CN115491474A - Cold rolling preparation method of GH696 high-temperature alloy strip for spring - Google Patents

Cold rolling preparation method of GH696 high-temperature alloy strip for spring Download PDF

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Publication number
CN115491474A
CN115491474A CN202211035466.6A CN202211035466A CN115491474A CN 115491474 A CN115491474 A CN 115491474A CN 202211035466 A CN202211035466 A CN 202211035466A CN 115491474 A CN115491474 A CN 115491474A
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cold rolling
percent
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equal
annealing
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肖东平
周扬
付建辉
陈琦
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Chengdu Advanced Metal Materials Industry Technology Research Institute Co Ltd
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Chengdu Advanced Metal Materials Industry Technology Research Institute Co Ltd
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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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/773—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material under reduced pressure or vacuum
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)

Abstract

The invention belongs to the technical field of high-temperature alloy strip preparation, and particularly relates to a cold rolling preparation method of a GH696 high-temperature alloy strip for springs. The method comprises the following steps: A. adopting a GH696 alloy cold-rolled sheet with the thickness of 1.2-2.0mm as a blank; B. annealing the blank by adopting a high vacuum resistance furnace; C. c, cold rolling the blank obtained in the step B by using a four-roller cold rolling mill; D. repeating the step B-C for 3-4 times; E. and D, carrying out final heat annealing treatment on the strip blank obtained in the step D by adopting a high vacuum resistance furnace, and carrying out final heat cold rolling by adopting a four-roller cold rolling mill after annealing to obtain a finished product. The strip prepared by the invention has excellent mechanical property after standard heat treatment, and the whole process of the strip adopts vacuum heat treatment, so that the surface quality of the strip is high.

Description

Cold rolling preparation method of GH696 high-temperature alloy strip for spring
Technical Field
The invention belongs to the technical field of high-temperature alloy strip preparation, and particularly relates to a cold rolling preparation method of a GH696 high-temperature alloy strip for springs.
Background
The GH696 alloy is an age hardening type high-temperature alloy taking Fe-25Ni-12Cr as a matrix. Mainly in gamma' (Ni) 3 AlTi) precipitation strengthening, and simultaneously assisted by Mo solid solution strengthening and trace B grain boundary strengthening. The alloy has high yield strength and endurance, creep strength, and good high temperature elastic properties. The method is widely applied to manufacturing fasteners, disc parts, springs and the like of turbines and compressors working for a long time below 650 ℃. Can be processed into products with various specifications such as bars, wires, plates, strips and the like. The preparation process of the GH696 alloy strip mainly comprises vacuum induction melting, vacuum consumable or electroslag remelting, forging and cogging, hot rolling, cold rolling, heat treatment and the like. For the GH696 alloy strip for the spring, the deformation and the solution treatment system in the cold rolling process have important influences on the mechanical property and the surface quality of a finished product.
The solution treatment requirement of HB5466 standard on GH696 strip is 950-1050 ℃. Research shows that when the GH696 alloy is subjected to solid solution, the gamma' phase is completely dissolved before 950 ℃; at 1000 ℃, the primary carbide strip is not fully dissolved, so that the growth of grains at the strip is hindered, and a grain strip zone with uneven thickness is formed; when the solid solution temperature exceeds 1020 ℃, the primary carbide strip is fully dissolved, and MC and M are caused 3 B 2 And eta phase partial dissolution reduces pinning effect on grain boundary, thereby causingHeat treatment of GH696 alloy [ J ] with increasing solution temperature and grain growth [ Dong Xiaofeng, ma Lingxiao]The Steel research institute, 2003,15 (07): 425-429.]. Along with the increase of the solid solution temperature, the tensile strength value at room temperature gradually increases, reaches the maximum at 1000-1020 ℃, and starts to decrease after 1050 ℃ (Zhou Jiangbo research on mechanical properties of GH696 cold-rolled sheet improvement [ J]Special Steel technology, 2014,20 (01): 36-37.]。
Li Diankui et al cold-drawn GH696 alloy wire at different cold working deformation amounts, and then subjected to aging heat treatment. The result shows that the strength of the alloy is obviously improved within the range of 30 percent along with the increase of the cold working deformation; after the deformation exceeds 30%, the strength is slowly increased; the deformation is in the range of 40-50%, and the tensile strength is slightly reduced. The increase of cold working deformation increases the internal energy of the alloy, promotes the precipitation of gamma' phase during aging, and obviously improves the strength and hardness of the alloy along with the increase of cold working deformation. However, the cold working deformation is not necessarily too large, and when the deformation is large, the internal energy of cold working increases and the precipitation-promoted γ' phase tends to grow large, and therefore the strength of the alloy tends to decrease [ Li Diankui, sun Desheng, study of GH696 iron-based age-hardened superalloy [ J ]. Shanghai Steel research, 1999 (02): 3-10 ]. The GH696 alloy strip is generally rolled by adopting a multi-roll cold rolling and roller hearth furnace intermediate annealing and acid pickling method, and has unstable mechanical property and high surface quality reject ratio of the strip. Therefore, it is necessary to develop cold rolling and solution annealing treatment process research of the GH696 alloy strip for the spring and improve the mechanical property and the surface quality of the strip.
Disclosure of Invention
The invention aims to provide a cold rolling preparation method of a GH696 high-temperature alloy strip for springs, which optimizes the deformation of each heat number of cold rolling by reasonably controlling an intermediate annealing system, and improves the mechanical property and the surface quality of the cold rolling strip.
In order to achieve the purpose, the technical scheme of the invention is as follows:
a cold rolling preparation method of a GH696 high-temperature alloy strip for springs comprises the following steps:
A. adopting a GH696 alloy cold-rolled sheet with the thickness of 1.2-2.0mm as a blank;
B. annealing the blank in a high vacuum resistance furnace at 1080-1100 deg.C for 10-20min under vacuum degree of less than 10 -3 Pa；
C. After annealing, a four-roller cold rolling mill is adopted for cold rolling treatment, and the cold rolling deformation is 20-40%;
D. repeating the step B-C for 3-4 times;
E. d, carrying out final annealing treatment on the strip blank obtained in the step D by adopting a high-vacuum resistance furnace, wherein the annealing temperature is 1020-1040 ℃, the heat preservation time is 10-20min, and the vacuum degree is less than 10 -3 And Pa, performing final hot cold rolling by using a four-roller cold rolling mill after annealing, wherein the total deformation of the final hot cold rolling is 30-35%, and thus obtaining a finished product.
In the above technical scheme, further, in the step a, the GH696 alloy comprises the following chemical components in percentage by weight: less than or equal to 0.10 percent of C, 10.0 to 12.5 percent of Cr, 21.0 to 25.0 percent of Ni, 1.00 to 1.60 percent of Mo, less than or equal to 0.80 percent of Al, 2.60 to 3.20 percent of Ti, less than or equal to 0.020 percent of B, less than or equal to 0.60 percent of Si, less than or equal to 0.60 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities.
In the above technical solution, further, the annealing cooling is performed by using argon gas to cool the substrate to room temperature.
In the above technical scheme, further, in the step C, the cold rolling is multi-pass rolling, the cold rolling deformation of each pass is less than or equal to 20%, and the tension of the rolling mill is 10-13KN.
In the above technical solution, further, in the step C, the cold rolling passes are 5 to 8.
In the above technical scheme, further, in the step E, the final hot cold rolling is multi-pass rolling, the cold rolling deformation of each pass is less than or equal to 20%, and the rolling mill tension is 10-13KN.
In the above technical solution, further, in the step E, the cold rolling pass is 5 to 8 times.
The invention has the beneficial effects that:
the invention adopts the process of vacuum annealing and cold rolling, optimizes the deformation of each heat number of cold rolling by reasonably controlling the annealing process parameters of the intermediate heat number and the finished product heat number of the cold rolling, obtains the high-temperature alloy strip with the thickness of 0.15-0.25mm, has excellent mechanical property after standard heat treatment, adopts vacuum heat treatment in the whole process of the strip, and has bright and smooth surface without an oxidation layer and other defects.
Detailed Description
The following examples are presented to enable one of ordinary skill in the art to more fully understand the present invention and are not intended to limit the invention in any way.
Example 1
A. Adopting a GH696 alloy cold-rolled sheet with the thickness of 2.0mm as a blank, wherein the GH696 alloy comprises the following chemical components in percentage by weight: less than or equal to 0.10 percent of C, 10.0 to 12.5 percent of Cr, 21.0 to 25.0 percent of Ni, 1.00 to 1.60 percent of Mo, less than or equal to 0.80 percent of Al, 2.60 to 3.20 percent of Ti, less than or equal to 0.020 percent of B, less than or equal to 0.60 percent of Si, less than or equal to 0.60 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities;
B. annealing the cold-rolled blank in a high vacuum resistance furnace at 1100 deg.C for 20min to obtain a vacuum degree of less than 10 -3 Pa, cooling to room temperature by adopting argon after heat preservation;
C. cold rolling the annealed blank by a four-roller cold rolling mill, wherein cold rolling passes are 5-8 times, the cold rolling deformation of the passes is less than or equal to 20%, and the tension of the mill is 11-13KN;
D. repeating the steps B-C3 times, wherein the cold rolling deformation scheme is as follows: δ 2.0mm → δ 1.2mm (deformation 40%) → δ 0.72mm (deformation 40%) → δ 0.50mm (deformation 30%) → δ 0.36mm (deformation 28%);
E. carrying out final annealing treatment on the strip blank with the diameter delta of 0.36mm by adopting a high vacuum resistance furnace, wherein the annealing temperature is 1040 ℃, the heat preservation time is 10min, and the vacuum degree is less than 10 -3 Pa, cooling to room temperature by adopting argon after heat preservation, and performing final hot cold rolling by adopting a four-roller cold rolling mill, wherein delta is 0.36mm → delta is 0.25mm, the total deformation is 30%, the cold rolling pass is 5-8 times, the cold rolling deformation of the pass is less than or equal to 20%, and the tension of the mill is 11-13KN.
The 0.25mm strip obtained by cold rolling in this example has a tensile strength of 1301-1310MPa and an elongation of 10-11.5% after standard heat treatment.
Example 2
A. Adopting a GH696 alloy cold-rolled sheet with the thickness of 1.2mm as a blank, wherein the GH696 alloy comprises the following chemical components in percentage by weight: less than or equal to 0.10 percent of C, 10.0 to 12.5 percent of Cr, 21.0 to 25.0 percent of Ni, 1.00 to 1.60 percent of Mo, less than or equal to 0.80 percent of Al, 2.60 to 3.20 percent of Ti, less than or equal to 0.020 percent of B, less than or equal to 0.60 percent of Si, less than or equal to 0.60 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities;
B. annealing cold-rolled blank in a high-vacuum resistance furnace at 1080 deg.C for 10min, wherein the vacuum degree is less than 10 -3 Pa, cooling to room temperature by adopting argon after heat preservation;
C. cold rolling the annealed blank by a four-roller cold rolling mill, wherein cold rolling passes are 5-8 times, the cold rolling deformation of the passes is less than or equal to 20%, and the tension of the mill is 10-11KN;
D. repeating the steps B-C3 times, wherein the cold rolling deformation scheme is as follows: δ 1.2mm → δ 0.72mm (deflection 40%) → δ 0.50mm (deflection 30%) → δ 0.36mm (deflection 28%) → δ 0.23mm (deflection 36%);
E. carrying out final annealing treatment on the strip blank with the diameter delta of 0.23mm by adopting a high vacuum resistance furnace, wherein the annealing temperature is 1020 ℃, the heat preservation time is 10min, and the vacuum degree is less than 10 -3 Pa, cooling to room temperature by adopting argon after heat preservation, and performing final hot cold rolling by adopting a four-roller cold rolling mill, wherein delta is 0.23mm → delta is 0.15mm, the total deformation is 35%, the cold rolling pass is 5-8 times, the cold rolling deformation of the pass is less than or equal to 20%, and the tension of the rolling mill is 10-11KN.
The 0.15mm strip obtained by cold rolling in this example has a tensile strength of 1324-1355MPa and an elongation of 9-9.5% after standard heat treatment.
The above examples are merely preferred embodiments of the present invention, and are not intended to limit the embodiments. The protection scope of the present invention shall be subject to the scope defined by the claims. Other variations and modifications may be made on the basis of the above description. Obvious variations or modifications of this invention are within the scope of the invention.

Claims (7)

1. A cold rolling preparation method of a GH696 high-temperature alloy strip for springs is characterized by comprising the following steps:
A. adopting a GH696 alloy cold-rolled sheet with the thickness of 1.2-2.0mm as a blank;
B. annealing the blank in a high vacuum resistance furnace at 1080-1100 deg.C for 10-20min under vacuum degree of less than 10 -3 Pa；
C. After annealing, cold rolling treatment is carried out by adopting a four-roller cold rolling mill, and the cold rolling deformation is 20-40%;
D. repeating the step B-C for 3-4 times;
E. d, carrying out final annealing treatment on the strip blank obtained in the step D by adopting a high-vacuum resistance furnace, wherein the annealing temperature is 1020-1040 ℃, the heat preservation time is 10-20min, and the vacuum degree is less than 10 -3 And Pa, performing final hot cold rolling by using a four-roller cold rolling mill after annealing, wherein the total deformation of the final hot cold rolling is 30-35%, and thus obtaining a finished product.
2. The preparation method of claim 1, wherein in the step A, the chemical compositions of the GH696 alloy in percentage by weight are as follows: less than or equal to 0.10 percent of C, 10.0 to 12.5 percent of Cr, 21.0 to 25.0 percent of Ni, 1.00 to 1.60 percent of Mo, less than or equal to 0.80 percent of Al, 2.60 to 3.20 percent of Ti, less than or equal to 0.020 percent of B, less than or equal to 0.60 percent of Si, less than or equal to 0.60 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.010 percent of S, and the balance of Fe and inevitable impurities.
3. The method of claim 1, wherein the annealing cooling is performed using argon gas to cool the wafer to room temperature.
4. The preparation method of claim 1, wherein in the step C, the cold rolling is multi-pass rolling, the cold rolling deformation of each pass is less than or equal to 20%, and the tension of the rolling mill is 10-13KN.
5. The method according to claim 4, wherein the number of cold rolling passes in step C is 5 to 8.
6. The preparation method of claim 1, wherein in the step E, the final hot cold rolling is multi-pass rolling, the cold rolling deformation of each pass is less than or equal to 20%, and the tension of the rolling mill is 10-13KN.
7. The preparation method according to claim 6, wherein in the step E, the number of cold rolling passes is 5 to 8.
CN202211035466.6A 2022-08-26 2022-08-26 Cold rolling preparation method of GH696 high-temperature alloy strip for spring Pending CN115491474A (en)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117683989A (en) * 2024-02-02 2024-03-12 成都先进金属材料产业技术研究院股份有限公司 High-temperature alloy sheet and preparation method thereof

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117683989A (en) * 2024-02-02 2024-03-12 成都先进金属材料产业技术研究院股份有限公司 High-temperature alloy sheet and preparation method thereof
CN117683989B (en) * 2024-02-02 2024-04-30 成都先进金属材料产业技术研究院股份有限公司 High-temperature alloy sheet and preparation method thereof

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