US3207637A - Structural steel and process for making same - Google Patents
Structural steel and process for making same Download PDFInfo
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- US3207637A US3207637A US160990A US16099061A US3207637A US 3207637 A US3207637 A US 3207637A US 160990 A US160990 A US 160990A US 16099061 A US16099061 A US 16099061A US 3207637 A US3207637 A US 3207637A
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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
- C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
Definitions
- Our present invention relates to the production of structural reinforcing rods and the like from steel.
- Another specific object of the invention is to provide a ribbed rod, known as deformed bar, having the physical characteristics set forth above.
- a further object of this invention is to provide a process for producing structural steel of such fine grain size that the aforestated desiderata of high elastic limit and deformability in the cold state can be realized along with a correspondingly great tensile strength, a large rate of resilient elongation and the ability of the cold-deformed element to return without rupture to its original state.
- composition when hot-rolled into a rod as more particularly described hereinafter, exhibits without further treatment the following physical characteristics:
- a rolling process according to the present invention which has been found to result in an extraordinary refine- 3,207,037 Patented Sept. 21, 1955 ment of the grain structure of the steel and a corresponding toughness thereof, requires for instance the following working conditions to be maintained:
- a very high roller pressure that produces a 12% to 15% reduction in the cross-sectional area of the Work piece in the terminal rolling stage, preferably during each of the last three finishing passes;
- a rapid cooling after rolling the temperature being reduced from a level of substantially 800 C. at the last rollers to about 500 C. by forced cooling (e.g. with circulating air, water sprays and/0r refrigerated supporting surfaces) at a rate which for rods of the usual diameters (e.g. from 6 to 40 mm.) should be at least 30% faster than the cooling time under normal ambient conditions; thus, with rods of 10 mm. diameter, for example, approximately seconds of cooling time are desirable in lieu of the usual seconds.
- forced cooling e.g. with circulating air, water sprays and/0r refrigerated supporting surfaces
- FIG. 1 a diagrammatic illustration of the preferred rolling process according to the invention and in FIG. 2 a deformed bar produced by this process and bent about a mandrel.
- the bar stock 10, of diameter d is passed successively between roller pairs 13' and 13", 12 and 12", 11' and 11" which in practice form part of a single pair of cylinders and represent the last three stages of a rolling mill, only the rollers effective in one dimension of compression being visible.
- the stock 10 is successively reduced by these rollers to diameters d d and d, the latter being its final diameter and being assumed to be about 10 mm.
- the rollers also serve to impress upon the surface of the stock a ribbed profile to produce a so-called deformed bar 10.
- the successive compressions of the stock to diameters d d and d involve each a step-down ratio of about 14: 13 corresponding to the aforestated cross-sectional reduction. This takes place in the temperature range of 800 to 900 C. with subsequent air cooling to 500 C. in about 100 seconds through suitable control of ambient conditions.
- FIG. 2 shows how the bar 10' produced by the process of FIG. 1 can be bent through 180 about a mandrel 20 Whose diameter D is only five times as great as the bar diameter d
- the bar so bent can also be returned to its original straight position, shown in dot-dash lines, without cracking.
- a process for making a bar of fine-grain structural steel comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by Weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of .silicon, and iron as substantially the entire remainder, to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
- each of three final rolling steps involves a reduction in crosssectional area of said stock by substantially 12 to 15 3.
- a process for making a bar of fine-grain structural steel comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in cross-sectional area by substantially 12 to 15% at each of three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
- a process for making a bar of weldable fine-grain structural steel comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, 0.15 to 0.50% by weight of chromium, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in cross-sectional area by substantially 12 to 15% at each of: three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
- a process for making a bar of fine-grain structural steel comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by Weight of manganese, 0.50 to 1.50% by weight of silicon, 0.10 to 0.20% by weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in cross-sectional area by substantially 12 to 15% at each of three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
- a process for making a bar of weldable fine-grain structural steel comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, 0.15 to 0.50% by weight of chromium, 0.10 to 0.20% by weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in crosssectional area by substantially 12 to 15% at each of three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
- said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, and iron as substantially the entire remainder produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 5 00 C.
- a bar of Weldable fine-grain alloy steel with a tensile strength of at least kg./mm., a yield point of at least 50 kg./mrn. and a high degree of cold deformability said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by Weight of silicon, 0.15 to 0.50% by weight of chromium, and iron as substantially the entire remainder, produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
- a bar of fine-grain alloy steel with a tensile strength of at least 75 kg./mm., a yield point of at least 50 kg./ mm. and a high degree of cold deformability said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by Weight of silicon, 0.10 to 0.20% by Weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron substantially as the entire remainder, produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
- a bar of weldable fine-grain alloy steel with a tensile strength of at least 75 kg./mm., a yield point of at least 50 kg./mm. and a high degree of cold deformability said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, 0.15 to 0.50% by weight of chromium, 0.10 to 0.20% by Weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron as substantially the entire remainder, produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
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Description
Sept. 21, 1965 B. MATUSCHKA ETAL 3,207,637
STRUCTURAL STEEL AND PROCESS FOR MAKING SAME Filed Dec. 21. 1961 F IG. 2
BERNHARD MATUSCHKA GIOVANNI MORINI INVENTORS.
United States Patent "ice 3,207,637 STRUCTURAL STEEL AND PROCESS FOR MAKING SAME Bernhard Matuschka, Spohrstrasse 49, Vienna, Austria, and Giovanni Morini, Giornico, Ticino, Switzerland Filed Dec. 21, 1961, Ser. No. 160,990 11 Claims. (Cl. I ls-12.4)
Our present invention relates to the production of structural reinforcing rods and the like from steel.
Heretofore the use of high-strength steels in prestressing or reinforcing rods for concrete structures or similar elements has been limited by the lack of ductility of such steels and their rupture when bent cold to a small radius. When they were used it was necessary to perform them at elevated temperatures before delivery to the building site. The inability to make on-the-job changes in the shape of these elements often required expensive reworking and resulted in delays in construction.
It is an object of this invention to provide an improved ferrous composition adapted to be used particularly for structural reinforcements of the type described.
More particularly, it is an object of the invention to provide a low-alloy steel which, when formed into a rod, will have an elastic limit greater than 45 and preferably 50 kg./mm. while being capable of cold bending through 180 and back about a mandrel whose diameter is less than seven times the rod diameter.
Another specific object of the invention, allied to the preceding one, is to provide a ribbed rod, known as deformed bar, having the physical characteristics set forth above.
It is also an object of the instant invention to provide a ferrous composition of the character described which can be easily welded.
A further object of this invention is to provide a process for producing structural steel of such fine grain size that the aforestated desiderata of high elastic limit and deformability in the cold state can be realized along with a correspondingly great tensile strength, a large rate of resilient elongation and the ability of the cold-deformed element to return without rupture to its original state.
The foregoing objects are realized, in accordance with the present invention, with the use of a steel alloy having substantially the following composition by weight:
Percent C 0.15 to 0.40 Mn 0.70 to 1.80 Si 0.50 to 1.50
Fe, remainder.
This composition, when hot-rolled into a rod as more particularly described hereinafter, exhibits without further treatment the following physical characteristics:
Tensile strength-above 75 kg./mm.
Yield pointabove 50 kg./mm.
Elastic elongation-15 to in a specimen five diameters long.
These values compare favorably with those of hitherto available concrete-reinforcing rods of steel which have a yield point of 40 to 45 kg./n1m. while being bendable in the cold state through only 120, with a reverse bending of only 20, about a mandrel whose diameter equals seven times the diameter of the rod. Steel produced according to this invention, however, can be bent through an angle of 180, on a mandrel whose diameter is only five times the rod diameter, and bent back to its original position without any sign of cracking.
A rolling process according to the present invention, which has been found to result in an extraordinary refine- 3,207,037 Patented Sept. 21, 1955 ment of the grain structure of the steel and a corresponding toughness thereof, requires for instance the following working conditions to be maintained:
(1) A very high roller pressure that produces a 12% to 15% reduction in the cross-sectional area of the Work piece in the terminal rolling stage, preferably during each of the last three finishing passes;
(2) A relatively low rolling temperature at this stage which lies near or even below the upper (but above the lower) temperature limit of the pearlite-austenite transition range i.e. between substantially 800 and 900 C.;
(3) A rapid cooling after rolling, the temperature being reduced from a level of substantially 800 C. at the last rollers to about 500 C. by forced cooling (e.g. with circulating air, water sprays and/0r refrigerated supporting surfaces) at a rate which for rods of the usual diameters (e.g. from 6 to 40 mm.) should be at least 30% faster than the cooling time under normal ambient conditions; thus, with rods of 10 mm. diameter, for example, approximately seconds of cooling time are desirable in lieu of the usual seconds.
It has also been surprisingly found in accordance with a feature of this invention that an addition of about 0.15 to 0.50% of chromium, by weight, further improves the .aforedescribed characteristics of fineness of the grain and toughness of the steel.
Moreover, it was found that the addition of about 0.10 to 0.20% of aluminum and about 0.05 to 0.20% of either titanium or vanadium, by Weight, produces a still further refinement of the grain and yields a steel, especially for low-temperature uses, that readily lends itself to welding. This admixture may be used in a steel with or without the chromium component mentioned above.
The accompanying drawing shows in FIG. 1 a diagrammatic illustration of the preferred rolling process according to the invention and in FIG. 2 a deformed bar produced by this process and bent about a mandrel.
In FIG. 1 the bar stock 10, of diameter d is passed successively between roller pairs 13' and 13", 12 and 12", 11' and 11" which in practice form part of a single pair of cylinders and represent the last three stages of a rolling mill, only the rollers effective in one dimension of compression being visible. The stock 10 is successively reduced by these rollers to diameters d d and d, the latter being its final diameter and being assumed to be about 10 mm. The rollers also serve to impress upon the surface of the stock a ribbed profile to produce a so-called deformed bar 10.
The successive compressions of the stock to diameters d d and d involve each a step-down ratio of about 14: 13 corresponding to the aforestated cross-sectional reduction. This takes place in the temperature range of 800 to 900 C. with subsequent air cooling to 500 C. in about 100 seconds through suitable control of ambient conditions.
FIG. 2 shows how the bar 10' produced by the process of FIG. 1 can be bent through 180 about a mandrel 20 Whose diameter D is only five times as great as the bar diameter d The bar so bent can also be returned to its original straight position, shown in dot-dash lines, without cracking.
What is claimed is:
1. A process for making a bar of fine-grain structural steel, comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by Weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of .silicon, and iron as substantially the entire remainder, to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
2. A process according to claim 1 wherein each of three final rolling steps involves a reduction in crosssectional area of said stock by substantially 12 to 15 3. A process according to claim 1 wherein the air cooling from said temperature to said level is carried out at a rate substantially 30% faster than cooling under normal ambient conditions.
4. A process for making a bar of fine-grain structural steel, comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in cross-sectional area by substantially 12 to 15% at each of three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
5. A process for making a bar of weldable fine-grain structural steel, comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, 0.15 to 0.50% by weight of chromium, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in cross-sectional area by substantially 12 to 15% at each of: three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
6. A process for making a bar of fine-grain structural steel, comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by Weight of manganese, 0.50 to 1.50% by weight of silicon, 0.10 to 0.20% by weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in cross-sectional area by substantially 12 to 15% at each of three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
7. A process for making a bar of weldable fine-grain structural steel, comprising the steps of successively rolling a stock of steel alloy, consisting essentially of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, 0.15 to 0.50% by weight of chromium, 0.10 to 0.20% by weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron as substantially the entire remainder, to progressively smaller diameters with a reduction in crosssectional area by substantially 12 to 15% at each of three final rolling steps, at a temperature of substantially 800 to 900 C., and cooling the rolled stock from said temperature to a level of approximately 500 C. at a rate substantially 30% faster than cooling under normal ambient conditions.
8. A bar of fine-grain alloy steel with a tensile strength of at least 75 kg/mm., a yield-point of at least 50 kg./
mm. and a high degree of cold deformability, said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, and iron as substantially the entire remainder produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 5 00 C.
9. A bar of Weldable fine-grain alloy steel with a tensile strength of at least kg./mm., a yield point of at least 50 kg./mrn. and a high degree of cold deformability, said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by Weight of silicon, 0.15 to 0.50% by weight of chromium, and iron as substantially the entire remainder, produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
10. A bar of fine-grain alloy steel with a tensile strength of at least 75 kg./mm., a yield point of at least 50 kg./ mm. and a high degree of cold deformability, said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by Weight of silicon, 0.10 to 0.20% by Weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron substantially as the entire remainder, produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
11. A bar of weldable fine-grain alloy steel with a tensile strength of at least 75 kg./mm., a yield point of at least 50 kg./mm. and a high degree of cold deformability, said steel being essentially composed of 0.15 to 0.40% by weight of carbon, 0.70 to 1.80% by weight of manganese, 0.50 to 1.50% by weight of silicon, 0.15 to 0.50% by weight of chromium, 0.10 to 0.20% by Weight of aluminum, 0.05 to 0.20% by weight of a metal selected from the group which consists of titanium and vanadium, and iron as substantially the entire remainder, produced by rolling a stock of steel alloy of the stated composition to progressively smaller diameters at a temperature of substantially 800 to 900 C., and rapidly cooling the rolled stock from said temperature to a level of approximately 500 C.
References Cited by the Examiner UNITED STATES PATENTS 2,576,223 11/51 Hofmann 148l2.4 2,716,080 8/55 Schwarz 148-12 2,901,346 8/59 Huddle et al 75-124 2,933,424 4/60 Canney 148-l2 2,987,394 6/61 Mueller 75124 FOREIGN PATENTS 609,730 10/48 Great Britain.
DAVID L. RECK, Primary Examiner.
RAY K. WINDHAM, Examiner.
Claims (1)
1. A PROCESS FOR MAKING A BAR OF FINE-GRAIN STRUCTURAL STEEL, COMPRISING THE STEPS OF SUCCESSIVELY ROLLING A STOCK OF STEEL ALLOY, CONSISTING ESSENTIALLY OF 0.15 TO 0.40% BY WEIGHT OF CARBON, 0.70 TO 1.80% BY WEIGHT OF MANGANESE, 0.50 TO 1.50% BY WEIGHT OF SILICON, AND IRON AS SUBSTANTIALLY THE ENTIRE REMAINDER, TO PROGRESSIVELY SMALLER DIAMETERS AT A TEMPERATURE OF SUBSTANTIALLY 800* TO 900*C., AND RAPIDLY COOLING THE ROLLED STOCK FROM SAID TEMPERATURE TO A LEVEL OF APPROXIMATELY 500*C.
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| Application Number | Priority Date | Filing Date | Title |
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| US160990A US3207637A (en) | 1961-12-21 | 1961-12-21 | Structural steel and process for making same |
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| Application Number | Priority Date | Filing Date | Title |
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| US160990A US3207637A (en) | 1961-12-21 | 1961-12-21 | Structural steel and process for making same |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1921168B1 (en) * | 1969-04-25 | 1970-07-09 | Huettenwerk Oberhausen Ag | Process for the production of welded wire mesh |
| DE1583803B1 (en) * | 1967-06-15 | 1971-07-01 | Louis Lille Lamendin | External tensioning device for rock bolts |
| US3656917A (en) * | 1966-09-10 | 1972-04-18 | Nippon Kokan Kk | Steel alloy tubes |
| US3661537A (en) * | 1969-07-16 | 1972-05-09 | Jones & Laughlin Steel Corp | Welded pipe structure of high strength low alloy steels |
| US3753796A (en) * | 1968-12-20 | 1973-08-21 | Bethlehem Steel Corp | Rolled steel having high strength and low impact transition temperature and method of producing same |
| JPS5112567B1 (en) * | 1970-12-29 | 1976-04-20 | ||
| DE2201855C2 (en) * | 1972-01-15 | 1982-03-04 | Estel Hoesch Werke Ag, 4600 Dortmund | Process for the production of high-strength, easily weldable and cold-deformable heavy and medium plates and their use |
| EP0058016A1 (en) * | 1981-01-27 | 1982-08-18 | Kabushiki Kaisha Kobe Seiko Sho | Process for producing steel wire or rods of high ductility and strength |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB609730A (en) * | 1944-10-30 | 1948-10-06 | Axel Frokjer Jensen | Improvements in and relating to the production of cold-treated reinforcing steel |
| US2576223A (en) * | 1948-02-17 | 1951-11-27 | Hofmann Fritz | Method of producing wear resistant steel rails |
| US2716080A (en) * | 1950-10-13 | 1955-08-23 | Schwarz Johannes | Process for increasing the strength of steel |
| US2901346A (en) * | 1956-05-04 | 1959-08-25 | Consett Iron Company Ltd | Mild steel |
| US2933424A (en) * | 1957-05-08 | 1960-04-19 | United States Steel Corp | Method of making cold headed wire |
| US2987394A (en) * | 1959-03-25 | 1961-06-06 | John J Mueller | Iron-aluminum base alloys |
-
1961
- 1961-12-21 US US160990A patent/US3207637A/en not_active Expired - Lifetime
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB609730A (en) * | 1944-10-30 | 1948-10-06 | Axel Frokjer Jensen | Improvements in and relating to the production of cold-treated reinforcing steel |
| US2576223A (en) * | 1948-02-17 | 1951-11-27 | Hofmann Fritz | Method of producing wear resistant steel rails |
| US2716080A (en) * | 1950-10-13 | 1955-08-23 | Schwarz Johannes | Process for increasing the strength of steel |
| US2901346A (en) * | 1956-05-04 | 1959-08-25 | Consett Iron Company Ltd | Mild steel |
| US2933424A (en) * | 1957-05-08 | 1960-04-19 | United States Steel Corp | Method of making cold headed wire |
| US2987394A (en) * | 1959-03-25 | 1961-06-06 | John J Mueller | Iron-aluminum base alloys |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3656917A (en) * | 1966-09-10 | 1972-04-18 | Nippon Kokan Kk | Steel alloy tubes |
| DE1583803B1 (en) * | 1967-06-15 | 1971-07-01 | Louis Lille Lamendin | External tensioning device for rock bolts |
| US3753796A (en) * | 1968-12-20 | 1973-08-21 | Bethlehem Steel Corp | Rolled steel having high strength and low impact transition temperature and method of producing same |
| DE1921168B1 (en) * | 1969-04-25 | 1970-07-09 | Huettenwerk Oberhausen Ag | Process for the production of welded wire mesh |
| US3661537A (en) * | 1969-07-16 | 1972-05-09 | Jones & Laughlin Steel Corp | Welded pipe structure of high strength low alloy steels |
| JPS5112567B1 (en) * | 1970-12-29 | 1976-04-20 | ||
| DE2201855C2 (en) * | 1972-01-15 | 1982-03-04 | Estel Hoesch Werke Ag, 4600 Dortmund | Process for the production of high-strength, easily weldable and cold-deformable heavy and medium plates and their use |
| EP0058016A1 (en) * | 1981-01-27 | 1982-08-18 | Kabushiki Kaisha Kobe Seiko Sho | Process for producing steel wire or rods of high ductility and strength |
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