EP0356417A1 - Procédé pour la fabrication de pièces tubulaires résistant à la corrosion sous tension, notamment de masses-tiges non magnétisables en acier austénitique et pièces ainsi obtenues - Google Patents
Procédé pour la fabrication de pièces tubulaires résistant à la corrosion sous tension, notamment de masses-tiges non magnétisables en acier austénitique et pièces ainsi obtenues Download PDFInfo
- Publication number
- EP0356417A1 EP0356417A1 EP89890199A EP89890199A EP0356417A1 EP 0356417 A1 EP0356417 A1 EP 0356417A1 EP 89890199 A EP89890199 A EP 89890199A EP 89890199 A EP89890199 A EP 89890199A EP 0356417 A1 EP0356417 A1 EP 0356417A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- temperature
- cooled
- tubular body
- wall
- stresses
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 230000007797 corrosion Effects 0.000 title claims abstract description 24
- 238000005260 corrosion Methods 0.000 title claims abstract description 24
- 238000000034 method Methods 0.000 title claims abstract description 22
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 17
- 239000010959 steel Substances 0.000 title claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 230000008569 process Effects 0.000 title claims abstract description 7
- 239000000463 material Substances 0.000 claims abstract description 18
- 238000005553 drilling Methods 0.000 claims abstract description 5
- 238000010791 quenching Methods 0.000 claims abstract description 3
- 230000000171 quenching effect Effects 0.000 claims abstract description 3
- 238000001816 cooling Methods 0.000 claims description 13
- 230000009471 action Effects 0.000 claims description 3
- 238000000137 annealing Methods 0.000 claims description 3
- 238000003754 machining Methods 0.000 claims description 3
- 230000001960 triggered effect Effects 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 239000007789 gas Substances 0.000 claims description 2
- 239000002826 coolant Substances 0.000 claims 1
- 239000007788 liquid Substances 0.000 claims 1
- 230000035939 shock Effects 0.000 claims 1
- 238000005336 cracking Methods 0.000 abstract description 15
- 238000010348 incorporation Methods 0.000 abstract 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 6
- 239000000243 solution Substances 0.000 description 5
- 238000005482 strain hardening Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000011265 semifinished product Substances 0.000 description 4
- TWRXJAOTZQYOKJ-UHFFFAOYSA-L Magnesium chloride Chemical class [Mg+2].[Cl-].[Cl-] TWRXJAOTZQYOKJ-UHFFFAOYSA-L 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000006399 behavior Effects 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 2
- 229910000799 K alloy Inorganic materials 0.000 description 2
- 206010070834 Sensitisation Diseases 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000010304 firing Methods 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 230000008313 sensitization Effects 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910019590 Cr-N Inorganic materials 0.000 description 1
- 229910019588 Cr—N Inorganic materials 0.000 description 1
- 229910017870 Cu—Ni—Al Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000013013 elastic material Substances 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 229910001629 magnesium chloride Inorganic materials 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Images
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
-
- 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
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes
Definitions
- precipitation hardened alloys with contents of approx. 33% Ni, 18% Cr, 2% Ti, 0.5% Al and 0.004% N should bring about significant improvements in the performance characteristics of drill collars or drill string parts.
- Another disadvantage is that high local strain hardening of the material, which is formed in the near-surface zone when mechanical pressure is applied, increases the tendency of the material to pitting. In the event of pitting, the compressive stress layer is undermined and stress corrosion cracking of the part increases.
- the mechanical application of residual compressive stresses in the surface layer of parts also has the disadvantage that only simple shapes or contours can be treated accordingly last operation must be done without subsequent calibration. It is therefore practically not possible to create residual compressive stresses in the near-surface zone on edges, threaded parts, in corners, holes and back-turns as well as on chamfers and discontinuous surface parts in order to prevent stress corrosion cracking.
- the invention was based on the objects of avoiding the above disadvantages and of creating a method for producing tubular bodies which are resistant to stress corrosion cracking, in particular non-magnetizable drill rods and rod parts made of austenitic steels.
- a further object of the invention relates to tubular bodies which are resistant to stress corrosion cracking and are produced by this method, in particular non-magnetizable drill rods and rod parts made of austenitic steel.
- the body after solution annealing, quenching and after deformation at a temperature of below 500 ° C to increase the material strength and after machining or drilling a hole to a temperature of 220 to 600 ° C, at least up to a temperature equalization with a temperature difference of at most 10 ° C in the body wall, at most a time t in minutes at a temperature T in ° C according to the context is kept, from this temperature or this starting temperature is cooled by increased removal of thermal energy at least from the inner surface of the tubular body and the cooled surface has a temperature drop of at least 100 ° C / min from the starting temperature to half the value between the starting temperature and room temperature.
- Tubular bodies produced in accordance with this process in particular non-magnetizable drill rods and rod parts made of austenitic steel, according to the invention have local tensile residual stresses of less than 100 N / mm2 in the zones near the surface to a depth of at least 8 mm. It is particularly preferred if the near-surface zones have residual compressive stresses to a depth of at least 4 mm, preferably at least 8 mm, and that the tensile residual stresses that may occur in the entire cross-section of the wall are less than 150 N / mm2, i.e. below the triggering voltage for stress corrosion cracking , preferably less than 120 N / mm2.
- tubular bodies, especially collars Due to a deformation of the blank at temperatures below 500 ° C, which serves to work harden or increase the yield strength of the material, tubular bodies, especially collars, show considerable differences in the local internal stresses in the wall, etc. compressive stresses on the outer surface and high tensile stresses on the surface of the hollow, i.e. the bore, which are well above the limit for triggering stress corrosion cracking. It has surprisingly been found that in a tubular body consisting of solution-annealed, quenched and cold-formed austenitic material, heating to appropriate temperatures while adhering to certain conditions with subsequent intensified cooling can cause stress states.
- the temperature difference in the pipe wall after heating to the initial temperature should be kept below 10 ° C. Longer holding times at the initial temperature have an unfavorable effect because this causes the solution-annealed, quenched and work-hardened steels, for example austenitic Mn-Cr steel, to be sensitized to inter-crystalline crack corrosion.
- tubular body is cooled from the starting temperature by increasing heat removal at least from the inner wall, because in the area of the inner surface of the wall the highest tensile stresses originating from cold working or work hardening have to be redistributed. Due to low cooling intensities, no sufficient residual stress redistribution is effected, so that the cooled surface of the tube wall must experience a temperature drop from the starting temperature to half the value between the starting temperature and room temperature of at least 100 ° C./min.
- the method according to the invention brings about a residual stress redistribution and can be used for the production of tubular bodies which are resistant to stress corrosion cracking, in particular non-magnetizable drill rods and rod parts made of austenistic steels.
- the prejudices of the professional world had to be overcome, e.g. that heating to higher initial temperatures leads to an unacceptable softening or lowering of the yield point of the cold-formed material, and that low initial temperatures can have no effect, because during the subsequent cooling process, only elastic material deformations occur arise.
- the increased strength and the high tensile stresses on the inner surface of the tube cause cracks, in particular longitudinal cracks, even when heated to the initial temperature.
- the corrosion specialist feared that renewed heating of a material quenched from solution temperature and work hardened would cause sensitization, which would make the material in chloride-containing media susceptible to grain breakdown or intergranular crack propagation.
- Fig. 1 shows schematically stress states in the wall of a tubular body.
- the stress redistribution by intensively cooling the tube wall from temperatures of, for example, 300 ° C. and 400 ° C. has the effect that the internal stresses in the entire tube wall are below 150 N / mm2, namely the triggering voltage of the stress corrosion cracking, and the body is therefore completely resistant to stress corrosion cracking. Compressive stresses down to a depth of more than 4 mm are achieved on the inner surface.
- Intensified cooling from an initial temperature of 550 ° C increases the internal compressive stresses and their effective range on the inner surface of the pipe wall (curve 6), which can be used for a recalibration by machining.
- Curve 2 shows the stress curve in a pipe wall, which can be set by a method according to AT-PS 364 592 or according to the prior art, high internal compressive stresses prevailing on the inner surface, but these compressive stresses at a small distance from the surface in pass high tensile stresses.
- the invention is illustrated further below by a practical example: A block weighing approx.
- the residual stresses on the AD were 0 ⁇ -157 N / mm2 (residual compressive stress) and on the ID +390 N / mm2 (residual tensile stress), the measured values representing the arithmetic mean of 3 measurements using the ring-core method.
- the tubular semi-finished product or rod (approx. 700 mm minimum length for the above sample) was heated in an electric furnace at 415 ° C, with a temperature difference in the tube wall at the end of the heating period of 0.8 ° C.
- jet cooling was initially carried out on the inside surface with a quantity of 1500 - 2500 l / min and after 10 to 30 s, preferably 20 s, also on the outside surface with a cooling water quantity of approx. 100 l / min and meter length with a temperature drop of the surface of approx. 350 ° C, at least to a temperature below 100 ° C.
- a drill string part was made from the semi-finished product and further samples were taken from it at the machined points. It was shown in the SCC test that cut-outs made in the pipe wall by milling, turning and planing as well as the NC-cut threads do not cause any cracks, which results from the non-critical residual stress condition in the entire volume of the part.
- the method according to the invention is particularly advantageous for austenitic steels with a directional analysis C: max. 0.2% by weight; Mn: 0-25% by weight; Cr: 12-30% by weight; Mo: 0-5% by weight; Ni: 0-75% by weight; N: 0-1% by weight; Ti: 0-3% by weight; Nb: 0-3% by weight; Cu: 0-3% by weight, rest of iron applicable.
- Mn-Cr austenites with 17-20% by weight Mn and 12-14% by weight Cr and Cr-Ni austenites with 17-24% by weight Cr and 10-20% by weight are particularly preferred.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Heat Treatment Of Articles (AREA)
- Earth Drilling (AREA)
- Coating With Molten Metal (AREA)
- Heat Treatments In General, Especially Conveying And Cooling (AREA)
- Physical Vapour Deposition (AREA)
- Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
- Electrolytic Production Of Non-Metals, Compounds, Apparatuses Therefor (AREA)
- Treatments Of Macromolecular Shaped Articles (AREA)
- Prevention Of Electric Corrosion (AREA)
- Extrusion Moulding Of Plastics Or The Like (AREA)
- Shaping Of Tube Ends By Bending Or Straightening (AREA)
- Heat Treatment Of Steel (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT1965/88 | 1988-08-04 | ||
AT1965/88A AT392802B (de) | 1988-08-04 | 1988-08-04 | Verfahren zur herstellung von spannungsrisskorrosionsbestaendigen rohrfoermigen koerpern, insbesondere nichtmagnetisierbaren schwerstangen aus austenitischen staehlen |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0356417A1 true EP0356417A1 (fr) | 1990-02-28 |
EP0356417B1 EP0356417B1 (fr) | 1993-05-26 |
Family
ID=3524888
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP89890199A Expired - Lifetime EP0356417B1 (fr) | 1988-08-04 | 1989-07-27 | Procédé pour la fabrication de pièces tubulaires résistant à la corrosion sous tension, notamment de masses-tiges non magnétisables en acier austénitique et pièces ainsi obtenues |
Country Status (10)
Country | Link |
---|---|
US (1) | US5026436A (fr) |
EP (1) | EP0356417B1 (fr) |
JP (1) | JPH0270884A (fr) |
KR (1) | KR900003387A (fr) |
AT (2) | AT392802B (fr) |
BR (1) | BR8903914A (fr) |
CA (1) | CA1334572C (fr) |
DE (1) | DE58904473D1 (fr) |
MX (1) | MX173658B (fr) |
NO (1) | NO174163C (fr) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1999019522A1 (fr) * | 1997-10-08 | 1999-04-22 | Mannesmann Ag | Procede pour eviter des tapures de trempe a la surface interieure d'un corps creux cylindrique |
CN110317941A (zh) * | 2019-08-13 | 2019-10-11 | 上海亦又新能源科技有限公司 | 一种地质钻杆公接头增强螺纹根部加工方法及其应用 |
DE102019123174A1 (de) * | 2019-08-29 | 2021-03-04 | Mannesmann Stainless Tubes GmbH | Austenitische Stahllegierung mit verbesserter Korrosionsbeständigkeit bei Hochtemperaturbeanspruchung |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3186678B2 (ja) * | 1997-12-10 | 2001-07-11 | 日産自動車株式会社 | ベルト式無段変速機用金属帯の製造方法 |
DE19813459A1 (de) * | 1998-03-26 | 1999-09-30 | Mettler Toledo Gmbh | Elastisch verformbares Bauteil und Verfahren zu seiner Herstellung |
US6406570B1 (en) * | 1998-03-26 | 2002-06-18 | Mettler-Toledo, Gmbh | Elastic component for a precision instrument and process for its manufacture |
US6012744A (en) * | 1998-05-01 | 2000-01-11 | Grant Prideco, Inc. | Heavy weight drill pipe |
KR100472931B1 (ko) * | 2002-08-09 | 2005-03-10 | 정동택 | 세라믹구 제조방법 |
JP4759302B2 (ja) * | 2004-04-06 | 2011-08-31 | 日立Geニュークリア・エナジー株式会社 | 熱処理方法及びその装置 |
GB201304771D0 (en) * | 2013-03-15 | 2013-05-01 | Petrowell Ltd | Heat treat production fixture |
JP7385174B2 (ja) * | 2019-12-11 | 2023-11-22 | Tdk株式会社 | 磁性シート、および、磁性シートを備えるコイルモジュール、並びに非接触給電装置。 |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE671131C (de) * | 1932-08-26 | 1939-02-01 | Kohle Und Eisenforschung G M B | Verfahren zur Erzeugung von elastischen Vorspannungen in Gegenstaenden aus Stahl |
DE3004872A1 (de) * | 1979-03-15 | 1980-09-18 | Usui Kokusai Sangyo Kk | Rohr fuer hochdruckfluessigkeit und verfahren zu dessen herstellung |
EP0035091A1 (fr) * | 1980-01-25 | 1981-09-09 | SCHOELLER-BLECKMANN Gesellschaft m.b.H. | Procédé et appareil pour la fabrication de barres lourdes en acier austénitique, non magnétisables et résistant à la corrosion fissurante sous tension |
EP0205828A1 (fr) * | 1985-06-10 | 1986-12-30 | Hoesch Aktiengesellschaft | Procédé et utilisation d'un acier pour la fabrication de tubes en acier à haute résistance aux gaz acides |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2115834B (en) * | 1982-03-02 | 1985-11-20 | British Steel Corp | Non-magnetic austenitic alloy steels |
JPS58167724A (ja) * | 1982-03-26 | 1983-10-04 | Kobe Steel Ltd | 石油掘削スタビライザ−用素材の製造方法 |
US4502886A (en) * | 1983-01-06 | 1985-03-05 | Armco Inc. | Austenitic stainless steel and drill collar |
AT381658B (de) * | 1985-06-25 | 1986-11-10 | Ver Edelstahlwerke Ag | Verfahren zur herstellung von amagnetischen bohrstrangteilen |
-
1988
- 1988-08-04 AT AT1965/88A patent/AT392802B/de not_active IP Right Cessation
-
1989
- 1989-07-27 EP EP89890199A patent/EP0356417B1/fr not_active Expired - Lifetime
- 1989-07-27 DE DE8989890199T patent/DE58904473D1/de not_active Expired - Fee Related
- 1989-07-27 AT AT89890199T patent/ATE89870T1/de not_active IP Right Cessation
- 1989-07-31 MX MX016993A patent/MX173658B/es unknown
- 1989-08-03 NO NO893152A patent/NO174163C/no unknown
- 1989-08-03 BR BR898903914A patent/BR8903914A/pt not_active Application Discontinuation
- 1989-08-03 JP JP1202283A patent/JPH0270884A/ja active Pending
- 1989-08-03 US US07/388,868 patent/US5026436A/en not_active Expired - Fee Related
- 1989-08-03 CA CA000607498A patent/CA1334572C/fr not_active Expired - Fee Related
- 1989-08-04 KR KR1019890011152A patent/KR900003387A/ko not_active Application Discontinuation
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE671131C (de) * | 1932-08-26 | 1939-02-01 | Kohle Und Eisenforschung G M B | Verfahren zur Erzeugung von elastischen Vorspannungen in Gegenstaenden aus Stahl |
DE3004872A1 (de) * | 1979-03-15 | 1980-09-18 | Usui Kokusai Sangyo Kk | Rohr fuer hochdruckfluessigkeit und verfahren zu dessen herstellung |
EP0035091A1 (fr) * | 1980-01-25 | 1981-09-09 | SCHOELLER-BLECKMANN Gesellschaft m.b.H. | Procédé et appareil pour la fabrication de barres lourdes en acier austénitique, non magnétisables et résistant à la corrosion fissurante sous tension |
EP0205828A1 (fr) * | 1985-06-10 | 1986-12-30 | Hoesch Aktiengesellschaft | Procédé et utilisation d'un acier pour la fabrication de tubes en acier à haute résistance aux gaz acides |
Non-Patent Citations (3)
Title |
---|
PATENT ABSTRACTS OF JAPAN, Band 3, Nr. 114 (C-59), 21. September 1979, Seite 93 C 59; & JP-A-54 94 415 (HITACHI SEISAKUSHO K.K.) 26-07-1979 * |
PATENT ABSTRACTS OF JAPAN, Band 8, Nr. 41 (C-211)[1478], 22. Februar 1984; & JP-A-58 199 814 (SHIN NIPPON SEITETSU K.K.) 21-11-1983 * |
PATENT ABSTRACTS OF JAPAN, Band 9, Nr. 254 (C-308)[1977], 11. Oktober 1985; & JP-A-60 106 916 (ISHIKAWAJIMA HARIMA JUKOGYO K.K.) 12-06-1985 * |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1999019522A1 (fr) * | 1997-10-08 | 1999-04-22 | Mannesmann Ag | Procede pour eviter des tapures de trempe a la surface interieure d'un corps creux cylindrique |
CN110317941A (zh) * | 2019-08-13 | 2019-10-11 | 上海亦又新能源科技有限公司 | 一种地质钻杆公接头增强螺纹根部加工方法及其应用 |
CN110317941B (zh) * | 2019-08-13 | 2020-12-15 | 上海亦又新能源科技有限公司 | 一种地质钻杆公接头增强螺纹根部加工方法及其应用 |
DE102019123174A1 (de) * | 2019-08-29 | 2021-03-04 | Mannesmann Stainless Tubes GmbH | Austenitische Stahllegierung mit verbesserter Korrosionsbeständigkeit bei Hochtemperaturbeanspruchung |
Also Published As
Publication number | Publication date |
---|---|
JPH0270884A (ja) | 1990-03-09 |
NO893152D0 (no) | 1989-08-03 |
CA1334572C (fr) | 1995-02-28 |
BR8903914A (pt) | 1990-03-27 |
AT392802B (de) | 1991-06-25 |
NO174163C (no) | 1994-03-23 |
US5026436A (en) | 1991-06-25 |
DE58904473D1 (de) | 1993-07-01 |
NO893152L (no) | 1990-02-05 |
MX173658B (es) | 1994-03-22 |
EP0356417B1 (fr) | 1993-05-26 |
NO174163B (no) | 1993-12-13 |
ATE89870T1 (de) | 1993-06-15 |
KR900003387A (ko) | 1990-03-26 |
ATA196588A (de) | 1990-11-15 |
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