CA2622410C - Process for manufacturing cold-formed precision steel pipes - Google Patents
Process for manufacturing cold-formed precision steel pipes Download PDFInfo
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- CA2622410C CA2622410C CA2622410A CA2622410A CA2622410C CA 2622410 C CA2622410 C CA 2622410C CA 2622410 A CA2622410 A CA 2622410A CA 2622410 A CA2622410 A CA 2622410A CA 2622410 C CA2622410 C CA 2622410C
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- 238000000034 method Methods 0.000 title claims abstract description 30
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 16
- 239000010959 steel Substances 0.000 title claims abstract description 16
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000002844 melting Methods 0.000 claims abstract description 4
- 230000008018 melting Effects 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims description 11
- 238000010791 quenching Methods 0.000 claims description 8
- 230000000171 quenching effect Effects 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 7
- 238000005496 tempering Methods 0.000 claims description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 3
- 230000003068 static effect Effects 0.000 claims description 3
- 239000000126 substance Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 238000005275 alloying Methods 0.000 abstract description 3
- 239000000463 material Substances 0.000 description 11
- 238000005452 bending Methods 0.000 description 3
- 238000010276 construction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 239000001361 adipic acid Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000009897 systematic effect Effects 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
-
- 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
- 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
- C21D6/00—Heat treatment 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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 Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Extraction Processes (AREA)
Abstract
The invention relates to a process for manufacturing cold-formed, in particular cold-drawn, precision steel pipes for application in particular as pressure-operated cylinder pipes with optimum addition of one or several alloying elements as well as impurities caused by melting. A seamless, hot-formed pipe blank or welded pipe blank made from a hot strip with defined starting condition is hereby drawn in one pass or in several passes into a finished pipe, and the pipe undergoes a heat treatment before the finishing pass.
Description
Process for Manufacturing Cold-Formed Precision Steel Pipes The invention relates to a process for manufacturing cold-formed, in particular cold-drawn, precision steel pipes.
Involved in particular in this context are precision steel pipes according to DIN EN
10305, part 1 and 2, which are under high internal pressure during operation and find application for example as cylindrical pipes in the hydraulic or pneumatic fields.
The basic manufacturing process of seamless or welded, cold-drawn precision steel pipes is described for example in the Stahlrohr Handbuch [Steel Pipe Handbook], 12. ed. 1995, Vulkan Verlag Essen.
Pipes manufactured in this way are characterized in particular by narrow wall thicknesses and diameter tolerances..
Starting product may either be a seamlessly produced hot-rolled pipe blank or a pipe blank made from a hot strip by means of high frequency induction welding (HFI welding).
This pipe blank, labeled also as hollow, is drawn in the following cold drawing process, which includes one or more passes, to the required final size (diameter, wall thickness) for the finished pipe.
Cold forming causes the material to solidify, i.e. yield point and strength thereof increase while elongation and toughness thereof become smaller at the same time.
This is a desired effect for many applications. As a consequence of the reduced deformation capability, it is, however, necessary to execute in some instances a recrystallizing heat treatment before carrying out further forming processes, so that the material can be cold formed again for the next drawing process.
The properties of precision steel pipes made in this way are described in DIN
EN
10305 part 1 and 2.
Unalloyed quality steels up to E 355 as well as higher strength grades up to StE 690 are used as steel grades.
In order to use such pipes under high pressure, e.g. as hydraulic cylinder pipes, they have to meet high standards as far as their toughness is concerned.
Hydraulic cylinders control movement patterns of many devices and machineries which are used, i.a., also outdoors at great temperature fluctuations.
When exposed to temperature conditions of up to -20 C, risk of harm to persons and material cannot be absolutely ruled out in view of the brittle fracture tendency of materials used to date for cylinders or pipes under pressure.
Tests have shown that a notch impact energy of 27 J at -20 C, as typically demanded heretofore, is not sufficient for standardized specimens to absolutely rule out structural failure as a result of brittle fracture at this temperature.
Comparative systematic tests of ready-for-use cylinder pipes, that include notch impact bending tests, drop weight tear tests, and structure tests have shown that a substantially ductile structural failure can be expected only when the notch impact energy is at a minimum value commensurate with a shear fracture area of 50% in the DWT test.
Involved in particular in this context are precision steel pipes according to DIN EN
10305, part 1 and 2, which are under high internal pressure during operation and find application for example as cylindrical pipes in the hydraulic or pneumatic fields.
The basic manufacturing process of seamless or welded, cold-drawn precision steel pipes is described for example in the Stahlrohr Handbuch [Steel Pipe Handbook], 12. ed. 1995, Vulkan Verlag Essen.
Pipes manufactured in this way are characterized in particular by narrow wall thicknesses and diameter tolerances..
Starting product may either be a seamlessly produced hot-rolled pipe blank or a pipe blank made from a hot strip by means of high frequency induction welding (HFI welding).
This pipe blank, labeled also as hollow, is drawn in the following cold drawing process, which includes one or more passes, to the required final size (diameter, wall thickness) for the finished pipe.
Cold forming causes the material to solidify, i.e. yield point and strength thereof increase while elongation and toughness thereof become smaller at the same time.
This is a desired effect for many applications. As a consequence of the reduced deformation capability, it is, however, necessary to execute in some instances a recrystallizing heat treatment before carrying out further forming processes, so that the material can be cold formed again for the next drawing process.
The properties of precision steel pipes made in this way are described in DIN
EN
10305 part 1 and 2.
Unalloyed quality steels up to E 355 as well as higher strength grades up to StE 690 are used as steel grades.
In order to use such pipes under high pressure, e.g. as hydraulic cylinder pipes, they have to meet high standards as far as their toughness is concerned.
Hydraulic cylinders control movement patterns of many devices and machineries which are used, i.a., also outdoors at great temperature fluctuations.
When exposed to temperature conditions of up to -20 C, risk of harm to persons and material cannot be absolutely ruled out in view of the brittle fracture tendency of materials used to date for cylinders or pipes under pressure.
Tests have shown that a notch impact energy of 27 J at -20 C, as typically demanded heretofore, is not sufficient for standardized specimens to absolutely rule out structural failure as a result of brittle fracture at this temperature.
Comparative systematic tests of ready-for-use cylinder pipes, that include notch impact bending tests, drop weight tear tests, and structure tests have shown that a substantially ductile structural failure can be expected only when the notch impact energy is at a minimum value commensurate with a shear fracture area of 50% in the DWT test.
2 This means for example for a St52 that the values to be attained in the notch impact bending test need to have a minimum value of about 80 J at operating temperature to provide the structural part with enough plastic deformation reserves to prevent the risk of a brittle, multipart disintegration of the structural part.
The notch impact energy determined in the notch impact bending test for the finished pipe cannot be raised to the necessary level by the currently employed manufacturing process.
The invention relates to a process for manufacturing cold-formed, in particular cold-drawn precision steel pipes for application in particular as pressure-operated cylinder pipes, to positively ensure a substantially ductile failure of the pipe in a simple and cost-efficient manner, even at operating temperatures of up to -20 C.
In one process aspect, the invention relates to a process for manufacturing a cold-formed, precision steel pipe with the following chemical composition in weight %:
C = 0.05 - 0.25, Si = 0.15 - 1.0, Mn = 1.0 - 3.5, Al = 0.020 - 0.060, V max. 0.20, N max 0.15, S max 0.03, Cr max. 0.80, Mo max. 0.65,
The notch impact energy determined in the notch impact bending test for the finished pipe cannot be raised to the necessary level by the currently employed manufacturing process.
The invention relates to a process for manufacturing cold-formed, in particular cold-drawn precision steel pipes for application in particular as pressure-operated cylinder pipes, to positively ensure a substantially ductile failure of the pipe in a simple and cost-efficient manner, even at operating temperatures of up to -20 C.
In one process aspect, the invention relates to a process for manufacturing a cold-formed, precision steel pipe with the following chemical composition in weight %:
C = 0.05 - 0.25, Si = 0.15 - 1.0, Mn = 1.0 - 3.5, Al = 0.020 - 0.060, V max. 0.20, N max 0.15, S max 0.03, Cr max. 0.80, Mo max. 0.65,
3 Ni max. 0.90, W max. 0.90, Ti max. 0.20, Nb max. 0.20, and the remainder iron and inevitable impurities, comprising:
melting said elements; and preparing a seamless, hot-formed pipe blank or welded pipe blank made from a hot strip drawn in one pass or in several passes into a finished pipe, and heat treating the pipe before the finishing pass, wherein the heat treatment comprises heating the pipe to a temperature of 910-940 C, cooling the pipe, and subsequently exposing the pipe to a tempering treatment. Suitably, the cold-formed pipe is cold-drawn.
Suitably, the cooling involves an accelerated cooling. Suitably, the accelerated cooling involves quenching. Suitably, the quenching is implemented by means of a water shower.
The cooling may also be carried out through exposure to static air. Suitably, the tempering treatment is carried out at a temperature range of 540 to 720 C. Suitably, the finish-drawn pipe is subjected to a final annealing. Suitably, the final annealing is carried out at a temperature range of 500 to 700 C.
In one use aspect, the invention relates to use of the pipe produced according to the process defined above, for a cylinder pipe under pressure.
Fig. 1 is a graph of test results for notch impact energy values on cylinder pipes produced by the process of the invention; and Fig. 2 is a graph comparing structural parts produced by the process of the present invention and a conventional process for ductile fracture behaviour.
3a ' 20337-627 According to the teaching of the invention, a process is applied in which the pipe blank is finish-drawn in one or more passes, wherein the pipe undergoes a heat treatment before finish-drawing, and the steel pipe has the following chemical composition (in %):
C = 0.05 - 0.25 Si = 0.15 - 1.0 Mn = 1.0 - 3.5 Al = 0.020 - 0.060 V max. 0.20 N max 0.150 S max 0.030, 3b with optional addition of one or more alloying elements such as Cr, Mo, Ni, W, Ti, or Nb as well as impurities caused by melting.
The optional addition of the alloying elements is dependent on the required property profile, i.e. according to the desired mechanical properties, and have advantageously the following contents (in weight-%):
Cr max. 0.80 Mo max. 0.65 Ni max. 0.90 W max. 0.90 Ti max. 0.20 Nb max. 0.20.
The heat treatment itself includes a classical hardening with subsequent tempering of the pipes. Austenitizing is carried out at temperatures of about 910-940 C
depending on the respective material, followed by a quenching process to form a hardening structure. Quenching may be executed using various quenching media, typically quenching is implemented by means of water using a water shower.
When using air-hardening materials, cooling may be realized through exposure to static air.
Tempering treatment follows hardening and is carried out at temperatures of about 540 - 720 C depending on the material.
The advantage of the proposed process is the realization of a very even homogenous microstructure with superior toughness by providing a heat treating step before the finishing pass, which microstructure is substantially maintained even after the finishing pass of the pipe. Tests have shown that the values for the notch impact energy at -20 C and 50% shear fracture area in the DWT test lie for
melting said elements; and preparing a seamless, hot-formed pipe blank or welded pipe blank made from a hot strip drawn in one pass or in several passes into a finished pipe, and heat treating the pipe before the finishing pass, wherein the heat treatment comprises heating the pipe to a temperature of 910-940 C, cooling the pipe, and subsequently exposing the pipe to a tempering treatment. Suitably, the cold-formed pipe is cold-drawn.
Suitably, the cooling involves an accelerated cooling. Suitably, the accelerated cooling involves quenching. Suitably, the quenching is implemented by means of a water shower.
The cooling may also be carried out through exposure to static air. Suitably, the tempering treatment is carried out at a temperature range of 540 to 720 C. Suitably, the finish-drawn pipe is subjected to a final annealing. Suitably, the final annealing is carried out at a temperature range of 500 to 700 C.
In one use aspect, the invention relates to use of the pipe produced according to the process defined above, for a cylinder pipe under pressure.
Fig. 1 is a graph of test results for notch impact energy values on cylinder pipes produced by the process of the invention; and Fig. 2 is a graph comparing structural parts produced by the process of the present invention and a conventional process for ductile fracture behaviour.
3a ' 20337-627 According to the teaching of the invention, a process is applied in which the pipe blank is finish-drawn in one or more passes, wherein the pipe undergoes a heat treatment before finish-drawing, and the steel pipe has the following chemical composition (in %):
C = 0.05 - 0.25 Si = 0.15 - 1.0 Mn = 1.0 - 3.5 Al = 0.020 - 0.060 V max. 0.20 N max 0.150 S max 0.030, 3b with optional addition of one or more alloying elements such as Cr, Mo, Ni, W, Ti, or Nb as well as impurities caused by melting.
The optional addition of the alloying elements is dependent on the required property profile, i.e. according to the desired mechanical properties, and have advantageously the following contents (in weight-%):
Cr max. 0.80 Mo max. 0.65 Ni max. 0.90 W max. 0.90 Ti max. 0.20 Nb max. 0.20.
The heat treatment itself includes a classical hardening with subsequent tempering of the pipes. Austenitizing is carried out at temperatures of about 910-940 C
depending on the respective material, followed by a quenching process to form a hardening structure. Quenching may be executed using various quenching media, typically quenching is implemented by means of water using a water shower.
When using air-hardening materials, cooling may be realized through exposure to static air.
Tempering treatment follows hardening and is carried out at temperatures of about 540 - 720 C depending on the material.
The advantage of the proposed process is the realization of a very even homogenous microstructure with superior toughness by providing a heat treating step before the finishing pass, which microstructure is substantially maintained even after the finishing pass of the pipe. Tests have shown that the values for the notch impact energy at -20 C and 50% shear fracture area in the DWT test lie for
4 transverse test specimen at a superior 80 J and for longitudinal test specimen at 100 J.
A possible demand by customers for a final annealing in the form of a stress-free annealing after the finishing pass leads to an additional improvement of the notch impact energy values and thus toughness of the structural part.
The final annealing is carried out advantageously at a temperature range of 700 C in dependence on the material, whereby care should be taken that the temperature should be precisely set in dependence on the material properties to be attained, like e.g. strength, elongation at fracture, and notch impact energy.
Test of pipes made in accordance with the process according to the invention have shown the elimination of the otherwise typically encountered ferritic-pearlitic microstructure of the construction steels with pronounced variations in the notch impact energy level in transverse as well as longitudinal test specimens in materials produced by the process according to the invention.
This is clearly shown by the test results for notch impact energy values on cylinder pipes of StE 460 mod., as illustrated in Figure 1. An almost identical notch impact energy level of up to about 180 J is reached in longitudinal as well as transverse direction.
As illustrated in Figure 2, the structural parts made from the steel pipe StE
mod. in accordance with the invention have, compared to the steel pipe produced in a conventional manner, a sufficiently high proportion of ductile fracture behavior at temperatures of up to -20 C, and thus have sufficient plastic deformation reserves to positively prevent the risk of a disintegration of the structural part into several parts.
The material concept according to the invention thus allows the operation of hydraulic cylinders even at the temperature range of up to -20 C.
In certain steel grades, there is the positive side effect of a significant increase of the strength values. This allows advantageously a reduction in wall thickness of the cylinder pipes by about up to 30% and thus a reduction in weight, satisfying the demands of lightweight construction.
In summary, it should be noted that the process in accordance with the invention for manufacturing cylinder pipes subject to pressure positively prevents a multipart structural failure even at operating temperatures of up to -20 C and moreover permits a reduction in wall thickness of the cylinder wall of up to 30%.
A possible demand by customers for a final annealing in the form of a stress-free annealing after the finishing pass leads to an additional improvement of the notch impact energy values and thus toughness of the structural part.
The final annealing is carried out advantageously at a temperature range of 700 C in dependence on the material, whereby care should be taken that the temperature should be precisely set in dependence on the material properties to be attained, like e.g. strength, elongation at fracture, and notch impact energy.
Test of pipes made in accordance with the process according to the invention have shown the elimination of the otherwise typically encountered ferritic-pearlitic microstructure of the construction steels with pronounced variations in the notch impact energy level in transverse as well as longitudinal test specimens in materials produced by the process according to the invention.
This is clearly shown by the test results for notch impact energy values on cylinder pipes of StE 460 mod., as illustrated in Figure 1. An almost identical notch impact energy level of up to about 180 J is reached in longitudinal as well as transverse direction.
As illustrated in Figure 2, the structural parts made from the steel pipe StE
mod. in accordance with the invention have, compared to the steel pipe produced in a conventional manner, a sufficiently high proportion of ductile fracture behavior at temperatures of up to -20 C, and thus have sufficient plastic deformation reserves to positively prevent the risk of a disintegration of the structural part into several parts.
The material concept according to the invention thus allows the operation of hydraulic cylinders even at the temperature range of up to -20 C.
In certain steel grades, there is the positive side effect of a significant increase of the strength values. This allows advantageously a reduction in wall thickness of the cylinder pipes by about up to 30% and thus a reduction in weight, satisfying the demands of lightweight construction.
In summary, it should be noted that the process in accordance with the invention for manufacturing cylinder pipes subject to pressure positively prevents a multipart structural failure even at operating temperatures of up to -20 C and moreover permits a reduction in wall thickness of the cylinder wall of up to 30%.
Claims (10)
1. A
process for manufacturing a cold-formed, precision steel pipe with the following chemical composition in weight %:
C = 0.05 - 0.25, Si = 0.15 - 1.0, Mn = 1.0 - 3.5, Al = 0.020 - 0.060, V max. 0.20, N max 0.15, S max 0.03, Cr max. 0.80, Mo max. 0.65, Ni max. 0.90, W max. 0.90, Ti max. 0.20, Nb max. 0.20, and the remainder iron and inevitable impurities, comprising:
melting said elements; and preparing a seamless, hot-formed pipe blank or welded pipe blank made from a hot strip drawn in one pass or in several passes into a finished pipe, and heat treating the pipe before the finishing pass, wherein the heat treatment comprises heating the pipe to a temperature of 910-940°C, cooling the pipe, and subsequently exposing the pipe to a tempering treatment.
process for manufacturing a cold-formed, precision steel pipe with the following chemical composition in weight %:
C = 0.05 - 0.25, Si = 0.15 - 1.0, Mn = 1.0 - 3.5, Al = 0.020 - 0.060, V max. 0.20, N max 0.15, S max 0.03, Cr max. 0.80, Mo max. 0.65, Ni max. 0.90, W max. 0.90, Ti max. 0.20, Nb max. 0.20, and the remainder iron and inevitable impurities, comprising:
melting said elements; and preparing a seamless, hot-formed pipe blank or welded pipe blank made from a hot strip drawn in one pass or in several passes into a finished pipe, and heat treating the pipe before the finishing pass, wherein the heat treatment comprises heating the pipe to a temperature of 910-940°C, cooling the pipe, and subsequently exposing the pipe to a tempering treatment.
2. The process according to claim 1, wherein the cold-formed pipe is cold-drawn.
3. The process according to claim 1 or 2, wherein the cooling involves an accelerated cooling.
4. The process according to claim 3, wherein the accelerated cooling involves quenching.
5. The process according to claim 4, wherein the quenching is implemented by means of a water shower.
6. The process according to claim 1, wherein the cooling is carried out through exposure to static air.
7. The process according to any one of claims 1 to 6, wherein the tempering treatment is carried out at a temperature range of 540 to 720°C.
8. The process according to any one of claims 1 to 7, wherein the finish-drawn pipe is subjected to a final annealing.
9. The process according to claim 7, wherein the final annealing is carried out at a temperature range of 500 to 700°C.
10. Use of the pipe produced according to the process defined in any one of claims 1 to 9, for a cylinder pipe under pressure.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102005046459.9 | 2005-09-21 | ||
| DE102005046459A DE102005046459B4 (en) | 2005-09-21 | 2005-09-21 | Process for the production of cold-finished precision steel tubes |
| PCT/DE2006/001457 WO2007033635A1 (en) | 2005-09-21 | 2006-08-18 | Process for manufacturing cold-formed precision steel pipes |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2622410A1 CA2622410A1 (en) | 2007-03-29 |
| CA2622410C true CA2622410C (en) | 2015-05-05 |
Family
ID=37420849
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2622410A Expired - Fee Related CA2622410C (en) | 2005-09-21 | 2006-08-18 | Process for manufacturing cold-formed precision steel pipes |
Country Status (12)
| Country | Link |
|---|---|
| US (1) | US20080302452A1 (en) |
| EP (1) | EP1926837B1 (en) |
| JP (1) | JP5679632B2 (en) |
| KR (1) | KR20080063313A (en) |
| CN (1) | CN101268203A (en) |
| BR (1) | BRPI0616367A8 (en) |
| CA (1) | CA2622410C (en) |
| DE (1) | DE102005046459B4 (en) |
| ES (1) | ES2470674T3 (en) |
| PL (1) | PL1926837T3 (en) |
| UA (1) | UA88573C2 (en) |
| WO (1) | WO2007033635A1 (en) |
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|---|---|---|---|---|
| WO2008000300A1 (en) * | 2006-06-29 | 2008-01-03 | Tenaris Connections Ag | Seamless precision steel tubes with improved isotropic toughness at low temperature for hydraulic cylinders and process for obtaining the same |
| DE102008010749A1 (en) * | 2008-02-20 | 2009-09-24 | V & M Deutschland Gmbh | Steel alloy for a low-alloyed steel for the production of high-strength seamless steel tubes |
| FR2939449B1 (en) * | 2008-12-09 | 2011-03-18 | Vallourec Mannesmann Oil & Gas France | LOW-ALLOY STEEL WITH HIGH ELASTICITY LIMIT AND HIGH RESISTANCE TO CRUSHING UNDER SULFIDE STRESS. |
| FR2942808B1 (en) * | 2009-03-03 | 2011-02-18 | Vallourec Mannesmann Oil & Gas | LOW-ALLOY STEEL WITH HIGH ELASTICITY LIMIT AND HIGH RESISTANCE TO CRUSHING UNDER SULFIDE STRESS. |
| CN102560283A (en) * | 2012-02-21 | 2012-07-11 | 张芝莲 | Big-caliber seamless alloy steel pipe |
| CN102553926A (en) * | 2012-02-21 | 2012-07-11 | 张芝莲 | Method for manufacturing large-caliber seamless alloy steel pipes |
| CN102653816B (en) * | 2012-05-02 | 2014-05-14 | 江苏华程工业制管股份有限公司 | Preparing process of alloy-steel pipe used for hydraulic cylinder tube |
| CN103409602A (en) * | 2013-08-09 | 2013-11-27 | 江苏华程工业制管股份有限公司 | Method for manufacturing alloy steel pipe for micro-decarburization high-strength highly abrasion-resistant cylinder sleeve |
| CN107075644B (en) * | 2014-10-30 | 2019-03-29 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacturing method |
| CN105081698A (en) * | 2015-09-01 | 2015-11-25 | 无锡贺邦金属制品有限公司 | Machining method of steel pipe |
| CN105385948B (en) * | 2015-11-06 | 2018-06-29 | 天津钢管集团股份有限公司 | It is more than the manufacturing method of 690MPa seamless pipes with yield strength from liter drilling platforms |
| CN105463311B (en) * | 2015-12-14 | 2017-11-07 | 徐州徐工液压件有限公司 | A kind of preparation method of cold-drawn high-precision |
| KR102242067B1 (en) | 2016-11-16 | 2021-04-19 | 제이에프이 스틸 가부시키가이샤 | High-strength steel sheet and its manufacturing method |
| CN110616366B (en) * | 2018-06-20 | 2021-07-16 | 宝山钢铁股份有限公司 | 125ksi steel grade sulfur-resistant oil well pipe and manufacturing method thereof |
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| FR2571740B1 (en) * | 1984-10-12 | 1988-05-06 | Decazeville Expl Siderurgie | MANGANESE STEEL FOR, IN PARTICULAR, CYCLE TUBES |
| JPS61213344A (en) * | 1985-03-18 | 1986-09-22 | Kawasaki Steel Corp | High toughness seamless steel pipe |
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| JP3318467B2 (en) * | 1995-05-29 | 2002-08-26 | 住友金属工業株式会社 | Manufacturing method of high strength and high toughness steel pipe with excellent workability |
| JPH10140250A (en) * | 1996-11-12 | 1998-05-26 | Sumitomo Metal Ind Ltd | Production of steel tube for air bag, having high strength and high toughness |
| US6173495B1 (en) * | 1999-05-12 | 2001-01-16 | Trw Inc. | High strength low carbon air bag quality seamless tubing |
| JP2001049343A (en) * | 1999-08-10 | 2001-02-20 | Sumitomo Metal Ind Ltd | Production of electric resistance welded tube for high toughness air bag |
| DE19942641A1 (en) * | 1999-08-30 | 2001-03-22 | Mannesmann Ag | Use of a steel alloy for the production of high-strength seamless steel pipes |
| US20020033591A1 (en) * | 2000-09-01 | 2002-03-21 | Trw Inc. | Method of producing a cold temperature high toughness structural steel tubing |
| EP1375683B1 (en) * | 2001-03-29 | 2012-02-08 | Sumitomo Metal Industries, Ltd. | High strength steel tube for air bag and method for production thereof |
| WO2002103070A1 (en) * | 2001-06-14 | 2002-12-27 | Kawasaki Steel Corporation | Method for producing steel pipe having high ductility |
| JP4186566B2 (en) * | 2002-09-19 | 2008-11-26 | 住友金属工業株式会社 | Manufacturing method of steel pipe for airbag having excellent low temperature toughness |
| US20050076975A1 (en) * | 2003-10-10 | 2005-04-14 | Tenaris Connections A.G. | Low carbon alloy steel tube having ultra high strength and excellent toughness at low temperature and method of manufacturing the same |
-
2005
- 2005-09-21 DE DE102005046459A patent/DE102005046459B4/en not_active Expired - Fee Related
-
2006
- 2006-08-18 KR KR1020087009217A patent/KR20080063313A/en active Search and Examination
- 2006-08-18 CN CNA2006800347631A patent/CN101268203A/en active Pending
- 2006-08-18 PL PL06775881T patent/PL1926837T3/en unknown
- 2006-08-18 EP EP06775881.3A patent/EP1926837B1/en not_active Not-in-force
- 2006-08-18 BR BRPI0616367A patent/BRPI0616367A8/en not_active IP Right Cessation
- 2006-08-18 WO PCT/DE2006/001457 patent/WO2007033635A1/en active Application Filing
- 2006-08-18 CA CA2622410A patent/CA2622410C/en not_active Expired - Fee Related
- 2006-08-18 ES ES06775881.3T patent/ES2470674T3/en active Active
- 2006-08-18 UA UAA200804698A patent/UA88573C2/en unknown
- 2006-08-18 JP JP2008531521A patent/JP5679632B2/en not_active Expired - Fee Related
- 2006-08-18 US US12/067,756 patent/US20080302452A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| CN101268203A (en) | 2008-09-17 |
| KR20080063313A (en) | 2008-07-03 |
| PL1926837T3 (en) | 2014-09-30 |
| CA2622410A1 (en) | 2007-03-29 |
| JP5679632B2 (en) | 2015-03-04 |
| UA88573C2 (en) | 2009-10-26 |
| DE102005046459A1 (en) | 2007-04-12 |
| JP2009509040A (en) | 2009-03-05 |
| BRPI0616367A2 (en) | 2011-06-14 |
| EP1926837B1 (en) | 2014-03-12 |
| US20080302452A1 (en) | 2008-12-11 |
| BRPI0616367A8 (en) | 2018-05-08 |
| DE102005046459B4 (en) | 2013-11-28 |
| WO2007033635A1 (en) | 2007-03-29 |
| BRPI0616367B1 (en) | 2017-11-28 |
| ES2470674T3 (en) | 2014-06-24 |
| EP1926837A1 (en) | 2008-06-04 |
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