US3592633A - High strength low alloy steel possessing sufficient weldability containing small amounts of nb,ti,and b - Google Patents
High strength low alloy steel possessing sufficient weldability containing small amounts of nb,ti,and b Download PDFInfo
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- US3592633A US3592633A US802715*A US3592633DA US3592633A US 3592633 A US3592633 A US 3592633A US 3592633D A US3592633D A US 3592633DA US 3592633 A US3592633 A US 3592633A
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- steel
- high strength
- low alloy
- strength low
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- 229910000922 High-strength low-alloy steel Inorganic materials 0.000 title abstract description 7
- 238000005275 alloying Methods 0.000 abstract description 8
- 238000010438 heat treatment Methods 0.000 abstract description 8
- 239000004615 ingredient Substances 0.000 abstract description 3
- 229910000831 Steel Inorganic materials 0.000 description 42
- 239000010959 steel Substances 0.000 description 42
- 239000010955 niobium Substances 0.000 description 12
- 239000010936 titanium Substances 0.000 description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 229910052799 carbon Inorganic materials 0.000 description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 238000003466 welding Methods 0.000 description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 239000011572 manganese Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 239000011651 chromium Substances 0.000 description 5
- 239000010949 copper Substances 0.000 description 5
- 229910052758 niobium Inorganic materials 0.000 description 5
- 229910052757 nitrogen Inorganic materials 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 4
- 238000009628 steelmaking Methods 0.000 description 4
- 238000005496 tempering Methods 0.000 description 4
- 229910052796 boron Inorganic materials 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 230000035945 sensitivity Effects 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- ZPUCINDJVBIVPJ-LJISPDSOSA-N cocaine Chemical compound O([C@H]1C[C@@H]2CC[C@@H](N2C)[C@H]1C(=O)OC)C(=O)C1=CC=CC=C1 ZPUCINDJVBIVPJ-LJISPDSOSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003389 potentiating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Definitions
- the present invention relates to high strength low alloy steels and, more particularly, to high strength steels for welding structural services.
- the low carbon steel possesses a yield point of more than 70 kg./mrn. and superior toughness and has been proved in reduced hardenability in welding and decreased crack sensitivity.
- the invention also contemplates providing a unique steel particularly adapted to be employed in the Welding structure.
- the present invention contemplates the manufacture of steels heat-treated with quenching of adapting liquids (containing water), gases (containing air), or mixtures of above media at a temperature from AC point to 1050 C. and then with tempering at a temperature of less than AC point.
- the steels of the present invention are composed of the following constituents:
- Carbon is one of the more potent and more economical strengthening elements. It is well known that carbon has the strongest influence upon hardenability of weld zone. Accordingly, it is to be desired that carbon content be low as much as possible. Carbon of more than 0.05%, however, is practical from this point of steel making. The upper limit of carbon content, which is 0.15%, is recommended, owing to the need of making 0.01 to 0.03% Nb solute at a quenching temperature of 900 C. to 1000 C., so as to cause Nb-carbide after tempering treatment.
- Niobium content must be determined in consideration of carbon content. According to our experimentations, it is shown that Nb of more than 0.05% scarcely contributed to strength steel. Also, it is impossible to obtain the required strength when Nb content is less than 0.005%
- the suitable Nb content in the present invention consists in the range of 0.005 to 0.05%.
- Manganese of 0.50% which is the lower limit is adopted in consideration of this point of steel making and of hotworkability. Also, 1.60% Mn which is the upper limit is determined in consideration of weldability.
- 0.15% to 0.7% molybdenum possibly causes strength of steel to markedly increase. However, when the content is more than 0.7%, weldability of steel is spoiled and when the content is less than 0.15 strength of steel is harmed.
- titanium is a useful element for improving hardenability of steel and for increasing strength of steel owing to precipitation of Ti-carbide in the tempering treatment stage.
- Nitrogen content has a serious influence on combination of Nb-Ti-B which is the main point in the present invention.
- the content must be limited within the range in which it is impossible to form its nitride. More than 0.007% nitrogen harms toughness of steel, owing to the formed Ti-nitride and causes Ti-carhide, which is effective for strength of steels 4 Examining the above-mentioned values, it is understood that maximum hardness in taper hardness test is far lower than the maximum value required by the same kind of high strength steel, such as Hv$430 in Japanese WES Standard. This fact shows that hardness of welding zone to decrease.
- Nitrogen content of the lower limit is 0.002% is markedly lowered according to keeping yield strength according to a restriction of steel making process. of 70 kg.mm. by means of a suitable combination of II! the range of the above-mentioned C l C Nb+Ti+B and at the same time main alloying elements, position, the following range is recommended as preferred such as C, Mn, Ni, Cr, Mo and the like, are far less than values: ordinary high-strength steels.
- High strength low alloy steels composed of 0.05 to As mentioned above, the present invention steel is com- 015% to t0 L posed of alloying of a small quantity of components, and to 150% Mn, and t0 5 t 080% demonstrates yield strength of more than 70 kg./mm. Cu, to 100% to (110% 0-002 to superior toughness and excellent weldability according to N, 0-005 to 0.04% Nb, 0.0005 to 0-00 heat treatment of quenching mother steel from more than 0-005 to (105% T1 and havlhg a V 4 Strength Q more 4C temperature and then of tempering at more than than Q' and POSSeSSIhg sufficleht weldahlllty- 5 C.
- High strength low alloy steels in accordance with The following Table 1 shows examples of the present inclalm 1h Whlch the alloying ingredients wmprise vention steel.
- steels are the presto 012% c, to 050% Si, L00 t0 ent invention steels.
- H to K which are out of 020 to 040% Cu, to 050% 0420 to 0360% the range of components based on the present invention, 04010 to 0'050% 0.005 to (105% 0- to these steels are shown in comparison with the present in- 0.03 Ti, 0.001 to 0.003% B, up to 0.005% N, vention steel.
- L steel is an ordinary high-strength low alloy 3.
- High strength low alloy steel in accordance with claim 2 wherein the steel following heat treatment is 5 quenched at a temperature from AC to 1050 C. and 3,368,887 2/1968 Clark 75-128R then is tempered at less than AC temperature.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
HIGH-STRENGTH LOW-ALLOY STEEL KEEPING YIELD STRENGTH OF MORE THAN 70 KG./MM.2 IN A FURTHER COORDINATED RELATIONSHIP WITH SPECIFIC SMALL AMOUNTS OF ALLOYING INGREDIENTS, PARTICULARLY NB+TI+B, AND POSSESSING GOOD TOUGHNESS AND SUFFICIENT WELDABILITY THROUGH AN ORDINARY QUENCHTEMPER HEAT-TREATMENT.
Description
United States Patent "ice 3,592,633 HIGH STRENGTH LOW ALLOY STEEL POS- SESSING SUFFICIENT WELDABILITY CON- TAINING SMALL AMOUNTS 0]? Nb, Ti, AND B Tatsumi Osuka, Junichi Tanaka, Michio Hayashida, and Yoshiaki Ono, Kawasaki-shi, Japan, assignors to Nippon Kokan Kabushiki Kaisha No Drawing. Filed Jan. 22, 1969, Ser. No. 802,715 Claims priority, application Japan, Jan. 22, 1968, 43/3,389 Int. Cl. C22c 37/10, 39/02 US. Cl. 75-124 4 Claims ABSTRACT OF THE DISCLOSURE High-strength low-alloy steel keeping yield strength of more than 70 kgjmm. in a further coordinated relationship with specific small amounts of alloying ingredients, particularly Nb+Ti+B, and possessing good toughness and sufficient weldability through an ordinary quenchtemper heat-treatment.
The present invention relates to high strength low alloy steels and, more particularly, to high strength steels for welding structural services.
It is well-known that many high-strength low alloy steels having yield points of more than 70 kg./mm. are employed widely or welding structural services. In such cases, both high strength and superior toughness are generally required. These characteristics were obtained by adding a considerable amount of alloying elements with ordinary quench-temper heat treatment. Such conditions of alloying elements, however, make hardenability of steels increase and are apt to bring about cracks at welding zone of steels. For elimination of said defects, preheating of more than 100 C. is generally required. The higher the pre-heating temperatures, the higher the cost becomes. Difliculties of such temperature control increase also in the field of welding steels.
It has now been discovered that by maintaining specified and coordinated ranges of alloying elements, the above defects can be completely eliminated. According to the present invention, the low carbon steel possesses a yield point of more than 70 kg./mrn. and superior toughness and has been proved in reduced hardenability in welding and decreased crack sensitivity.
It is an object of the present invention to provide a novel high strength low alloy steel, particularly containing 0.005% to 0.04% Nb, 0.0005% to 0.005 B and 0.005% to 0.05% Ti.
Other objects and advantages will become apparent from the following descriptions and illustrative examples. The invention also contemplates providing a unique steel particularly adapted to be employed in the Welding structure.
Generally speaking, the present invention contemplates the manufacture of steels heat-treated with quenching of adapting liquids (containing water), gases (containing air), or mixtures of above media at a temperature from AC point to 1050 C. and then with tempering at a temperature of less than AC point.
The steels of the present invention are composed of the following constituents:
3,592,633 Patented July 13, 1971 Percent by weight C 0.05-0.15 Si 0.10-0.70 Mn+Ni 0.50-2.00 But Mn 0.50-1.60 Ni 0.03-0.80 Mo 0.15-0.70 Cu 0.05-0.80 Cr 0.03-1.00 Sol. Al 0.01-0.1 N 0.002-0007 Nb 0.005-0.04 B 00005-0005 Ti 0005-005 The remainder: Fe and unavoidable impurities.
The reasons for the limited ranges above mentioned for the constituents of the present invention steel are as follows:
Carbon is one of the more potent and more economical strengthening elements. It is well known that carbon has the strongest influence upon hardenability of weld zone. Accordingly, it is to be desired that carbon content be low as much as possible. Carbon of more than 0.05%, however, is practical from this point of steel making. The upper limit of carbon content, which is 0.15%, is recommended, owing to the need of making 0.01 to 0.03% Nb solute at a quenching temperature of 900 C. to 1000 C., so as to cause Nb-carbide after tempering treatment.
Niobium content must be determined in consideration of carbon content. According to our experimentations, it is shown that Nb of more than 0.05% scarcely contributed to strength steel. Also, it is impossible to obtain the required strength when Nb content is less than 0.005% The suitable Nb content in the present invention consists in the range of 0.005 to 0.05%.
Manganese of 0.50% which is the lower limit is adopted in consideration of this point of steel making and of hotworkability. Also, 1.60% Mn which is the upper limit is determined in consideration of weldability.
Up to 0.8% nickel causes toughness of steel to increase and results in economical benefits.
When copper content is above 0.5%, nickel must be added simultaneously. More than 0.03% chromium possibly causes strength and hardenability of steel to increase.
0.15% to 0.7% molybdenum possibly causes strength of steel to markedly increase. However, when the content is more than 0.7%, weldability of steel is spoiled and when the content is less than 0.15 strength of steel is harmed.
More than 0.1% aluminum decreases cleanliness and spoils weldability of steel. Also less than 0.01% aluminum brings about a bad influence to addition of boron in steel making stage.
When silicon content is above 0.7% toughness and weldability of steel is harmed.
Up to 0.7% boron possibly causes hardenability of steel to increase without a bad influence to toughness and workability of steel.
0.005% to 0.05% titanium is a useful element for improving hardenability of steel and for increasing strength of steel owing to precipitation of Ti-carbide in the tempering treatment stage.
Nitrogen content has a serious influence on combination of Nb-Ti-B which is the main point in the present invention. By reasons of which nitrogen has powerful aflinity to the above three elements, particularly Ti, the content must be limited within the range in which it is impossible to form its nitride. More than 0.007% nitrogen harms toughness of steel, owing to the formed Ti-nitride and causes Ti-carhide, which is effective for strength of steels 4 Examining the above-mentioned values, it is understood that maximum hardness in taper hardness test is far lower than the maximum value required by the same kind of high strength steel, such as Hv$430 in Japanese WES Standard. This fact shows that hardness of welding zone to decrease. Nitrogen content of the lower limit is 0.002% is markedly lowered according to keeping yield strength according to a restriction of steel making process. of 70 kg.mm. by means of a suitable combination of II! the range of the above-mentioned C l C Nb+Ti+B and at the same time main alloying elements, position, the following range is recommended as preferred such as C, Mn, Ni, Cr, Mo and the like, are far less than values: ordinary high-strength steels.
Pfifcent y Weight As for crack sensitivity, also it is shown that occurence C 04064112 f some Crack in the present invention steels can be comi pletely eliminated on condition of simple pre-heating of MII+NI 1130-0-60 75 C. in comparison with high preheating of 100 C. for Cu 02043-40 ordinary high-strength steel. Cr 0420-0-60 Although the present invention has been described in Mo 02043-60 conjunction 'with preferred examples, it is to be under- Sol A1 0010-01150 stood that modifications and variations may be resorted to Nb 013054103 without departing from the spirit and scope of the inven- Ti (1014103 tion as those skilled in the art will readily understand. B What we claim is: N less than O-OOS 1. High strength low alloy steels composed of 0.05 to As mentioned above, the present invention steel is com- 015% to t0 L posed of alloying of a small quantity of components, and to 150% Mn, and t0 5 t 080% demonstrates yield strength of more than 70 kg./mm. Cu, to 100% to (110% 0-002 to superior toughness and excellent weldability according to N, 0-005 to 0.04% Nb, 0.0005 to 0-00 heat treatment of quenching mother steel from more than 0-005 to (105% T1 and havlhg a V 4 Strength Q more 4C temperature and then of tempering at more than than Q' and POSSeSSIhg sufficleht weldahlllty- 5 C. High strength low alloy steels in accordance with The following Table 1 shows examples of the present inclalm 1h Whlch the alloying ingredients wmprise vention steel. In Table 1 from A to G, steels are the presto 012% c, to 050% Si, L00 t0 ent invention steels. And from H to K, which are out of 020 to 040% Cu, to 050% 0420 to 0360% the range of components based on the present invention, 04010 to 0'050% 0.005 to (105% 0- to these steels are shown in comparison with the present in- 0.03 Ti, 0.001 to 0.003% B, up to 0.005% N, vention steel. L steel is an ordinary high-strength low alloy 3. High strength low alloy steel in accordance with steel. claim 1, wherein the steel following heat treatment is TABLE I Mechanical properties Chemical composition Chemical compound Elonga- Yield Tensile tion, vIrs, vTr,1s 0 Si Mn P 5 Cu Ni Cr Mo Nb Tl B Al N point strength vEo 0. 0. 14....000 0.13 1.05 0.020 0.015 0.30 0.25 0.44 0.42 0.012 0.03 0.002 0.035 0.0051 77.1 80.0 23.1 18.7 -94 -100 13.... 0.11 0.10 1.10 0.018 0.011 0.31 0.20 0.40 0.42 0.015 0.03 0.002 0.030 0.0045 75.8 80.2 22.5 24.3 -58 -03 0.... 0.10 0.10 1.00 0.015 0.014 0.24 0.31 0.44 0.42 0.017 0.02 0.001 0.030 0.0035 81.2 83.4 23.3 17.9 -52 -97 D --0. 10 0.21 1.24 0.014 0.014 0.24 0.27 0. 0.42 0.021 0.02 0.003 0.048 0.0041 83.3 85.1 23.3 10.7 -00 -102 0.10 0.22 1.29 0.023 0.013 0.30 0.03 0.54 0.30 0.010 0.02 0.002 0.042 0.0007 78.7 83.2 24.8 18.9 -120 0.10 0.20 1.23 0.022 0.007 0.27 0.03 0.57 0.38 0.015 0.01 0.002 0.042 0.0005 78.7 83.1 23.0 19.2 -74 -111 G-.. 0.12 0.17 1.24 0.022 0.010 0.30 0.03 0.53 0.39 0.033 0.02 0.002 0.002 0.0002 70.0 83.1 23.9 14.9 -42 -73 H 10 0.13 1.10 0.020 0.010 0.30 0.27 0.44 0.40 0.012 0.03 0.002 0.040 0.0112 70.7 75.8 23.0 10.9 -7 -45 1--.. 0.10 0.24 1.27 0.021 0.017 0.28 0.03 0.57 0.39 'Ir. 0.02 0.002 0.050 0.0004 05.1 72.0 28.0 21.5 -103 -120 0.10 0.20 1.20 0.021 0.013 0.28 0.04 0.53 0.39 0.010 0.00 0.002 0.030 0.0009 77.7 82.9 24.5 11.0 -18 -58 K... 0.12 0.23 1.30 0.023 0.015 0.38 0.20 0.48 0.40 0.015 Tr. 0.002 0.028 0.0110 00.3 75.2 20.7 23.9 -72 L 0.12 0.20 0.80 0.010 0.018 0.27 0.85 0.53 0.54 V0.05 Tr. 0.004 0.028 0.0005 77.1 83.0 23.5 11.3 -89 -104 l KgJmmJ. 2 KgrnJcmfi.
In Table II, the values of which hardness and crack sensitivity of B, C, D and L steels in Table I are tested by means of both taper hardness test and y-type slit crack test methods are shown.
quenched at a temperature from AC to 1050 C. and then is tempered at less than AC temperature.
4. High strength low alloy steel in accordance with claim 2, wherein the steel following heat treatment is 5 quenched at a temperature from AC to 1050 C. and 3,368,887 2/1968 Clark 75-128R then is tempered at less than AC temperature.
HYLAND BIZOT, Primary Examiner References Cited UNITED STATES PATENTS 5 CL 2,750,233 6/1956 Loveless 75-124 75125128R;148-31 3,216,823 11/1965 Gulya 7s 124 CEL 33 a g g; 9
Patent No. 3'592'633 Dated y 1971 Inventoflg) TATSUMI OSUKA et al It is certified t hat error appears in th e above-identified patent and that said Letters Patent are hereby corrected as shown below: f
Column 4, line 24 (Claim 1, line 3) before "0.05" insert "0 15 to O 70% M0" Signed and sealed this 15th day of February 1972.
(SEAL) Attest:
EDWARD M.FLETCHER,JR. ROBERT GOT'ISCHALK Attesting Officer Commissioner of Patents
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP338968 | 1968-01-22 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3592633A true US3592633A (en) | 1971-07-13 |
Family
ID=11555988
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US802715*A Expired - Lifetime US3592633A (en) | 1968-01-22 | 1969-01-22 | High strength low alloy steel possessing sufficient weldability containing small amounts of nb,ti,and b |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US3592633A (en) |
| DE (1) | DE1903070A1 (en) |
| FR (1) | FR2000542A1 (en) |
| GB (1) | GB1210795A (en) |
| SE (1) | SE344215B (en) |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3717508A (en) * | 1970-11-04 | 1973-02-20 | Bethlehem Steel Corp | Method of improving stability of boron hardenability effect in alloy steels |
| US3955971A (en) * | 1974-12-11 | 1976-05-11 | United States Steel Corporation | Alloy steel for arctic service |
| US4043807A (en) * | 1974-01-02 | 1977-08-23 | The International Nickel Company, Inc. | Alloy steels |
| US4062705A (en) * | 1973-07-31 | 1977-12-13 | Nippon Steel Corporation | Method for heat treatment of high-toughness weld metals |
| US4065331A (en) * | 1976-10-08 | 1977-12-27 | Alan Wood Steel Company | Rolled low carbon niobium steel |
| US4080225A (en) * | 1976-10-08 | 1978-03-21 | Alan Wood Steel Company | Low temperature, weldable, low alloy steel |
| US4115155A (en) * | 1974-05-03 | 1978-09-19 | Bethlehem Steel Corporation | Low carbon high yield and tensile strength steel and method of manufacture |
| US4123261A (en) * | 1976-10-21 | 1978-10-31 | Stora Kopparbergs Bergslags Ab | Titanium-stabilized deep drawing steel suitable for hot galvanizing |
| US4185998A (en) * | 1978-12-07 | 1980-01-29 | United States Steel Corporation | Steel with improved low temperature toughness |
| US4210445A (en) * | 1977-10-18 | 1980-07-01 | Kobe Steel, Ltd. | Niobium-containing weldable structural steel having good weldability |
| US5743929A (en) * | 1995-08-23 | 1998-04-28 | The Boc Group, Inc. | Process for the production of high purity carbon dioxide |
| US6315946B1 (en) | 1999-10-21 | 2001-11-13 | The United States Of America As Represented By The Secretary Of The Navy | Ultra low carbon bainitic weathering steel |
| FR2847592A1 (en) * | 2002-11-27 | 2004-05-28 | Ispat Unimetal | Steel for the fabrication of high performance precision mechanical components by either hot or cold deformation processes, has a bainitic structure |
| US10392285B2 (en) | 2012-10-03 | 2019-08-27 | Johns Manville | Submerged combustion melters having an extended treatment zone and methods of producing molten glass |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2396805A2 (en) * | 1977-07-06 | 1979-02-02 | Ugine Aciers | Quenched steels with optimum hardenability - obtd. by using specific amts. of boron, nitrogen, aluminium, and titanium and/or zirconium |
| GB2155035B (en) * | 1984-02-29 | 1988-07-27 | Skf Steel Eng Ab | Steel ring |
| EP0460591A1 (en) * | 1990-06-05 | 1991-12-11 | The Ferrous Wheel Group, Inc. | High performance high strength low alloy steel |
| US5213634A (en) * | 1991-04-08 | 1993-05-25 | Deardo Anthony J | Multiphase microalloyed steel and method thereof |
| FR2688009B1 (en) * | 1992-02-28 | 1994-05-27 | Lorraine Laminage | PROCESS FOR THE PREPARATION OF A STEEL SHEET AND STEEL SHEET OBTAINED BY THIS PROCESS. |
| FR2764308B1 (en) * | 1997-06-04 | 1999-07-23 | Thyssen France Sa | PROCESS FOR THE MANUFACTURE OF A STEEL FOR LARGE DIMENSION MOLDS |
-
1969
- 1969-01-22 US US802715*A patent/US3592633A/en not_active Expired - Lifetime
- 1969-01-22 FR FR6901072A patent/FR2000542A1/fr not_active Withdrawn
- 1969-01-22 GB GB3547/69A patent/GB1210795A/en not_active Expired
- 1969-01-22 SE SE819/69A patent/SE344215B/xx unknown
- 1969-01-22 DE DE19691903070 patent/DE1903070A1/en active Pending
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3717508A (en) * | 1970-11-04 | 1973-02-20 | Bethlehem Steel Corp | Method of improving stability of boron hardenability effect in alloy steels |
| US4062705A (en) * | 1973-07-31 | 1977-12-13 | Nippon Steel Corporation | Method for heat treatment of high-toughness weld metals |
| US4043807A (en) * | 1974-01-02 | 1977-08-23 | The International Nickel Company, Inc. | Alloy steels |
| US4115155A (en) * | 1974-05-03 | 1978-09-19 | Bethlehem Steel Corporation | Low carbon high yield and tensile strength steel and method of manufacture |
| US3955971A (en) * | 1974-12-11 | 1976-05-11 | United States Steel Corporation | Alloy steel for arctic service |
| US4065331A (en) * | 1976-10-08 | 1977-12-27 | Alan Wood Steel Company | Rolled low carbon niobium steel |
| US4080225A (en) * | 1976-10-08 | 1978-03-21 | Alan Wood Steel Company | Low temperature, weldable, low alloy steel |
| US4123261A (en) * | 1976-10-21 | 1978-10-31 | Stora Kopparbergs Bergslags Ab | Titanium-stabilized deep drawing steel suitable for hot galvanizing |
| US4210445A (en) * | 1977-10-18 | 1980-07-01 | Kobe Steel, Ltd. | Niobium-containing weldable structural steel having good weldability |
| US4185998A (en) * | 1978-12-07 | 1980-01-29 | United States Steel Corporation | Steel with improved low temperature toughness |
| US5743929A (en) * | 1995-08-23 | 1998-04-28 | The Boc Group, Inc. | Process for the production of high purity carbon dioxide |
| US6315946B1 (en) | 1999-10-21 | 2001-11-13 | The United States Of America As Represented By The Secretary Of The Navy | Ultra low carbon bainitic weathering steel |
| FR2847592A1 (en) * | 2002-11-27 | 2004-05-28 | Ispat Unimetal | Steel for the fabrication of high performance precision mechanical components by either hot or cold deformation processes, has a bainitic structure |
| WO2004050935A1 (en) * | 2002-11-27 | 2004-06-17 | Mittal Steel Gandrange | Ready-use low-carbon steel mechanical component for plastic deformation and method for making same |
| US20070051434A1 (en) * | 2002-11-27 | 2007-03-08 | Ispat-Unimetal | Ready-use low-carbon steel mechanical component for plastic deformation and method for making same |
| US10392285B2 (en) | 2012-10-03 | 2019-08-27 | Johns Manville | Submerged combustion melters having an extended treatment zone and methods of producing molten glass |
Also Published As
| Publication number | Publication date |
|---|---|
| DE1903070A1 (en) | 1972-06-15 |
| GB1210795A (en) | 1970-10-28 |
| FR2000542A1 (en) | 1969-09-12 |
| SE344215B (en) | 1972-04-04 |
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