CN113897514A - Titanium alloy for oil and gas exploitation and preparation method thereof - Google Patents
Titanium alloy for oil and gas exploitation and preparation method thereof Download PDFInfo
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- CN113897514A CN113897514A CN202111230778.8A CN202111230778A CN113897514A CN 113897514 A CN113897514 A CN 113897514A CN 202111230778 A CN202111230778 A CN 202111230778A CN 113897514 A CN113897514 A CN 113897514A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B23/00—Tube-rolling not restricted to methods provided for in only one of groups B21B17/00, B21B19/00, B21B21/00, e.g. combined processes planetary tube rolling, auxiliary arrangements, e.g. lubricating, special tube blanks, continuous casting combined with tube rolling
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- 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
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
Abstract
The invention belongs to the technical field of oil and gas exploitation, and provides a titanium alloy for oil and gas exploitation and a preparation method thereof. The addition of the alpha-phase stabilizing element Al can improve the tensile strength and the yield strength of the titanium alloy, and can ensure that the titanium alloy has higher thermal stability and good weldability. Beta phase stabilizing elements V, Mo and Cr can increase the tensile strength and yield strength of titanium alloy. Meanwhile, Mo can also refine grains and resist CO2Corrosion and H2And S corrosion. Cr is a para-titanium alloyThe strength and toughness of the alloy are better; in addition, Cr has a high β -stabilizing effect on titanium; and Cr has a higher diffusion coefficient in the titanium alloy; therefore, the titanium alloy has low resistance to thermal deformation and good plastic deformability. In addition, the addition of the beta-phase stabilizing element can increase the addition amount of the Al element in alpha-Ti without premature occurrence of alpha2And the strengthening effect on the titanium alloy is obvious.
Description
Technical Field
The invention relates to the technical field of oil and gas exploitation, in particular to a titanium alloy for oil and gas exploitation and a preparation method thereof.
Background
With the further development of petroleum and natural gas, the oil and gas field development in the west and the southwest of China has high temperature (more than 140 ℃), high pressure (more than 100MPa), well depth (more than 5000m) and high corrosion medium (CO)2、H2S、Cl-) The characteristics of (1). At present, nickel-based alloy pipes and high-chromium stainless steel pipes are mostly used in the drilling and exploitation processes of petroleum and natural gas. However, with the shortage of petroleum resources, the number of oil wells and gas wells with good well conditions and small depth is small, and more oil wells and gas wells are concentrated in areas with severe underground environments. When the high-chromium stainless steel pipe is used in oil and gas fields with severe environment, corrosion leakage often occurs. The high-chromium stainless steel pipe has the following problems with the nickel-based alloy pipe besides the problem of insufficient corrosion resistance: 1) nickel is a strategic national resource, and the use of nickel in large quantities is not favorable for national safety. 2) The specific gravity is higher, and the requirement on a matched drilling machine is higher. 3) The elastic modulus is large, and the drill rod is not suitable for short-radius oil wells.
Because the titanium alloy has the advantages of light specific gravity and small elastic modulus, the titanium alloy has the potential of replacing nickel-based alloy pipes and high-chromium stainless steel pipes for candidate materials for oil and gas exploitation. Although the titanium alloy in the prior art has various types, the tensile strength is not more than 950MPa at present, and the transverse impact toughness of the pipe can be kept to be more than or equal to 40J/cm2And has excellent resistance to (CO)2、H2S、Cl-) The titanium alloy of the corrosive medium is suitable for the severe environment of oil and gas exploitation.
Disclosure of Invention
In view of the above, the present invention aims to provide a titanium alloy for oil and gas exploitation and a preparation method thereof. Of the titanium alloy of the inventionThe tensile strength is more than 950MPa, the yield strength is more than 860MPa, the elongation is more than 12 percent, and the longitudinal V-shaped impact toughness is 60J/cm2Above, transverse impact toughness of 40J/cm2Above, and can resist corrosion medium (CO)2、H2S、Cl-) Making it useful for oil and gas production.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a titanium alloy for oil and gas exploitation, which comprises the following components in percentage by weight:
5.0 to 6.5 percent of Al, 1.6 to 2.5 percent of V, 2.6 to 4.0 percent of Zr, 1.0 to 2.0 percent of Mo, 0.9 to 1.8 percent of Cr, 0.06 to 0.12 percent of O, and the balance of Ti and inevitable impurities.
The invention also provides a preparation method of the titanium alloy for oil and gas exploitation, which comprises the following steps:
mixing alloy raw materials, and smelting to obtain a titanium alloy ingot;
and forging the titanium alloy ingot to obtain the oil-gas exploitation titanium alloy.
Preferably, the forging is performed for 1 to 3 times;
when the number of times of forging is 1, the forging comprises first hot forging;
when the forging times are 2 times, the forging comprises sequentially carrying out first hot forging and second hot forging;
when the forging times are 3, the forging comprises sequentially carrying out first hot forging, second hot forging and third hot forging;
the heating temperature of the first hot forging is 1070 to 1170 ℃;
the heating temperature of the second fire forging is 1000-1050 ℃ independently;
the heating temperature of the third hot forging is 1000-1050 ℃ or T independentlyβ-(20～50)℃；TβIs the phase transition point of titanium.
Preferably, the forging further comprises:
heating and extruding the obtained forging product to obtain a titanium alloy black skin pipe;
carrying out heat treatment on the titanium alloy black skin pipe to obtain the titanium alloy for oil and gas exploitation;
the oil-gas extraction adopts titanium alloy as a pipe.
Preferably, when the heating temperature of the last-time forging of the forging is 1000-1170 ℃, the heating temperature of the heating extrusion is Tβ+(20～40)℃；
When the heating temperature of the last-time forging of the forging is TβWhen the temperature is (20-50) DEG C, the heating temperature of the heating extrusion is Tβ-(20～50)℃；
The heating temperature of the last fire forging of the forging is more than or equal to the heating temperature of the heating extrusion;
the extrusion ratio of the heating extrusion is 5-8.
Preferably, the forging further comprises:
carrying out cross piercing, hot rolling and sizing on the obtained forging product in sequence to obtain a titanium alloy black skin pipe;
carrying out heat treatment on the titanium alloy black skin pipe to obtain the titanium alloy for oil and gas exploitation;
the oil-gas extraction adopts titanium alloy as a pipe.
Preferably, when the heating temperature of the last-time forging of the forging is 1000-1170 ℃, the heating temperature of the cross-piercing is Tβ+(20～40)℃；
When the heating temperature of the last-time forging of the forging is TβAt the temperature of (20 to 50) DEG C, the heating temperature of the cross-piercing is Tβ-(20～50)℃；
The heating temperature of the last fire forging of the forging is more than or equal to the heating temperature of the cross-piercing;
the deformation amount of the cross-piercing is 50-60%.
Preferably, the hot rolling deformation amount is 55 to 65%.
Preferably, the sizing deformation is 18-25%.
Preferably, the heat treatment comprises a normal annealing or a double annealing;
the temperature of the common annealing is 800-1000 ℃, and the heat preservation time is 1 h;
the double annealing comprises high-temperature annealing and low-temperature annealing in sequence; the high-temperature annealing temperature is 850-930 ℃, and the heat preservation time is 1 h; the temperature of the low-temperature annealing is 480-560 ℃, and the heat preservation time is 4-8 h.
The invention provides a titanium alloy for oil and gas exploitation, which comprises the following components in percentage by weight: 5.0 to 6.5 percent of Al, 1.6 to 2.5 percent of V, 2.6 to 4.0 percent of Zr, 1.0 to 2.0 percent of Mo, 0.9 to 1.8 percent of Cr, 0.06 to 0.12 percent of O, and the balance of Ti and inevitable impurities. The addition of the alpha-phase stabilizing element Al can improve the tensile strength and the yield strength of the titanium alloy, and can ensure that the titanium alloy has higher thermal stability and good weldability. Beta phase stabilizing elements V, Mo and Cr can increase the tensile strength and yield strength of titanium alloy. Meanwhile, Mo can also refine grains and resist CO2Corrosion and H2And S corrosion. Cr belongs to an element with better comprehensive effect on the strength and toughness of titanium; in addition, Cr has a high beta-stabilizing effect on titanium, and has a high diffusion coefficient in titanium alloy; therefore, the titanium alloy has low resistance to thermal deformation and good plastic deformability. In addition, the addition of the beta-phase stabilizing element can increase the addition amount of the Al element in alpha-Ti without premature occurrence of alpha2And the strengthening effect on the titanium alloy is obvious. The invention controls Al + V + Mo + Cr in the titanium alloy for oil and gas exploitation to be less than or equal to 13%, and can also improve the impact toughness of the titanium alloy for oil and gas exploitation.
The data of the examples show that: the titanium alloy provided by the invention has the room-temperature tensile strength of 960-1090 MPa, the yield strength of 895-975 MPa, the elongation of 12-16% and the longitudinal V-shaped impact toughness of 82-107J/cm2Transverse impact toughness of 47-56J/cm2And can resist corrosion medium (CO)2、H2S、Cl-) Making it useful for oil and gas production.
Furthermore, the total content of alpha phase stabilization element (Al) and beta phase stabilization element (V, Mo, Cr) is controlled to be less than 13%, so that the tensile strength, yield strength, toughness, corrosion resistance, process plasticity and strengthening heat treatment capability of the titanium alloy, especially the process plasticity and strengthening heat treatment capability, can be further improved.
Detailed Description
The invention provides a titanium alloy for oil and gas exploitation, which comprises the following components in percentage by weight:
5.0 to 6.5 percent of Al, 1.6 to 2.5 percent of V, 2.6 to 4.0 percent of Zr, 1.0 to 2.0 percent of Mo, 0.9 to 1.8 percent of Cr, 0.06 to 0.12 percent of O, and the balance of Ti and inevitable impurities.
In the present invention, the starting materials used in the present invention are preferably commercially available products unless otherwise specified.
The titanium alloy for oil and gas exploitation provided by the invention comprises 5.0-6.5 wt% of Al, preferably 5.3-6.2 wt%, and further preferably 5.5-5.9 wt%. In the present invention, Al is an alpha phase stabilizing element and can raise the phase transition point of titanium. The Al can improve the strength of the titanium alloy, and when the content of the aluminum is 6-7%, the titanium alloy has high thermal stability and good weldability. However, when the Al content is more than 4.4%, α of the titanium alloy appears2The titanium alloy is embrittled, and the hot processing performance of the titanium alloy is reduced; the invention can improve the addition of Al element in alpha-Ti by adding beta-phase stabilizing element without generating alpha prematurely2And the strengthening effect on the titanium alloy is obvious. According to the invention, the content of Al is controlled to be 5.0-6.5%, so that the yield strength and tensile strength of the titanium alloy can be increased, and the titanium alloy can be ensured to have good hot-working performance.
Based on the weight percentage of Al, the titanium alloy for oil and gas exploitation provided by the invention comprises 1.6-2.5% of V, preferably 1.8-2.4%, and more preferably 2.0-2.2%. In the invention, V is a eutectic beta stable element, which can improve the strength of the titanium alloy and reduce the plasticity and corrosion resistance of the titanium alloy; v can also reduce the phase transformation point T of titaniumβIf the titanium alloy is to be plastically deformed in the two-phase region, the transformation point should be as high as possible. In additionIn addition, V-containing master alloys are costly. The content of V is adjusted to 1.6-2.5%, so that the titanium alloy has excellent yield strength, tensile strength, plasticity and corrosion resistance, and the cost of the titanium alloy is reasonably controlled.
Based on the weight percentage of Al, the titanium alloy for oil and gas exploitation provided by the invention comprises 2.6-4.0% of Zr, preferably 2.8-3.8%, and more preferably 3.0-3.5%. In the present invention, Zr is a neutral element, and can lower the transformation point of titanium, but has a small influence. Zr can also play a role in solid solution strengthening and alpha phase stabilization, can also improve the tensile strength and heat resistance of the titanium alloy at room temperature and high temperature, refine crystal grains and improve welding performance; however, Zr is less effective in strengthening. The Zr content of the invention is determined to be 2.6-4.0%, which can improve the stability of alpha phase of titanium alloy and simultaneously improve the toughness and welding performance of titanium alloy.
Based on the weight percentage of Al, the titanium alloy for oil and gas exploitation provided by the invention comprises 1.0-2.0% of Mo, preferably 1.2-1.8%, and more preferably 1.3-1.6%. In the invention, Mo is a eutectic beta stable element, which can improve the strength of the titanium alloy, wherein the effect of Mo on improving the strength is more obvious than that of V; mo can also refine grains and resist CO2And H2S corrosion; however, Mo is disadvantageous to the plasticity and weldability of the titanium alloy. Therefore, the content of Mo is controlled to be 1.0-2.0%, so that the yield strength and tensile strength of the titanium alloy are ensured; and improves the CO resistance of the titanium alloy2And H2S corrosion performance.
Based on the weight percentage of Al, the titanium alloy for oil and gas exploitation provided by the invention comprises 0.9-1.8% of Cr, preferably 1.0-1.6%, and more preferably 1.2-1.5%. In the invention, Cr is a eutectoid beta-phase stable element, has strong strengthening effect on the beta-phase of the titanium alloy and has larger effect than that of eutectic elements Mo and V; cr belongs to an element with better comprehensive effect on the strength and toughness of titanium, and in addition, Cr has high beta stabilization effect on titanium, has higher diffusion coefficient in titanium alloy, lower resistance and better plastic deformation capability during thermal deformation; however, Cr forms brittle intermetallic compounds with Ti, which reduces the toughness of the titanium alloy. The invention controls the content of Cr to be 0.9-1.8%, and ensures the strength and toughness of the titanium alloy.
In the invention, Al + V + Mo + Cr in the titanium alloy is less than or equal to 13% in the oil-gas exploitation. The total content of alpha phase stabilization element (Al) and beta phase stabilization element (V, Mo, Cr) is controlled to be less than 13%, so that the tensile strength, yield strength, toughness, corrosion resistance, process plasticity and strengthening heat treatment capability of the titanium alloy, especially the process plasticity and strengthening heat treatment capability, can be further improved.
Based on the weight percentage of Al, the titanium alloy for oil and gas exploitation provided by the invention comprises 0.06-0.12% of O, preferably 0.07-0.10%, and more preferably 0.08-0.09%. In the present invention, O is the most inexpensive strengthening element and improves the room temperature and high temperature strength of the titanium alloy. However, too high an amount of O leads to deterioration of processability. According to the invention, the O content is controlled to be 0.06-0.12%, and the yield strength, tensile strength and good hot workability of the titanium alloy are ensured.
Based on the weight percentage of Al, the titanium alloy for oil and gas exploitation provided by the invention comprises the balance of Ti. The titanium alloy of the invention takes titanium as a substrate, and ensures that the obtained titanium alloy has the advantages of light specific gravity and small elastic modulus.
The titanium alloy for oil and gas exploitation provided by the invention comprises inevitable impurities based on the weight percentage of Al.
The invention also provides a preparation method of the titanium alloy for oil and gas exploitation, which comprises the following steps:
mixing alloy raw materials, and smelting to obtain a titanium alloy ingot;
and forging the titanium alloy ingot to obtain the oil-gas exploitation titanium alloy.
According to the invention, alloy raw materials are mixed, and electron beam cold hearth smelting and vacuum consumable arc smelting are sequentially carried out to obtain the titanium alloy ingot.
In the present inventionIn the invention, the alloy raw materials preferably include: titanium sponge, aluminum-vanadium master alloy, aluminum-molybdenum master alloy, aluminum-chromium master alloy, chromium metal, zirconium sponge, aluminum bean and TiO2And (3) pulverizing. The content of each metal in the alloy raw material is not particularly limited as long as the content of each element in the titanium alloy can be satisfied by mass percentage.
After the alloy raw materials are mixed, the invention preferably further comprises pressing the obtained alloy raw material mixture into an electrode. The size of the electrode is not particularly limited in the present invention as long as the subsequent melting can be performed.
In the present invention, the melting preferably includes electron beam cold hearth melting (EB) and/or vacuum consumable arc melting (VAR), and more preferably vacuum consumable arc melting (VAR) or electron beam cold hearth melting (EB) + vacuum consumable arc melting (VAR).
In the invention, when the smelting is preferably vacuum consumable arc smelting (VAR), the number of times of the vacuum consumable arc smelting is preferably 2-3 times; when the number of times of the vacuum consumable arc melting is preferably 2, the vacuum consumable arc melting preferably comprises sequentially performing a first vacuum consumable arc melting and a second vacuum consumable arc melting; the first vacuum consumable arc melting conditions include: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 10-30 kA, and the smelting voltage is preferably 30-40V; the conditions of the second vacuum consumable arc melting include: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 20-40 kA, and the smelting voltage is preferably 30-40V.
In the present invention, when the number of times of the vacuum consumable arc melting is preferably 3, the vacuum consumable arc melting preferably includes sequentially performing a first vacuum consumable arc melting, a second vacuum consumable arc melting, and a third vacuum consumable arc melting. In the present invention, the conditions of the first vacuum consumable arc melting include: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 10-30 kA, and the smelting voltage is preferably 30-40V; the conditions of the second vacuum consumable arc melting include: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 20-40 kA, and smelting is carried outThe smelting voltage is preferably 30-40V: the third vacuum consumable arc melting conditions include: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 20-30 kA, and the smelting voltage is preferably 30-40V.
In the present invention, when the melting is preferably electron beam cold hearth melting (EB) + vacuum consumable arc melting (VAR), it is preferably 1 electron beam cold hearth melting (EB) +1 vacuum consumable arc melting (VAR) or 1 electron beam cold hearth melting (EB) +2 vacuum consumable arc melting (VAR). In the invention, when the smelting is preferably 1 electron beam cold hearth smelting (EB) +1 vacuum consumable arc smelting (VAR); the conditions for electron beam cold hearth melting preferably include: the vacuum degree is preferably 10-1Pa, the smelting current is preferably 1-10A, and the smelting voltage is preferably 20-40 kV; the conditions for the vacuum consumable arc melting preferably include: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 10-30 kA, and the smelting voltage is preferably 30-40V.
In the present invention, when the melting is preferably 1 electron beam cold hearth melting (EB) +2 vacuum consumable arc melting (VAR); the conditions of the electron beam cold hearth smelting comprise: the degree of vacuum is preferably 10-1Pa, the smelting current is preferably 1-10A, and the smelting voltage is preferably 20-40 kV; the 2-time vacuum consumable arc melting preferably comprises a first vacuum consumable arc melting and a second vacuum consumable arc melting which are sequentially carried out; the conditions of the first vacuum consumable arc melting comprise that the vacuum degree is preferably 10-1Pa, the smelting current is preferably 10-30 kA, and the smelting voltage is preferably 30-40V; the conditions of the second vacuum consumable arc melting include that the vacuum degree is preferably 10-1Pa, the smelting current is preferably 20-40 kA, and the smelting voltage is preferably 30-40V.
After obtaining the titanium alloy ingot, forging the titanium alloy ingot to obtain the oil-gas exploitation titanium alloy.
In the present invention, the number of forging is preferably 1 to 3.
In the present invention, when the number of times of forging is preferably 1, the forging preferably includes first hot forging; the heating temperature of the first hot forging is preferably 1070 to 1170 ℃.
In the present invention, when the number of times of forging is preferably 2 times, the forging preferably includes sequentially performing first hot forging and second hot forging; the heating temperature of the first hot forging is preferably 1070-1170 ℃; the heating temperature of the second hot forging is preferably 1000-1050 ℃.
In the present invention, when the number of times of forging is preferably 3 times, the forging preferably includes sequentially performing first fire forging, second fire forging, and third fire forging; the heating temperature of the first hot forging is preferably 1070-1170 ℃; the heating temperature of the second fire forging is preferably 1000-1050 ℃; the heating temperature of the third hot forging is preferably 1000-1050 ℃ or Tβ-(20～50)℃；TβIs the phase transition point of titanium.
The invention preferably further comprises peeling the forged product. The invention does not specifically limit the peeling operation, and the peeling operation known to those skilled in the art can be adopted.
After forging, the invention preferably further comprises the step of heating and extruding the obtained forged product to obtain the titanium alloy black skin pipe; carrying out heat treatment on the titanium alloy black skin pipe to obtain the titanium alloy for oil and gas exploitation; the oil-gas extraction adopts titanium alloy as a pipe. In the present invention, the heating and pressing are preferably performed after peeling.
In the present invention, when the heating temperature of the last forging of the forging is 1000 to 1170 ℃, the heating temperature of the heating extrusion is preferably Tβ+ (20-40) DEG C; the heating temperature of the last fire forging of the forging is preferably more than or equal to the heating temperature of the heating extrusion; .
In the present invention, when the heating temperature of the last forging of the forging is TβWhen the temperature is (20-50) DEG C, the heating temperature of the heating extrusion is preferably Tβ- (20 to 50) DEG C; the heating temperature of the last fire forging of the forging is preferably more than or equal to the heating temperature of the heating extrusion.
In the present invention, the extrusion ratio of the heating extrusion is preferably 5 to 8.
In the present invention, the heat treatment preferably includes normal annealing or double annealing.
In the invention, the temperature of the common annealing is preferably 800-1000 ℃, and the heat preservation time is preferably 1 h. In the invention, the rate of raising the temperature to the temperature of the common annealing is preferably 8-12 ℃/min. After the ordinary annealing, the present invention preferably further comprises air-cooling the obtained ordinary annealed product to room temperature.
In the present invention, the double annealing preferably includes sequentially performing high-temperature annealing and low-temperature annealing; the high-temperature annealing temperature is preferably 850-930 ℃, and the heat preservation time is preferably 1 h; the rate of raising the temperature to the high-temperature annealing temperature is preferably 8-12 ℃/min; after the high-temperature annealing, the present invention preferably further comprises air-cooling the obtained high-temperature annealed product. In the invention, the temperature of the low-temperature annealing is preferably 480-560 ℃, and the heat preservation time is preferably 4-8 h; the rate of raising the temperature to the low-temperature annealing temperature is preferably 5-8 ℃/min. After the low-temperature annealing, the invention preferably further comprises air cooling the obtained low-temperature annealed product.
After the forging, the present invention preferably further comprises: carrying out cross piercing, hot rolling and sizing on the obtained forging product in sequence to obtain a titanium alloy black skin pipe; carrying out heat treatment on the titanium alloy black skin pipe to obtain the titanium alloy for oil and gas exploitation; the oil-gas extraction adopts titanium alloy as a pipe.
In the present invention, when the heating temperature of the last forging of the forging is 1000 to 1170 ℃, the temperature of the cross-piercing is preferably Tβ+ (20-40) DEG C; the heating temperature of the last fire forging of the forging is preferably more than or equal to the heating temperature of the cross-piercing.
In the present invention, when the heating temperature of the last forging of the forging is TβWhen the temperature is (20-50) DEG C, the heating temperature of the cross-piercing is preferably Tβ- (20 to 50) DEG C; the heating temperature of the last fire forging of the forging is preferably more than or equal to the heating temperature of the cross-piercing.
In the present invention, the amount of deformation of the cross piercing is preferably 50 to 60%.
In the present invention, the hot rolling deformation is preferably 55 to 65%.
In the present invention, the amount of deformation of the sizing is preferably 18 to 25%.
In the present invention, the heat treatment includes normal annealing or double annealing. In the present invention, the parameters and operations of the normal annealing and the dual annealing are consistent with the above technical solutions, and are not described herein again.
The titanium alloy for oil and gas exploitation and the preparation method thereof provided by the present invention are described in detail below with reference to examples, but they should not be construed as limiting the scope of the present invention.
Example 1
The titanium alloy for oil and gas exploitation comprises the following components in percentage by weight: 5.0% of Al, 2.5% of V, 3.0% of Zr, 2.0% of Mo, 1.8% of Cr, 0.07% of O, and the balance of Ti and inevitable impurities.
Raw materials: grade 1 titanium sponge with the particle size of 3-25.4 mm; the particle size of the aluminum-vanadium alloy is 1-6 mm; the particle size of the aluminum-molybdenum alloy is 0.1-0.8 mm; the particle size of the aluminum-chromium alloy is 1-3 mm; 0-grade sponge zirconium with the particle size of 3-12.7 mm; the particle size of the metal chromium is 1-3 mm; the particle size of the aluminum beans is 8-13 mm; TiO 22Powder with a particle size of 100 meshes.
(1) Mixing aluminum-vanadium alloy, aluminum-molybdenum alloy, aluminum-chromium alloy, chromium metal, aluminum beans, 0-grade sponge zirconium and 1-grade sponge titanium, pressing into electrodes, and then smelting for three times in a vacuum consumable electrode furnace to obtain a titanium alloy ingot with the diameter of 720mm, wherein the vacuum degrees of the three times of smelting are all 10-1Pa, the current of the first smelting is 19kA, and the smelting voltage is 32V; the current of the second smelting is 27kA, and the smelting voltage is 34V; the current of the third smelting is 29kA, and the smelting voltage is 36V.
(2) Forging the titanium alloy ingot obtained in the step (1) for three times; the heating temperature of the first hot forging is 1150 ℃, the heating temperature of the second hot forging is 1050 ℃, the heating temperature of the third hot forging is 1000 ℃, and the titanium alloy bar with phi 160mm is freely forged and drawn.
(3) Peeling the titanium alloy bar material obtained in the step (2) to obtain a titanium alloy polished rod with the diameter of phi 150mm, and then carrying out polishingAt TβAnd keeping the temperature at +40 ℃, namely 960 ℃ for 120-240 min, performing cross rolling perforation until the diameter is 180 x 13mm, and performing hot rolling until the diameter is 60.8 x 7.0mm to obtain the titanium alloy pipe.
(4) Heating the titanium alloy pipe obtained in the step (3) to 800 ℃ at a speed of 10 ℃/min, preserving heat for 1h, air cooling, and carrying out common annealing, and marking as No. 1 heat treatment;
and (4) heating the titanium alloy pipe obtained in the step (3) to 890 ℃ at a speed of 10 ℃/min, preserving heat for 1h, cooling in air to room temperature, heating to 480 ℃ at a speed of 5 ℃/min, preserving heat for 6h, cooling in air to room temperature, and carrying out double heat treatment. The heat treatment was described as 1' # heat treatment.
(5) And (4) straightening the pipe obtained in the step (4), and performing rough polishing and fine polishing by using surface polishing and grinding equipment to obtain a finished titanium alloy oil pipe with the diameter of 60.3 multiplied by 6.45 mm.
Testing the room-temperature tensile strength of the finished titanium alloy oil pipe obtained in the step (5) by GB/T228.1-2010, and testing the V-shaped impact toughness of the finished titanium alloy oil pipe obtained in the step (5) by GB/T229-2S+5MPa CO2+250000mg/L Cl-The high-temperature high-pressure corrosion test is carried out under the environmental conditions, the dynamic rotating speed is 300 r/min, the test time is 30 days, and the average annual corrosion rate is calculated according to the standard NACE RP0775-2005 after the test.
The tensile strength of the finished titanium alloy oil pipe subjected to the No. 1 heat treatment at room temperature is 960MPa, the yield strength is 895MPa, the elongation is 16%, and the longitudinal and transverse full-size Charpy V-shaped impact toughness is 82J/cm2And 47J/cm2(ii) a After the tube is welded by electron beams, the tensile strength of the welding seam at room temperature is 965MPa, the yield strength is 900MPa, the elongation is 15.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact toughness is 76J/cm respectively2And 41J/cm2(ii) a Uniform annual corrosion rate of 1.1X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
The room-temperature tensile strength of the 1' # heat-treated finished titanium alloy oil pipe is 980MPa, the yield strength is 910MPa, the elongation is 15 percent, and the longitudinal and transverse full-size Charpy V-shaped impact toughness is 88J/cm2And 50J/cm2(ii) a After the tube is welded by electron beams, the tensile strength of the welding seam at room temperature is 990MPa, and the yield strength915MPa, elongation of 14.0 percent and longitudinal and transverse full-size Charpy V-shaped impact toughness of 75J/cm2And 42J/cm2(ii) a Uniform annual corrosion rate of 1.3X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
Example 2
The titanium alloy for oil and gas exploitation comprises the following components in percentage by weight: 5.3 percent of Al, 2.0 percent of V, 2.6 percent of Zr, 1.0 percent of Mo, 0.9 percent of Cr, 0.07 percent of O, and the balance of Ti and inevitable impurities.
Raw materials: grade 1 titanium sponge with the particle size of 3-25.4 mm; the particle size of the aluminum-vanadium alloy is 1-6 mm; the particle size of the aluminum-molybdenum alloy is 0.1-0.8 mm; the particle size of the aluminum-chromium alloy is 1-3 mm; the particle size of the metal chromium is 1-3 mm; 0-grade sponge zirconium with the particle size of 3-12.7 mm; the particle size of the aluminum beans is 8-13 mm; TiO 22Powder with a particle size of 100 meshes.
(1) Mixing aluminum-vanadium alloy, aluminum-molybdenum alloy, aluminum-chromium alloy, chromium metal, aluminum beans, 0-grade sponge zirconium and 1-grade sponge titanium, pressing into electrodes, and then smelting twice in a vacuum consumable electrode furnace to obtain a titanium alloy ingot with the diameter of 560mm, wherein the vacuum degrees of the two smelting are 10-1Pa, the current for the first smelting is 11kA, and the smelting voltage is 30V; the current of the second smelting is 19kA, and the smelting voltage is 32V.
(2) Forging the titanium alloy ingot obtained in the step (1) for one time, wherein the heating temperature of the first-time forging is 1150 ℃; obtaining the titanium alloy bar with the diameter of 332 mm.
(3) Peeling the titanium alloy bar obtained in the step (2) to obtain a titanium alloy polished rod with the diameter of 320mm, and then performing polishing at TβAnd (3) keeping the temperature at 995 ℃ for 260-380 min, performing cross rolling perforation until the diameter is 380X 28mm, performing hot rolling until the diameter is 370X 14mm, and sizing until the diameter is 341X 10.15 mm.
(4) And (4) heating the titanium alloy pipe obtained in the step (3) to 850 ℃ at a speed of 10 ℃/min, preserving heat for 1h, cooling in air, and carrying out common annealing, wherein the record is 2# heat treatment.
And (4) heating the titanium alloy pipe obtained in the step (3) to 925 ℃ at a speed of 10 ℃/min, preserving heat for 1h, cooling in air to room temperature, heating to 560 ℃ at a speed of 5 ℃/min, preserving heat for 4h, cooling in air to room temperature, and carrying out double heat treatment. The heat treatment was noted as 2' # heat treatment.
(5) And (4) straightening the pipe obtained in the step (4), and performing rough polishing and fine polishing by using surface polishing and grinding equipment to obtain a finished sleeve pipe with the diameter of phi 340.4 multiplied by 9.65 mm.
The room-temperature tensile strength of the finished sleeve obtained in the test (5) is tested by GB/T228.1-2010, and the V-shaped impact toughness of the finished sleeve obtained in the test (5) is tested by GB/T229-2S+5MPa CO2+250000mg/L Cl-The high-temperature high-pressure corrosion test is carried out under the environmental conditions, the dynamic rotating speed is 300 r/min, the test time is 30 days, and the average annual corrosion rate is calculated according to the standard NACE RP0775-2005 after the test.
The room-temperature tensile strength of the finished sleeve after the No. 2 heat treatment is 975MPa, the yield strength is 910MPa, the elongation is 14 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 103J/cm respectively2And 52J/cm2(ii) a Uniform annual corrosion rate of 1.6X 10-4mm/a; after argon arc welding, the tensile strength of the welding seam at room temperature is 985MPa, the yield strength is 910MPa, the elongation is 11.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 94J/cm respectively2And 46J/cm2(ii) a No pitting, stress corrosion cracking and crevice corrosion.
The room-temperature tensile strength of the finished sleeve after the 2' # heat treatment is 990MPa, the yield strength is 915MPa, the elongation is 14.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact powers are respectively 105J/cm2And 55J/cm2(ii) a After argon arc welding, the tensile strength of the welding seam at room temperature is 998MPa, the yield strength is 920MPa, the elongation is 11.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 97J/cm respectively2And 48J/cm2(ii) a Uniform annual corrosion rate of 1.7X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
Example 3
The titanium alloy for oil and gas exploitation comprises the following components in percentage by weight: 5.6 percent of Al, 2.2 percent of V, 2.8 percent of Zr, 1.5 percent of Mo, 1.2 percent of Cr, 0.08 percent of O, and the balance of Ti and inevitable impurities.
Raw materials: grade 1 titanium sponge with the particle size of 3-25.4 mm; the particle size of the aluminum-vanadium alloy is 1-6 mm; aluminiumThe particle size of the molybdenum alloy is 0.1-0.8 mm; the particle size of the aluminum-chromium alloy is 1-3 mm; the particle size of the metal chromium is 1-3 mm; 0-grade sponge zirconium with the particle size of 3-12.7 mm; the particle size of the aluminum beans is 8-13 mm; TiO 22Powder with a particle size of 100 meshes.
(1) Mixing aluminum-vanadium alloy, aluminum-molybdenum alloy, aluminum-chromium alloy, metal chromium, aluminum beans, 0-grade sponge zirconium and 1-grade sponge titanium, pressing into electrodes, and then performing 1-time electron beam cold hearth melting (EB) and 1-time vacuum consumable arc melting (VAR) to obtain phi 720mm titanium alloy ingots, wherein the vacuum degrees of the EB melting and the VAR melting are both 10-1Pa, EB smelting current is 6A, and smelting voltage is 30 kV; the VAR smelting current is 29kA, and the smelting voltage is 35V.
(2) Forging the titanium alloy ingot obtained in the step (1) twice, wherein the heating temperature of the first hot forging is 1100 ℃, and the heating temperature of the second hot forging is 1000 ℃ to obtain a titanium alloy bar with phi of 160 mm;
(3) peeling the titanium alloy bar obtained in the step (2) to obtain a titanium alloy polished rod with the diameter of phi 150mm, and then performing TβAnd keeping the temperature at +20 ℃, namely 970 ℃, keeping the temperature for 120-240 min, performing cross rolling perforation until the diameter is 180 x 15mm, and hot rolling until the diameter is 60.8 x 7.6 mm.
(4) And (4) heating the titanium alloy pipe obtained in the step (3) to 1000 ℃ at a speed of 10 ℃/min, preserving the temperature for 1h, cooling in air, and carrying out common annealing, wherein the mark is 3# heat treatment.
And (4) heating the titanium alloy pipe obtained in the step (3) to 920 ℃ at the speed of 10 ℃/min, preserving heat for 1h, cooling in air to room temperature, heating to 560 ℃ at the speed of 5 ℃/min, preserving heat for 4h, cooling in air to room temperature, and carrying out double heat treatment. The heat treatment was noted as 3' # heat treatment.
(5) And (4) straightening the pipe obtained in the step (4), and performing rough polishing and fine polishing by using surface polishing and grinding equipment to obtain a finished drill rod with the diameter of 60.3 multiplied by 7.1 mm.
The room-temperature tensile strength of the finished drill rod is obtained by adopting the GB/T228.1-2010 testing step (5), and the V-shaped impact toughness of the finished drill rod is obtained by adopting the GB/T229-2S+5MPa CO2+250000mg/L Cl-The dynamic rotating speed is 300 r/min, the test time is 30 days, and the average is calculated according to the standard NACE RP0775-2005 after the testAnnual corrosion rate.
The room-temperature tensile strength of the finished drill rod subjected to the No. 3 heat treatment is 1020MPa, the yield strength is 930MPa, the elongation is 14 percent, and the longitudinal and transverse full-size Charpy V-shaped impact powers are 102J/cm respectively2And 54J/cm2(ii) a Uniform annual corrosion rate of 0.98X 10-4mm/a; after argon arc welding, the tensile strength of the welding seam at room temperature is 1015MPa, the yield strength is 920MPa, the elongation is 10.5 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 93J/cm respectively2And 48J/cm2(ii) a No pitting, stress corrosion cracking and crevice corrosion.
The room-temperature tensile strength of the finished product drill rod subjected to the 3' # heat treatment is 1050MPa, the yield strength is 945MPa, the elongation is 14 percent, and the longitudinal and transverse full-size Charpy V-shaped impact powers are 107J/cm respectively2And 56J/cm2(ii) a After argon arc welding, the tensile strength of the welding seam at room temperature is 1045MPa, the yield strength is 940MPa, the elongation is 10.5 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 96J/cm2And 49J/cm2(ii) a Uniform annual corrosion rate of 1.07X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
Example 4
The titanium alloy for oil and gas exploitation comprises the following components in percentage by weight: 6.0% of Al, 1.6% of V, 3.5% of Zr, 1.2% of Mo, 1.0% of Cr, 0.10% of O and the balance of Ti and inevitable impurities.
Raw materials: grade 1 titanium sponge with the particle size of 3-25.4 mm; the particle size of the aluminum-vanadium alloy is 1-6 mm; the particle size of the aluminum-molybdenum alloy is 0.1-0.8 mm; the particle size of the aluminum-chromium alloy is 1-3 mm; the particle size of the metal chromium is 1-3 mm; 0-grade sponge zirconium with the particle size of 3-12.7 mm; the particle size of the aluminum beans is 8-13 mm; TiO 22Powder with the grain diameter of 100 meshes;
(1) mixing aluminum-vanadium alloy, aluminum-molybdenum alloy, aluminum-chromium alloy, metal chromium, aluminum beans, 0-grade sponge zirconium and 1-grade sponge titanium, pressing into electrodes, and then performing 1-time electron beam cold hearth furnace smelting (EB) and 2-time vacuum consumable arc smelting (VAR) in a vacuum consumable arc furnace to obtain phi 820mm titanium alloy ingots, wherein the vacuum degrees of EB smelting and VAR smelting are both vacuum degrees10-1Pa, EB smelting current is 6A, and smelting voltage is 30 kV; the first VAR smelting current is 29kA, the smelting voltage is 35V, the second VAR smelting current is 33kA, and the smelting voltage is 36V.
(2) Forging the titanium alloy ingot obtained in the step (1) for three times, wherein the heating temperature of the first hot forging is 1170 ℃, the heating temperature of the second hot forging is 1050 ℃, and the heating temperature of the third hot forging is TβFreely forging and drawing a titanium alloy bar with phi of 225mm at the temperature of minus 20 ℃, namely 950 ℃;
(3) peeling the titanium alloy bar obtained in the step (2) to obtain a phi 213mm titanium alloy polished rod, drilling and boring to obtain the phiOuter cover213×ΦInner partA 90mm pipe billet.
(4) Putting the tube blank rod obtained in the step (3) in TβHeating at-30 ℃, namely 940 ℃, preserving heat for 50-170 min, and extruding into a pipe with the diameter of 114.8 multiplied by 16.5 mm.
(5) And (4) heating the pipe obtained in the step (4) to 880 ℃ at the speed of 10 ℃/min, preserving heat for 1h, cooling in air, and carrying out common annealing, wherein the heat treatment is marked as No. 4 heat treatment.
And (3) heating the pipe obtained in the step (4) to 940 ℃ at the speed of 10 ℃/min, preserving heat for 1h, cooling in air to room temperature, heating to 540 ℃ at the speed of 5 ℃/min, preserving heat for 6h, cooling in air to room temperature, and carrying out double heat treatment. The heat treatment was noted as 4' # heat treatment.
(6) And (5) straightening the pipe obtained in the step (5), and performing rough polishing and fine polishing by using surface polishing and grinding equipment to obtain a finished oil pipe with the diameter of 114.3 multiplied by 16 mm.
Testing the room-temperature tensile strength of the finished oil pipe obtained in the step (6) by adopting GB/T228.1-2010, and testing the V-shaped impact toughness of the finished oil pipe obtained in the step (6) by adopting GB/T229-2S+5MPa CO2+250000mg/L Cl-The high-temperature high-pressure corrosion test is carried out under the environmental conditions, the dynamic rotating speed is 300 r/min, the test time is 30 days, and the average annual corrosion rate is calculated according to the standard NACE RP0775-2005 after the test.
The room-temperature tensile strength of the 4# heat-treated finished oil pipe is 1075MPa, the yield strength is 950MPa, the elongation is 13%, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 92J/cm respectively2And 48J/cm2(ii) a Uniform annual corrosion rate of 2.5X 10-4mm/a; after the tube is welded by electron beams, the tensile strength of the welding seam at room temperature is 1075MPa, the yield strength is 946MPa, the elongation is 10.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 85J/cm respectively2And 42J/cm2(ii) a No pitting, stress corrosion cracking and crevice corrosion.
The room-temperature tensile strength of the 4' # heat-treated finished oil pipe is 1090MPa, the yield strength is 975MPa, the elongation is 12 percent, and the longitudinal and transverse full-size Charpy V-shaped impact powers are 96J/cm respectively2And 50J/cm2(ii) a After argon arc welding, the tensile strength of the welding line at room temperature can reach 1085MPa, the yield strength is 970MPa, the elongation is 10.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact power is 91J/cm2And 41J/cm2(ii) a Uniform annual corrosion rate of 2.3X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
Example 5
The titanium alloy for oil and gas exploitation comprises the following components in percentage by weight: 6.5% of Al, 2.4% of V, 4.0% of Zr, 1.3% of Mo, 1.5% of Cr, 0.06% of O and the balance of Ti and inevitable impurities.
Raw materials: grade 1 titanium sponge with the particle size of 3-25.4 mm; the particle size of the aluminum-vanadium alloy is 1-6 mm; the particle size of the aluminum-molybdenum alloy is 0.1-0.8 mm; the particle size of the aluminum-chromium alloy is 1-3 mm; the particle size of the metal chromium is 1-3 mm; 0-grade sponge zirconium with the particle size of 3-12.7 mm; the particle size of the aluminum beans is 8-13 mm; TiO 22Powder with a particle size of 100 meshes.
(1) Mixing aluminum-vanadium alloy, aluminum-molybdenum alloy, aluminum-chromium alloy, chromium metal, aluminum beans, 0-grade sponge zirconium and 1-grade sponge titanium, pressing into electrodes, and then smelting twice in a vacuum consumable electrode furnace to obtain titanium alloy cast ingots with the diameter of 640mm, wherein the vacuum degrees of the twice smelting are both 10-1Pa, the current of the first smelting is 18kA, and the smelting voltage is 32V; the current of the second smelting is 24kA, and the smelting voltage is 35V.
(2) And (3) forging the titanium alloy ingot obtained in the step (1) twice, wherein the heating temperature of the first hot forging is 1070 ℃, the heating temperature of the second hot forging is 1000 ℃, and the titanium alloy ingot is subjected to precision forging to obtain a titanium alloy bar with the diameter of 185 mm.
(3) Peeling the titanium alloy bar obtained in the step (2) to obtain a titanium alloy polished rod with phi 179mm, drilling and boring to obtain phiOuter cover179×ΦInner part72mm pipe billet.
(4) Putting the tube blank rod obtained in the step (3) in TβAnd (3) preserving the heat at the temperature of minus 20 ℃, namely 940 ℃ for 140-260 min, and extruding to obtain the pipe with the diameter of 89.4 multiplied by 12.6 mm.
(5) And (3) heating the pipe material in the step (4) to 880 ℃ at the speed of 10 ℃/min, preserving heat for 1h, cooling in air, and carrying out common annealing, wherein the mark is 5# heat treatment.
And (3) heating the pipe material in the step (4) to 930 ℃ at the speed of 10 ℃/min, preserving heat for 1h, cooling in air to room temperature, heating to 540 ℃ at the speed of 5 ℃/min, preserving heat for 6h, cooling in air to room temperature, and carrying out double heat treatment. The heat treatment was noted as 5' # heat treatment.
(6) And (5) straightening the pipe obtained in the step (5), and performing rough polishing and fine polishing by using surface polishing and grinding equipment to obtain a finished oil pipe with the diameter of 88.9 multiplied by 12.09 mm.
Testing the room-temperature tensile strength of the finished oil pipe obtained in the step (6) by adopting GB/T228.1-2010, and testing the V-shaped impact toughness of the finished oil pipe obtained in the step (6) by adopting GB/T229-2S+5MPa CO2+250000mg/L Cl-The high-temperature high-pressure corrosion test is carried out under the environmental conditions, the dynamic rotating speed is 300 r/min, the test time is 30 days, and the average annual corrosion rate is calculated according to the standard NACE RP0775-2005 after the test.
The room-temperature tensile strength of the finished product oil pipe subjected to the No. 5 heat treatment is 1085MPa, the yield strength is 950MPa, the elongation is 13%, and the longitudinal and transverse full-size Charpy V-shaped impact powers are 88J/cm respectively2And 49J/cm2(ii) a After argon arc welding, the tensile strength of the welding seam at room temperature is 1075MPa, the yield strength is 940MPa, the elongation is 11.0 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 80J/cm respectively2And 42J/cm2(ii) a Uniform annual corrosion rate of 2.3X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
The room-temperature tensile strength of the finished product oil pipe subjected to the 5' # heat treatment is 1090MPa, the yield strength is 975MPa, the elongation is 12 percent, and the longitudinal and transverse full-size Charpy V-shaped impact powers are respectively 92J/cm2And 52J/cm2(ii) a After argon arc welding, the tensile strength of the welding line at room temperature is 1085MPa, the yield strength is 970MPa, the elongation is 10.5 percent, and the longitudinal and transverse full-size Charpy V-shaped impact energy is 83J/cm2And 43J/cm2(ii) a Uniform annual corrosion rate of 1.8X 10-4mm/a; no pitting, stress corrosion cracking and crevice corrosion.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. The titanium alloy for oil and gas exploitation is characterized by comprising the following components in percentage by weight:
5.0 to 6.5 percent of Al, 1.6 to 2.5 percent of V, 2.6 to 4.0 percent of Zr, 1.0 to 2.0 percent of Mo, 0.9 to 1.8 percent of Cr0, 0.06 to 0.12 percent of O, and the balance of Ti and inevitable impurities.
2. The method of making a titanium alloy for oil and gas production as set forth in claim 1, comprising the steps of:
mixing alloy raw materials, and smelting to obtain a titanium alloy ingot;
and forging the titanium alloy ingot to obtain the oil-gas exploitation titanium alloy.
3. The production method according to claim 2, wherein the number of times of forging is 1 to 3 times;
when the number of times of forging is 1, the forging comprises first hot forging;
when the forging times are 2 times, the forging comprises sequentially carrying out first hot forging and second hot forging;
when the forging times are 3, the forging comprises sequentially carrying out first hot forging, second hot forging and third hot forging;
the heating temperature of the first hot forging is 1070 to 1170 ℃;
the heating temperature of the second fire forging is 1000-1050 ℃ independently;
the heating temperature of the third hot forging is 1000-1050 ℃ or T independentlyβ-(20～50)℃；TβIs the phase transition point of titanium.
4. The method of manufacturing according to claim 3, further comprising, after forging:
heating and extruding the obtained forging product to obtain a titanium alloy black skin pipe;
carrying out heat treatment on the titanium alloy black skin pipe to obtain the titanium alloy for oil and gas exploitation;
the oil-gas extraction adopts titanium alloy as a pipe.
5. The method according to claim 4, wherein the heating temperature of the heating extrusion is T when the heating temperature of the final forging of the forging is 1000 to 1170 ℃β+(20～40)℃；
When the heating temperature of the last-time forging of the forging is TβWhen the temperature is (20-50) DEG C, the heating temperature of the heating extrusion is Tβ-(20～50)℃；
The heating temperature of the last fire forging of the forging is more than or equal to the heating temperature of the heating extrusion;
the extrusion ratio of the heating extrusion is 5-8.
6. The method of manufacturing according to claim 3, further comprising, after forging:
carrying out cross piercing, hot rolling and sizing on the obtained forging product in sequence to obtain a titanium alloy black skin pipe;
carrying out heat treatment on the titanium alloy black skin pipe to obtain the titanium alloy for oil and gas exploitation;
the oil-gas extraction adopts titanium alloy as a pipe.
7. The method according to claim 6, wherein the cross-piercing is performed at a heating temperature T when the final forging of the forging is performed at 1000 to 1170 ℃β+(20～40)℃；
When the heating temperature of the last-time forging of the forging is TβAt the temperature of (20 to 50) DEG C, the heating temperature of the cross-piercing is Tβ-(20～50)℃；
The heating temperature of the last fire forging of the forging is more than or equal to the heating temperature of the cross-piercing;
the deformation amount of the cross-piercing is 50-60%.
8. The production method according to claim 6, wherein the hot rolling has a deformation amount of 55 to 65%.
9. The method according to claim 6, wherein the sizing has a deformation amount of 18 to 25%.
10. The production method according to claim 4 or 6, wherein the heat treatment includes normal annealing or double annealing;
the temperature of the common annealing is 800-1000 ℃, and the heat preservation time is 1 h;
the double annealing comprises high-temperature annealing and low-temperature annealing in sequence; the high-temperature annealing temperature is 850-930 ℃, and the heat preservation time is 1 h; the temperature of the low-temperature annealing is 480-560 ℃, and the heat preservation time is 4-8 h.
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| US4067734A (en) * | 1973-03-02 | 1978-01-10 | The Boeing Company | Titanium alloys |
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