US3684589A - Method for producing a minimum-ridging type 430 stainless steel - Google Patents
Method for producing a minimum-ridging type 430 stainless steel Download PDFInfo
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- US3684589A US3684589A US77679A US3684589DA US3684589A US 3684589 A US3684589 A US 3684589A US 77679 A US77679 A US 77679A US 3684589D A US3684589D A US 3684589DA US 3684589 A US3684589 A US 3684589A
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- stainless steel
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- temperature
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- 239000010965 430 stainless steel Substances 0.000 title abstract description 12
- 238000004519 manufacturing process Methods 0.000 title description 3
- 238000000034 method Methods 0.000 abstract description 25
- 230000008569 process Effects 0.000 abstract description 20
- 230000009467 reduction Effects 0.000 abstract description 10
- 238000000137 annealing Methods 0.000 description 22
- 238000005098 hot rolling Methods 0.000 description 12
- 229910000831 Steel Inorganic materials 0.000 description 11
- 239000010959 steel Substances 0.000 description 11
- 238000005097 cold rolling Methods 0.000 description 7
- 238000005554 pickling Methods 0.000 description 7
- 229910001220 stainless steel Inorganic materials 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 4
- 239000011651 chromium Substances 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000010955 niobium Substances 0.000 description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000001627 detrimental effect Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000002411 adverse Effects 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
Classifications
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
-
- 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
Definitions
- An object of this invention is to provide a new and improved process for providing AISI Type 430 stainless steel sheet and strip :which is more effective than the prior art processes in minimizing the ridging problems associated therewith.
- Another object of this invention is to provide a process for producing Type 430 stainless steel sheet and strip having substantially reduced ridging characteristics when subjected to severe cold forming operations, and further having tensile properties equivalent or superior to those of prior art Type 430 stainless steel sheet and strip.
- a further object of this invention is to provide Type 430 stainless steel sheet and strip which can be drawn with minimum ridging in the strained portion thereof.
- the alloy may of course contain the usual steelmaking impurities in amounts insufiicient to affect the alloys properties.
- the process of this invention involves the careful control of all processing parameters in producing the sheet from slab form.
- processing parameters Of critical significance are the hot rolling temperatures, the box annealing times and temperatures following hot rolling, the cold reduction, and the continuous annealing temperatures following cold reduction.
- the preferred process of this invention comprises (1) hot rolling of a slab of Type 430 stainless steel between 1850 and 1950 F. to a thickness of from 0.1 to 0.25 inch; (2) box annealing the hot rolled product at a temperature between 1750 to 1900 F. for at least one hour, and then continuing the box anneal for at least two hours at a reduced temperature of from 14 50 to 1500 F and then furnace cooling the annealed product; 3) pickling and cold rolling the annealed product with a cold reduction of from 35 to and (4) finally continuous annealing the cold rolled product at a temperature of from 1400 to 1500 F. and pickling the cold rolled and annealed sheet or strip product. Steps (3) and (4) may be repeated if necessary in order to attain a product thinner than can be achieved with a. 7 5% cold reduction.
- this inventive process requires lower, critical box annealing temperatures as compared to prior art practices. Whereas box annealing temperatures are usually in the subcritical range, i.e., 1450-1500 F., prior art literature has taught that in order to minimize ridging in a Type 430 steel, higher box annealing temperatures of about 1950" F. are necessary. Contrary to both prior art practices, this process requires a critical annealing temperature not greater than 1900" F., and preferably within the range 1750 to 1900 F., for at least one hour, and then an even lower critical temperature of from 1450 to 1500 F. for at least two more hours.
- the box anneal be performed in a non-oxidizing, non-nitrogen containing atmosphere, such as hydrogen, in order to minimize annealing border, i.e., a heavily oxidized outer edge on the annealed coil.
- the dual temperature feature of the box anneal is primarily to prevent an undesirable open surface characteristic. That is to say, the pickling to remove surface scale following the box anneal has a tendency of producing an open or pitted surface. We believe this is caused by the pickling solution dissolving surface metal adjacent to precipitated carbides at the grain boundaries, which are formed during the box anneal. This detrimental open surface can be markedly reduced by lowering the temperature of the annealing furnace after at least one hour as described. This low temperature treatment reduces the susceptibility of the grain boundaries to attack by the pickling solution. If preferred, the metal can be completely cooled to ambient temperatures between the 1750-1900 F. anneal and the 1450-4500 F. anneal without adverse effect.
- the cold rolling procedure following the box anneal should reduce the annealed hot band from about 35 to about 75%.
- the extent of cold reduction seems to have little or no effect on ridging characteristics.
- total cold reductions of from 35 to 75% are critical to achieve a substantially greater degree of ridging resistance.
- the hot rolling temperatures and the box annealing times and temperatures do not individually have a significant eflect on the steels ridging behavior unless both of the other operations are practiced within the critical ranges.
- there is an unexplainable interaction between hot rolling temperatures, annealing times and temperatures and the degree of cold rolling which, when properly combined, will yield a Type 430 stainless steel sheet or strip having a substantially greater resistance to ridging than is possible with prior art practices.
- the final anneal, and any other intermediate anneal during cold rolling should be a continuous anneal at a temperature within the range 1400 to 1500 F.
- This anneal is a simple stress relief anneal below the transformation temperature, and is substantially the same as has been the practice in prior art processes and, therefore, needs no further discussion.
- specimens 1 /2 inch wide by 14 inches long were cut from the finished product in the longitudinal direction and then polished to a mirror finish. All specimens were then strained 15% in tension at room temperature. Specimens were visually examined and rated for severity of ridging according to the following arbitrary scale: 0none; 1very slight; 2slight; 3-moderate; 4severe; and 5-very severe.
- a process for producing a Type 430 stainless steel sheet product with substantially reduced ridging characteristics when drawn comprising forming a steel slab having the composition by weight percent:
- Percent carbon up to 0.15 manganese up to 1.0 silicon up to 1.0 chromium 16 to 18 iron, balance except for incidental impurities;
- hot rolling said slab at a temperature of from 1850 to 1950 F. to a thickness of from 0.1 to 0.25 inch; box annealing the hot rolled steel at a first annealing temperature of from 1750 to 1900 F. for at least one hour, and then at a second annealing temperature of from 1450 to 1500 F. for at least two hours; cold rolling the annealed steel to final thickness with a reduction of from 35 to continuous annealing the cold rolled steel at from 1400 to 1500 F.; and cooling the steel product.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A PROCESS FOR PRODUCING A TYPE 430 STAINLESS STEEL SHEET PRODUCT WITH SUBSTANTIALLY REDUCED RIDGING CHARACTERISTICS WHEN DRAWN. COMMENCING IN SLAB FORM, THE TYPE 430 STEEL IS HOT ROLLED AT 1850 TO 1950* F. TO A THICKNESS OF 0.1 TO 0.25 INCH; BOX ANNEALED AT 1750 TO 1900* F. FOR AT LEAST ONE HOUR AND THEN AT 1450 TO 1500* F. FOR AT LEAST TWO HOURS; COLD ROLLED WITH A THICKNESS REDUCTION OF FROM 35 TO 75%; AND CONTINUOUS ANNEALED AT FROM 1400 TO 1500% F.
Description
United States Patent O 3,684,589 METHOD FOR PRODUCING A MINIMUM- RIDGING TYPE 430 STAINLESS STEEL Kenneth G. Brickner, OHara Township, Allegheny County, and George A. Ratz, Bethel Park Borough,
Pa., assignors to United States Steel Corporation No Drawing. Filed Oct. 2, 1970, Ser. No. 77,679
Int. Cl. CZld 9/46, 9/48 US. Cl. 148-12 2 Claims ABSTRACT OF THE DISCLOSURE BACKGROUND OF THE INVENTION It is Well known that the 17% chromium ferritic stainless sheet steels (i.e., AISI Type 430 stainless steels) usually exhibit a surface defect known as ridging or roping when subjected to severe cold forming operations such as deep drawing. This defect appears as narrow raised areas similar to corrugations parallel to the cold rolling direction. Ridging is of course detrimental to the appearance of the drawn part, and expensive grinding and polishing operations are required to suitably improve the appearance.
Although many processes and procedures have been developed to overcome the ridging problems associated with the AISI Type 430 stainless steels, these processes have not been altogether satisfactory, at least from a commercial point of view. According to one process for example (US. Pat. No. 2,965,479), ridging can be eliminated by adding small amounts of columbium to the alloy. Although this process is used commercially to a limited extent, it greatly adds to the cost of the product, not only because of the cost of the columbium itself, but because the columbium causes processing ditficulties resulting in lower yields. Most other procedures for reducing the ridging problem have involved the careful control of processing parameters, i.e., rolling and annealing, to eflFect particular microstructures allegedly found to be non-ridging in nature. Of particular significance to this invention is a process disclosed in US. Pat. No. 2,851,384, Waxweiler, Sept. 9, 1958. According to this patent, ridging is minimized by increasing the amount of austenite to above 35% at the hot rolling temperatures, and then subjecting the steel to carefully controlled heat treatments to randomize the texture or orientation of the hot rolled grains. The austenite content is controlled through close control of carbon, nitrogen, silicon, nickel and manganese in a 14-18% chromium stainless steel. Although this process, and other prior art proceses, are effective to some extent in minimizing ridging in conventional Type 430 stainless steels, none of the prior art processes have been completely successful in eliminating the ridging problem. Hence, there still remains considerable area for improvement.
SUMMARY OF THE INVENTION An object of this invention is to provide a new and improved process for providing AISI Type 430 stainless steel sheet and strip :which is more effective than the prior art processes in minimizing the ridging problems associated therewith.
'ice
Another object of this invention is to provide a process for producing Type 430 stainless steel sheet and strip having substantially reduced ridging characteristics when subjected to severe cold forming operations, and further having tensile properties equivalent or superior to those of prior art Type 430 stainless steel sheet and strip.
A further object of this invention is to provide Type 430 stainless steel sheet and strip which can be drawn with minimum ridging in the strained portion thereof.
These and other objects and advantages will become apparent from the following detailed description of this invention.
DESCRIPTION OF THE PREFERRED EMBODIMENT The process of this invention is applicable to the A151 Type 430 stainless steels which have a nominal composition as follows:
Percent Carbon max 0.15 Manganese max 1.0 Silicon max 1 .0 Chromium 16-18 Iron, balance.
Besides the above listed elements, the alloy may of course contain the usual steelmaking impurities in amounts insufiicient to affect the alloys properties.
Stated briefly, the process of this invention, whereby a Type 430 stainless steel is produced with minimum ridging characteristics, involves the careful control of all processing parameters in producing the sheet from slab form. Of critical significance are the hot rolling temperatures, the box annealing times and temperatures following hot rolling, the cold reduction, and the continuous annealing temperatures following cold reduction.
More specifically, the preferred process of this invention comprises (1) hot rolling of a slab of Type 430 stainless steel between 1850 and 1950 F. to a thickness of from 0.1 to 0.25 inch; (2) box annealing the hot rolled product at a temperature between 1750 to 1900 F. for at least one hour, and then continuing the box anneal for at least two hours at a reduced temperature of from 14 50 to 1500 F and then furnace cooling the annealed product; 3) pickling and cold rolling the annealed product with a cold reduction of from 35 to and (4) finally continuous annealing the cold rolled product at a temperature of from 1400 to 1500 F. and pickling the cold rolled and annealed sheet or strip product. Steps (3) and (4) may be repeated if necessary in order to attain a product thinner than can be achieved with a. 7 5% cold reduction.
Although the details of the microstructural development and the cross relationships between the various parameters are not completely understood, we have found that each of the above specified parameters is critical if an improved minimum-ridging product is to be achieved.
In the manufacture of Type 430 stainless steel sheet and strip by prior art practices, conventional slab hot rolling temperatures of about 2100 to 2200" F. are utilized. In the practice of this invention, however, lower slab hot rolling temperatures of from 1850 to 1950 F. are critical to achieve the substantially increased ridging resistance which characterizes the invention. When this rolling temperature range is used, the finishing temperature of the hot rolling operation is not critical nor are the individual hot reductions. As in prior art practices, therefore, we prefer to hot roll sufficient to produce a hot band of from 0.1 to 0.25 inch thick.
In a like manner, this inventive process requires lower, critical box annealing temperatures as compared to prior art practices. Whereas box annealing temperatures are usually in the subcritical range, i.e., 1450-1500 F., prior art literature has taught that in order to minimize ridging in a Type 430 steel, higher box annealing temperatures of about 1950" F. are necessary. Contrary to both prior art practices, this process requires a critical annealing temperature not greater than 1900" F., and preferably within the range 1750 to 1900 F., for at least one hour, and then an even lower critical temperature of from 1450 to 1500 F. for at least two more hours. During the first hour of box annealing within the range 1750 to 1900 F., temperatures in the low end of the range are preferred in order to minimize grain coarsening. Such grain coarsening frequently causes an orange peel effect on the surface of deep drawn articles, which, like ridging, is undesirable insofar as appearance is concerned. It is further preferred that the box anneal be performed in a non-oxidizing, non-nitrogen containing atmosphere, such as hydrogen, in order to minimize annealing border, i.e., a heavily oxidized outer edge on the annealed coil.
The dual temperature feature of the box anneal, as described above, is primarily to prevent an undesirable open surface characteristic. That is to say, the pickling to remove surface scale following the box anneal has a tendency of producing an open or pitted surface. We believe this is caused by the pickling solution dissolving surface metal adjacent to precipitated carbides at the grain boundaries, which are formed during the box anneal. This detrimental open surface can be markedly reduced by lowering the temperature of the annealing furnace after at least one hour as described. This low temperature treatment reduces the susceptibility of the grain boundaries to attack by the pickling solution. If preferred, the metal can be completely cooled to ambient temperatures between the 1750-1900 F. anneal and the 1450-4500 F. anneal without adverse effect.
As stated above, the cold rolling procedure following the box anneal should reduce the annealed hot band from about 35 to about 75%. When the hot band is produced in accordance with conventional prior art practices, the extent of cold reduction seems to have little or no effect on ridging characteristics. However, in the practice of this invention, and for reasons we cannot explain, wherein the critical hot rolling temperatures are followed and the critical box anneal parameters maintained as described, total cold reductions of from 35 to 75% are critical to achieve a substantially greater degree of ridging resistance. In a like manner, the hot rolling temperatures and the box annealing times and temperatures do not individually have a significant eflect on the steels ridging behavior unless both of the other operations are practiced within the critical ranges. Hence there is an unexplainable interaction between hot rolling temperatures, annealing times and temperatures and the degree of cold rolling which, when properly combined, will yield a Type 430 stainless steel sheet or strip having a substantially greater resistance to ridging than is possible with prior art practices.
As stated above, the final anneal, and any other intermediate anneal during cold rolling should be a continuous anneal at a temperature within the range 1400 to 1500 F. This anneal is a simple stress relief anneal below the transformation temperature, and is substantially the same as has been the practice in prior art processes and, therefore, needs no further discussion.
The pickling procedures following the box anneal and the continuous anneal are of course merely to remove surface scale and may, therefore, conform to any prior art pickling process.
The following examples of tests and the results thereof TABLE I Chemical compositions of the steels investigated (percent) Steel 0 Mn P 8 Si Cr Ni Cu Mo N From these two heats many test specimens were prepared and processed at differing parameters to ascertain the varying elfects of the differing parameters. The variables studied in detail were (1) initial slab rolling temperature; (2) finishing temperature of slab hot rolling; (3) box annealing temperature; (4) boX annealing time; (5) method of cooling after box annealing; (6) and amount of cold reduction.
For testing purposes, specimens 1 /2 inch wide by 14 inches long were cut from the finished product in the longitudinal direction and then polished to a mirror finish. All specimens were then strained 15% in tension at room temperature. Specimens were visually examined and rated for severity of ridging according to the following arbitrary scale: 0none; 1very slight; 2slight; 3-moderate; 4severe; and 5-very severe.
Although the detailed data on all the tests conducted and the results obtained is too voluminous to be presented here, it can be said that those specimens processed within the limits of this invention had an average ridging rating of 0.8. Other specimens wherein one or more of the processing parameters fell outside the scope of this invention had average ridging ratings of about 2.2.
We claim:
1. A process for producing a Type 430 stainless steel sheet product with substantially reduced ridging characteristics when drawn, comprising forming a steel slab having the composition by weight percent:
Percent carbon up to 0.15 manganese up to 1.0 silicon up to 1.0 chromium 16 to 18 iron, balance except for incidental impurities;
hot rolling said slab at a temperature of from 1850 to 1950 F. to a thickness of from 0.1 to 0.25 inch; box annealing the hot rolled steel at a first annealing temperature of from 1750 to 1900 F. for at least one hour, and then at a second annealing temperature of from 1450 to 1500 F. for at least two hours; cold rolling the annealed steel to final thickness with a reduction of from 35 to continuous annealing the cold rolled steel at from 1400 to 1500 F.; and cooling the steel product.
2. The process of claim 1 in which the cold rolling and continuous annealing steps are repeated.
References Cited UNITED STATES PATENTS 2,808,353 10/1957 Leffingwell et al. l48-l2 3,128,211 4/1964 Waxweiler 148-12 3,139,358 6/1964 Graziano 14812 3,141,800 7/196'4 Reichenbach 14812 3,490,956 1/1970 Wilton 148l2 L. DEWAYNE RUTLEDGE, Primary Examiner W. W. STALLARD, Assistant Examiner
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US7767970A | 1970-10-02 | 1970-10-02 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3684589A true US3684589A (en) | 1972-08-15 |
Family
ID=22139463
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US77679A Expired - Lifetime US3684589A (en) | 1970-10-02 | 1970-10-02 | Method for producing a minimum-ridging type 430 stainless steel |
Country Status (8)
| Country | Link |
|---|---|
| US (1) | US3684589A (en) |
| BE (1) | BE772998A (en) |
| CA (1) | CA956551A (en) |
| DE (1) | DE2147624A1 (en) |
| FR (1) | FR2109811A5 (en) |
| GB (1) | GB1322135A (en) |
| IT (1) | IT942660B (en) |
| NL (1) | NL7113539A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3776784A (en) * | 1972-07-14 | 1973-12-04 | Steel Corp | Method of processing stainless steel strips or sheets |
| USRE28494E (en) * | 1972-07-14 | 1975-07-29 | Method of processing stainless steel strips or sheets | |
| US3936323A (en) * | 1975-01-13 | 1976-02-03 | Allegheny Ludlum Industries, Inc. | Method for producing ferritic stainless steel having high anisotropy |
| EP0045958A2 (en) * | 1980-08-09 | 1982-02-17 | Nippon Steel Corporation | Ferrite stainless steel sheets having excellent workability and process for producing the same |
| US4421572A (en) * | 1982-03-18 | 1983-12-20 | The United States Of America As Represented By The United States Department Of Energy | Thermomechanical treatment of alloys |
| US20150206996A1 (en) * | 2012-05-23 | 2015-07-23 | Jfe Steel Corporation | Solar cell substrate made of stainless steel foil and method for manufacturing the same |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2753989B1 (en) * | 1996-10-02 | 1999-12-24 | Steel Authority Of India Limit | IMPROVED PROCESS FOR PRODUCING TWO-PHASE FERRITIC STAINLESS STEEL HAVING HIGH FORMATABILITY AND CONTAINING 17% CHROMIUM |
| KR100625907B1 (en) * | 1998-12-18 | 2006-09-26 | 아웃토컴푸 스테인레스 에이비 | Method for manufacturing of strips and rolling mill line |
| CN112501489B (en) * | 2020-10-31 | 2022-05-13 | 日照宝华新材料有限公司 | Production method of 300 MPa-grade low-carbon hot rolled steel without transverse fracture defect |
-
1970
- 1970-10-02 US US77679A patent/US3684589A/en not_active Expired - Lifetime
-
1971
- 1971-09-15 CA CA122,930A patent/CA956551A/en not_active Expired
- 1971-09-20 GB GB4377471A patent/GB1322135A/en not_active Expired
- 1971-09-23 BE BE772998A patent/BE772998A/en unknown
- 1971-09-23 DE DE19712147624 patent/DE2147624A1/en active Pending
- 1971-09-24 FR FR7134382A patent/FR2109811A5/fr not_active Expired
- 1971-10-01 IT IT70230/71A patent/IT942660B/en active
- 1971-10-01 NL NL7113539A patent/NL7113539A/xx unknown
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3776784A (en) * | 1972-07-14 | 1973-12-04 | Steel Corp | Method of processing stainless steel strips or sheets |
| USRE28494E (en) * | 1972-07-14 | 1975-07-29 | Method of processing stainless steel strips or sheets | |
| US3936323A (en) * | 1975-01-13 | 1976-02-03 | Allegheny Ludlum Industries, Inc. | Method for producing ferritic stainless steel having high anisotropy |
| EP0045958A2 (en) * | 1980-08-09 | 1982-02-17 | Nippon Steel Corporation | Ferrite stainless steel sheets having excellent workability and process for producing the same |
| EP0045958A3 (en) * | 1980-08-09 | 1982-04-07 | Nippon Steel Corporation | Process for producing ferrite stainless steel sheets having excellent workability |
| US4421572A (en) * | 1982-03-18 | 1983-12-20 | The United States Of America As Represented By The United States Department Of Energy | Thermomechanical treatment of alloys |
| US20150206996A1 (en) * | 2012-05-23 | 2015-07-23 | Jfe Steel Corporation | Solar cell substrate made of stainless steel foil and method for manufacturing the same |
| US10312385B2 (en) * | 2012-05-23 | 2019-06-04 | Jfe Steel Corporation | Solar cell substrate made of stainless steel foil and method for manufacturing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| NL7113539A (en) | 1972-04-05 |
| DE2147624A1 (en) | 1972-04-06 |
| FR2109811A5 (en) | 1972-05-26 |
| CA956551A (en) | 1974-10-22 |
| IT942660B (en) | 1973-04-02 |
| GB1322135A (en) | 1973-07-04 |
| BE772998A (en) | 1972-03-23 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| AS | Assignment |
Owner name: USX CORPORATION, A CORP. OF DE, STATELESS Free format text: MERGER;ASSIGNOR:UNITED STATES STEEL CORPORATION (MERGED INTO);REEL/FRAME:005060/0960 Effective date: 19880112 |