USRE28790E - High-strength low-alloy steels having improved formability - Google Patents
High-strength low-alloy steels having improved formability Download PDFInfo
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- USRE28790E USRE28790E US05/522,524 US52252474A USRE28790E US RE28790 E USRE28790 E US RE28790E US 52252474 A US52252474 A US 52252474A US RE28790 E USRE28790 E US RE28790E
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- 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
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- 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
Definitions
- This invention relates to high-strength low-alloy steels characterized by a desirable balance and uniformity of physical properties and distinguished by their formability and reduced directionality.
- the steels are of superior formability and reduced directionality, that is, the longitudinal (parallel to the rolling direction) and transverse (across the rolling direction) properties of the steels, with respect to notch toughness and ductility, are more nearly the same.
- the improved formability and reduced directionality are brought about through the use of an inclusion shape-control agent comprising either zirconium, a rare earth, or mischmetal which, of course, is a mixture of rare earths.
- an inclusion shape-control agent results in the formation of substantially spherically-shaped inclusions which retain their spherical shape in the finished material.
- This inclusion morphology results in a reduction of the directionality of the steels by improving their resistance to ductile fracture in the transverse direction and by making their longitudinal and transverse ductilities more nearly alike. In addition, the formability of the steels is improved.
- the steels of the invention employ either vanadium or columbium as a strengthening agent and are processed within definite finishing and collecting temperature ranges to produce desired properties in the steel directly off the hot-mill.
- an object of the present invention is to provide low-alloy steels having high strength in combination with good toughness and ductility, superior formability and reduced directionality.
- Another object of the invention is to provide such steels characterized in a hot-rolled finished condition by yield strengths in excess of 45,000 p.s.i., ultimate tensile strengths in excess of 60,000 p.s.i., ductilities as measured by percent elongation (2 inches) in excess of 20% and good toughness.
- Still another object of the invention is to provide such steels having improved resistance to ductile fracture in the transverse direction.
- FIGS. 1 through 10 are photographic reproductions of steel specimens which have been subjected to bending tests and illustrate the improved formability of the steels of the invention.
- the steels of the present invention are fully killed and have the following general chemistry: carbon, .06% to .20%; manganese, .50% to 1.4%; columbium, .01% to .08% or vanadium, .04% to .12%; silicon, .5% maximum; sulfur, .04% maximum; phosphorus, .04% maximum; an inclusion shape-control agent comprising either .06% to .02% zirconium, .01% to .10% of a rare earth, or .01% to .10% mischmetal; and balance iron.
- the preferred steels of the invention consists essentially of .10% to .15% carbon, .9% to 1.2% manganese, .02% to .04% columbium or .04% to .07% vanadium, .05% maximum silicon, .025% maximum sulfur, .03% maximum phosphorus, .08% to .12% zirconium or .01% to .10% of a rear earth 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.
- the steels to possess the desired characteristics and properties of a yield strength in excess of 45,000 p.s.i., an ultimate tensile strength in excess of 60,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 20% and a superior toughness are hot-rolled finished in the temperature range of 1550° F. to 1650° F. and collected by coiling or pilling within a temperature range of 1025° F. to 1175° F.
- the steel must be cooled at a rate within a range of 20° F. to 135° F. per second to maintain finishing and coiling temperatures within these ranges.
- Steels finished and/or collected at temperatures in excess of the temperatures set out above generally exhibit strengths below a yield strength of 45,000 p.s.i. and an ultimate tensile strength of 60,000 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 desired 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 the lower finishing temperatures.
- the inclusion shape-control agents cause the sulfide inclusions in the steel to retain a spherical form, resulting in a significant improvement in the formability of the material and reducing the directionality of the steels.
- the inclusions become elongated during hot rolling and aligned parallel to the rolling direction and contribute to the differences in ductility and impact energy absorbed (100% ductile fracture) between longitudinal and transverse test sections 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 first 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 reduced directionality of the steels of the invention with respect to increased transverse impact shelf energies and more nearly alike transverse and longitudinal ductilities is shown in the table. All of the steels listed in the table were hot-rolled finished within 1550° F. to 1650° F. and collected within 1025° F. to 1175° F. While Steel 1 contained .01% zirconium it is considered to have not been treated with zirconium since that amount of zirconium is insufficient to bring about the desired inclusion morphology.
- the specimens for which the data of the table were obtained comprised one-half size Charpy V-notch samples, except for Steel 5 where one-third size samples were employed.
- the impact energies set out in the table are at 100% ductile fracture of the specimens.
- FIGS. 1 through 10 of the drawings The improved formability of the steels of the invention is shown by FIGS. 1 through 10 of the drawings. Samples were sheared from Steels 1 through 10 of the table and subjected to a 90° bend. The inside bend radius for all specimens except the specimens of Steel 5 was .250 inch. The inside bend radius for the specimens of Steel 5 was .125 inch.
- FIGS. 1 through 10 represent specimens taken from Steels 1 through 10 of the table, respectively. As shown in the drawings, the steels which did not contain zirconium, FIGS. 1, 3, 5, 7 and 9, cracked upon bending. Of the specimens from the steels containing zirconium, FIGS. 2, 4, 6, 8 and 10, only specimens from Steels 6 and 8 exhibited cracking, but to a very minor degree and substantially less than the specimens of the steels having approximately the same chemistry but not containing zirconium.
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Abstract
Fully killed high-strength low-alloy steels consisting essentially of .06% to .20% carbon, .50% to 1.4% manganese, .01% to .08% columbium or .04% to .12% vanadium, .05% maximum silicon, .04% maximum sulfur, .04% maximum phosphorus and an inclusion shape-control agent comprising either .06% to .20% zirconium, 0.1% to .10% of a rare earth or .01% to .10% mischmetal are characterized in a hot-rolled finished condition by yield strengths in excess of 45,000 p.s.i., ultimate tensile strengths in excess of 60,000 p.s.i., ductilities as measured by percent elongation (2 inches) in excess of 20%, good toughness, superior formability and reduced directionality. The steels are hot-rolled finished in the temperature range 1550° F. to 1650° F., cooled at a rate within the range 20° F. to 135° F. per second and collected by coiling or piling within a temperature range of 1025° F. to 1175° F.
Description
.Iadd.This application is an application for reissue of our Patent No. 3,666,570 issued May 30, 1972. .Iaddend.
This invention relates to high-strength low-alloy steels characterized by a desirable balance and uniformity of physical properties and distinguished by their formability and reduced directionality.
We have developed a class of high-strength low-alloy steels which in a hot-rolled finished condition exhibit good toughness, ductility and strength. In addition, the steels are of superior formability and reduced directionality, that is, the longitudinal (parallel to the rolling direction) and transverse (across the rolling direction) properties of the steels, with respect to notch toughness and ductility, are more nearly the same. The improved formability and reduced directionality are brought about through the use of an inclusion shape-control agent comprising either zirconium, a rare earth, 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 inclusions which retain their spherical shape in the finished material. This inclusion morphology results in a reduction of the directionality of the steels by improving their resistance to ductile fracture in the transverse direction and by making their longitudinal and transverse ductilities more nearly alike. In addition, the formability of the steels is improved.
The steels of the invention employ either vanadium or columbium as a strengthening agent and are processed within definite finishing and collecting temperature ranges to produce desired properties in the steel directly off the hot-mill.
Accordingly, an object of the present invention is to provide low-alloy steels having high strength in combination with good toughness and ductility, superior formability and reduced directionality. Another object of the invention is to provide such steels characterized in a hot-rolled finished condition by yield strengths in excess of 45,000 p.s.i., ultimate tensile strengths in excess of 60,000 p.s.i., ductilities as measured by percent elongation (2 inches) in excess of 20% and good toughness. Still another object of the invention is to provide such steels having improved resistance to ductile fracture in the transverse direction.
These and other objects and advantages of the present invention will become apparent from the following detailed description thereof with reference to the drawings wherein FIGS. 1 through 10 are photographic reproductions of steel specimens which have been subjected to bending tests and illustrate the improved formability of the steels of the invention.
The steels of the present invention are fully killed and have the following general chemistry: carbon, .06% to .20%; manganese, .50% to 1.4%; columbium, .01% to .08% or vanadium, .04% to .12%; silicon, .5% maximum; sulfur, .04% maximum; phosphorus, .04% maximum; an inclusion shape-control agent comprising either .06% to .02% zirconium, .01% to .10% of a rare earth, or .01% to .10% mischmetal; and balance iron.
The preferred steels of the invention consists essentially of .10% to .15% carbon, .9% to 1.2% manganese, .02% to .04% columbium or .04% to .07% vanadium, .05% maximum silicon, .025% maximum sulfur, .03% maximum phosphorus, .08% to .12% zirconium or .01% to .10% of a rear earth 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.
The steels to possess the desired characteristics and properties of a yield strength in excess of 45,000 p.s.i., an ultimate tensile strength in excess of 60,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 20% and a superior toughness are hot-rolled finished in the temperature range of 1550° F. to 1650° F. and collected by coiling or pilling within a temperature range of 1025° F. to 1175° F. For the typical length of a modern hot-mill run-out table and conventional rolling speeds, the steel must be cooled at a rate within a range of 20° F. to 135° F. per second to maintain finishing and coiling temperatures within these ranges. Steels finished and/or collected at temperatures in excess of the temperatures set out above generally exhibit strengths below a yield strength of 45,000 p.s.i. and an ultimate tensile strength of 60,000 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 desired 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 the lower finishing temperatures.
As noted above, the inclusion shape-control agents cause the sulfide inclusions in the steel to retain a spherical form, resulting in a significant improvement in the formability of the material and reducing the directionality of the steels. In the absence of an inclusion shapecontrol agent, the inclusions become elongated during hot rolling and aligned parallel to the rolling direction and contribute to the differences in ductility and impact energy absorbed (100% ductile fracture) between longitudinal and transverse test sections 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 highstrength 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 first 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 reduced directionality of the steels of the invention with respect to increased transverse impact shelf energies and more nearly alike transverse and longitudinal ductilities is shown in the table. All of the steels listed in the table were hot-rolled finished within 1550° F. to 1650° F. and collected within 1025° F. to 1175° F. While Steel 1 contained .01% zirconium it is considered to have not been treated with zirconium since that amount of zirconium is insufficient to bring about the desired inclusion morphology. The specimens for which the data of the table were obtained comprised one-half size Charpy V-notch samples, except for Steel 5 where one-third size samples were employed. The impact energies set out in the table are at 100% ductile fracture of the specimens.
TABLE
__________________________________________________________________________
Ultimate
Thick-
Yield
tensile
Percent
Impact
Chemistry (wt. percent) Treat-
Test ness
strength
strength
elongation
energy,
Steel
C Mn Si Al V Cb Zr N ment direction
(in.)
(p.s.i.)
(p.s.i.)
(2") ft.-lbs.
__________________________________________________________________________
1 .10
.90
.052
.075
0.47 .01
.007
None Longitudinal
.250
55,700
71,300
30.5 70
Transverse
.250
56,700
71,400
28.0 18
2 .11
1.07
.047
.073
.05 .10
.007
Zr Longitudinal
.250
49,300
69,200
30.0 60
Transverse
.250
50,300
68,800
31.0 40
3 .12
1.07
.27
.008
.034 .007
None Longitudinal
.312
57,400
77,100
30.0
Transverse
.312
59,700
78,200
24.5 18
4 .12
1.10
.27
.072
.04 .091
.007
Zr Longitudinal
.250
59,100
77,100
26.5 63
Transverse
.250
61,400
78,200
230 40
5 .13
1.04
.27
.065
.033 .007
None Longitudinal
.179
56,600
78,500
25.0 27
Transverse
.179
60,700
78,200
23.5 9
6 .11
1.11
.24
.073
.041 .104
.000
Zr Longitudinal
.312
59,300
79,000
25.0
Transverse
.312
67,100
80,700
24.0 29
7 16
.83
.037
.005 .054 None Longitudinal
.312
67,400
83,700
28.5 41
Transverse
.312
69,600
85,700
24.5 17
8 .12
.109
.27
.071
.039 .087
.007
Zr Longitudinally
.250
64,100
83,000
23.0
Transverse
.250
67,100
81,500
21.5 33
9 .15
1.14
.35
.063
.08 None Longitudinally
.274
72,600
94,900
28.5 47
Transverse
.274
72,100
92,200
24.0 19
10 .14
.90
.021
.061 .042
.11
.006
Zr Longitudinal
.250
74,000
86,700
24.5 40
Transverse
.250
76,300
89,700
21.5 29
__________________________________________________________________________
The improved formability of the steels of the invention is shown by FIGS. 1 through 10 of the drawings. Samples were sheared from Steels 1 through 10 of the table and subjected to a 90° bend. The inside bend radius for all specimens except the specimens of Steel 5 was .250 inch. The inside bend radius for the specimens of Steel 5 was .125 inch. FIGS. 1 through 10 represent specimens taken from Steels 1 through 10 of the table, respectively. As shown in the drawings, the steels which did not contain zirconium, FIGS. 1, 3, 5, 7 and 9, cracked upon bending. Of the specimens from the steels containing zirconium, FIGS. 2, 4, 6, 8 and 10, only specimens from Steels 6 and 8 exhibited cracking, but to a very minor degree and substantially less than the specimens of the steels having approximately the same chemistry but not containing zirconium.
Equivalent reduced directionality and improved formability is obtained using rare earths and mischmetal rather than zirconium as the inclusion shape-control agent. In this regard, we have found that in order to maintain a given strength level for the steels of the invention containing vanadium and employing zirconium as the inclusion shape control agent it is necessary to increase the carbon content of the steel. This is because the strength of the steel is derived from vanadium nitride precipitates and when zirconium is added the nitrogen preferentially combines with the zirconium and strengthening by the formation of vanadium nitrides does not occur. However, when rare earths or mischmetal are used as the inclusion shape control agent, additional carbon is not needed to maintain a given strength level.
Claims (9)
1. A .[.kill.]. .Iadd.killed .Iaddend.high-strength low-alloy 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 temperature range of 1025° F. to 1175° F., the steel being characterized in a hot rolled condition by a yield strength in excess of 45,000 p.s.i., an ultimate tensile strength in excess of 60,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 20%, good toughness and formability and reduced directionality, said steel consisting essentially of .06% to .20% carbon, .50% to 1.4% manganese, a strengthening agent selected from the group consisting of .01% to .08% columbium and .04% to .12% vanadium, .5% maximum silicon, suflur in an amount up to .04%, .04% maximum phosphorus, a sulfide inclusion shape-control agent selected from the group consisting of .06% 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.Iadd., said zirconium being present in a minimum of 0.02% zirconium +6.5 (wt. percent N).Iaddend..
2. The steel of claim 1 wherein the strengthening agent comprises .01% to .08% columbium.
3. The steel of claim 1 wherein the strengthening agent comprises .04% to .12% vanadium and the sulfide inclusion shape-control agent comprises .01% to .10% of a rare earth.
4. A killed high-strength low-alloy 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 temperature range of 1025° F. to 1175° F. the steel being characterized in a hot rolled condition by a yield strength in excess of 45,000 p.s.i., an ultimate tensile strength in excess of 60,000 p.s.i., ductility as measured by percent elongation (2 inches) in excess of 20%, good toughness and formability and reduced directionality, said steel consisting essentially of .10% to .15% carbon, .9% to 1.2% manganese, a strengthening agent selected from the group consisting of .02% to .04% columbium and .04% to .07% vanadium, .05% maximum silicon, sulfur in an amount up to .025%, .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.Iadd., said zirconium being present in a minimum of at least 0.02% zirconium +6.5 (wt. percent N).Iaddend..
5. The steel of claim 4 wherein the strengthening agent comprises .02% to .04% columbium.
6. The steel of claim 5 wherein the sulfide inclusion shape-control agent comprises .08% to .12% zirconium.
7. The steel of claim 5 wherein the sulfide inclusion shape-control agent comprises .01% to .10% of a rare earth.
8. The steel of claim 4 wherein the strengthening agent comprises .04% to .07% vanadium.
9. The steel of claim 8 wherein the sulfide inclusion shape-control agent comprises .01% to .10% of a rare earth.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US05/522,524 USRE28790E (en) | 1969-07-16 | 1974-11-11 | High-strength low-alloy steels having improved formability |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US84240769A | 1969-07-16 | 1969-07-16 | |
| US05/522,524 USRE28790E (en) | 1969-07-16 | 1974-11-11 | High-strength low-alloy steels having improved formability |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US84240769A Reissue | 1969-07-16 | 1969-07-16 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| USRE28790E true USRE28790E (en) | 1976-04-27 |
Family
ID=27060836
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US05/522,524 Expired - Lifetime USRE28790E (en) | 1969-07-16 | 1974-11-11 | High-strength low-alloy steels having improved formability |
Country Status (1)
| Country | Link |
|---|---|
| US (1) | USRE28790E (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0030309A2 (en) * | 1979-12-06 | 1981-06-17 | Preussag Stahl Aktiengesellschaft | Hot rolled strip or plate of denitrided steel and process for its production |
Citations (5)
| 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 |
| US3375105A (en) * | 1965-10-22 | 1968-03-26 | Vanadium Corp Of America | Method for the production of fine grained steel |
-
1974
- 1974-11-11 US US05/522,524 patent/USRE28790E/en not_active Expired - Lifetime
Patent Citations (5)
| 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 |
| US3375105A (en) * | 1965-10-22 | 1968-03-26 | Vanadium Corp Of America | Method for the production of fine grained steel |
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. * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0030309A2 (en) * | 1979-12-06 | 1981-06-17 | Preussag Stahl Aktiengesellschaft | Hot rolled strip or plate of denitrided steel and process for its production |
| EP0030309A3 (en) * | 1979-12-06 | 1982-05-12 | Stahlwerke Peine-Salzgitter Ag | Hot rolled strip or plate of denitrided steel and process for its production |
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|---|---|---|---|
| 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 |
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| 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 |
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| 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 |