CN113560364A

CN113560364A - GH3230 alloy plate and preparation method thereof

Info

Publication number: CN113560364A
Application number: CN202110823998.5A
Authority: CN
Inventors: 魏育君; 裴丙红; 王瑞; 付建辉; 何小林; 冯旭; 罗胜江; 肖桂华; 杨磊
Original assignee: Pangang Group Jiangyou Changcheng Special Steel Co Ltd
Current assignee: Pangang Group Jiangyou Changcheng Special Steel Co Ltd
Priority date: 2021-07-21
Filing date: 2021-07-21
Publication date: 2021-10-29

Abstract

The invention provides a preparation method of a GH3230 alloy plate, which comprises the following steps: carrying out vacuum induction melting and electroslag remelting on alloy raw materials in sequence to obtain a steel ingot; forging, rolling and carrying out heat treatment on the steel ingot to obtain a GH3230 alloy plate; according to the invention, by adjusting, optimizing and improving the preparation process of the cold-rolled sheet, the surface, size and performance of the high-lanthanum-content hard-deformation high-temperature alloy sheet meet the standard and the use requirements of users, a qualified high-lanthanum-content hard-deformation high-temperature alloy cold-rolled sheet product is produced, the product quality is improved, and more economic benefits are created for enterprises. The invention also provides a GH3230 alloy plate.

Description

GH3230 alloy plate and preparation method thereof

Technical Field

The invention belongs to the technical field of alloy plates, and particularly relates to a GH3230 alloy plate and a preparation method thereof.

Background

Along with the continuous improvement of the performance of the aero-engine, the temperature and the pressure of the inlet and the temperature rise of the outlet of the combustion chamber gradually rise, and the heat radiation intensity of high-temperature fuel gas to the wall surface of the flame tube is enhanced, so that the high-temperature alloy plate used by the flame tube is a key material of the aero-engine.

In addition, the low-expansion high-temperature alloy cold-rolled sheet is a novel material for aeroengines, and the produced qualified cold-rolled sheet has very strong practical significance, contributes to national defense construction, and has remarkable social benefit.

Disclosure of Invention

In view of the above, the invention aims to provide a GH3230 alloy plate and a preparation method thereof, and the GH3230 alloy plate prepared by the method provided by the invention has better performance.

The invention provides a preparation method of a GH3230 alloy plate, which comprises the following steps:

carrying out vacuum induction melting and electroslag remelting on alloy raw materials in sequence to obtain a steel ingot;

forging, rolling and carrying out heat treatment on the steel ingot to obtain a GH3230 alloy plate;

the alloy comprises the following raw materials:

0.08-0.12 wt% of C;

21.5 to 22.5 wt% of Cr;

13.5 to 14.0 wt% of W;

2.0-2.4 wt% of Mo;

0.50-0.70 wt% Mn;

0.30-0.40 wt% of Al;

0.1-0.3 wt% of La;

0.45-0.55 wt% of Si;

less than or equal to 0.015 wt% of B;

p is less than or equal to 0.03 wt%;

less than or equal to 0.015 wt% of S;

less than or equal to 0.1 wt% of Ti;

cu of less than or equal to 0.5 wt%;

less than or equal to 3.0 wt% of Fe;

3.0-4.0 wt% of Co;

the balance being Ni.

Preferably, an electro-hydraulic hammer is adopted for cogging in the forging process;

the diameter of the steel ingot is 300-310 mm.

Preferably, the method for cogging the electro-hydraulic hammer comprises the following steps:

sequentially carrying out primary heating, octagonal beating, furnace returning and heating, chamfering, edge folding and forging thickness.

Preferably, the temperature of the primary heating is 1200-1220 ℃;

the temperature of the furnace returning and heating is 1200-1220 ℃.

Preferably, the heating temperature of the heat treatment is 1220-1230 ℃;

the cooling mode of the heat treatment is water cooling.

Preferably, the forging further comprises:

and carrying out soaking treatment on the steel ingot.

Preferably, the rolling comprises:

hot rolling is performed first and then cold rolling is performed.

Preferably, the hot rolling method comprises:

firstly carrying out rough rolling and then carrying out finish rolling;

the heating temperature of the rough rolling is 1150-1170 ℃;

the heating temperature of the finish rolling is 1100-1120 ℃.

Preferably, the cold rolling deformation is more than 25%.

The invention provides a GH3230 alloy plate prepared by the method in the technical scheme, and the alloy plate comprises the following components:

0.05 to 0.15 wt% of C;

20.0-24.0 wt% of Cr;

13.0 to 15.0 wt% of W;

1.0 to 3.0 wt% of Mo;

0.30 to 1.00 wt% Mn;

0.20 to 0.50 wt% of Al;

0.005-0.05 wt% of La;

0.25 to 0.75 wt% of Si;

less than or equal to 0.015 wt% of B;

p is less than or equal to 0.03 wt%;

less than or equal to 0.015 wt% of S;

less than or equal to 0.1 wt% of Ti;

cu of less than or equal to 0.5 wt%;

less than or equal to 3.0 wt% of Fe;

less than or equal to 5.0 wt% of Co;

the balance being Ni.

The invention adopts a process route of vacuum induction and electroslag remelting, and obtains a finished cold-rolled sheet product through forging cogging, blank hot rolling, cold rolling, multiple cold rolling, solution heat treatment and acid-base washing, thereby producing a qualified high-temperature alloy cold-rolled sheet product with high lanthanum content and difficult deformation. In the invention, GH3230 is a novel nickel-based high-temperature alloy which is subjected to solid solution strengthening by C, W, Mo, when the C content is more than 0.15 wt%, a large amount of C chemical phases are precipitated in the alloy to reduce the plasticity sharply, and the C is controlled at a lower level; when the La content is 0-0.087 wt%, the influence of the La content on the tensile plasticity of the alloy at room temperature is small, but when the La content exceeds 0.048 wt%, the yield strength of the alloy is reduced, and after the La content reaches 0.087 wt%, more La-rich phase components are separated out from the alloy, so that the oxidation resistance is reduced; the La addition amount of the alloy raw materials cannot be too low in the proportioning process, and the La element can be recovered to be 0.005-0.05 wt% after the excessively high La is subjected to vacuum smelting and electroslag burning loss. According to the invention, through adjusting, optimizing and improving the preparation process of the cold-rolled sheet, the surface, size and performance of the high-lanthanum-content hard-deformation high-temperature alloy sheet meet the standard and the use requirements of users, a qualified high-lanthanum-content hard-deformation high-temperature alloy cold-rolled sheet product is produced, the product quality is improved, and more economic benefits are created for enterprises.

Detailed Description

The technical solutions in the embodiments of the present invention will be clearly and completely described below, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments. All other examples, which may be modified or appreciated by those of ordinary skill in the art based on the examples given herein, are intended to be within the scope of the present invention. It should be understood that the embodiments of the present invention are only for illustrating the technical effects of the present invention, and are not intended to limit the scope of the present invention. In the examples, the methods used were all conventional methods unless otherwise specified.

the alloy comprises the following raw materials:

0.08-0.12 wt% of C;

21.5 to 22.5 wt% of Cr;

13.5 to 14.0 wt% of W;

2.0-2.4 wt% of Mo;

0.50-0.70 wt% Mn;

0.30-0.40 wt% of Al;

0.1-0.3 wt% of La;

0.45-0.55 wt% of Si;

less than or equal to 0.015 wt% of B;

p is less than or equal to 0.03 wt%;

less than or equal to 0.015 wt% of S;

less than or equal to 0.1 wt% of Ti;

cu of less than or equal to 0.5 wt%;

less than or equal to 3.0 wt% of Fe;

3.0-4.0 wt% of Co;

the balance being Ni.

In the invention, the components of the alloy raw material are the components of the alloy raw material after the alloy raw material is mixed, and the mass content of C in the alloy raw material is preferably 0.1%; the mass content of Cr is preferably 22%; the mass content of W is preferably 13.8%; the mass content of Mo is preferably 2.1-2.3%, more preferably 2.2%; the mass content of Mn is preferably 0.6%; the mass content of Al is preferably 0.4%; the mass content of La is preferably 0.2%; the mass content of Si is preferably 0.5%; the mass content of B is preferably 0.006-0.01, more preferably 0.007-0.009%, and most preferably 0.08%; the mass content of P is preferably 0.01-0.03%, more preferably 0.02%, and most preferably 0; the mass content of S is preferably 0.005-0.015%, more preferably 0.008-0.012%, most preferably 0.01%, most preferably 0; the mass content of Ti is preferably 0.01-0.08%, more preferably 0.02-0.06%, most preferably 0.03-0.05%, and most preferably 0; the mass content of Cu is preferably 0.1-0.5%, more preferably 0.2-0.4%, most preferably 0.3%, most preferably 0; the mass content of Fe is preferably 1-3%, more preferably 1.5-2.5%, most preferably 2%, and most preferably 0; the mass content of Co is preferably 1 to 5%, more preferably 2 to 4%, more preferably 3 to 4%, and most preferably 4%.

The invention has no special limitation on the types and sources of the alloy raw materials, and the raw materials for preparing GH3230 alloy, which are well known to those skilled in the art, can be adopted, and for example, elemental elements or alloys containing the required components can be adopted.

In the invention, GH3230 is a novel nickel-based high-temperature alloy which is subjected to solid solution strengthening by C, W, Mo, when the C content is more than 0.15 wt%, a large amount of C chemical phases are precipitated in the alloy to reduce the plasticity sharply, and the C is controlled at a lower level; when the La content is 0-0.087 wt%, the influence of the La content on the tensile plasticity of the alloy at room temperature is small, but when the La content exceeds 0.048 wt%, the yield strength of the alloy is reduced, and after the La content reaches 0.087 wt%, more La-rich phase components are separated out from the alloy, so that the oxidation resistance is reduced; therefore, the addition of La should not be too high during smelting, and about 0.2 wt% is preferred because La is burnt during vacuum smelting and electroslag.

In the invention, the steel ingot prepared by batching the alloy raw materials according to the composition ratio is qualified in composition and smooth in forging.

The invention adopts a process route of vacuum induction and electroslag remelting to obtain a steel ingot, and the cold-rolled sheet is produced by the working procedures of forging, rolling, cold rolling, solid solution, acid and alkali washing and the like. The invention adopts a process route of vacuum induction and electroslag remelting to produce the high-lanthanum-content hard-deformation high-temperature alloy GH3230(GH230) cold-rolled sheet, and particularly controls the surface, size, performance and the like of the GH3230 high-temperature alloy to produce the GH3230(GH230) alloy cold-rolled sheet with qualified components.

In the invention, the electrode is smelted by adopting a smelting process of a vacuum induction furnace, and the steel ingot is obtained by remelting the electrode with electroslag.

In the invention, the vacuum degree in the vacuum melting process is preferably less than 1 Pa; the equipment is optimized to operate normally and transmit the electric materials; in the vacuum melting process, the power is preferably adjusted according to the conditions in the furnace; in the vacuum melting process, preferably, sampling and analyzing all elements after Al, B-Fe and Si are added, and then adjusting chemical components as required; and preferably, before adding La, electrolytic Mn and Ni-Mg in the vacuum melting process, adjusting the temperature and filling argon.

In the invention, after the vacuum melting is finished, casting is preferably carried out to obtain the electrode rod.

In the present invention, the ingot mold used in the casting process is preferably scalded with molten steel, clean and rust-free.

In the present invention, the casting is preferably performed under vacuum.

In the invention, the setting range of the pressure pendulum in the electroslag remelting process is preferably 5.0-4.0V, more preferably 4.8-4.2V, and most preferably 4.6-4.4V; the melting speed is preferably 4.0-3.5 kg/min, more preferably 3.6-3.8 kg/min, and most preferably 3.7 kg/min; in the electroslag remelting process, the whole Ar gas flow is preferably 40-80L/min, more preferably 50-70L/min, and most preferably 60L/min; the water temperature is preferably controlled to be 45-60 ℃, more preferably 50-55 ℃, and most preferably 52-53 ℃; the bottom pad and the arc striking agent are preferably made of the steel (GH2130 alloy).

In the present invention, the forging preferably further comprises:

and carrying out homogenization heat treatment on the steel ingot.

In the present invention, the method of homogenizing heat treatment preferably includes:

raising the temperature to 1170-1190 ℃ at the temperature lower than 700 ℃ and preserving the temperature.

In the invention, the temperature rise time is preferably not less than 3 hours, preferably to 1175-1185 ℃, and more preferably to 1180 ℃; the heat preservation time is preferably 45 to 55 hours, more preferably 46 to 50 hours, and most preferably 48 hours.

In the present invention, the forging is preferably cogging forging, and preferably multiple forging is employed.

In the invention, the diameter of the steel ingot is preferably 300-310 mm, more preferably 303-307 mm, and most preferably 305 mm.

In the invention, the heating temperature in the casting process is preferably 1200-1220 ℃, more preferably 1205-1215 ℃, and most preferably 1210 ℃.

In the invention, the forging process is preferably performed by using an electro-hydraulic hammer.

In the present invention, the method for cogging the electro-hydraulic hammer preferably includes:

In the present invention, it is preferable that the step of returning and heating to the forging thickness is repeated in the process of cogging the electro-hydraulic hammer.

In the present invention, the method of the primary heating process preferably includes:

heating to 1200-1220 deg.C below 700 deg.C, and maintaining the temperature.

In the invention, the heating time is preferably not less than 3 hours, the heating temperature is preferably 1205-1215 ℃, and most preferably 1210 ℃; the heat preservation time is preferably 4-5 hours, and more preferably 4.5 hours.

In the invention, the octagonal hammering is that the flat anvil forging hammer bar is octagonal.

In the invention, the remelting heating is that the remelting heating is needed after the forging temperature is lower.

In the invention, the temperature of the annealing heating is preferably 1200-1220 ℃, more preferably 1205-1215 ℃, and most preferably 1210 ℃; the time of the furnace returning and heating is preferably 0.8-1.2 hours, and most preferably 1 hour.

In the invention, the chamfering is to forge the material edge angle to a flat angle by using a flat anvil.

In the invention, the edge closing is to beat the material by using a flat anvil to deform the material in the Y direction.

In the invention, the forging thickness is the deformation of the forging hammer along the Z direction along the main deformation direction.

In the invention, the GH3230 alloy is easy to crack in the forging process, the method provided by the invention directly cracks a consumable ingot with the diameter of 305mm by using an electro-hydraulic hammer, a press is not used for cogging, the electro-hydraulic hammer adopts a unique hammering method, the steel ingot can be prevented from cracking, namely, the method of repeatedly heating, chamfering, edge folding and forging the thickness by multiple fire times is adopted, the tedious work of sheathing for cogging of the press is reduced, and the cogging can be finished with quality and quantity conservation.

In the present invention, the rolling preferably includes, before:

and cleaning the surface of the forged plate blank and then rolling.

In the present invention, the rolling includes:

hot rolling is performed first and then cold rolling is performed.

In the present invention, the hot rolling method preferably includes:

firstly carrying out rough rolling and then carrying out finish rolling.

In the invention, the rough rolling heating temperature in the hot rolling process is preferably 1150-1170 ℃, more preferably 1155-1170 ℃, and most preferably 1170 ℃; the finish rolling heating temperature is preferably 1100-1120 ℃, more preferably 1105-1115 ℃, and most preferably 1110 ℃; the final rolling temperature is preferably more than 950 ℃, more preferably more than 1000 ℃, the rolling rhythm is compact, and the final rolling temperature is higher than the best; the maximum deformation of the pass is preferably less than or equal to 25%, more preferably 22-25%, and most preferably 23-24%; one-time large deformation in the rolling process can ensure uniform grain size.

In the invention, the heating time in the hot rolling process is preferably 1.5min/mm + 3-5 min; namely, hot rolling time is set according to the thickness of a required product, the heating time per millimeter is 1.5min, and the thorough burning time is 3-5 min.

In the invention, the deformation of the semi-finished product in one rolling process in the cold rolling process is preferably 30-35%, more preferably 31-34%, and most preferably 32-33%, the semi-finished product in the cold rolling process refers to a blank between multiple cold rolling, such as a primary cold rolling semi-finished product and a secondary cold rolling semi-finished product, and when the high-temperature alloy is subjected to cold rolling, multiple cold rolling is generally performed according to the rolling process; the deformation of the finished product (the finished product obtained in the last rolling process) in the cold rolling process is preferably more than 25 percent, more preferably 27-28 percent, after the thickness is reduced, the deformation is more difficult, but the deformation rate needs to be kept more than 25 percent, and the grain size mixed crystal of the finished product caused by small deformation is avoided.

In the invention, the deformation rate of each rolling process is preferably controlled in the cold rolling process, large deformation is favorable for fully crushing the tissue, but due to material limitation, excessively high deformation rate is unrealistic, the deformation rate of a semi-finished product in the rolling process is preferably kept above 30%, and the deformation rate of the last rolling process is more than 25%.

In the present invention, the heat treatment is preferably performed in a roller hearth furnace. In the invention, the heating temperature in the heat treatment process is preferably 1220-1230 ℃, more preferably 1222-1228 ℃, more preferably 1224-1226 ℃, and most preferably 1225 ℃; the cooling mode in the heat treatment process is preferably water cooling, and the GH3230 alloy plate prepared by the method has better performance; the time of the heat treatment is preferably 1.5min/mm + 3-5 min, namely the heating time is set according to the thickness of a required product, the heating time per millimeter is 1.5min, and the thorough-heating time is 3-5 min.

In the invention, the heat treatment enables the plate to be subjected to solution treatment in the continuous heat treatment furnace, so that the crystal grains are fully recrystallized, and the purposes of uniform grain size and standard mechanical property of the finished product are achieved.

In the invention, GH3230 is aging strengthening high-temperature alloy, the cold rolling deformation is difficult, and in order to achieve the purpose of reducing GH3230 strengthening, semi-finished products and finished products need to use a water cooling mode after solid solution, so that a large amount of strengthening phases are prevented from being separated out, and the cold rolling can be finished; the heating temperature of the heat treatment is preferably 1220-1230 ℃, and a water cooling mode is adopted to avoid overhigh strength which exceeds a standard range.

In the present invention, it is preferable that the heat treatment further comprises:

and (4) carrying out acid-base washing, leveling and straightening on the heat-treated product to obtain the GH3230 alloy plate.

The method of acid/base washing, leveling and straightening is not particularly limited in the present invention, and a method of acid/base washing well known to those skilled in the art may be used.

In the present invention, after the straightening is completed, the straightening preferably further includes:

and shearing, sampling, inspecting and packaging the product subjected to value correction and warehousing after the product is qualified in flaw detection.

The invention also provides a GH3230 alloy plate prepared by the method in the technical scheme. In the invention, the alloy plate comprises the following components:

0.05 to 0.15 wt% of C;

20.0-24.0 wt% of Cr;

13.0 to 15.0 wt% of W;

1.0 to 3.0 wt% of Mo;

0.30 to 1.00 wt% Mn;

0.20 to 0.50 wt% of Al;

0.005-0.05 wt% of La;

0.25 to 0.75 wt% of Si;

less than or equal to 0.015 wt% of B;

p is less than or equal to 0.03 wt%;

less than or equal to 0.015 wt% of S;

less than or equal to 0.1 wt% of Ti;

cu of less than or equal to 0.5 wt%;

less than or equal to 3.0 wt% of Fe;

less than or equal to 5.0 wt% of Co;

the balance being Ni.

In the invention, the mass content of C is preferably 0.08-0.12%, and more preferably 0.1%; the mass content of the Cr is preferably 21-23%, and more preferably 22%; the mass content of W is preferably 13.5-14.5%, and more preferably 14%; the mass content of Mo is preferably 1.5-2.5%, and more preferably 2%; the mass content of Mn is preferably 0.4-0.9%, more preferably 0.5-0.8%, and most preferably 0.6-0.7%; the mass content of the Al is preferably 0.3-0.4%; the mass content of the La is preferably 0.01-0.04%, and more preferably 0.02-0.03%; the mass content of Si is preferably 0.3-0.7%, more preferably 0.4-0.6%, and most preferably 0.5%; the mass content of B is preferably 0.005-0.012%, more preferably 0.008-0.01%; the mass content of P is preferably 0.01-0.03%, and more preferably 0.02%; the mass content of S is preferably 0.005-0.012%, more preferably 0.008-0.01%; the mass content of Ti is preferably 0.03-0.07%, and more preferably 0.05%; the mass content of Cu is preferably 0.1-0.5%, more preferably 0.2-0.4%, and most preferably 0.3%; the mass content of the Fe is preferably 1-3%, more preferably 1.5-2.5%, and most preferably 2%; the mass content of Co is preferably 1 to 5%, more preferably 2 to 4%, and most preferably 3%.

In the invention, the thickness of the GH3230 alloy plate is preferably 0.6-3 mm, more preferably 1-2.5 mm, and most preferably 1.5-2 mm.

Example 1

A GH3230 alloy sheet having a thickness of 1.2mm was prepared by the following method:

forging, rolling, heat treating, acid and alkali washing, leveling and straightening the steel ingot to obtain a GH3230 alloy plate;

the alloy raw materials are mixed according to the following table:

element(s)

C

Cr

W

Mo

Mn

Al

La

Si

Is prepared into

0.10wt％

22.0wt％

13.8wt％

2.2wt％

0.60wt％

0.40wt％

0.2wt％

0.50wt％

Element(s)

B

P

S

Ti

Cu

Fe

Co

Ni

Is prepared into

0.008wt％

/

4.0wt％

Balance of

In the vacuum induction smelting process, the vacuum degree of the vacuum induction furnace is less than 1Pa, and the equipment can be used for conveying the electric materials when running normally; during melting, the power can be adjusted at any time according to the conditions in the furnace, the whole elements are sampled and analyzed after Al, B-Fe and Si are added, the chemical components are adjusted according to the optimal requirements, and proper temperature adjustment and argon filling are needed before La, Mn and Ni-Mg are electrolyzed;

pouring after vacuum melting: the ingot mould of the electrode bar needs to be scalded by molten steel, cleaned and rustless; pouring is carried out under vacuum, and pouring speed and filling quality are controlled during pouring;

the pressing pendulum in the electroslag remelting process is set in a range: 5.0-4.0V; setting the melting speed to be 4.0-3.5 kg/min; full range of Ar gas flow: 40-80L/min; controlling water temperature: 45-60 ℃; the bottom pad and the arc striking agent are both made of the steel (GH3230 alloy);

the forging process comprises the following steps: sequentially carrying out primary heating, octagonal beating, furnace returning and heating, chamfering, edge folding and forging thickness; the primary heating comprises the following steps: heating to a temperature of less than 700 ℃, keeping the temperature for 48 hours when the temperature is more than or equal to 3 hours and 1180 +/-10 ℃, discharging and forging; the heating temperature in the forging process is 1200-1220 ℃, the heating temperature after remelting is 1200-1220 ℃, the heating time is about 1h, and the processes of remelting, heating, chamfering, edge folding and forging thickness are repeatedly carried out in the forging process until the forging is carried out to the required size;

the rolling is hot rolling and then cold rolling;

the hot rolling is firstly rough rolling and then finish rolling; the heating temperature of rough rolling is 1150-1170 ℃, the heating temperature of finish rolling is 1100-1120 ℃, and the finishing temperature is more than 1000 ℃; the pass deformation is 22-25%; the heating time is 1.5min/mm + 3-5 min; the large deformation is ensured once in the rolling process, and the uniform grain size can be ensured; the hot rolling process was carried out from a billet having a thickness of 28mm to a semi-finished product having a thickness of 2.5mm for a total of 6 passes (1 pass of rough rolling and 5 passes of finish rolling).

The deformation of each rolling process of the semi-finished product in the cold rolling process is 30-35%, and grain size mixed crystals of the finished product caused by small deformation are avoided; the rolling deformation of the finished product is 27-28%; in the cold rolling process, 4 rolling passes are carried out from the semi-finished product with the thickness of 2.5mm to the cold-rolled sheet with the thickness of 0.8mm, wherein the rolling passes are respectively 2.5mm-1.90mm-1.42mm-1.07mm-0.8 mm.

The heating temperature in the heat treatment process is 1120-1230 ℃, the cooling mode is water cooling, and the heating time is 1.5min/mm + 3-5 min, so that the plate has better performance.

The product prepared in the embodiment 1 of the invention is subjected to component and performance detection according to the following methods, GB/T223 chemical analysis method for steel and alloy, GB/T228 room temperature tensile test method for metal materials, GB/T232 bending test method for metal materials, GB/T6394 average grain size assessment method for metal, GB/T6395 high temperature tensile endurance test method for metal; the detection result is as follows:

the components of the electrode bar obtained by pouring after vacuum induction melting are as follows:

the steel ingot obtained after electroslag remelting comprises the following components:

element(s)

C

Cr

W

Mo

Mn

Al

La

Si

0.088wt％

0.017wt％

Element(s)

B

P

S

Ti

Cu

Fe

Co

Ni

/

0.012

/

Balance of

Note: after electroslag remelting, the contents of Cr, W, Mo, Mn, Al, Si, B and Co are not detected, and the contents of the elements are consistent with the contents of the elements in the electrode bar.

The performance test results of the prepared finished plate are as follows:

example 2

GH3230 alloy plates having a thickness of 2.0mm were prepared as follows:

the alloy raw materials are mixed according to the following table:

element(s)

C

Cr

W

Mo

Mn

Al

La

Si

Is prepared into

0.10wt％

22.0wt％

13.8wt％

2.2wt％

0.60wt％

0.40wt％

0.2wt％

0.50wt％

Element(s)

B

P

S

Ti

Cu

Fe

Co

Ni

Is prepared into

0.008wt％

/

4.0wt％

Balance of

the pressing and arranging range in the electroslag remelting process is as follows: 5.0-4.0V; setting the melting speed: 4.0-3.5 kg/min; full range of Ar gas flow: 40-80L/min; controlling water temperature: 45-60 ℃; the steel (GH3230 alloy) is used as the base pad and the arc striking agent.

the rolling is hot rolling and then cold rolling;

the hot rolling is firstly rough rolling and then finish rolling; the heating temperature of rough rolling is 1150-1170 ℃, the heating temperature of finish rolling is 1100-1120 ℃, and the finishing temperature is more than 1000 ℃; the pass deformation is 22-25%; the heating time is 1.5min/mm + 3-5 min; the large deformation is ensured once in the rolling process, and the uniform grain size can be ensured; the hot rolling was carried out from a billet having a thickness of 28mm to a semi-finished product having a thickness of 3.6mm for a total of 4 passes (1 pass of rough rolling and 3 passes of finish rolling).

The deformation of each rolling process of the semi-finished product in the cold rolling process is 30-35%, and grain size mixed crystals of the finished product caused by small deformation are avoided; the rolling deformation of the finished product is 27-28%; in the cold rolling process, 2 rolling passes are performed from the semi-finished product with the thickness of 3.6mm to the cold-rolled sheet with the thickness of 0.8mm, and the rolling passes are respectively 3.6mm-2.7mm-2.0 mm.

The product prepared in example 2 of the present invention was tested for components and properties according to the method described in example 1, and the test results were:

element(s)

C

Cr

W

Mo

Mn

Al

La

Si

0.085wt％

0.02wt％

Element(s)

B

P

S

Ti

Cu

Fe

Co

Ni

/

0.011

/

Balance of

The performance test results of the prepared finished plate are as follows:

according to the embodiments, the process route of vacuum induction and electroslag remelting is adopted, and a cold-rolled sheet finished product is obtained through forging cogging, blank hot rolling and cold rolling, multiple cold rolling, solution heat treatment and acid-base washing, so that a qualified high-lanthanum-content hard-deformation high-temperature alloy cold-rolled sheet product is produced. In the invention, GH3230 is a novel nickel-based high-temperature alloy which is subjected to solid solution strengthening by C, W, Mo, when the C content is more than 0.15 wt%, a large amount of C chemical phases are precipitated in the alloy to reduce the plasticity sharply, and the C is controlled at a lower level; when the La content is 0-0.087 wt%, the influence of the La content on the tensile plasticity of the alloy at room temperature is small, but when the La content exceeds 0.048 wt%, the yield strength of the alloy is reduced, and after the La content reaches 0.087 wt%, more La-rich phase components are separated out from the alloy, so that the oxidation resistance is reduced; the La addition amount of the alloy raw materials cannot be too low in the proportioning process, and the La element can be recovered to be 0.005-0.05 wt% after the excessively high La is subjected to vacuum smelting and electroslag burning loss. According to the invention, through adjusting, optimizing and improving the preparation process of the cold-rolled sheet, the surface, size and performance of the high-lanthanum-content hard-deformation high-temperature alloy sheet meet the standard and the use requirements of users, a qualified high-lanthanum-content hard-deformation high-temperature alloy cold-rolled sheet product is produced, the product quality is improved, and more economic benefits are created for enterprises.

While only the preferred embodiments of the present invention have been shown and described, it will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention.

Claims

1. A preparation method of a GH3230 alloy sheet material comprises the following steps:

the alloy comprises the following raw materials:

0.08-0.12 wt% of C;

21.5 to 22.5 wt% of Cr;

13.5 to 14.0 wt% of W;

2.0-2.4 wt% of Mo;

0.50-0.70 wt% Mn;

0.30-0.40 wt% of Al;

0.1-0.3 wt% of La;

0.45-0.55 wt% of Si;

less than or equal to 0.015 wt% of B;

p is less than or equal to 0.03 wt%;

less than or equal to 0.015 wt% of S;

less than or equal to 0.1 wt% of Ti;

cu of less than or equal to 0.5 wt%;

less than or equal to 3.0 wt% of Fe;

3.0-4.0 wt% of Co;

the balance being Ni.

2. The method of claim 1, wherein the forging is performed using an electro-hydraulic hammer for cogging;

the diameter of the steel ingot is 300-310 mm.

3. The method of claim 2, wherein the method of electro-hydraulic hammer cogging comprises:

4. The method according to claim 3, wherein the temperature of the primary heating is 1200 to 1220 ℃;

the temperature of the furnace returning and heating is 1200-1220 ℃.

5. The method according to claim 1, wherein the heating temperature of the heat treatment is 1220 to 1230 ℃;

the cooling mode of the heat treatment is water cooling.

6. The method of claim 1, further comprising, prior to the forging:

and carrying out soaking treatment on the steel ingot.

7. The method of claim 1, wherein the rolling comprises:

hot rolling is performed first and then cold rolling is performed.

8. The method of claim 7, wherein the method of hot rolling comprises:

firstly carrying out rough rolling and then carrying out finish rolling;

the heating temperature of the rough rolling is 1150-1170 ℃;

the heating temperature of the finish rolling is 1100-1120 ℃.

9. The method of claim 7, wherein the cold rolling has a deformation of > 25%.

10. A GH3230 alloy sheet prepared by the method of claim 1, having the composition:

0.05 to 0.15 wt% of C;

20.0-24.0 wt% of Cr;

13.0 to 15.0 wt% of W;

1.0 to 3.0 wt% of Mo;

0.30 to 1.00 wt% Mn;

0.20 to 0.50 wt% of Al;

0.005-0.05 wt% of La;

0.25 to 0.75 wt% of Si;

less than or equal to 0.015 wt% of B;

p is less than or equal to 0.03 wt%;

less than or equal to 0.015 wt% of S;

less than or equal to 0.1 wt% of Ti;

cu of less than or equal to 0.5 wt%;

less than or equal to 3.0 wt% of Fe;

less than or equal to 5.0 wt% of Co;

the balance being Ni.