GB2066290A - Processes for producing high strength cold rolled steel sheets - Google Patents
Processes for producing high strength cold rolled steel sheets Download PDFInfo
- Publication number
- GB2066290A GB2066290A GB8037996A GB8037996A GB2066290A GB 2066290 A GB2066290 A GB 2066290A GB 8037996 A GB8037996 A GB 8037996A GB 8037996 A GB8037996 A GB 8037996A GB 2066290 A GB2066290 A GB 2066290A
- Authority
- GB
- United Kingdom
- Prior art keywords
- sheet
- temperature
- rolled steel
- steel
- cold rolled
- 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.)
- Granted
Links
- 238000000034 method Methods 0.000 title claims description 23
- 239000010960 cold rolled steel Substances 0.000 title claims description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 62
- 239000010959 steel Substances 0.000 claims abstract description 62
- 238000001816 cooling Methods 0.000 claims abstract description 43
- 238000002791 soaking Methods 0.000 claims abstract description 23
- 238000011282 treatment Methods 0.000 claims abstract description 17
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 14
- 238000005098 hot rolling Methods 0.000 claims abstract description 5
- 238000005097 cold rolling Methods 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims description 8
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 239000000654 additive Substances 0.000 claims description 3
- 238000009628 steelmaking Methods 0.000 claims description 3
- 239000000203 mixture Substances 0.000 abstract description 10
- 238000003303 reheating Methods 0.000 abstract description 5
- 229910000851 Alloy steel Inorganic materials 0.000 abstract 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 9
- 239000011572 manganese Substances 0.000 description 8
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 5
- 230000002411 adverse Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 239000011574 phosphorus Substances 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 238000007654 immersion Methods 0.000 description 3
- 239000003973 paint Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000007664 blowing Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 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 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000012216 screening Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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
- C21D8/0447—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 characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A low-alloy steel is subjected to hot rolling, optionally hot coiling, then cold rolling and continuous annealing. The continuous annealing is performed by soaking the sheet at 730 to 850 DEG C for from 20 seconds to 2 minutes, whereafter the sheet is rapidly cooled with a cooling rate of from 30 to 300 DEG C/sec. If required, an overageing treatment at 300-500 DEG C may be imparted to the sheet, preferably by stopping the rapid cooling at an appropriate temperature to avoid reheating of the sheet. The composition of the steel is as follows: Element Wt% C 0.05-0.12 Si 1.2 max Mn 0.7-1.5 P 0.04-0.15 Sol Al 0.01-0.10 Fe [and impurities] Balance. e
Description
SPECIFICATION
Processes for producing high strength cold rolled steel sheets
This invention relates to processes for producing high strength cold rolled steel sheets. Steel strips as well as cut steel sheets are collectively referred to hereinafter as "sheet".
In recent years, more and more high strength cold rolled steel sheets are being used for automobile care bodies. The production of such high strength cold rolled steel sheets has predominantly been performed by processes utilizing continuous annealing. However, in such production processes, large amounts of elements such as C, Mn, Si, P and Cr, are required to be added to the steel to improve the strength.
When these elements, for example C, Mn and Si, are contained in the steel in large amounts, the weldability of the steel is adversely affected, such that the strength of the welded portion is deteriorated or the susceptibility to fatigue failure of the welded portion is increased. Furthermore excessive contents of these elements also produce undesirable effects on the paintability (paint adhesion) of the steel when a paint coating is applied to final products made from the steel.
For all these reasons, demands have increasingly been made for new arts which can produce high strength cold rolled steel sheets having excellent working characteristics but with lesser contents of these elements.
Therefore, the principal object of the present invention is to provide a process for producing high strength cold rolled steel sheets which can meet the above demands.
Accordingly, this invention provides a process for producing a high strength cold rolled steel sheet, which comprises hot rolling a steel containing (by weight) from 0.05 to 0. 12% C, not more than 1.2% Si, 0.7 to 1.5% Mn, 0.04 to 0.15% P, 0.01% to 0.10% sol.Al with the balance being Fe, normal steel-making additives and unavoidable impurities, cold rolling the hot rolled steel sheet, and subjecting the cold rolled steel sheet to continuous annealing comprising soaking the sheet within a temperature range of from 730 to 850"C for a period of not less than 20 seconds, and then rapidly cooling the continuously annealed sheet with a cooling rate ranging from 30 to 300"C/sec.
It will be appreciated that the basic technical features of the present invention lie in addition of strength-improving elements which produce adverse effect on weldability and paintability to as low a level as possible, and that the primary cooling after soaking in a final continuous annealing is performed at a controlled rapid cooling rate. It is found that steel sheet made by the process of the present invention have properties which at least in part solve the problems mentioned above, but still have strengths of typically 50 to 80 kg/mm2 strength as well as being well-balanced so far as strength and ductility are concerned.
Carbon, silicon and manganese are each effective to impart strength to the steel, and particularly carbon and manganese must be contained in amounts of not less than 0.05% and no. less than 0.7% respectively for carbon and manganese. However, excessive contents of these elements produce adverse effects on the weldability and paintability of the final steel, and for this reason the upper limits of these elements are set at 0. 12% for carbon, 1.2% for silicon and 1.5% for manganese, respectively.
Phosphorus is the most desirable element for imparting strength to the steel, because it can effectively give strength to the steel without substantially adversely effecting the weldability and paintability, unlike carbon, manganese and silicon. However, phosphorus contents of less than 0.04% will not produce the desired strength and therefore the phosphorus content should be at least 0.04%. On the other hand, when the phosphorus content is excessive, the balance between strength and ductility deteriorates and at the same time, the weldability is lowered, although the adverse effect on this property is not so great. Therefore, the upper limit of the phosphorus content is set at 0. 15%.
Aluminum (sol.Al) is necessary for deoxidation of the steel, but less than 0.01% Al is not enough for this purpose, whereas it is not necessary to add aluminum in amounts of more than 0.10%.
Regarding other normal steel-making additives, a small content of these is preferable, but they may be added if necessary.
Steel slabs having the chemical composition as defined above are prepared by the conventional continuous casting process or ingot-breaking process, and these steel slabs are then hot rolled and cold rolled before being subjected to continuous annealing according to the present invention. Regarding the coiling temperature in the hot rolling step, a higher temperature is better, and it is preferable to adopt a coiling temperature of for example, 650GC or higher, to obtain a good strength-to-ductility balance.
The continuous annealing step of the process of this invention comprises one of the following two heat cycles. The first heat cycle ccmprises heating > soaking + rapid cooling, and the second heat cycle comprises heating > soaking > rapid cooling to an overageing treatment temperature ) overageing treatment.
In the first heat cycle, rapid heating of the steel is desirable from the points of view of productivity and so on, and for this purpose, a jet stream heating system is most preferable.
Regarding the soaking, it is performed within a temperature range of from 730 to 850"C for a period ranging from 20 seconds to preferably not more than 2 minutes, because if the temperature is lower than 730"C and the period is shorter than 20 seconds, satisfactory recrystailization and grain growth cannot be achieved, and hence the desired ductility cannot be assured. On the other hand, when the soaking temperature is higher than 850"C, it is excessively high and the strength-ductility balance is destroyed. The soaking time may be longer than 2 minutes, but an excessively long soaking time requires a long furnace, thus giving rise to economic disadvantages. Therefore, the upper limit of the soaking time is preferably set at 2 minutes.
After the completion of soaking, the steel sheet is subjected to rapid cooling. The optimum cooling rate for the rapid cooling ranges from 30 to 300"C/sec., because with a cooling rate below 30 C/sec., the amount of alloying elements mentioned hereinbefore must be increased in order to obtain the desired strength in the resultant steel. However, increasing the amount of alloying elements would induce a deterioration in the weldability and paintability. On the other hand, when the cooling rate is larger than 300"C/sec., the amount of martensite formed by the rapid cooling increases, and this deteriorates the strength-to-ductility balance.For all of these reasons, the cooling rate for the rapid cooling subsequent to the completion of the soaking is limited to the range of from 30 to 300"C/sec. In this way, in combination with the specific steel composition, a high strength cold rolled steel sheet well balanced between strength and ductility and having excellent weldability and paintability can be obtained most economically.
The cooling rate as defined above is difficult to achieve by conventional cooling methods, such as immersion in water, gas screening and water jets, but can easily be achieved by blowing a vapour-liquid mixture on to the steel sheet. The advantage of this cooling method is that a uniform cooling effect across the width of the steel strip can be obtained in spite of the rapid cooling, so that the shape of the steel strip can be improved and a uniform quality of material assured. A further advantage of this cooling method is that it is possible to control the terminal point of the cooling at a desired strip temperature. This is very advantageous for performing the second heat cycle.
In performing the first heat cycle, it is preferred for the steel sheet after the soaking to be cooled slowly from the soaking temperature within the range of from 730 to 850"C down to a temperature ranging from 720 to 650'C, with a cooling rate of not larger than 20"C/second, where-after the sheet is cooled with the cooling rate ranging from 30 to 300 C/sec. This can give rise to a further improvement in the strength-to-ductility balance, although the strength is slightly lowered.
The second heat cycle includes an overaging treatment, which may be performed in the temperature range of from 500 to 300"C so as to precipitate the carbon in solid solution in the steel, and to improve the ductility of the steel. In this heat cycle, the rapid cooling having a cooling rate in the range of from 30 to 300"C/sec. subsequent to the completion of the soaking is terminated at the overageing temperature, so that the steel sheet is immediately subjected to the overageing treatment without the necessity to reheat the steel.
In this way, the heat cycle of cooling to room temperature followed by reheating to the overageing temperature can be avoided, so that the distribution of carbon precipitates is significantly improved and fine precipitates of carbon do not appear in the ferrite grains: instead, relatively large precipitates of carbon appear at the grain boundaries. Under this condition, a satisfactory ductility can be obtained by the overageing treatment.
In performing the second heat cycle, the steel sheet is preferably slowly cooled from the soaking temperature ranging from 730 to 850"C to a temperature ranging from 720 to 650"C, with a cooling rate of not larger than 20"C/sec. Then, the sheet should be cooled to the overageing temperature ranging from 500 to 3O0'C at the cooling rate ranging from 30 to 300"C/sec. By this process, a further improvement in the strength-to-ductility balance can be obtained, although the strength is slightly lowered.
As described above, two types of heat cycle can be adopted following the soaking at the annealing temperature. When more importance is placed on the low yield ratio (yield point/tensile strength), the first type of heat cycle should be used, but when more importance is placed on the strength-to-ductility balance the second type of heat cycle is preferred.
Regarding the overageing treatment time, it may be the same as in conventional such treatments, and thus typically range from 30 seconds to 5 minutes.
This invention extends to steel sheet whenever made by a process of this invention, as described above.
In order that this invention may better be understood, certain specific Examples thereof will now be described in detail.
Steel slabs having the compositions as shown in Table 1 were prepared and hot rolled into hot rolled steel strips of 2.5 mm in thickness, and then cold rolled into cold rolled steel strips of 0.7 mm in thickness. The cold rolled steel strips thus-obtained were subjected to continuous annealing under conditions having various cooling rates, with or without an overageing treatment, as shown in Table 2.
In the cases where the overageing treatment was performed (heat cycles d, e and j), the cooling after the annealing soaking was effected to the room temperature for heat cycle d, whereafter reheating to the overageing temperature was performed, whilst for heat cycles e and j, the cooling after the annealing soaking was terminated at the overageing temperature and the overageing treatment was performed without rehati ng.
The weldability and paintability of the resultant steel sheets are shown in Table 1. From this, it can be seen that steels A and B had a similar chemical composition, but the cooling terminal point was controlled and the overageing treatment (e) was performed with steel A, whereas the overageing treatment (d) was performed after reheating with steel B. A comparison of steel A with steel B clearly shows steel A had a lower yield point and a greater elongation than steel B, indicating that control of the cooling terminal point is more advantageous.
In the cases of steels C and D, the compositions were adjusted so as to produce tensile strengths of about 60 kg/mm2. Steel C is cooled at a rate of 30"C/sec. (b), and steel D is cooled by immersion in water (h); the result is that steel C has a better yield point and elongation than steel D.
In the cases of steels E and F, the compositions were adjusted so as to produce tensile strengths of about 70 kg/mm2; steel E was slowly cooled at 10 C/sec. (a) whereas steel F was rapidly cooled at 100"C/sec. (c). Because steel E required an increased amount of alloying elements to obtain the required strength when using the continuous annealing condition (a), both the paintability and weldability of this steel were poor.
Lastly, in the cases of steels G and H, steel G was rapidly cooled at 300"C/sec (f), and steel
H was rapidly cooled at 350"C/sec. (g). The elongation was low for steel H due to the excessively high cooling rate.
I and J represent examples of the present invention where the steel sheets after the soaking were slowly cooled to the starting temperature (690go) of the rapid cooling with a cooling rate of 10 C/sec. The resultant steel sheets of I and J showed better ductility and an improved strength-to-ductility balance as compared with steels A and E (which also represent examples of the present invention) although the strength was slightly lower.
As will be well understood from the foregoing examples A, C, E, G, I and J of the present invention, cold rolled steel sheet having a good balance between strength and ductility and having excellent paintability and weldability can be obtained by the present invention.
Table 1 Steel Compositions andTest Results
Resultant Mechanical Properties
Compositions (%) Heat
Cycle Y.P. T.S. Paint" Weld-"
C Si Mn P soLAl Applied (kg/mm) (kg/mm) Y.R. El(%) abitity ability
Present
Invfention A 0.062 0.05 1.02 0.06 0.030 e 34.6 52.5 0.66 33.0 O O
Conventional B " " " " " d 36.4 53.2 0.68 29.0 O O
Present
Invention C 0.070 0.60 1.46 0.10 0.050 b 32.1 60.5 0.53 29.8 O O
Conventional D 0.050 0.30 1.20 0.05 0.044 h 41.6 61.2 0.68 21.3 O O
Present
Invention E 0.100 0.92 1.25 0.06 0.028 c 32.6 72.0 0.45 29.0 O O
Conventional F 0.066 0.02 1.75 0.01 0.042 a 33.5 71.5 0.47 23.0 X X
Present
Invention G 0.107 1.02 1.30 0.05 0.033 f 39.8 80.0 0.50 19.3 O O
Conventional H 0.099 0.95 1.46 0.01 0.028 g 42.0 79.3 0.53 16.1 O O
Present
Invemtion I 0.100 0.92 1.25 0.06 0.028 i 31.0 69.8 0.44 30.5 O O
" J 0.062 0.05 1.02 0.06 0.030 j 33.4 51.7 0.65 34.2 O O * O represents satisfactory paintability ; x represents poor paintability ** Weldability was testedbythe cross tensile test at a spot welded portion O represents satisfactory strength ; x represents unsatisfactory
strength Table 2
Continuous Annealing Conditions
Soaking Teminal Conditions: Cooling Temperature Overageing Conditions Temp. ( C) Conditions of Cooling X Time (sec.) ( C/sec.) ( C) Reheating Temp. ( C) X Time (sec.) a 10 Room - - Temperature b 30 ,, - - c 100 ,, - - d 100 ,, performed 400 X 60 e 50 X 60 100 400 not 4OOX60 performed f 300 Room - Temperature 9 350 ,, - - h Water 20 - Immersion Above 690 C : 10 Below 690 C : Room 100 Temperature Above 690 C : q 10 not 400 X 60 Below 690 C : performed 100 400
Claims (11)
1. A process for producing a high strength cold rolled steel sheet, which comprises hot rolling a steel containing (by weight) from 0.05 to 0.12% C, not more than 1.2% Si, 0.7 to 1.5% Mn, 0.04 to 0.15% P, 0.01% to 0.10% solAl with the balance being Fe, normal steelmaking additives and unavoidable impurities, cold rolling the hot rolled steel sheet, and subjecting the cold rolled steel sheet to continuous annealing comprising soaking the sheet within a temperature range of from 730 to 850 C for a period of not less than 20 seconds, and then rapidly cooling the continuously annealed sheet with a cooling rate ranging from 30 to 300 C/sec.
2. A process according to claim 1, in which an overageing treatment is performed on the sheet following the rapid cooling thereof.
3. A process according to claim 2, in which the overageing treatment is performed within the temperature range of from 300 to 500 C.
4. A process according to claim 3, in which the rapid cooling step is terminated when the sheet temperature is in the range of from 500 to 300 C. and the overageing treatment is then immediately performed.
5. A process according to any of claims 2 to 4, in which the overageing treatment is performed for a period of from 30 sec. to 5 min.
6. A process according to any of the preceding claims, in which at the end of the annealing soaking, the temperature of the sheet is relatively slowly reduced to lie within the range of from 720 to 650 C, whereafter the temperature is rapidly reduced at a rate within the range of from 30 to 300OC/sec.
7. A process according to claim 6, in which the relatively slow rate of temperature reduction does not exceed 20 C/sec.
8. A process according to any of the preceding claims, in which the sheet is hot-coiled during the hot-rolling step, the hot-coiling temperature being at least 650 C.
9. A process for producing a high strength cold rolled steel sheet as claimed in claim 1 and substantially es hereinbefore described.
10. A process for producing a high strength cold rolled steel sheet substantially as described in any one of Examples A, C, E, G, I and J set out hereinbefore.
11. High strength cold rolled steel sheet whenever made by a process according to any of the preceding claims.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP54153392A JPS5825733B2 (en) | 1979-11-27 | 1979-11-27 | Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| GB2066290A true GB2066290A (en) | 1981-07-08 |
| GB2066290B GB2066290B (en) | 1983-03-23 |
Family
ID=15561479
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| GB8037996A Expired GB2066290B (en) | 1979-11-27 | 1980-11-27 | Processes for producing high strenght cold rolled steel sheets |
Country Status (10)
| Country | Link |
|---|---|
| JP (1) | JPS5825733B2 (en) |
| BE (1) | BE886351A (en) |
| BR (1) | BR8007715A (en) |
| CA (1) | CA1142068A (en) |
| DE (1) | DE3044338A1 (en) |
| FR (1) | FR2470164A1 (en) |
| GB (1) | GB2066290B (en) |
| IT (1) | IT1134492B (en) |
| NL (1) | NL184789C (en) |
| SE (1) | SE435733B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5935653A (en) * | 1982-08-19 | 1984-02-27 | Kawasaki Steel Corp | High-tension hot-rolled steel plate |
| JPS60144658U (en) * | 1984-02-29 | 1985-09-25 | リグナイト株式会社 | Corrosion-resistant structure of steel sheet piles |
| MX165036B (en) * | 1987-04-10 | 1992-10-16 | Signode Corp | CONTINUOUS TREATMENT OF COLD ROLLED CARBON MANGANESE STEEL |
| JP5717631B2 (en) * | 2009-07-08 | 2015-05-13 | 東洋鋼鈑株式会社 | Cold-rolled steel sheet manufacturing method and cold-rolled steel sheet excellent in press formability |
| CN105483354B (en) * | 2015-12-23 | 2017-09-29 | 中钢集团邢台机械轧辊有限公司 | The heat treatment method of large high-speed steel cold roll |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4923727B1 (en) * | 1969-12-16 | 1974-06-18 | ||
| JPS5551410B2 (en) * | 1974-01-31 | 1980-12-24 | ||
| JPS5157623A (en) * | 1974-11-18 | 1976-05-20 | Nippon Kokan Kk | Takaitosoyakitsukekokaseitosugureta hijikoseiomotsukochoryokureienkohanno seizohoho |
| JPS5536051B2 (en) * | 1974-12-05 | 1980-09-18 | ||
| US4033789A (en) * | 1976-03-19 | 1977-07-05 | Jones & Laughlin Steel Corporation | Method of producing a high strength steel having uniform elongation |
| BE846024A (en) * | 1976-09-09 | 1977-03-09 | PROCESS FOR THE CONTINUOUS THERMAL TREATMENT OF SHEETS |
-
1979
- 1979-11-27 JP JP54153392A patent/JPS5825733B2/en not_active Expired
-
1980
- 1980-11-24 NL NLAANVRAGE8006403,A patent/NL184789C/en not_active IP Right Cessation
- 1980-11-25 DE DE19803044338 patent/DE3044338A1/en active Granted
- 1980-11-25 SE SE8008248A patent/SE435733B/en not_active IP Right Cessation
- 1980-11-26 BR BR8007715A patent/BR8007715A/en not_active IP Right Cessation
- 1980-11-26 BE BE2/58878A patent/BE886351A/en not_active IP Right Cessation
- 1980-11-26 FR FR8025127A patent/FR2470164A1/en active Granted
- 1980-11-27 IT IT26282/80A patent/IT1134492B/en active
- 1980-11-27 CA CA000365649A patent/CA1142068A/en not_active Expired
- 1980-11-27 GB GB8037996A patent/GB2066290B/en not_active Expired
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| NL184789C (en) | 1989-11-01 |
| JPS5677330A (en) | 1981-06-25 |
| DE3044338C2 (en) | 1987-01-08 |
| FR2470164B1 (en) | 1984-11-09 |
| BR8007715A (en) | 1981-06-09 |
| FR2470164A1 (en) | 1981-05-29 |
| DE3044338A1 (en) | 1981-06-25 |
| NL184789B (en) | 1989-06-01 |
| SE8008248L (en) | 1981-05-28 |
| IT1134492B (en) | 1986-08-13 |
| BE886351A (en) | 1981-03-16 |
| CA1142068A (en) | 1983-03-01 |
| GB2066290B (en) | 1983-03-23 |
| SE435733B (en) | 1984-10-15 |
| NL8006403A (en) | 1981-07-01 |
| IT8026282A0 (en) | 1980-11-27 |
| JPS5825733B2 (en) | 1983-05-30 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PE20 | Patent expired after termination of 20 years |
Effective date: 20001126 |