USRE28791E - High-strength plain carbon steels having improved formability - Google Patents
High-strength plain carbon steels having improved formability Download PDFInfo
- Publication number
- USRE28791E USRE28791E US05/522,526 US52252674A USRE28791E US RE28791 E USRE28791 E US RE28791E US 52252674 A US52252674 A US 52252674A US RE28791 E USRE28791 E US RE28791E
- Authority
- US
- United States
- Prior art keywords
- steel
- excess
- strength
- zirconium
- control agent
- 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
- 229910000975 Carbon steel Inorganic materials 0.000 title claims abstract description 9
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 41
- 239000010959 steel Substances 0.000 claims abstract description 41
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims abstract description 24
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 24
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910001122 Mischmetal Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 239000010703 silicon Substances 0.000 claims abstract description 6
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 5
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 239000011574 phosphorus Substances 0.000 claims abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 5
- 239000011593 sulfur Substances 0.000 claims abstract description 5
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 claims description 9
- 229910052761 rare earth metal Inorganic materials 0.000 claims 2
- 150000002910 rare earth metals Chemical class 0.000 claims 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- 238000001816 cooling Methods 0.000 description 6
- 238000007792 addition Methods 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 238000011084 recovery Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910000922 High-strength low-alloy steel Inorganic materials 0.000 description 1
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- 229910052777 Praseodymium Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- QEFYFXOXNSNQGX-UHFFFAOYSA-N neodymium atom Chemical compound [Nd] QEFYFXOXNSNQGX-UHFFFAOYSA-N 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- -1 or rare earths Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- PUDIUYLPXJFUGB-UHFFFAOYSA-N praseodymium atom Chemical compound [Pr] PUDIUYLPXJFUGB-UHFFFAOYSA-N 0.000 description 1
- 229910052706 scandium Inorganic materials 0.000 description 1
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Definitions
- This invention relates generally to high-strength steels and particularly to high-strength plain carbon steels of superior formability.
- the steels of the invention also exhibit superior formability resulting from the use of an inclusion shape-control agent comprising either zirconium, or rare earths, or mischmetal which, of course, is a mixture of rare earths.
- an inclusion shape-control agent results in the formation of substantially spherically shaped inclusion which retain their spherical shape in the hot-rolled finished material.
- an object of the present invention is to provide plain carbon steels having high strength in combination with good toughness and ductility and superior formability.
- Another object of the invention is to provide such steels characterized in a hot-rolled finished condition by yield strengths in excess of 35,000 p.s.i., ultimate tensile strengths in excess of 55,000 p.s.i., ductilities as measured by percent elongation (2 inches) in excess of 30% and good toughness.
- Still another object of the invention is to provide such steels which can be bent without cracking about an inside radius which is equal to or less than about one-half the thickness of the steels.
- the steels of the present invention are fully killed and have the following general chemistry: carbon, .06% to .20%; manganese, .4% to 1.2%; slicon, .005% to .3%; sulfur, .04% maximum; phosphorus, .04% maximum; an inclusion shape-control agent comprising either .05% to .20% zirconium, or .01% to .10% of rare earths or .01% to .10% mischmetal; and balance iron.
- the preferred steels of the invention consist essentially of .12% to .16% carbon, .5% to .7% manganese, .1% maximum silicon, .02% maximum sulfur, .03% maximum phosphorus, .08% to .12% zirconium or .01% to .10% of rare earths or mischmetal, balance iron.
- Rare earths which are employed in the steels of the invention are, for example, cerium, lanthanum, praseodymium, neodymium, yttrium and scandium.
- Steels to possess the desired characteristics and properties of a yield strength in excess of 35,000 p.s.i., an ultimate tensile strength in excess of 55,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 30% and good toughness are hot-rolled finished in the temperature range of 1550° F. to 1650° F., cooled at a rate within the range of 20° F. to 135° F. per second and collected by coiling or piling within a preferred temperature range of 1025° F. to 1175° F.
- Steels finished and/or collected at temperatures in excess of the temperatures set out above or cooled at a rate less than 20° F. per second generally exhibit strengths below a yield strength of 35,000 p.s.i.
- the steels do not have as good impact properties as steels hot rolled within the temperature ranges set out above.
- Steels finished or coiled below the preferred temperature ranges exhibit ductilities as measured by percent elongation inferior to the ductilities of steels of the invention.
- low finishing temperatures result in production liabilities in that rolling speeds must be slower to achieve lower finishing temperatures.
- the inclusion shape-control agents cause the sulfide inclusions in the steels to retain a spherical form, resulting in a significant improvement in the formability of the material.
- certain inclusions become elongated during hot rolling and aligned parallel to the rolling direction and adversely affect the formability of the steels.
- Zirconium additions are made when the mold is about one-third full and the additions completed by the time the mold is about two-thirds full. Typical zirconium recoveries achieved employing this method of addition are about 60%.
- the zirconium additions can also be made to the ladle after the heat is tapped. However, the steel in the ladle must be fully killed to assure good zirconium recovery. In this technique, it is important to employ good teeming practice to minimize oxygen or nitrogen entrainment during teeming which adversely affects zirconium recovery.
- the heat from which the products of Table I were processed had an analysis of .14% C, .16% Mn and .06% Si.
- the lower finishing and coiling temperatures of the coiled products together with their more rapid cooling rates resulted in their smaller grain size and higher strength and improved notch toughness, as shown by their lower fracture appearance transition temperatures (FATT), as compared with the plate products.
- Heat No. 427829 was a plain carbon steel containing .14% carbon, .28% manganese and .06% silicon.
- Heat No. COM-2 was a plain carbon steel containing .12% carbon, .44% manganese and .05% silicon. The faster cooling rates resulted in reduced ferrite grain sizes which bring about the higher yield strengths and improved toughness.
Abstract
Fully killed high-strength plain carbon steels consisting essentially of 0.06% to .20% carbon, .4% to 1.2% manganese, .005% to .3% silicon, .04% maximum sulfur, .04% maximum phosphorus, an inclusion shape control agent comprising .05% to .20% zirconium, or .01% to .10% of rare earths or .01% to .10% mischmetal, balance iron are characterized in a hot-rolled finished condition by a yield strength in excess of 35,000 p.s.i., an ultimate tensile strength in excess of 55,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 30%, good toughness and superior formability. The steels are hot-rolled finished in the temperature range 1550° F. to 1650° F., cooled at a rate within the temperature range 20° F. to 135° F. per second and collected by coiling or piling within a temperature range of 900° F. to 1200° F., preferably between 1025° F. to 1175° F.
Description
This invention relates generally to high-strength steels and particularly to high-strength plain carbon steels of superior formability.
We have developed a class of high-strength plain carbon steels which in a hot-rolled finished condition exhibit good ductility and a toughness and strength previously available only in steels containing an alloy strengthening agent or steels heat treated after hot rolling. The improved properties are brought about by hot rolling the steels under critical temperature conditions. The steels of the invention also exhibit superior formability resulting from the use of an inclusion shape-control agent comprising either zirconium, or rare earths, or mischmetal which, of course, is a mixture of rare earths. The use of an inclusion shape-control agent results in the formation of substantially spherically shaped inclusion which retain their spherical shape in the hot-rolled finished material.
Accordingly, an object of the present invention is to provide plain carbon steels having high strength in combination with good toughness and ductility and superior formability. Another object of the invention is to provide such steels characterized in a hot-rolled finished condition by yield strengths in excess of 35,000 p.s.i., ultimate tensile strengths in excess of 55,000 p.s.i., ductilities as measured by percent elongation (2 inches) in excess of 30% and good toughness. Still another object of the invention is to provide such steels which can be bent without cracking about an inside radius which is equal to or less than about one-half the thickness of the steels.
These and other objects and advantages of the present invention will become apparent from the following detailed description thereof.
The steels of the present invention are fully killed and have the following general chemistry: carbon, .06% to .20%; manganese, .4% to 1.2%; slicon, .005% to .3%; sulfur, .04% maximum; phosphorus, .04% maximum; an inclusion shape-control agent comprising either .05% to .20% zirconium, or .01% to .10% of rare earths or .01% to .10% mischmetal; and balance iron.
The preferred steels of the invention consist essentially of .12% to .16% carbon, .5% to .7% manganese, .1% maximum silicon, .02% maximum sulfur, .03% maximum phosphorus, .08% to .12% zirconium or .01% to .10% of rare earths or mischmetal, balance iron. Rare earths which are employed in the steels of the invention are, for example, cerium, lanthanum, praseodymium, neodymium, yttrium and scandium.
Steels to possess the desired characteristics and properties of a yield strength in excess of 35,000 p.s.i., an ultimate tensile strength in excess of 55,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 30% and good toughness are hot-rolled finished in the temperature range of 1550° F. to 1650° F., cooled at a rate within the range of 20° F. to 135° F. per second and collected by coiling or piling within a preferred temperature range of 1025° F. to 1175° F. Steels finished and/or collected at temperatures in excess of the temperatures set out above or cooled at a rate less than 20° F. per second generally exhibit strengths below a yield strength of 35,000 p.s.i. and an ultimate tensile strength of 55,000 p.s.i. In addition, the steels do not have as good impact properties as steels hot rolled within the temperature ranges set out above. Steels finished or coiled below the preferred temperature ranges exhibit ductilities as measured by percent elongation inferior to the ductilities of steels of the invention. In addition, low finishing temperatures result in production liabilities in that rolling speeds must be slower to achieve lower finishing temperatures.
As noted above, the inclusion shape-control agents cause the sulfide inclusions in the steels to retain a spherical form, resulting in a significant improvement in the formability of the material. In the absence of an inclusion shape-control agent, certain inclusions become elongated during hot rolling and aligned parallel to the rolling direction and adversely affect the formability of the steels.
Sufficient zirconium is added to the steels of the invention so that there is a minimum of .02% zirconium in the steel in excess of the zirconium which combines with the nitrogen in the steel to form nitrides. For a typical high-strength low alloy steel containing .006% nitrogen, therefore, approximately a minimum of .06% zirconium is added to the steel. The minimum amount of zirconium required is given by the following formula: Percent zirconium=0.02% zirconium+6.5 (wt. percent N). The zirconium is preferably added to the steel in the ingot mold during teeming. Zirconium additions are made when the mold is about one-third full and the additions completed by the time the mold is about two-thirds full. Typical zirconium recoveries achieved employing this method of addition are about 60%. The zirconium additions can also be made to the ladle after the heat is tapped. However, the steel in the ladle must be fully killed to assure good zirconium recovery. In this technique, it is important to employ good teeming practice to minimize oxygen or nitrogen entrainment during teeming which adversely affects zirconium recovery.
The significance of processing the steels within a finishing temperature range of 1550° F. to 1650° F., cooling the steel at a rate within the temperature range 20° F. to 135° F. per second and collecting the steel within a preferred temperature range of 1025° F. to 1175° F. is demonstrated in Table I.
TABLE I
__________________________________________________________________________
Longi-
Rolling tudinal
temperatures
Cooling Ultimate
Percent
Grain
impact
(° F.)
rate,
Yield tensile
elon-
size trans.
Gage Fin- Col- ° F. per
strength,
strength,
gation
(ASTM
temp. (°F.)
Product
inch ish lected
second.sup.1
p.s.i.
p.s.i.
(8") No./)
(50% FATT)
__________________________________________________________________________
Coil 0.250
1,630
1,050
40 40,900
64,700
28.0 9.6 -50
0.312
1,610
1,070
35 38,900
66,200
29.5 10.4 -55
Plate 0.250
1,790
1,300
2 35,600
62,400
26.5 8.9 -25
0.312
1,760
1,350
2 32,700
60,000
31.0 7.6 -15
__________________________________________________________________________
.sup.1 Cooling rate between the finishing and collecting temperature.
The heat from which the products of Table I were processed had an analysis of .14% C, .16% Mn and .06% Si. The lower finishing and coiling temperatures of the coiled products together with their more rapid cooling rates resulted in their smaller grain size and higher strength and improved notch toughness, as shown by their lower fracture appearance transition temperatures (FATT), as compared with the plate products.
The improved properties brought about by the increased cooling rates of the invention are shown in Table II.
TABLE II
__________________________________________________________________________
Longi-
tudinal
impact
Ultimate
Percent trans.
Yield tensile
elon-
Grain
temp.
Heat Gage,
(°F./
strength,
strength,
gation
size (°F.) (50%
No. inch
seconds)
p.s.i.
p.s.i.
(1") (ASTM)
FATT)
__________________________________________________________________________
427829
0.50
2 30,300
51,600
36.5 6.6 >+70
0.50
66 47,700
63,700
36.5 8.8 -20
COM-2 0.50
2 33,300
55,000
37.5 7.0 +70
0.50
73 47,600
65,900
37.5 9.4 -10
__________________________________________________________________________
Heat No. 427829 was a plain carbon steel containing .14% carbon, .28% manganese and .06% silicon. Heat No. COM-2 was a plain carbon steel containing .12% carbon, .44% manganese and .05% silicon. The faster cooling rates resulted in reduced ferrite grain sizes which bring about the higher yield strengths and improved toughness.
The improved formability of the steels of the invention is shown in Table III.
TABLE III
__________________________________________________________________________
Minimum
bend
radius
Shelf energy without
Chemistry (weight percent)
Yield ft.-lbs. in
50% ductile-brittle
cracking
Gage, strength,
1/2 size charpy
transfer temp.,
transverse
Heat No.
inch
C Mn Si S P Zr
Al p.s.i.
V-notch specimens
(°F.)
sample
__________________________________________________________________________
957220
0.280
.19
.39
.042
.020
.007
--
.030
42,600
Longitudinal, 54
Longitudinal,
1T
Transverse, 17
Transverse, -10
957007
0.250
.14
.50
.010
.019
.010
.08
.035
40,500
Longitudinal, 61
Longitudinal,
.2T
Transverse, 38
Transverse,
__________________________________________________________________________
-60
The improved bending properties of material from Heat No. 957007, containing zirconium as a shape-control agent, is demonstrated by the fact that steels from that heat could be bent about an inside radius of a minimum of .2 inch of their thickness without cracking, whereas steels from Heat No. 957220, which did not contain an inclusion shape-control agent, could only be bent about a minimum inside radius equal to its thickness before cracking. Crack lengths less than 0.10 inch were discounted. The table further shows that the zirconium contributed to improved toughness, particularly in the transverse direction. Equivalent improved formability and toughness is obtained using rare earths or mischmetal rather than zirconium as the inclusion shape-control agent.
Claims (6)
1. A killed high-strength plain carbon steel which has been hot-rolled finished in the temperature range 1550° F. to 1650° F., cooled at a rate within the range of 20° F. to 135° F. per second, and collected within a preferred temperature range of 1025° F. to 1175° F., the steel being characterized in a hot rolled condition by a yield strength in excess of 35,000 p.s.i., an ultimate tensile strength in excess of 55,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 30%, good toughness and formability, said steel consisting essentially of .06% to .20% carbon, .4% to 1.2% manganese, .005% to .3% silicon, sulfur in an amount up to .04%, .04% maximum phosphorus, a sulfide inclusion shape-control agent selected from the group consisting of .05% to .20% zirconium, .01% to .10% of a rare earth and .01% to .10% mischmetal, balance iron, the sulfide inclusions in the steel having a substantially spherical shape.
2. The steel of claim 1 wherein the sulfide inclusion shape-control agent comprises .05% to .20% zirconium.
3. The steel of claim 1 wherein the sulfide inclusion shape-control agent comprises .01% to .10% of rare earths.
4. A killed high-strength plain carbon steel which has been hot-rolled finished in the temperature range 1550° F. to 1650° F., cooled at a rate within the range of 20° F. to 135° F. per second, and collected within a preferred temperature range of 1025° F. to 1175° F., the steel being characterized in a hot rolled condition by a yield strength in excess of 35,000 p.s.i., an ultimate tensile strength in excess of 55,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 30%, good toughness and formability, said steel consisting essentially of .12% to .[..15%.]. .Iadd..16% .Iaddend.carbon, .5% to .7% manganese, .[..3%.]. .Iadd..1% .Iaddend.maximum silicon, sulfur in an amount up to .02%, .03% maximum phosphorus, a sulfide inclusion shape-control agent selected from the group consisting of .08% to .12% zirconium, .01% to .10% of a rare earth and .01% to .10% mischmetal, balance iron, the sulfide inclusions in the steel having a substantially spherical shape.
5. The steel of claim 4 wherein the sulfide inclusion shape-control agent comprises .[..05% to .20%.]. .Iadd..08% to .12% .Iaddend.zirconium.
6. The steel of claim 4 wherein the sulfide inclusion shape-control agent comprises .01% to .10% of rare earths.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US05/522,526 USRE28791E (en) | 1969-07-16 | 1974-11-11 | High-strength plain carbon steels having improved formability |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US84233869A | 1969-07-16 | 1969-07-16 | |
| US05/522,526 USRE28791E (en) | 1969-07-16 | 1974-11-11 | High-strength plain carbon steels having improved formability |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US84233869A Reissue | 1969-07-16 | 1969-07-16 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| USRE28791E true USRE28791E (en) | 1976-04-27 |
Family
ID=27060837
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US05/522,526 Expired - Lifetime USRE28791E (en) | 1969-07-16 | 1974-11-11 | High-strength plain carbon steels having improved formability |
Country Status (1)
| Country | Link |
|---|---|
| US (1) | USRE28791E (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2360717A (en) * | 1942-11-27 | 1944-10-17 | Cerium Corp | Method of eliminating aluminate and silicate inclusions |
| US2683662A (en) * | 1951-10-31 | 1954-07-13 | Molybdenum Corp | Manufacture of iron and steel and products obtained |
| US3102831A (en) * | 1960-08-10 | 1963-09-03 | Molybdenum Corp | Production of columbium containing steels |
| US3333987A (en) * | 1964-12-02 | 1967-08-01 | Inland Steel Co | Carbon-stabilized steel products and method of making the same |
-
1974
- 1974-11-11 US US05/522,526 patent/USRE28791E/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2360717A (en) * | 1942-11-27 | 1944-10-17 | Cerium Corp | Method of eliminating aluminate and silicate inclusions |
| US2683662A (en) * | 1951-10-31 | 1954-07-13 | Molybdenum Corp | Manufacture of iron and steel and products obtained |
| US3102831A (en) * | 1960-08-10 | 1963-09-03 | Molybdenum Corp | Production of columbium containing steels |
| US3333987A (en) * | 1964-12-02 | 1967-08-01 | Inland Steel Co | Carbon-stabilized steel products and method of making the same |
Non-Patent Citations (1)
| Title |
|---|
| Lichy et al., Control of Sulfide Shape in Low Carbon Al-Killed Steel, Journal of Metals, July 1965, pp. 769-775. * |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| AS | Assignment |
Owner name: JONES & LAUGHLIN STEEL, INCORPORATED Free format text: MERGER;ASSIGNORS:JONES & LAUGHLIN STEEL CORPORATION, A CORP. OF PA.;YOUNGTOWN SHEET & TUBE COMPANY,A CORP. OF OH. (MERGED INTO);NEW J&L STEEL CORPRATION, A CORP. OF DE., (CHANGED TO);REEL/FRAME:004510/0801 Effective date: 19851018 |
|
| AS | Assignment |
Owner name: LTV STEEL COMPANY, INC., Free format text: MERGER AND CHANGE OF NAME EFFECTIVE DECEMBER 19, 1984, (NEW JERSEY);ASSIGNORS:JONES & LAUGHLIN STEEL, INCORPORATED, A DE. CORP. (INTO);REPUBLIC STEEL CORPORATION, A NJ CORP. (CHANGEDTO);REEL/FRAME:004736/0443 Effective date: 19850612 |
|
| AS | Assignment |
Owner name: SANWA BUSINESS CREDIT CORPORATION, A CORP. OF DE Free format text: SECURITY INTEREST;ASSIGNOR:WARREN CONSOLIDATED INDUSTRIES, INC.;REEL/FRAME:005368/0616 Effective date: 19900129 |