WO1979000644A1 - High strength steel and process of making - Google Patents
High strength steel and process of making Download PDFInfo
- Publication number
- WO1979000644A1 WO1979000644A1 PCT/US1979/000064 US7900064W WO7900644A1 WO 1979000644 A1 WO1979000644 A1 WO 1979000644A1 US 7900064 W US7900064 W US 7900064W WO 7900644 A1 WO7900644 A1 WO 7900644A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- steel
- strip
- silicon
- martensite
- aluminum
- Prior art date
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 67
- 239000010959 steel Substances 0.000 title claims abstract description 67
- 238000000034 method Methods 0.000 title claims description 6
- 230000008569 process Effects 0.000 title claims description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 23
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 21
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 21
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 20
- 230000032683 aging Effects 0.000 claims abstract description 20
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 20
- 239000011574 phosphorus Substances 0.000 claims abstract description 20
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 18
- 239000010703 silicon Substances 0.000 claims abstract description 18
- 238000010791 quenching Methods 0.000 claims abstract description 15
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 230000009977 dual effect Effects 0.000 claims abstract description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 8
- 230000000171 quenching effect Effects 0.000 claims abstract description 7
- 229910000655 Killed steel Inorganic materials 0.000 claims abstract description 6
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 6
- 238000003303 reheating Methods 0.000 claims abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 10
- 238000005496 tempering Methods 0.000 claims description 9
- 238000000137 annealing Methods 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 8
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 239000011572 manganese Substances 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 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 description 3
- 238000004519 manufacturing process Methods 0.000 claims description 3
- 150000001768 cations Chemical class 0.000 claims description 2
- 238000005097 cold rolling Methods 0.000 abstract description 7
- 239000003973 paint Substances 0.000 abstract description 6
- 238000012360 testing method Methods 0.000 description 23
- 238000007792 addition Methods 0.000 description 6
- 229910000975 Carbon steel Inorganic materials 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 4
- 230000008901 benefit Effects 0.000 description 4
- 230000001419 dependent effect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 230000009467 reduction Effects 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 239000005997 Calcium carbide Substances 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 238000002347 injection Methods 0.000 description 2
- 239000007924 injection Substances 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- CLZWAWBPWVRRGI-UHFFFAOYSA-N tert-butyl 2-[2-[2-[2-[bis[2-[(2-methylpropan-2-yl)oxy]-2-oxoethyl]amino]-5-bromophenoxy]ethoxy]-4-methyl-n-[2-[(2-methylpropan-2-yl)oxy]-2-oxoethyl]anilino]acetate Chemical compound CC1=CC=C(N(CC(=O)OC(C)(C)C)CC(=O)OC(C)(C)C)C(OCCOC=2C(=CC=C(Br)C=2)N(CC(=O)OC(C)(C)C)CC(=O)OC(C)(C)C)=C1 CLZWAWBPWVRRGI-UHFFFAOYSA-N 0.000 description 2
- KKEBXNMGHUCPEZ-UHFFFAOYSA-N 4-phenyl-1-(2-sulfanylethyl)imidazolidin-2-one Chemical compound N1C(=O)N(CCS)CC1C1=CC=CC=C1 KKEBXNMGHUCPEZ-UHFFFAOYSA-N 0.000 description 1
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 238000012935 Averaging Methods 0.000 description 1
- 0 C[C@](C(CC1)=CC)C1=*C Chemical compound C[C@](C(CC1)=CC)C1=*C 0.000 description 1
- 229910000922 High-strength low-alloy steel Inorganic materials 0.000 description 1
- 241000282342 Martes americana Species 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 229940037003 alum Drugs 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 229910001568 polygonal ferrite Inorganic materials 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000000135 prohibitive effect Effects 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 208000016261 weight loss Diseases 0.000 description 1
- 238000003466 welding 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
- 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
-
- 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
- C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
Definitions
- This invention relates to a novel high strength steel and to a process for making.
- a primary object of the present invention is to provide, without the use of costly alloy additions, a novel and improved steel having good ductility which is suitable for use in sheet form for automotive applications and the like and which is not subject to room temperature aging but which has a high work hardening rate and age harden- ing response so that stamping and paint baking result in high strength in the finished part.
- a more specific object of the invention is to provide a high strength low alloy steel of the fore- going character which exhibits a minimum total elongation of 18%, is free from ductility loss due to room temperature aging, and which, in the final fabricated part, exhibits a yield strength of at least 550 Pa (80 ksi) .
- a further object of the invention is to pro ⁇ vide a novel process for making a steel of the fore ⁇ going character.
- the above-described objects of the invention are achieved by cold rolling a low carbon aluminum-killed steel containing added phosphorus and silicon as ferrite strengtheners continuously heating the cold rolled strip to an inter-critical temperature such that from about 5% to about 25% austenite is present, water quenching to obtain a dual phase ferrite-martensite microstructure having an average volume fraction of martensite of from about 5% to about 25%, and reheating to a sub- critical temperature to temper the steel.
- the re ⁇ sultant sheet or strip has good formability, is free from ductility loss due to room temperature aging, and after straining and aging during fabrication of a formed " part, the desired high strength level is developed.
- the steel product exhibits a minimum of 18% total elongation prior to stamping and a minimum yield strength of 550 MPa (80 ksi) after stamping followed by a typical automotive paint bake cycle.
- This combination of properties allows design engineers to take advantage of po- tential weight reductions by utilizing the high strength of the steel while permitting part fabri ⁇ cation without extensive modification of existing dies.
- the martensite content is kept low enough so that the cold rolled product has a minimum total elongation of 18%, but a moderately high strength level of from about 400 to about 500 MPa (58-73 ksi), dependent upon the carbon content, is realized by including silicon and phosphorus in the steel as ferrite strengtheners.
- the dual phase product has a high strain hardening capacity, and the final fabricated part exhibits the desired mini ⁇ mum yield strength of 550 MPa (80 ksi) .
- the dual phase microstructure is obtained by rapid quenching from an inter-critical temperature within a controlled narrow range at a cooling rate which is in excess of the critical cooling rate and which is high enough so that phosphorus does not migrate and relocate at the grain boundaries where it would cause poor ductility. Instead, the phosphorus remains within the ferrite grains, and the desired stiffening effect of phosphorus is realized while re ⁇ taining acceptable ductility. Moreover, the cold rolled sheet product of the present invention is not subject to detrimental room temperature aging due to nitrogen since the steel is aluminum-killed.
- the steel composition of the present invention consists essentially of the following, with the bal ⁇ ance essentially iron:
- the maxi ⁇ mum silicon and manganese contents are such that rapid quenching with water, rather than air cooling, is necessary in order to obtain the desired ferrite- martensite microsctructure. To eliminate room tem ⁇ perature aging problems, the steel is fully killed
- the hot metal from the blast furnace is refined in a basic oxygen converter.
- the hot metal may be subjected to conven ⁇ tional desulfurization, e.g. by calcium carbide injection, prior to being charged to the basic oxygen converter.
- the required additions of alum ⁇ inum, silicon, and phosphorus, may be carried out in the ladle prior to ingot casting or continuous casting.
- the usual hot rolling and cold rolling prac ⁇ tices may be used to provide cold rolled coils for subsequent continuous annealing in accordance with the invention.
- the finishing temperature may be from about 785°C to about 955°C, and the coiling temperature may be from about 480°C to about 705°C.
- the percent cold reduction may range from about 40% to about 80%, but a relatively high degree of cold reduction of from about 50% to about 75% is preferred in order to obtain a fine grain size after the annealing step.
- the thickness of the cold rolled strip may be from about 0.3 mm to about 3 mm.
- the cold rolled strip is processed, in accord ⁇ ance with the invention, in a continuous annealing line in which the strip is (1) heated in a soak section to a temperature between the A ] _ and A3 critical points, (2) water quenched in a quench section at a rapid rate to obtain a dual phase ferrite-martensite microstructure, and (3) reheated in a tempering section to a subcritical tempera ⁇ ture and cooled to ambient temperature.
- the strip is temper rolled for flatness.
- the inter-critical soak temperature must be carefully controlled in the soak section of the continuous annealing line, preferably with + 10°C, for partially austenitizing the steel to the desired extent and thereby realizing the aim ductility and yield strength in the quenched and tempered product.
- the cold rolled strip is heated to a narrow temperature range between the A ] _ and the A3 critical points such that from about 5% to about 25% austenite is present.
- the strip is heated at a soak temperature of from about 745°C to about 845°C for a period of from about 20 to about 120 seconds.
- the partially austenitized strip passes from the soak furnace into a water quench zone of any suitable design capable of rapidly quenching the strip at a rate in excess of the critical cooling rate so that all of the austenite present is con- verted into martensite which is uniformly distrib ⁇ uted in fine grain polygonal ferrite.
- the average volume fraction of martensite present in the quench ⁇ ed product is from about 5% to about 25%.
- a preferred quench system utilizes submerged nozzles such as dis ⁇ closed in Taylor et al U.S. Patent Nos. 3,360,202 and 3,410,734.
- the cooling rate will ordinarily be in excess of 1000°C/sec.
- the rapid quench rate also has the advantage of avoiding relocation of phosphorus to the gain boun ⁇ daries which would impair the ductility of the product.
- the quenched strip is reheated to a sub-critical temperature, e.g. from about i50°C to about 480°C for a period of from about 5 to about 300 seconds, in order to effect tempering of the relatively high carbon content martensite.
- the strip is then cooled to substantially ambient tem ⁇ perature and, when necessary, temper rolled for flatness in the conventional manner to obtain a cold reduction not in excess of 2%.
- the esultant steel sheet or strip product has a minimum total elongation of 18% and a yield strength of from about 400 to about 500 MPa (58 - 73 ksi) , dependent upon the carbon content.
- the product has excellent formability for automotive and other applications, and after stamping and a typical paint bake cycle the yield strength of the fabricated part exceeds the required minimum of 550 MPa (80 ksi) and in most cases is in excess of 620 MPa (90 ksi) .
- the excess aluminum present in the killed steel ties up all the nitrogen present so that there is no loss of ductility due to room temperature aging.
- the uniformity of properties within a coil is excellent, e.g.
- the variation in yield strength being less than 40 MPa (6 ksi) .
- the latter is an important property for a stamping die which is set up for springback con ⁇ trol.
- the product has excellent spot weldability and compares favorably in this respect with aluminum-killed AISI 1006 steel.
- Hot Rolling Conditions Hot Band Reduction Coil Size Steel Finishing Temp. Coiling Temp, Size (mm) (%) (mm)
- test coils were then processed in a con ⁇ tinuous annealing line having in sequence a soak furnace, a water quench system with submerged nozzles, a tempering furnace, a final water cooling tank for cooling the strip to room temperature, and a temper mill.
- the line was operated at speeds ranging from 90 metres/min. for the 1.2 mm thick strip to 130 metres/min. for the 0.5 mm strip, with the heating times varying inversely with the line speed. For example, at a line speed of 110 metres/ min. for the 0.8 mm strip, the heating times in the soak furnace and the tempering furnace were 70 and 65 seconds, respectively.
- the strip temperature in the soak furnace and in the tempering furnace as determined from radiation pyrometer measurements, were about 788° and 260°C, respectively, and these temperatures were controlled within about + 10°C.
- Tables III and IV The results of the tensile tests, averaged for each coil, are presented in Tables III and IV for the 0.07% carbon and the 0.10% carbon steels, re ⁇ spectively.
- A.R refers to the "as-received" steel condition following the quench, temper and temper-roll treat- ment performed on the continuous annealing line
- S&A refers to the steel prop ⁇ erties which resulted from straining the as-re ⁇ ceived steel 2% in tension and aging for one hour at 204°C, which is a simulation of a stamping and pain- baking treatment.
- Formability and microstructural characterization parameters are presented in Table V. Included in this table are full curve "n" values,
- cup height and hole expansion are only about 25 to 35% less for the test steel at any particular gauge, while the yield strength dif- ferences are greater by a factor of two or more.
- the attainment of the high part strength fol- lowing forming and paint-baking is dependent on the ability of the steel to respond to the aging treatment. Since all portions of a formed part may not receive 2% strain and the paint cycle may not always consist of one hour at 204°C (400°F) , the effects of lesser amounts of pre-strain and lower aging temperatures on strained and aged properties of the 0.8 mm test steel were also investigated. It was found that for an aging temperature of 204°C, the minimum strength of 550 MPa (80 ksi) is attain- ed without any prestrain. This indicates that the strain imparted by the temper rolling is sufficient to produce the minimum required strain aging re-
- the weldability of the test steel was also evaluated along with that of AISI 1006 using a range of weld evaluation criteria.
- the welding lobe curves showed that the steel of the resent invention is quite similar to plain carbon steel in terms of weld time - weld current flexibility with no hold- time restrictions being required.
- mechan ⁇ ical testing of the welds showed, in most cases, high strength levels commensurate with the base metal strength.
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)
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE7979900260T DE2965340D1 (en) | 1978-02-21 | 1979-02-07 | High strength steel and process of making |
| CA000321076A CA1118619A (en) | 1978-02-21 | 1979-02-08 | High strength steel and process of making |
| IT7948055A IT7948055A0 (it) | 1978-02-21 | 1979-02-20 | Procedimento per produrre un acciaio di elevata resistenza e prodotto cosi' ottenuto |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US87927378A | 1978-02-21 | 1978-02-21 | |
| US879273 | 1978-02-21 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| WO1979000644A1 true WO1979000644A1 (en) | 1979-09-06 |
Family
ID=25373793
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| PCT/US1979/000064 WO1979000644A1 (en) | 1978-02-21 | 1979-02-07 | High strength steel and process of making |
Country Status (4)
| Country | Link |
|---|---|
| EP (1) | EP0009050B1 (enrdf_load_stackoverflow) |
| JP (1) | JPS55500221A (enrdf_load_stackoverflow) |
| DE (1) | DE2965340D1 (enrdf_load_stackoverflow) |
| WO (1) | WO1979000644A1 (enrdf_load_stackoverflow) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0053913A1 (en) * | 1980-12-04 | 1982-06-16 | Uss Engineers And Consultants, Inc. | Method for producing high-strength deep-drawable dual-phase steel sheets |
| EP0196470A1 (en) * | 1985-03-08 | 1986-10-08 | Hoogovens Groep B.V. | Method of manufacturing dual phase strip steel and steel strip manufactured by the method |
| AU600449B2 (en) * | 1985-09-16 | 1990-08-16 | Illinois Tool Works Inc. | Heat treatment method for strapping |
| CN111088415A (zh) * | 2020-02-12 | 2020-05-01 | 首钢集团有限公司 | 铁素体-马氏体非调质钢、高强螺栓及其制备方法 |
Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2867531A (en) * | 1957-01-31 | 1959-01-06 | Gen Motors Corp | Corrosion-resistant low alloy steel |
| US3193417A (en) * | 1962-12-05 | 1965-07-06 | Inland Steel Co | Enameling steel |
| US3619302A (en) * | 1968-11-18 | 1971-11-09 | Yawata Iron & Steel Co | Method of heat-treating low temperature tough steel |
| US3655465A (en) * | 1969-03-10 | 1972-04-11 | Int Nickel Co | Heat treatment for alloys particularly steels to be used in sour well service |
| US3827924A (en) * | 1971-05-21 | 1974-08-06 | Nippon Steel Corp | High-strength rolled steel sheets |
| DE2503988A1 (de) * | 1974-01-31 | 1975-08-07 | Nippon Kokan Kk | Verfahren zum herstellen von hochfestem, kalt reduziertem stahl bei kontinuierlicher waermebehandlungsstufe |
| US4062705A (en) * | 1973-07-31 | 1977-12-13 | Nippon Steel Corporation | Method for heat treatment of high-toughness weld metals |
| US4067756A (en) * | 1976-11-02 | 1978-01-10 | The United States Of America As Represented By The United States Department Of Energy | High strength, high ductility low carbon steel |
| US4072543A (en) * | 1977-01-24 | 1978-02-07 | Amax Inc. | Dual-phase hot-rolled steel strip |
-
1979
- 1979-02-07 JP JP50048579A patent/JPS55500221A/ja active Pending
- 1979-02-07 WO PCT/US1979/000064 patent/WO1979000644A1/en unknown
- 1979-02-07 DE DE7979900260T patent/DE2965340D1/de not_active Expired
- 1979-09-11 EP EP19790900260 patent/EP0009050B1/en not_active Expired
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2867531A (en) * | 1957-01-31 | 1959-01-06 | Gen Motors Corp | Corrosion-resistant low alloy steel |
| US3193417A (en) * | 1962-12-05 | 1965-07-06 | Inland Steel Co | Enameling steel |
| US3619302A (en) * | 1968-11-18 | 1971-11-09 | Yawata Iron & Steel Co | Method of heat-treating low temperature tough steel |
| US3655465A (en) * | 1969-03-10 | 1972-04-11 | Int Nickel Co | Heat treatment for alloys particularly steels to be used in sour well service |
| US3827924A (en) * | 1971-05-21 | 1974-08-06 | Nippon Steel Corp | High-strength rolled steel sheets |
| US4062705A (en) * | 1973-07-31 | 1977-12-13 | Nippon Steel Corporation | Method for heat treatment of high-toughness weld metals |
| DE2503988A1 (de) * | 1974-01-31 | 1975-08-07 | Nippon Kokan Kk | Verfahren zum herstellen von hochfestem, kalt reduziertem stahl bei kontinuierlicher waermebehandlungsstufe |
| US4067756A (en) * | 1976-11-02 | 1978-01-10 | The United States Of America As Represented By The United States Department Of Energy | High strength, high ductility low carbon steel |
| US4072543A (en) * | 1977-01-24 | 1978-02-07 | Amax Inc. | Dual-phase hot-rolled steel strip |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0053913A1 (en) * | 1980-12-04 | 1982-06-16 | Uss Engineers And Consultants, Inc. | Method for producing high-strength deep-drawable dual-phase steel sheets |
| EP0196470A1 (en) * | 1985-03-08 | 1986-10-08 | Hoogovens Groep B.V. | Method of manufacturing dual phase strip steel and steel strip manufactured by the method |
| AU600449B2 (en) * | 1985-09-16 | 1990-08-16 | Illinois Tool Works Inc. | Heat treatment method for strapping |
| CN111088415A (zh) * | 2020-02-12 | 2020-05-01 | 首钢集团有限公司 | 铁素体-马氏体非调质钢、高强螺栓及其制备方法 |
| CN111088415B (zh) * | 2020-02-12 | 2021-11-19 | 首钢集团有限公司 | 铁素体-马氏体非调质钢、高强螺栓及其制备方法 |
Also Published As
| Publication number | Publication date |
|---|---|
| EP0009050A4 (en) | 1981-01-28 |
| DE2965340D1 (en) | 1983-06-16 |
| JPS55500221A (enrdf_load_stackoverflow) | 1980-04-17 |
| EP0009050A1 (en) | 1980-04-02 |
| EP0009050B1 (en) | 1983-05-11 |
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