前苏联专利SU1342426A3 Method of manufacturing pipes for producing oil and gas

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专利摘要:
A high performance carbon steel tubular for critical Oil Country applications and a process for its preparation are disclosed. The tubular is particularly adapted for use in deep wells where the tubular may be subjected to high pressure, wide temperature ranges, and/or corrosive environments, which may include hydrogen sulfide, carbon dioxide, and brine water, together with hydrocarbons. The process comprises forming the steel into tubular form, intercritically heat treating the form, removing surface defects, cold working the tubular form to finished dimensions, intercritically heat treating the tubular form, and quenching and tempering the finished tubular.
公开号:SU1342426A3
申请号:SU823443207
申请日:1982-05-07
公开日:1987-09-30
发明作者:Брисан Грир Джеймс
申请人:Лоун Стар Стил Компани (Фирма)；
IPC主号:

专利说明:

The invention relates to ferrous metallurgy, in particular, to the manufacture of pipes for oil and gas production, which are exposed to high pressures, temperatures and the corrosive effects of hydrogen sulfide, carbon dioxide and saturated solutions of salt and hydrocarbons during operation in deep wells.
The aim of the invention is to increase the resistance to hydrogen sulfide cracking.
The method is carried out as follows.
From steel containing,%: 0.20-0.35 C; 0.35-0.9 MP; 0.8-1.5 Cr; 0.15-0.75 Mo, no more than 0.25 Ni, no more than 0.35 Cu, no more than 0.35 Si, no more than 0.04 S, no more than 0.04 P, the rest of the iron subjected to double electroslag remelting receive continuous cast billet. Due to the precise control of the cooling rate during the crystallization process of such a preform, the metal separation process is suppressed.
In order to obtain a finer-grained steel structure in the finished pipe, it is important to ensure that such a structure is obtained at all stages of the pipe manufacturing process. Hot forming of a billet with an extrusion orifice into a sleeve, the cross section of which should exceed 10-40% of the finished pipe, allows grinding the initial cast steel structure. In addition, the shaping of the liner by extrusion makes it possible to remove defects on the surface of the cast billet by grinding, since they are arranged axially along the liner after extrusion to recrystallize the steel and obtain a finer grain. Received
extrusion of the sleeve is subjected to heat. Section 317.14 mm, of which after
up to the intercritical interval A –A, the lead is dependent on the liner wall thickness and cooling.
Getting a pipe of a given size liner on the mandrel.
Cold deformation of the liner with a decrease in its size of less than 10% does not lead to a noticeable grinding of the grain after subsequent heat treatment, and deformation with a change in the dimensions of the liner more than 40% is not possible without intermediate heat treatment.
Cold prokdtka on the mandrel is made after removal of the surface50
55
firmware and extrusion were obtained sleeves with a diameter of 193.68 mm and a wall thickness of 12.75 and 30.5 mm. The resulting liners were quenched by austentiation for 45 minutes at 913 ° C and cooled with water from the outside and from inside to 93 ° C to obtain a martensitic structure. After that, the sleeves were subjected to tempering at 677-704 C with a latch for 1 h and then cooled with a spray of water. Such a process for the manufacture of pipes by thermoforming by extrusion and final heat treatment by closed defects. During cold rolling on the mandrel, the inner and outer surfaces of the pipe are cleaned as a result of a decrease in the depth of the sanding marks, and thus the toughness of the steel increases. In addition, such a drawing reduces the thickness variation of the pipe walls and improves the accuracy of its geometric dimensions. After cold rolling, the pipe is heated to the intercritical interval AC-A is held and cooled in order to recrystallize and grind the structure of cold-deformed steel. Thermal treatment from the intercritical interval suppresses grain growth. The holding time is determined from the condition that it is necessary to complete the complete recrystallization of steel for pipes with a wall thickness of 12.75 to 25.4 mm, this time is 0.25 and 1 h, respectively. After this, the pipe is subjected to a final heat treatment consisting of quenching from 899 to 927 ° C after holding for 1 h with water cooling. In case the pipe wall thickness exceeds 12.75 mm, the pipe is cooled with water both from the outside and from the inside. Pipes with a wall thickness of less than 12.75 mm are cooled from the outside. Cooling with water is carried out up to 37-93 C. Hardened pipes are tempered at the martensitic structure at 593-732 ° C to obtain the required yield strength and hardness. The method was tested in the manufacture of casing pipes from steel of two heats, the chemical composition of which is given in table. one.
The steels obtained by double electroshaft remelting were poured into continuously cast square billets.
0
five
firmware and extrusion were obtained sleeves with a diameter of 193.68 mm and a wall thickness of 12.75 and 30.5 mm. The resulting liners were quenched by austentiation for 45 minutes at 913 ° C and cooled with water from the outside and from inside to 93 ° C to obtain a martensitic structure. After that, the sleeves were subjected to tempering at 677-704 C with a latch for 1 h and then cooled with a spray of water. Such a process for the manufacture of pipes by hot molding by extrusion and final heat treatment by means of
hats and high tempering provide the required strength characteristics. The results of the test tubes are given in Table. 2,
At the same time, a part of continuously cast billets from steel of both heats was extruded to obtain sleeves with a wall thickness of 18.08 mm, which were then processed by the proposed method. To do this, they were subjected to heat treatment from the intercritical interval by heating to 802 ° C with a pressure of 20 minutes and subsequent slow cooling to the temperature of the completion of the phase transformation. After the final ad hoc cooling, the sleeves were ground to a outside diameter. To remove the defects, they were cold rolled on a mandrel to obtain a finished pipe with a diameter of 177.8 mm and a wall thickness of 15.88 mm. In this case, the cross section of the liner exceeds the cross section of the finished pipe by approximately 20%. The finished pipes were again subjected to heat treatment from the intercritical interval according to the described mode, and then quenched by austenitization for 45 minutes at 913 ° C and cooled with water from the outside and from the inside to 93 ° C and subsequent tempering at 697 ° C with succession for 45 min and cooling spray of water.
Samples were taken from the resulting pipe batches to determine the yield strength and resistance to stress corrosion cracking.
A comparative analysis of the data obtained shows that in pipes with different wall thicknesses made in a known manner, a threshold destruction is observed (no destruction at a peak of 720 hours) for steel with two heats under a load of 80 to 85 kgf. In the pipes manufactured by the proposed method, the increase in the threshold destruction under loads from 85 to 90 kgf is noticeably, the test results are given in table. 3
At the same time, in pipes manufactured both by the known and proposed methods, anomalous destruction is observed under a load of 75 kgf. Since the time to breakdown is shortened at higher loads, testing all the parameters indicates that the error in the experiments is the same. With accelerated laboratory testing
n 5 Q
five
five
0
five
Zo
Typically, the accepted threshold strength is 75% of the specified minimum yield strength of steel, which in this case is 67.5 kgf / mm, although pipes made by both methods meet the requirements for hydrogen sulfide resistance. cracking, and the pipes made by the proposed method have a higher threshold strength at a higher load, which is 100% of the minimum yield strength of steel.

权利要求:
Claims (6)
[1]
1. A method of manufacturing pipes for the extraction of oil and gas, mainly of steel containing O, 2-0.35% ° C, 0.35-0.9% Mn, 0.8-1.5% Cg, 0.15 -0.75% Mo, not more than 0.25 Ni, not more than 0.35% Cu, not more than 0.35% Si, not more than 0.04% S, not more than 0.04% P, the rest of iron, including hot forming the billet into the sleeve, cleaning the surface, cold rolling to obtain the finished pipe, quenching and tempering, because, in order to increase the resistance to hydrogen sulfide cracking, hot forming is carried out before the cross section of the sleeve is obtained, exceeding 10-40% of the section is ready tube, and after hot forming and cold rolling is produced in the heating interval t AU - AC2) speed and cooling for the recrystallization and grain refining.
[2]
.2. A method according to claim 1, characterized in that the hot molding of the preform into the sleeve is carried out by extrusion.
[3]
3. The method according to claim 1, wherein the cleaning of the surface is carried out by chiffing.
[4]
4. Method PS of claim 1, that is, that cold rolling with the finished pipe is carried out on a mandrel.
[5]
5. A method according to claim 1, characterized in that after hot forming and cold rolling, heating is performed up to 760-815 ° C with a holding time of 0.25-1 hours.
.
[6]
6. The method according to claim 1, characterized in that the quenching of the pipes is carried out at 899-927 ° C, after holding for 1 hour with cooling to 37-93 ° C.
51342426
Table 1
Component
Content, wt.%
Melting 1
Melting 2
0.30 0.57 1.20 0.54 0.14 0.24
0.32 0.79 1.03 0.10 0.21
Truva
Yield point, kgf / mm
95
193.68 X 30.5 mm
5991
I 38
88.3
55
105
(13.t)
193.68 X 30.5 mm 91
In 39
86
Note. The time in hours until the specimen is destroyed is given in parentheses, 720NF — the test is completed at a discharge time of 720 h without disrupting the specimen. Pipes 59, 38, 55 are made of steel smelting, and pipe No. 39 is made of steel smelting 2.
Continuation of table 1
5 Component
Content, wt.%
Melting 1
I
Melting 2
Si Sn
V
Al fe
0.25 0.012 0.096 0.004
0.34 0.009 0.12 0.005
Rest
t a b l and c a 2
kgf / time before destruction, h
8075J
70
)
720NF
(624)
720NF
)
720NF
720NF 720NF
720NF 720NF 720NF
720NF 720NF
(217) 720NF
. 720NF 720NF 720NT
720NF 720NF, 720KF 720NF 720NF 720NF
Note. The time in hours before destruction is shown in parentheses.
720KF — The test was completed with a holding time of 720 hours without destroying the sample. 620NF — The test was terminated due to severe weather conditions in the laboratory. If pipes 35 and 41 are made of steel smelting 1,
Editor Y. Sereda
Compiled by A. Székely
Tehred M. Didyk Proof-reader V. Girn
Order 4448/59 Circulation 549Subscription
VNIIGSh of the USSR State Committee
for inventions and discoveries 113035, Moscow, Zh-35, Raushsk nab., 4/5
Production and printing company, Uzhgorod, st. Project, 4
Table 3

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同族专利:

公开号 | 公开日

ES511959A0|1983-05-01|

EP0064730A2|1982-11-17|

US4354882A|1982-10-19|

AU8345682A|1982-11-11|

KR860002139B1|1986-12-11|

NO157371B|1987-11-30|

DE3269575D1|1986-04-10|

AT18439T|1986-03-15|

AU539144B2|1984-09-13|

EP0064730A3|1983-02-02|

JPS57207113A|1982-12-18|

ES8306187A1|1983-05-01|

NO821498L|1982-11-09|

ZA823134B|1983-03-30|

BR8202630A|1983-04-19|

EP0064730B1|1986-03-05|

CA1197761A|1985-12-10|

NO157371C|1988-03-09|

JPH0335362B2|1991-05-28|

KR830010207A|1983-12-26|

引用文献:

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法律状态:

优先权:

申请号 | 申请日 | 专利标题

US06/261,919|US4354882A|1981-05-08|1981-05-08|High performance tubulars for critical oil country applications and process for their preparation|

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