WO2021133345A1 - Micro-alloy steel composition with improved mechanical properties - Google Patents
Micro-alloy steel composition with improved mechanical properties Download PDFInfo
- Publication number
- WO2021133345A1 WO2021133345A1 PCT/TR2020/051354 TR2020051354W WO2021133345A1 WO 2021133345 A1 WO2021133345 A1 WO 2021133345A1 TR 2020051354 W TR2020051354 W TR 2020051354W WO 2021133345 A1 WO2021133345 A1 WO 2021133345A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- weight
- ratio
- maximum
- steel composition
- micro
- Prior art date
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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
- Laminated Bodies (AREA)
Abstract
The invention particularly relates to a micro alloy steel composition comprising; carbon (C) in a ratio of 0.15 - 0.2 % by weight, nitrogen (N) in a ratio of 0.007 % maximum by weight, silicon (Si) in a ratio of 0.25 % maximum by weight, manganese (Mn) in a ratio of 1.1 % maximum by weight, chromium (Cr) in a ratio of 0.6 % maximum by weight, molybdenum (Mo) in a ratio of 0.1 % maximum by weight, nickel (Ni) in a ratio of 0.1% maximum by weight, vanadium (V) in a ratio of 0.15 % maximum by weight, aluminum (Al) in a ratio of 0.05 - 0.15 % by weight, phosphorus (P) in a ratio of 0.03 % maximum by weight, sulphur (S) in a ratio of 0.03 % maximum by weight and copper (Cu) in a ratio of 0.25 % maximum by weight with yield strength of 475 - 550 MPa and tensile strength of 680 - 720 MPa.
Description
Micro-alloy steel composition with improved mechanical properties
Technical Field
The invention relates to a micro-alloy steel composition for which mechanical properties such as yield strength and tensile strength are improved to be used in automotive parts that require high strength and that are produced by forging.
The invention particularly relates to a micro alloy steel composition comprising; carbon (C) in a ratio of 0.15 - 0.2 % by weight, nitrogen (N) in a ratio of 0.007 % maximum by weight, silicon (Si) in a ratio of 0.25 % maximum by weight, manganese (Mn) in a ratio of 1.1 % maximum by weight, chromium (Cr) in a ratio of 0.6 % maximum by weight, molybdenum (Mo) in a ratio of 0.1 % maximum by weight, nickel (Ni) in a ratio of 0.1% maximum by weight, vanadium (V) in a ratio of 0.15 % maximum by weight, aluminum (Al) in a ratio of 0.05 - 0.15 % by weight, phosphorus (P) in a ratio of 0.03 % maximum by weight, sulphur (S) in a ratio of 0.03 % maximum by weight and copper (Cu) in a ratio of 0.25 % maximum by weight with yield strength of 475 - 550 MPa and tensile strength of 680 - 720 MPa.
State of the Art
Micro alloy steels have an important position among steel types by constituting approximately 12 % of the world’s steel production. These steels, which are used in all major steel markets in many parts of the world, play an important role in the automotive, gas and oil pipelines, construction, and transportation industries.
Specific development characteristics of micro alloy steels are steels with perlite and without perlite. Features such as formability, thickness, and weldability etc. are significantly increased by substantially reducing the carbon ratio. Said features are generally required in the production of high strength and lightweight parts by forming the same. Although the carbon ratio is low, the yield limit of these steels can only reach 500 N/mm2 with controlled rolling with the grain refinement and hardening effects of micro alloy elements as aluminum (Al), niobium (Nb), titanium (Ti), vanadium (V).
Niobium (Nb), titanium (Ti), vanadium (V) and aluminium (Al), which are used as alloy elements in micro alloy steels, have a direct effect on the mechanical properties of the material and form carbide, nitride or carbonitride. Carbides, nitrides and carbonitrides formed by micro alloy elements remain insoluble in the austenite phase in case the dissolving
temperatures are not exceeded during hot forming processes. These insoluble hard structures provide to obtain both a small - grain steel structure and an increase in the toughness of the material by preventing austenite grain growth.
In the state of the art, feature of increasing the amount of carbon in the alloy and grain refinement of the micro alloy elements are used so as to obtain high strength. The high carbon steel alloy is exposed to heat treatment after hot forging and a secondary treatment is required so as to increase strength. On the other hand, in the state of the art, micro alloy steels cannot increase the strength of the forged material as much as the heat treated high carbon alloy. While the yield strength of the steel alloy in the high carbon C45E standard is 500 MPa and the tensile strength is 750 - 850 MPa, the yield strength is 435 MPa and the tensile strength is between 580 - 780 MPa in the micro alloy steel.
1141M and C45E alloys are used in the production of automotive parts produced by forging in the prior art. The yield strength of 1141M steel is 435Mpa, the tensile strength is 580- 780Mpa, the hardness is 230-250HV and the yield strength of C45E steel is 500MPa, the tensile strength is 700- 850MPa and the hardness is 220-280HV. In order for these steels to be used in automotive parts, they must be applied heat treatment process. The heat treatment process increases production costs. In addition, the steels used in the prior art cannot reach the desired high strength values for many automotive parts. Therefore, these parts are broken over time. As mentioned, the increase in strength as a result of a costly application with the heat treatment process and the low yield strength in micro-alloy steel reveal the need to develop a new steel alloy.
The patent application numbered CA2666677A1 is found in the literature regarding the subject matter. The invention relates to the production process of steel and high strength, segmented machine parts. The inventive chemical composition of the steel contains 0.40 - 0.60 % carbon (C), 0.20 - 1.00 % silicon (Si), 0.50 - 1.50 % manganese (Mn), max. 1 % chromium (Cr), max. 0.5 % nickel (Ni), max. 0.2 % molybdenum (Mo), max. 0.050 % niobium (Nb), max. 0.3 % vanadium (V), max. 0.05 % aluminium (Al), 0.005 - 0.02 % nitrogen (N) by weight, the remainder consists of iron (Fe) in balance with the other elements and impurities.
Patent application numbered EP1070153B1 relates to a steel composition containing; 0.6 - 0.65 % carbon (C), max. 0.4 % silicon (Si), 0.6 - 0.9 % manganese (Mn), 0.03 - 0.07 % phosphorus (P), 0.07 - 0.11 % Sulphur (S), max. 0.5 % chromium (Cr), max. 0.1 % molybdenum (Mo), max. 0.5 % nickel (Ni), max. 0.5 % copper (Cu), max. 0.5 % aluminium (Al), max. 0.03 % nitrogen (N) by weight, vanadium and iron.
As can be seen in said applications, there are many steel compositions in the state of the art. However, the requirement of micro alloy steel alloys with high strength and high yield strength is increasing day by day.
As a result, due to the abovementioned disadvantages, deficiencies, there is a requirement to make an innovation in the relevant technical field.
The Aim of the Invention
The present invention relates to a micro-alloy steel composition with improved mechanical properties that meets the aforementioned requirements, eliminates the all disadvantages and brings some additional advantages.
The main purpose of the invention is to present a micro-alloy steel composition with higher values than existing products in terms of mechanical properties such as yield strength, tensile strength, and hardness, to be used in automotive parts produced by forging and requiring high strength.
The aim of the invention is to provide a high strength low alloy steel composition.
The aim of the invention is to obtain a steel composition with a yield strength of 475-550 MPa, a tensile strength of 680-720 MPa and a hardness of 210-230 HV after controlled forging.
The aim of the invention is to activate the strength increasing mechanism by using 0.15-0.2% carbon by weight and a maximum of 0.15% vanadium by weight.
The aim of the invention is to benefit from the grain refining effect of aluminum together with vanadium.
The aim of the invention is to ensure that the grain refining elements can reveal their effect due to the fact that in 100-130 seconds in primary cooling, heat transfer coefficient is 60-60- 100 W/m2K, in 1200-1500 seconds in secondary cooling, heat transfer coefficient is 25-60 W/m2K, which is required for forging temperature and post-forging cooling environment.
The aim of the invention is to present a steel composition with a minimum tensile strength starting with a value higher than 17% compared to standard micro alloy steel.
An aim of the invention is to improve the mechanical properties of the steel composition by benefiting from the abilities of intermediate atoms such as C, N and elements such as Mn, Si, Ni, V and Al to make nitride, carbide and carbonitride.
An object of the invention is to provide a steel composition that will eliminate the adverse effect on weldability that may arise from the presence of carbides in the alloy composition.
An object of the invention is to obtain a fine-grained and multi-phase microstructure by making use of the property that TTT and CCT diagrams change according to the alloy element.
In order to fulfill the aims described above, the invention is a micro alloy steel composition, characterized by comprising the following; carbon (C) in a ratio of 0.15 - 0.2 % by weight, nitrogen (N) in a ratio of 0.007 % maximum by weight, silicon (Si) in a ratio of 0.25 % maximum by weight, manganese (Mn) in a ratio of 1.1 % maximum by weight, chromium (Cr) in a ratio of 0.6 % maximum by weight, molybdenum (Mo) in a ratio of 0.1 % maximum by weight, nickel (Ni) in a ratio of 0.1% maximum by weight, vanadium (V) in a ratio of 0.15 % maximum by weight, aluminum (Al) in a ratio of 0.05 - 0.15 % by weight, phosphorus (P) in a ratio of 0.03 % maximum by weight, sulphur (S) in a ratio of 0.03 % maximum by weight and copper (Cu) in a ratio of 0.25 % maximum by weight.
Micro alloy steel composition production method in order to fulfill the aims of the invention comprising the following process steps,
• obtaining the steel composition produced by micro alloying in the form of billets by continuous casting method,
• converting the produced billets into cylindrical semi - finished products in the round long group by hot rolling,
• forming precipitation by subjecting the long semi - finished products to the controlled hot forging and cooling phases, characterized in that;
• said forging temperature is at 950 - 1150°C, the heat coefficient of the primary cooling after forging is 60 - 100 W/m2K for 100 - 130 seconds and the secondary cooling is 25 - 60 W/m2K for 1200 - 1500 seconds under atmospheric conditions.
The structural and characteristic features of the present invention will be understood clearly by the following detailed description and therefore the evaluation shall be made by taking the detailed description into consideration. Detailed Description of the Invention
In this detailed description, the micro-alloy steel composition with improved mechanical properties is described only for a better understanding of the subject and without any limiting effect. The invention is a micro-alloy steel composition with improved mechanical properties such as yield strength and tensile strength for use in automotive parts that require high strength and are produced by forging; wherein it comprises 0.15-0.2% by weight of carbon (C), maximum of 0.007% by weight of nitrogen (N), maximum of 0.25% by weight silicon (Si), maximum of 1.1% by weight of manganese (Mn), maximum of 0.6% by weight of chromium (Cr), maximum of 0.1% by weight of molybdenum (Mo), maximum of 0.1% by weight of nickel (Ni), maximum of 0.15% by weight of vanadium (V), 0.05-0.15% by weight of aluminum (Al), maximum of 0.03% by weight of phosphorus (P), maximum of 0.03% by weight of sulphur (S) and maximum of 0.25% by weight of copper (Cu). The inventive formulation of the micro alloy steel composition;
First of all the alloy elements are determined so as to obtain the inventive formulation of the micro alloy steel composition. The amount and diversity of alloy elements in the steel composition are important parameters for developing the mechanical features.
The features of intermediate atoms such as C, N and elements such as Mn, Si, Ni and Al are used so as to make nitride, carbide and carbonitride, in order to make different strength increasing mechanisms to occur in combination. On the other hand, fine grain and multi phase microstructure is obtained by benefiting from the variable feature of TTT and CCT diagrams.
Secondly, hot forging methodology is formed. Temperature and deformation rates in the hot forging process are rearranged with respect to the original alloy. Finally, a cooling process is applied. The cooling regime for the target microstructure (ferrite, perlite, bainite) is determined according to the TTT and CCT diagrams.
Martensite and bainite conversion in the iron - carbon phase diagram, has an important position in the hardening mechanism of the alloy, in the iron - carbon phase diagram. However, cooling rates are significantly higher than balance conditions due to process conditions in industrial steel production. The iron - carbon phase diagram used in determining the phase conversion with the increase of the cooling rate is not used. The most important reason for this is that said diagram is formed under very slow cooling conditions. Thus, diagrams which are called TTT and indicate the change of phase conversion due to temperature and time are used at high cooling rates.
In fast - cooled steels, the aspects as when the austenite will begin conversion, how long the conversion will be completed and what products will be formed as a result are determined by means of the isothermal transformation diagrams. Thus, TTT diagrams are preferred in determining the phase transformations that will occur in the alloy depending on the super cooling conditions as a function of temperature and time.
It is required to change the conversion curve so as to see the time and temperature effects separately in the conversion reaction. The curves showing this situation are called continuous cooling conversion curves (CCT). CCT diagrams can be used for all heat treatments that also include continuous cooling. The main aim of CCT diagrams is to foresee which structure elements will be obtained and thus which hardness can be obtained by using the cooling curve. These diagrams ensure determining the phase or phases contained in the
final microstructures to be obtained after both isothermal heat treatments where the temperature is kept constant and the conversion in continuous cooling.
The aluminum used with vanadium in the steel composition of the invention shows a grain refining effect. By using 0.15-20% carbon by weight and maximum of 0.15% vanadium by weight together, the strength increasing mechanism is activated.
The tensile strength of the steel composition of the invention starts at a value higher than at least 17% compared to standard micro-alloy steel.
By means of the elements constituting the steel composition of the invention and their applicable amounts by weight, the negative effect on weldability that may occur due to the presence of carbides in the alloy composition is eliminated.
Production method of the inventive micro alloy steel composition;
• The composition of steel produced by micro - alloying is obtained in the form of billets by continuous casting method by using electric arc furnace, ladle furnace, vacuum furnace and tundish dipping closed ceramic tube respectively,
• Converting the produced billets into cylindrical semi - finished products in the round long group by hot rolling,
• Exposing long semi - finished products to controlled hot forging and cooling phases,
• Obtaining a steel alloy with desired mechanical values with the precipitate hardening mechanism,
Said forging temperature used in the inventive production method occurs at 950 - 1150°C, the heat coefficient of the primary cooling after forging is 60 - 100 W/m2K for 100 - 130 seconds and the secondary cooling occurs 25 - 60 W/m2K for 1200 - 1500 seconds under atmospheric conditions.
V-C-N precipitates are formed with 25-45% ferrite, 25-35% perlite and 15-20% bainite phase with the inventive production method.
The micro-alloy steel composition obtained by the production method of the invention is preferably a steel that does not break under high torque (between 1000Nm and 60000Nm) and can be used in automotive parts and cardan shaft.
Mechanical features of the inventive micro alloy steel composition;
• Yield strength 475-550 MPa,
• Tensile strength 680-720 MPa,
• Hardness 210-230 HV,
• Equivalent carbon value is 0.43-0.45 Ceq.
Claims
1. A micro-alloy steel composition, characterized by comprising the following; carbon (C) in a ratio of 0.15 - 0.2 % by weight, nitrogen (N) in a ratio of 0.007 % maximum by weight, silicon (Si) in a ratio of 0.25 % maximum by weight, manganese (Mn) in a ratio of 1.1 % maximum by weight, chromium (Cr) in a ratio of 0.6 % maximum by weight, molybdenum (Mo) in a ratio of 0.1 % maximum by weight, nickel (Ni) in a ratio of 0.1% maximum by weight, vanadium (V) in a ratio of 0.15 % maximum by weight, aluminum (Al) in a ratio of 0.05 - 0.15 % by weight, phosphorus (P) in a ratio of 0.03 % maximum by weight, sulphur (S) in a ratio of 0.03 % maximum by weight and copper (Cu) in a ratio of 0.25 % maximum by weight.
2. A micro alloy steel composition that comprises the following process steps according the claim 1;
• obtaining the steel composition produced by micro alloying in the form of billets by continuous casting method,
• converting the produced billets into cylindrical semi - finished products in the round long group by hot rolling,
• forming precipitation by subjecting the long semi - finished products to the controlled hot forging and cooling phases, characterized in that;
• said forging temperature is at 950-1150°C, the heat coefficient of the primary cooling after forging is 60 - 100 W/m2K for 100 - 130 seconds and the secondary cooling is 25 - 60 W/m2K for 1200 - 1500 seconds under atmospheric conditions.
3. Micro alloy steel composition obtained with a method according to claim 2, characterized in that; the precipitate formed consists of V-C-N, 25-45 % ferrite, 25-35 % perlite and 15-20 % bainite phase.
4. Micro alloy steel composition obtained with a method according to claim 2, characterized in that; it has a yield strength of 475-550 MPa.
5. Micro alloy steel composition obtained with a method according to claim 2, characterized in that; it has a tensile strength of 680-720 MPa.
6. Micro alloy steel composition obtained with a method according to claim 2, characterized in that; it has a hardness of 210-230 HV.
7. Micro alloy steel composition obtained with a method according to claim 2, characterized in that; it has an equivalent carbon value of 0.43-0.45 Ceq.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| TR2019/21223A TR201921223A2 (en) | 2019-12-24 | 2019-12-24 | Composition of micro-alloyed steel with improved mechanical properties |
| TR2019/21223 | 2019-12-24 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| WO2021133345A1 true WO2021133345A1 (en) | 2021-07-01 |
Family
ID=74856911
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| PCT/TR2020/051354 WO2021133345A1 (en) | 2019-12-24 | 2020-12-22 | Micro-alloy steel composition with improved mechanical properties |
Country Status (2)
| Country | Link |
|---|---|
| TR (1) | TR201921223A2 (en) |
| WO (1) | WO2021133345A1 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2023014332A1 (en) * | 2021-08-04 | 2023-02-09 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | High-strength micro-alloyed steel |
| WO2023014330A1 (en) * | 2021-08-04 | 2023-02-09 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | New micro-alloy steel |
| WO2023014331A3 (en) * | 2021-08-04 | 2023-03-02 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | Next-generation micro-alloyed steel |
| WO2023101641A1 (en) * | 2021-11-30 | 2023-06-08 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | High-strength micro-alloyed steel and related production method |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07204734A (en) * | 1994-01-20 | 1995-08-08 | Nippon Steel Corp | Manufacture of high tension and high toughness butt welded steel tube |
| JPH0885844A (en) * | 1994-09-19 | 1996-04-02 | Kawasaki Steel Corp | Resistance welded tube excellent in corrosion grooving resistance |
| JP2001030036A (en) * | 1999-07-23 | 2001-02-06 | Nkk Joko Kk | High strength nontempered steel parts and its manufacture |
| US6217678B1 (en) * | 1998-04-21 | 2001-04-17 | Kabushiki Kaisha Kobe Seiko Sho | Steel wire rod or bar with good cold deformability and machine parts made thereof |
-
2019
- 2019-12-24 TR TR2019/21223A patent/TR201921223A2/en unknown
-
2020
- 2020-12-22 WO PCT/TR2020/051354 patent/WO2021133345A1/en active Application Filing
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07204734A (en) * | 1994-01-20 | 1995-08-08 | Nippon Steel Corp | Manufacture of high tension and high toughness butt welded steel tube |
| JPH0885844A (en) * | 1994-09-19 | 1996-04-02 | Kawasaki Steel Corp | Resistance welded tube excellent in corrosion grooving resistance |
| US6217678B1 (en) * | 1998-04-21 | 2001-04-17 | Kabushiki Kaisha Kobe Seiko Sho | Steel wire rod or bar with good cold deformability and machine parts made thereof |
| JP2001030036A (en) * | 1999-07-23 | 2001-02-06 | Nkk Joko Kk | High strength nontempered steel parts and its manufacture |
Non-Patent Citations (2)
| Title |
|---|
| AL SULTANI KADHIM F. ET AL: "Characterization of Corrosion Behavior of Low Carbon Steel Oil Pipelines by Crude Oil", RES. J. RECENT SCI., vol. 5, no. 5, 31 May 2016 (2016-05-31), pages 7 - 13, XP055793788 * |
| E.J. PAVLINA ET AL: "Correlation of Yield Strength and Tensile Strength with Hardness for Steels", JOURNAL OF MATERIALS ENGINEERING AND PERFORMANCE., vol. 17, no. 6, 1 December 2008 (2008-12-01), US, pages 888 - 893, XP055550915, ISSN: 1059-9495, DOI: 10.1007/s11665-008-9225-5 * |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2023014332A1 (en) * | 2021-08-04 | 2023-02-09 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | High-strength micro-alloyed steel |
| WO2023014330A1 (en) * | 2021-08-04 | 2023-02-09 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | New micro-alloy steel |
| WO2023014331A3 (en) * | 2021-08-04 | 2023-03-02 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | Next-generation micro-alloyed steel |
| WO2023101641A1 (en) * | 2021-11-30 | 2023-06-08 | Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ | High-strength micro-alloyed steel and related production method |
Also Published As
| Publication number | Publication date |
|---|---|
| TR201921223A2 (en) | 2021-07-26 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO2021133345A1 (en) | Micro-alloy steel composition with improved mechanical properties | |
| JP5833751B2 (en) | Ultra-high strength wear-resistant steel sheet and method for producing the same | |
| US4812182A (en) | Air-cooling low-carbon bainitic steel | |
| WO2009154235A1 (en) | Steel for heat treatment | |
| KR20160072099A (en) | A high-hardness hot-rolled steel product, and a method of manufacturing the same | |
| JP2014520954A5 (en) | ||
| EP1910583A1 (en) | Corrosion-resistant, cold-formable, machinable, high strength, martensitic stainless steel | |
| TWI650433B (en) | Cold work tool steel | |
| JP6217671B2 (en) | Thick steel plate with excellent wear resistance in high temperature environments | |
| JP2021517609A (en) | Forged parts of bainite steel and its manufacturing method | |
| EP3209806A1 (en) | An ultra-high strength thermo-mechanically processed steel | |
| WO2020169410A1 (en) | High strength steel with improved mechanical properties | |
| US20120315181A1 (en) | Stainless mold steel with lower delta ferrite content | |
| US20130243639A1 (en) | Tool steel for extrusion | |
| US7067019B1 (en) | Alloy steel and article made therefrom | |
| JP2004190138A (en) | Cooled and annealed bainite steel parts and its producing method | |
| RU2456368C1 (en) | High-strength dynamic impact resistant steel and method for production of this steel sheets | |
| WO2021133343A1 (en) | High strength, low alloy steel composition | |
| JP7333327B2 (en) | new duplex stainless steel | |
| JP2023530420A (en) | hot work tool steel | |
| US7828910B2 (en) | Method and process for thermochemical treatment of high-strength, high-toughness alloys | |
| RU2813066C1 (en) | Method for producing high-strength steel sheet | |
| WO2023014331A2 (en) | Next-generation micro-alloyed steel | |
| RU2813069C1 (en) | Method for producing high-strength steel sheet | |
| WO2023014332A1 (en) | High-strength micro-alloyed steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| 121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 20859682 Country of ref document: EP Kind code of ref document: A1 |
|
| NENP | Non-entry into the national phase |
Ref country code: DE |
|
| 122 | Ep: pct application non-entry in european phase |
Ref document number: 20859682 Country of ref document: EP Kind code of ref document: A1 |