US3290183A - Method of producing anticorrosion high tensile strength rail - Google Patents
Method of producing anticorrosion high tensile strength rail Download PDFInfo
- Publication number
- US3290183A US3290183A US218429A US21842962A US3290183A US 3290183 A US3290183 A US 3290183A US 218429 A US218429 A US 218429A US 21842962 A US21842962 A US 21842962A US 3290183 A US3290183 A US 3290183A
- Authority
- US
- United States
- Prior art keywords
- rail
- less
- steel
- tensile strength
- rails
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
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
- C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
-
- 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
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
Definitions
- the chromium content in the rail of the present invention is about 2.0 to 6.0% to give corrosionresistance and strength.
- the chromium content is less than about 2%, there is very little corrosion- Fuklwka, and 1530 Kimura, Tobfiia, Fukuoka, Japan, 5 resistance.
- corrosion- $0 zf 3 81 Steel n -i resistance does not increase sufficiently to make the rail a P l' 0 economical.
- 218,429 content is less than about 1% or preferably about 0.1 to 3 Chime (CL 14g 12 0 0.4%. Less than about 1.0% of each of nickel, vanadium, boron, copper, titanium and niobium may be added to The inventi'en relates to method for Pmd'ucmg Corro increase the strength and toughness or corrosion-resistance sion-resistant high tensile strength rails.
- Rails aemany'used in every P Y today "i largely Ln producing the rail of the present invention, a steel Classified with respect to their Composltlons as high f 15 ingot having the above composition is bloomed, is then steel rails and low carbon medium manganese steel rails. slowly Cooled is heheated and is then mhed into a rail In Japan, most of the rails are carbon steel rails which and the rail is then Cooled at a properlyeemmned eeehng are intermediate between the above mentioned two kinds.
- the rail can thereafter be air eliminate the defects of conventional rails with respect to cooled to mom vtermyermure ft the finish 1 then corrosion and fatigueresistance and to provide rails hav- 35 tempered at about 400 t 800 C. and again air-cooled. ing high Corrosion and fatigue'fesieta'nee- By this procedure, rails high in conr-osi-omresistance,
- Another object of the present invention is to give toughtoughness and f tj i t are obtained ness and anticorrosion to rolled rails and to provide rails Blooming er Lrolling f rails can be Tehlaeed other in which the Production of flakes is preventedprocesses such as, for example, pressing, extrusion or
- the rail according to the present invention is composed 4O fo i Of about t0 0., about t-O CI, less Table 1 show thehemical compnsitions of a corrothan about 10% less fihan about less than sion-resistant high tensile strength rail according to the about 10% Si and the remainder being Fe and unavoidpresent invention and of a current carbon steel rail.
- Table 2 shows the results of tests conducted with the contain less than about 1.0% Ni, less than about 0.5 V, id n less than about 1.0% Cu, less than about 0.01% B, less than about 0.5% Ti and/or less than about 0.5 Nb.
- Table 1 In the rail of the present invention, high toughness and corrosion-resistance are achieved by properly controlling C Si Mn P 8 Cr M0 the cooling rate of the rail after rolling it, or by tempering 5 the rail after cooling to room temperature.
- the rail according to the present invention can contain g' f lfi e e carbon in a range of about 0.25 to 0.05% in view of its rail 0.65 0.13 0.81 0.014 0.025 self-hardenability and the precipitation of carbide at high Table 2 V-notch Charpy value Rotary bending fatigue Corrosion in mm./ 111 kg.-rn./cm. limit in kgjmm. half year Yield Tensile Elcnga- Reduc- Hardpoirtin strength tion in tion of ness in Room Smooth, Sprayed lag/mm. in Percent area in Brinell tempera- 20 C. Smooth With corroded Exposed with kg./mm.
- Table 3 Air-cooled to Air-cooled to Slow cooling from each temperature during air cooling after finish-rolling the room term the room temerature after peratuer after a o oing directly being reheated 500 0. 550 O. 600' O. 650 C. 700 O. 150 0.
- the corrosion-resistant high tensile strength rail of the present invention has a yield point, tensile strength and fatigue limit 1.5 to 1.8 times as high, an elongation and reduction of area not substantially different, an impact value several times as high and a much higher low-temperature impact value.
- the corrosion-resistance of the rail of the present invention is more than three times as high.
- reheating after blooming and slow cooling treatments after the finish-rolling are the most essential conditions. These operations improve the elongation and reduction of area values.
- Current carbon steel rails are not affected by reheating and slow cooling. That is, current rails have substantially the same mechanical properties When slowly cooled to room temperature after being rolled as they do when they are not slowly cooled. Therefore, with reference to Tables 2 and 3, as compared with current carbon steel rails under the same conditions, i.e.
- the rail of the present invention has a much higher tensile strength and hardness but is lower in elongation and reduction of area. It is therefore evident, that according to the present invention, a very high tensile strength is obtained, hardness and strength are not altered or are higher, the rates of elongation and reduction of area are equal to those of current carbon steel rails, and high corrosion-resistance is attained. Further, it is seen in Table 3 that the elongation and reduction of area of the rail of the present invention are more improved by reheating before rolling than by directly [rolling and are further improved by slow cooling from 500 to 750 C. after finishrolling.
- a method of manufacturing steel rail which is high in tensile strength and anti-corrosiveness which comprises subjecting a steel containing from 0.05 to 0.25% carbon, from 2.0 to 6.0% chromium, trom about 0.10% to less than 1.0% molybdenum, less than 1.0 silicon, and less than 1.5% manganese to a blooming rolling, cooling the rolled steel down to a temperature below the A transformation point of the steel, again heating said steel up to a rolling temperature, at which temperature said steel is rolled in rail, and the-n gradually cooling said rail from a temperature above 500 to 700 C. down to 150 C., over a period in excess of 7 hours.
- a method of manufacturing steel rail which is high in tensile strength and anti-corrosiveness which comprises subjecting a steel containing from 0.05 to 0.25% carbon, from 2.0 to 6.0% chromium, less than 1.5% manganese, from 0.1 to 1.0% molybdenum and less than 1.0% silicon as main components, adding an element selected from a group consisting of less than 1.0% nickel, less than 0.5% vanadium, less than 0.5 niobium, less than 1.0% copper, less than 0.01% boron, less than 0.5% titanium, and mixture thereof and the rest being Fe, to a blooming rolling, subjecting the bloomed material to a finishrollin-g, to rail, subjecting the trail to an air-cooling after the finishrolling, putting the rail into a heat-keeping furnace, when the temperature of the rail becomes 500 to 750 C., in which the rail is gradually cooled from a range of 500 to 750 C. down to a range of 150 to 200 C. for more than 7 hours.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Description
United States Patent Ofiice Patented Dec. 6, 1966 3 290 183 a METHOD or rnonucirso ANTICORROSION men I TENSILE STRENGTH RAIL Tadashi Ohtake, Tohata, Fukuoka; Koichi Aoki, Yawata,
temperatures. The chromium content in the rail of the present invention is about 2.0 to 6.0% to give corrosionresistance and strength. When the chromium content is less than about 2%, there is very little corrosion- Fuklwka, and 1530 Kimura, Tobfiia, Fukuoka, Japan, 5 resistance. When it is more than about 6%, corrosion- $0 zf 3 81 Steel n -i resistance does not increase sufficiently to make the rail a P l' 0 economical. Mol bdenum eatl irn roves both strength Claims Prmmy applecaimn Japan 1961 and toughness. hi the prese rit 15365555, the molybdenum N Drawing. Filed Aiig. 21, 1962, Ser. No. 218,429 content is less than about 1% or preferably about 0.1 to 3 Chime (CL 14g 12 0 0.4%. Less than about 1.0% of each of nickel, vanadium, boron, copper, titanium and niobium may be added to The inventi'en relates to method for Pmd'ucmg Corro increase the strength and toughness or corrosion-resistance sion-resistant high tensile strength rails. but they are not necessary ingredieme Rails aemany'used in every P Y today "i largely Ln producing the rail of the present invention, a steel Classified with respect to their Composltlons as high f 15 ingot having the above composition is bloomed, is then steel rails and low carbon medium manganese steel rails. slowly Cooled is heheated and is then mhed into a rail In Japan, most of the rails are carbon steel rails which and the rail is then Cooled at a properlyeemmned eeehng are intermediate between the above mentioned two kinds. rate or the rail eeeled to room temperatm-e is then In some parts of Europe and America, rails containing tempered very small amounts of Cr and V or Si-Mn series h Y When the rail of the present invention is rolled and been .eXPeTimemauY manufactured In order is then cooled in air, the hardening rate is so great that fatigueresistance or high tensile strengths However, these the rail becomes very m m Further because f h rails contain only small amounts of alloys and are not hairs Strong tendency to flake the finishrehed rail is intended to have corrosion-resistance. In carbon steel slowly .eoeled to obtain toughness and to prevent the rails used today, the amount of breaks due to both c r -Q- mation of flakes. By such heat-treatment, the formation Sion and fatigue and due cormslon and electrolytic of flakes is prevented, toughness is attained and, at the Corrosion are Very highon the other hand the fatlgue same time, corrosion and fatigue-resistance are increased. limit of current carbon steel rails is to kg./nrm. POT vSuch h .t t m f after mining the mil, it is But, in old rails which have been used to some extent, f bl to p the rail into, a h keeping .fumaee or the fatigue limit decreases due to their exposure to cor- 30 a soaking hit e the temperawfe of the nail has roding environments. Current rails are not yet satisreached about 750 to Qdurihg the aipeeeh'ng The factory with respect Corrosion fatigue-resistance rail is slowly cooled therein for more than about 7 hours Object the Present inventlon 15 completely to about 200 to 150 C. The rail can thereafter be air eliminate the defects of conventional rails with respect to cooled to mom vtermyermure ft the finish 1 then corrosion and fatigueresistance and to provide rails hav- 35 tempered at about 400 t 800 C. and again air-cooled. ing high Corrosion and fatigue'fesieta'nee- By this procedure, rails high in conr-osi-omresistance,
Another object of the present invention is to give toughtoughness and f tj i t are obtained ness and anticorrosion to rolled rails and to provide rails Blooming er Lrolling f rails can be Tehlaeed other in which the Production of flakes is preventedprocesses such as, for example, pressing, extrusion or The rail according to the present invention is composed 4O fo i Of about t0 0., about t-O CI, less Table 1 show thehemical compnsitions of a corrothan about 10% less fihan about less than sion-resistant high tensile strength rail according to the about 10% Si and the remainder being Fe and unavoidpresent invention and of a current carbon steel rail. able impurities and y eiPeumSlianees, Table 2 shows the results of tests conducted with the contain less than about 1.0% Ni, less than about 0.5 V, id n less than about 1.0% Cu, less than about 0.01% B, less than about 0.5% Ti and/or less than about 0.5 Nb. Table 1 In the rail of the present invention, high toughness and corrosion-resistance are achieved by properly controlling C Si Mn P 8 Cr M0 the cooling rate of the rail after rolling it, or by tempering 5 the rail after cooling to room temperature. Ra f th present The rail according to the present invention can contain g' f lfi e e carbon in a range of about 0.25 to 0.05% in view of its rail 0.65 0.13 0.81 0.014 0.025 self-hardenability and the precipitation of carbide at high Table 2 V-notch Charpy value Rotary bending fatigue Corrosion in mm./ 111 kg.-rn./cm. limit in kgjmm. half year Yield Tensile Elcnga- Reduc- Hardpoirtin strength tion in tion of ness in Room Smooth, Sprayed lag/mm. in Percent area in Brinell tempera- 20 C. Smooth With corroded Exposed with kg./mm. Percent ture notch with outdoors salt water water L o L 0 Hail of the present invention 76.8 130.6 11.6 20.9 374 8.12 3.89 6.52 3. 51 55.0 28.0 31.0 0.022 0.55 Current carbon steel rail 43.3 87.5 13.8 23.5 249 1.30 0.65 32.0 15.0 20.0 0.078 0.
Table 3 Air-cooled to Air-cooled to Slow cooling from each temperature during air cooling after finish-rolling the room term the room temerature after peratuer after a o oing directly being reheated 500 0. 550 O. 600' O. 650 C. 700 O. 150 0.
fed and rolled and rolled Tensile strength in kg./mm. 122.4 135.0 133 .1 133 .3 132.9 134.0 133 .8 134.1 Elongation in percent 2.3 5.8 6.7 7.6 9.9 13.0 11.8 11.9 Reduction of area in percent 4.7 8 .7 12.8 14.5 19 .9 25 .2 28 .7 28 .3 V-notch Charpy value in kg.-n1 /cm 2 7 .2 7 .7 7 .8 7 .7 7 .8 8 .1 8 .1 8 .2 Hardness in Brinell 385 382 376 375 373 372 363 367 As apparent from these result-s, as compared with the current carbon steel rail, the corrosion-resistant high tensile strength rail of the present invention has a yield point, tensile strength and fatigue limit 1.5 to 1.8 times as high, an elongation and reduction of area not substantially different, an impact value several times as high and a much higher low-temperature impact value. On the other hand, the corrosion-resistance of the rail of the present invention is more than three times as high. In the process for producing rails according to the present invention, reheating after blooming and slow cooling treatments after the finish-rolling are the most essential conditions. These operations improve the elongation and reduction of area values. Current carbon steel rails are not affected by reheating and slow cooling. That is, current rails have substantially the same mechanical properties When slowly cooled to room temperature after being rolled as they do when they are not slowly cooled. Therefore, with reference to Tables 2 and 3, as compared with current carbon steel rails under the same conditions, i.e. slowly cooled to room temperature after being rolled, the rail of the present invention has a much higher tensile strength and hardness but is lower in elongation and reduction of area. It is therefore evident, that according to the present invention, a very high tensile strength is obtained, hardness and strength are not altered or are higher, the rates of elongation and reduction of area are equal to those of current carbon steel rails, and high corrosion-resistance is attained. Further, it is seen in Table 3 that the elongation and reduction of area of the rail of the present invention are more improved by reheating before rolling than by directly [rolling and are further improved by slow cooling from 500 to 750 C. after finishrolling.
What we claim is:
1. A method of manufacturing steel rail which is high in tensile strength and anti-corrosiveness which comprises subjecting a steel containing from 0.05 to 0.25% carbon, from 2.0 to 6.0% chromium, trom about 0.10% to less than 1.0% molybdenum, less than 1.0 silicon, and less than 1.5% manganese to a blooming rolling, cooling the rolled steel down to a temperature below the A transformation point of the steel, again heating said steel up to a rolling temperature, at which temperature said steel is rolled in rail, and the-n gradually cooling said rail from a temperature above 500 to 700 C. down to 150 C., over a period in excess of 7 hours.
2. A method as in claim 1, in which a mixture of elements selected from a group consisting of less than 1.0% nickel, less than 0.5% vanadium, less than 1.0% copper, less than 0.01% boron, less than 0.5% titanium and [less than 0.5% niobium are added to the main components of the steel.
3. A method of manufacturing steel rail which is high in tensile strength and anti-corrosiveness which comprises subjecting a steel containing from 0.05 to 0.25% carbon, from 2.0 to 6.0% chromium, less than 1.5% manganese, from 0.1 to 1.0% molybdenum and less than 1.0% silicon as main components, adding an element selected from a group consisting of less than 1.0% nickel, less than 0.5% vanadium, less than 0.5 niobium, less than 1.0% copper, less than 0.01% boron, less than 0.5% titanium, and mixture thereof and the rest being Fe, to a blooming rolling, subjecting the bloomed material to a finishrollin-g, to rail, subjecting the trail to an air-cooling after the finishrolling, putting the rail into a heat-keeping furnace, when the temperature of the rail becomes 500 to 750 C., in which the rail is gradually cooled from a range of 500 to 750 C. down to a range of 150 to 200 C. for more than 7 hours.
References Cited by the Examiner UNITED STATES PATENTS 1,277,372 9/1918 Birunner 148l2 1,721,555 7/1929 Hamilton et a1. l26 1,925,029 8/1933 Brunner 14812 FOREIGN PATENTS 797,762 2/1936 France.
324,686 1/1930 Great Britain.
340,819 1/1930 Great Britain.
517,118 1/ 1940 Great Britain.
731,684 6/1955 Great Britain.
DAVID L. RECK, Primary Examiner. P. WEINSTEIN, Assistant Examiner.
Claims (1)
1. A METHOD OF MANUFACTURING STEEL RAIL WHICH IS HIGH IN TENSILE STRENGTH AND ANTI-CORROSIVENESS WHICH COMLESS THAN 1.0% MOLYBDENUM, LESS THAN 1.0 SILICON, AND LESS THAN 1.5% MENGANESE TO A BLOOMING ROLLING, COOLING PRISES SUBJECTING A STEEL CONTAINING FROM 0.05 TO 0.25% CARBON, FROM 2.0 TO 6.0% CHROMIUM, FROM ABOUT 0.10% TO THE ROLLED STEEL DOWN TO A TEMPERATURE BELOW THE A1 TRANSFORMATION POINT OF THE STEEL, AGAIN HEATING SAID STEEL UP TO A ROLLING TEMPERATURE, AT WHICH TEMPERATURE SAID STEEL IS ROLLED IN RAIL, AND THEN GRADUALLY COOLING SAID RAIL FROM A TEMPERATURE ABOVE 500 TO 700*C. DOWN TO 150*C., OVER A PERIOD IN EXCESS OF 7 HOURS.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3122561 | 1961-08-29 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3290183A true US3290183A (en) | 1966-12-06 |
Family
ID=12325465
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US218429A Expired - Lifetime US3290183A (en) | 1961-08-29 | 1962-08-21 | Method of producing anticorrosion high tensile strength rail |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US3290183A (en) |
| CH (1) | CH412954A (en) |
| GB (1) | GB1016497A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3531279A (en) * | 1964-12-05 | 1970-09-29 | Thyssen Huette Ag | Ferritic columbium containing,chromium - molybdenum steel,containing nickel |
| US3539338A (en) * | 1966-06-28 | 1970-11-10 | Nippon Kokan Kk | High-temperature alloy steel containing cr and mo |
| US3539404A (en) * | 1967-05-15 | 1970-11-10 | Youngstown Sheet And Tube Co | Method of making a low alloy steel |
| US3640114A (en) * | 1967-07-27 | 1972-02-08 | Teledyne Inc | Method of hot rolling metal |
| US3645723A (en) * | 1969-11-28 | 1972-02-29 | Bethlehem Steel Corp | Quenched and tempered low-alloy steel |
| US3847600A (en) * | 1969-08-27 | 1974-11-12 | Nippon Kokan Kk | High temperature alloy steel |
| DE3515198A1 (en) * | 1984-04-28 | 1985-10-31 | Akebono Brake Industry Co., Ltd., Tokio/Tokyo | Iron-containing brake disc material |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2684109B2 (en) * | 1990-03-13 | 1997-12-03 | 株式会社 日本製鋼所 | Overlay stainless clad steel with excellent peel resistance made of low alloy steel for high temperature and high pressure |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1277372A (en) * | 1917-02-01 | 1918-09-03 | John Brunner | Process of treating steel shapes. |
| US1721555A (en) * | 1927-12-03 | 1929-07-23 | American Steel Foundries | Steel |
| GB324686A (en) * | 1928-09-29 | 1930-01-29 | Christer Peter Sandberg | Improvements relating to the manufacture of railway and tramway rails |
| GB340819A (en) * | 1929-04-23 | 1931-01-08 | Krupp Ag | Improved manufacture of articles requiring high resistibility to the action of hot gases, vapours, and liquids such as pressure receptacles |
| US1925029A (en) * | 1933-03-25 | 1933-08-29 | Brunner John | Heat treatment of steel rails |
| FR797762A (en) * | 1935-11-16 | 1936-05-04 | Steel composition for the manufacture of articles which do not undergo any seizure treatment | |
| GB517118A (en) * | 1938-07-13 | 1940-01-22 | Ver Oberschlesische Huttenwerk | Improvements in and relating to improved steels and the application thereof |
| GB731684A (en) * | 1951-06-13 | 1955-06-15 | Deutsche Edelstahlwerke Ag | Steel for articles having high hot strength |
-
1962
- 1962-08-13 GB GB30936/62A patent/GB1016497A/en not_active Expired
- 1962-08-21 US US218429A patent/US3290183A/en not_active Expired - Lifetime
- 1962-08-28 CH CH1023162A patent/CH412954A/en unknown
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1277372A (en) * | 1917-02-01 | 1918-09-03 | John Brunner | Process of treating steel shapes. |
| US1721555A (en) * | 1927-12-03 | 1929-07-23 | American Steel Foundries | Steel |
| GB324686A (en) * | 1928-09-29 | 1930-01-29 | Christer Peter Sandberg | Improvements relating to the manufacture of railway and tramway rails |
| GB340819A (en) * | 1929-04-23 | 1931-01-08 | Krupp Ag | Improved manufacture of articles requiring high resistibility to the action of hot gases, vapours, and liquids such as pressure receptacles |
| US1925029A (en) * | 1933-03-25 | 1933-08-29 | Brunner John | Heat treatment of steel rails |
| FR797762A (en) * | 1935-11-16 | 1936-05-04 | Steel composition for the manufacture of articles which do not undergo any seizure treatment | |
| GB517118A (en) * | 1938-07-13 | 1940-01-22 | Ver Oberschlesische Huttenwerk | Improvements in and relating to improved steels and the application thereof |
| GB731684A (en) * | 1951-06-13 | 1955-06-15 | Deutsche Edelstahlwerke Ag | Steel for articles having high hot strength |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3531279A (en) * | 1964-12-05 | 1970-09-29 | Thyssen Huette Ag | Ferritic columbium containing,chromium - molybdenum steel,containing nickel |
| US3539338A (en) * | 1966-06-28 | 1970-11-10 | Nippon Kokan Kk | High-temperature alloy steel containing cr and mo |
| US3539404A (en) * | 1967-05-15 | 1970-11-10 | Youngstown Sheet And Tube Co | Method of making a low alloy steel |
| US3640114A (en) * | 1967-07-27 | 1972-02-08 | Teledyne Inc | Method of hot rolling metal |
| US3847600A (en) * | 1969-08-27 | 1974-11-12 | Nippon Kokan Kk | High temperature alloy steel |
| US3645723A (en) * | 1969-11-28 | 1972-02-29 | Bethlehem Steel Corp | Quenched and tempered low-alloy steel |
| DE3515198A1 (en) * | 1984-04-28 | 1985-10-31 | Akebono Brake Industry Co., Ltd., Tokio/Tokyo | Iron-containing brake disc material |
Also Published As
| Publication number | Publication date |
|---|---|
| GB1016497A (en) | 1966-01-12 |
| CH412954A (en) | 1966-05-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US7879160B2 (en) | Cold rolled dual-phase steel sheet | |
| US5545269A (en) | Method for producing ultra high strength, secondary hardening steels with superior toughness and weldability | |
| US7959747B2 (en) | Method of making cold rolled dual phase steel sheet | |
| EP3504349B1 (en) | Method for producing a high-strength steel strip with improved properties for further processing, and a steel strip of this type | |
| DE3142782C2 (en) | ||
| US5098491A (en) | Method of producing steel sheets for porcelain enameling and the same | |
| US7608156B2 (en) | High strength cold rolled steel sheet and method for manufacturing the same | |
| US4581066A (en) | Corrosion resistant alloy | |
| EP0796928A1 (en) | Multiple phase steel and process for its manufacture | |
| DE102016117508B4 (en) | Process for producing a flat steel product from a medium manganese steel and such a flat steel product | |
| US3290183A (en) | Method of producing anticorrosion high tensile strength rail | |
| US6562152B2 (en) | High strength steel plate having improved workability and plating adhesion and process for producing the same | |
| US20230243008A1 (en) | Electro-galvanized super-strength dual-phase steel resistant to delayed cracking, and manufacturing method therefor | |
| WO2018050637A1 (en) | Method for producing a hot or cold strip and/or a flexibly rolled flat steel product made of a high-strength manganese steel and flat steel product produced by said method | |
| DE102016115618A1 (en) | Process for producing a high-strength steel strip with improved properties during further processing and such a steel strip | |
| JPS625986B2 (en) | ||
| DE1558508B2 (en) | USING A MARTENSITE HARDENABLE CHROME NICKEL STEEL | |
| JPS58126956A (en) | High-strength steel sheet with superior press workability | |
| JPS5839770A (en) | Production of high-strength zinc hot dipped steel plate | |
| DE102016204194A1 (en) | Spring components made of a steel alloy and manufacturing process | |
| JPH0215145A (en) | Working and heating hardened hot rolled steel plate | |
| DE1558508C (en) | Use of a martensite-hardenable chromium-nickel steel | |
| KR890002612B1 (en) | Process for manufacturing steel of structure having a good tungsten | |
| KR890002029B1 (en) | Producing method of high tension steel sheet for zn hot dipping | |
| KR920000766B1 (en) | Method of producing a high strength hot rolled steel sheet with an excellency toughness in low temperature |