 416,203
[30] Foreign Application Priority Data [5 7] ABSTRACT Nov. 15, 1972 Great Britain 52805/72 Low nd Steel rod is given a pearme structure d i then cold-drawn to initiate work hardening. The rod is [52] US. Cl. 148/12 B, 148/l2.4 then drawn through a die producing a reduction in [5 l] ll lt. CI C2ld 9/52 area of between 0 and 40 percent h i l i [58] Field of Search 148/12 B, 12.4 the die is heated to 3 0 450 and then f ibl cooled. [56] References Cited UNITED STATES PATENTS 5 Claims, No Drawings 2,756,169 7/1956 Corson et al. l48/l2.4
1 PRODUCTION .01 LOW ALLOY STEEL WIRE The present invention relates to low alloy steel wire.
The mechanical properties of drawn carbon-steel wire can be manipulated and controlled by subjecting the wire to oil quench hardening and tempering. It would be desirable to be able to treat low alloy steel so as to'produce wire which has better mechanical'properties than oil quench hardened and tempered wire, espe- 2 (preferably 28 percent); heating the wire leaving the die to 300450C (preferably 420C and forcibly cooling the wire.
It can be seen that the reduction in area is low -40 percent); the tension on the wire leaving the die is only that needed to draw it through the die and does not necessarily produce permanent elongation; and the temperature to which the wire is heated is quite low (300-450C The heat treatment to produce the pearlite structure lower relaxation- 10 preferably comprises heating above the AC point, Great Britain Pat. No. 748,357 describes a method ofli to d h ldi t a temperature b tw 550 treating cold drawn wire, in which the wire is drawn to d 700C h preferred temperature b i 50C f its final Size in a die and, as 1631/65 the 118,15 heated lowed by cooling in air. Of course, the heat treated rod to a given temperature and then quenched, While it is will be cleaned and given a drawing coat before the inisubjected to a tensile stress sufficient to induce permati l d wi pa s. nent elongation. According to Great Britain Patent No. Th i v ntio will be described further, by way of ex- 5 the wife my be heat treated, before the fi ample only, with reference to three steel compositions, drawing operation, by heating the wire to above the viz. a carbon steel: 0.67 percent Swedish carbon steel; AC point followed by isothermal quenching to about and two low alloy steels: British Standard EN 47 75C. (chromium-vanadium) and EN 48a (silicon chro- Great Britain Patent No. l 285 998 describes a mium). The analyses of the three steels are shown in method of making low-alloy steel wire, in which wire Table 1.
TABLE 1 Specification. wt% C Mn S P Cr V Si Swedish 0.65-0.80 0.40-0.80 0.040max 0.040max 0.35max EN 47 0.45-0.55 0.50-0.80 0.050max 0.050max 0.50-0.80 0.15min 0.50max EN 48:: 0.50-0.00 0.00-0.90 0.050max 0.050max 0.55-0.85 1.35-1.65
material is first given a heat treatment involving heating to a temperature 50-150C above the AC point, air cooling to just above the Ms point, and reheating to 450-650C, followed by air cooling. Then follows multi-hole cold drawing to the finished size, with a reduction in area of at least 40 percent. The finished wire is tempered, preferably at 440C or higher, without tensile stress or quenching. The steel has a high silicon content.
Neither of these methods is applicable to a wide range of low alloy steels.
The present invention provides a method of producing low alloy steel wire from low alloy steel rod, the method comprising heat treating the rod to produce a pearlite structure; cold drawing the rod to initiate work hardening and thereby raise the tensile strength; drawing the part-drawn rod through a drawing die to reduce As-rolled rod (5 mm diameter) of each steel composition was initially austenitised, cooled to 650C and held at this temperature, and then allowed to cool in air; this provided a pearlite structure. The rod was cleaned, provided with a drawing coat, and drawn to a diameter of 4.4 mm; this initiated work hardening and raised the tensile strength.
The part-drawn rod was then further drawn, during which operation it was subjected to a reduction in area of 25 percent, to finish at 3.85 mm diameter. As soon as the wire emerged from the die, it was heated to 420C and then quenched from this temperature by forcible cooling using an air blast or water spray.
The resulting wire had a tensile strength ranging from 158 to 175 kgf/mm The mechanical properties of the wire obtained from each steel composition are shown in Table 11. The properties of the as drawn wire (not the cross-sectional area by between 10 and 40 percent heated after drawing) are shown for comparison.
TABLE 11 WIRE Cr-V Cr-V as Si-Cr Si-Cr as 0.69% C. 0.69% C drawn drawn as drawn Size mm, 3.86 3.85 3.86 3.85 3.83 3 U'l'S kgf/mm 175.2 171.8 166.0 158.9 170.0 176.5 (0.2 172.6 151.2 160.9 136.6 148.2 146.5 PS. (01 171.5 138.7 158.5 123.3 146.2 128.8 (0.01 153.3 88.0 134.5 70.9 130.2 77.3 1. of P kgf/mm 132.5 68.7 106.8 53.7 112.8 58.0 P.S. (0.2 98.5 88 96.8 85.9 87.0 82.7
as (0.1 UTS (0.01 87.6 51.2 81.0 44.6 76.4 43.8 L of P (7r UTS) 75.5 40.0 64.3 33.8 65.8 32.8 EXIO" 21.1 19.6 20.3 18.7 21.2 19.3 '71- E1. 50mm 9.0 5.0 9.0 6.0 8.5 4.0 71' E1. 250mm 4.2 2.0 5.2 2.6 5.0 1.4 5 R ofA 54. 56 58 49 53 Torsion on X 22 28 .27 42 25 33 dia.
TABLE ll-(ontinued WIRE Cr-V Cr-V as Si-Cr Si-Cr as 0.69% C. 0.69% C drawn drawn as drawn Torsion quality A A A A A A Bends on mm 8 l0 l3 l4 6 9 radius.
U'IS=ullimate tensile strength L of P=limil of proportionality R of A=rcduction of area at fracture P.S=prool stress li=Youngs modulus Wire from all three steels shows a remarkable in- TABLE Ill-Continued crease in flow stress characteristics after the heat- Element weight% treatment at 420C followed by quenching, the 0.2 per- 7 g 7 i I cent proof stresses are superior to those normally Vanadium (mo/2.00 achieved by oil hardening and tempering. l l- (mo/0'50 Niobium (HO/3.00 The results obtained for the low alloy steels are mg g 7 WA, H I nificantly better than those for the carbon steel. A posl claim,
sible explanation is that low temperature heat treatment under tension may promote a dislocation locking mechanism involving interstitial carbon and nitrogen atoms, creating a condition similar to strain ageing. Additions of such alloying elements as chromium, silicon, and vanadium, may promote an interaction between dislocations and alloy carbides, resulting in a further increase in flow stress.
Alloying elements which appear to have an influence on flow stress are listed in Table lll together with the percentage ranges within which the influence appears to be significant.
Various modifications may be made within the scope of the invention. For instance, the rod can be given the pearlite structure by a heat treatment comprising controlled cooling of the rod as it leaves the hot rolling mill.
l. A method of producing low alloy steel wire from low alloy steel rod, the method comprising heat treating the rod to produce a pearlite structure; cold drawing the rod to initiate work hardening and thereby raise the tensile strength; drawing the part-drawn rod through a drawing die to reduce the cross-sectional area by between 10 and 40 percent; heating the wire leaving the die to 300450C; and forcibly cooling the wire.
2. A method as claimed in claim 1, in which the heat treatment to produce a pearlite structure comprises heating above the AC point, cooling to and holding at a temperature between 550 and 700C, and then cooling in air.
3. A method as claimed in claim 2, in which the holding temperature between 500 and 700C is 650C.
4. A method as claimed in claim 1, in which the heat treatment to produce a pearlite structure is carried out on rod leaving a rolling mill.
5. A method as claimed in claim 1, in which the low alloy steel of which the rod is made contains, by weight:
C 0.30-1.00 percent, and alloying elements selected from the following elements in the following ranges: Mn 0.20-l.50%, Si 0.l0-4.00%, Cr 0.l04.00%, S 0.050% maximum, P 0.050% maximum, Mo 0.l02.00%, Cu 0.l0-3.00%, Ni 0.l0-5.00%, Ti
v0.l02.00, V 2.00% maximum, N 0.50% maximum,
and Nb 0. l03.00%, the balance being Fe and impurities.
Claims (5)
1. A METHOD OF PRODUCING LOW ALLOY STEEL WIRE FROM LOW ALLOY STEEL ROD, THE METHOD COMPRISING HEAT TREATING THE ROD TO PRODUCE A PEARLITE STRUCTURE, COLD DRAWING THE ROD TO INITIATE WORK HARDENING AND THEVEBY RAISE THE TENSILE STRENGTH; DRAWING THE PART-DRAWN ROD THROUGH A DRAWING DIE TO REDUCE THE CORSSSECTIONAL AREA BY BETWEEN 10 AND 40 PERCENT; HEATING THE WIRE LEAVING THE DIE TO 300*-450=C; AND FORCIBLY COOLING THE WIRE.
2. A method as claimed in claim 1, in which the heat treatment to produce a pearlite structure comprises heating above the AC3 point, cooling to and holding at a temperature between 550* and 700*C, and then cooling in air.
3. A method as claimed in claim 2, in which the holding temperature between 500* and 700*C is 650*C.
4. A method as claimed in claim 1, in which the heat treatment to produce a pearlite structure is carried out on rod leaving a rolling mill.
5. A method as claimed in claim 1, in which the low alloy steel of which the rod is made contains, by weight: C 0.30-1.00 percent, and alloying elements selected from the following elements in the following ranges: Mn 0.20-1.50%, Si 0.10-4.00%, Cr 0.10-4.00%, S 0.050% maximum, P 0.050% maximum, Mo 0.10-2.00%, Cu 0.10-3.00%, Ni 0.10-5.00%, Ti 0.10-2.00, V 2.00% maximum, N 0.50% maximum, and Nb 0.10-3.00%, the balance being Fe and impurities.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB5280572A GB1400872A (en) | 1972-11-15 | 1972-11-15 | Production of low alloy steel wire |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3844848A true US3844848A (en) | 1974-10-29 |
Family
ID=10465383
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US00416203A Expired - Lifetime US3844848A (en) | 1972-11-15 | 1973-11-15 | Production of low alloy steel wire |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US3844848A (en) |
| JP (1) | JPS5046511A (en) |
| DE (1) | DE2356791A1 (en) |
| GB (1) | GB1400872A (en) |
| SE (1) | SE387369B (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| US4040688A (en) * | 1973-12-08 | 1977-08-09 | Industriewerk Schaeffler Ohg | Novel cylindrical rollers |
| 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 |
| US4390377A (en) * | 1981-01-12 | 1983-06-28 | Hogg James W | Novel continuous, high speed method of galvanizing and annealing a continuously travelling low carbon ferrous wire |
| EP1524323A1 (en) * | 2002-07-22 | 2005-04-20 | Suzuki Metal Industry Co., Ltd. | Process for producing oil tempered wire |
| EP1698712A1 (en) * | 2005-03-03 | 2006-09-06 | Kabushiki Kaisha Kobe Seiko Sho | Steels for high-strength springs excellent in cold workability and quality stability |
| US20120091663A1 (en) * | 2009-03-26 | 2012-04-19 | Laszlo Pelsoeczy | Nitriding Grade Steel Material Composition for Manufacturing Piston Rings and Cylinder Liners |
| CN109023123A (en) * | 2018-10-12 | 2018-12-18 | 石横特钢集团有限公司 | A kind of production method of 840MPa grades of hot rolling anchor pole reinforcing bar |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5848017B2 (en) * | 1977-12-16 | 1983-10-26 | 日「鉄」溶接工業株式会社 | Intermediate annealing method for steel wire for welding |
| US4448617A (en) * | 1980-08-05 | 1984-05-15 | Aichi Steel Works, Ltd. | Steel for a vehicle suspension spring having good sag-resistance |
| JP2802155B2 (en) * | 1990-09-21 | 1998-09-24 | 株式会社神戸製鋼所 | Method for producing high-strength steel wire without heat treatment and excellent in fatigue resistance and wear resistance |
| CN112126850B (en) * | 2020-08-24 | 2022-02-22 | 上海衍衡新材料科技有限公司 | Corrosion-resistant card clothing steel and preparation method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2756169A (en) * | 1950-10-19 | 1956-07-24 | John A Roebling S Sons Corp | Method of heat treating hot rolled steel rods |
| US3011928A (en) * | 1960-01-18 | 1961-12-05 | Morgan Construction Co | Method for heat treating hot rolled steel rods |
| 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 |
| US3645805A (en) * | 1969-11-10 | 1972-02-29 | Schloemann Ag | Production of patented steel wire |
| US3711338A (en) * | 1970-10-16 | 1973-01-16 | Morgan Construction Co | Method for cooling and spheroidizing steel rod |
-
1972
- 1972-11-15 GB GB5280572A patent/GB1400872A/en not_active Expired
-
1973
- 1973-11-13 SE SE7315320A patent/SE387369B/en unknown
- 1973-11-14 DE DE2356791A patent/DE2356791A1/en active Pending
- 1973-11-15 US US00416203A patent/US3844848A/en not_active Expired - Lifetime
- 1973-11-15 JP JP48128675A patent/JPS5046511A/ja active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2756169A (en) * | 1950-10-19 | 1956-07-24 | John A Roebling S Sons Corp | Method of heat treating hot rolled steel rods |
| US3011928A (en) * | 1960-01-18 | 1961-12-05 | Morgan Construction Co | Method for heat treating hot rolled steel rods |
| 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 |
| US3645805A (en) * | 1969-11-10 | 1972-02-29 | Schloemann Ag | Production of patented steel wire |
| US3711338A (en) * | 1970-10-16 | 1973-01-16 | Morgan Construction Co | Method for cooling and spheroidizing steel rod |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4040688A (en) * | 1973-12-08 | 1977-08-09 | Industriewerk Schaeffler Ohg | Novel cylindrical rollers |
| 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 |
| US4390377A (en) * | 1981-01-12 | 1983-06-28 | Hogg James W | Novel continuous, high speed method of galvanizing and annealing a continuously travelling low carbon ferrous wire |
| EP1524323A4 (en) * | 2002-07-22 | 2006-02-01 | Suzuki Metal Industry Co Ltd | Process for producing oil tempered wire |
| EP1524323A1 (en) * | 2002-07-22 | 2005-04-20 | Suzuki Metal Industry Co., Ltd. | Process for producing oil tempered wire |
| EP1698712A1 (en) * | 2005-03-03 | 2006-09-06 | Kabushiki Kaisha Kobe Seiko Sho | Steels for high-strength springs excellent in cold workability and quality stability |
| US20060196584A1 (en) * | 2005-03-03 | 2006-09-07 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Steels for high-strength springs excellent in cold workability and quality stability |
| US7618498B2 (en) | 2005-03-03 | 2009-11-17 | (Kobe Steel, Ltd.) | Steels for high-strength springs excellent in cold workability and quality stability |
| US20120091663A1 (en) * | 2009-03-26 | 2012-04-19 | Laszlo Pelsoeczy | Nitriding Grade Steel Material Composition for Manufacturing Piston Rings and Cylinder Liners |
| US9650702B2 (en) * | 2009-03-26 | 2017-05-16 | Federal-Mogul Burscheid Gmbh | Nitridable piston rings |
| CN109023123A (en) * | 2018-10-12 | 2018-12-18 | 石横特钢集团有限公司 | A kind of production method of 840MPa grades of hot rolling anchor pole reinforcing bar |
Also Published As
| Publication number | Publication date |
|---|---|
| GB1400872A (en) | 1975-07-16 |
| SE387369B (en) | 1976-09-06 |
| DE2356791A1 (en) | 1974-05-16 |
| JPS5046511A (en) | 1975-04-25 |
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