CN103498075A - Preparation method of deformation-resistant high-temperature alloy and deformation-resistant high-temperature alloy part - Google Patents
Preparation method of deformation-resistant high-temperature alloy and deformation-resistant high-temperature alloy part Download PDFInfo
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Abstract
The invention provides a deformation-resistant high-temperature alloy and a preparation method thereof. With the preparation method, quality of a deformation-resistant high-temperature alloy ingot is improved, thermo-plasticity of the deformation-resistant high-temperature alloy is improved, and cracking during a forging thermal processing process is prevented. The deformation-resistant high-temperature alloy comprises the contents of, by weight: no less than 0% and no more than 0.1% of C, no less than 16.5% and no more than 19.5% of Cr, no less than 13.5% and no more than 16.0% of Co, no less than 1.0% and no more than 2.0% of W, no less than 2.5% and no more than 3.5% of Mo, no less than 2.0% and no more than 3.0% of Al, no less than 4.5% and no more than 5.5% of Ti, no less than 0% and no more than 1.0% of Fe, no less than 0.01% and no more than 0.03% of B, no less than 0% and no more than 0.06% of Zr, no less than 0% and no more than 0.002% of S, no less than 0% and no more than 0.15% of Si, no less than 0% and no more than 0.15% of Mn, and balance of Ni and inevitable impurities.
Description
Technical field
The present invention relates to the alloy smelting field, specifically, the preparation method who relates to a kind of difficult wrought superalloy and a kind of difficult wrought superalloy part, this preparation method can improve the quality of difficult wrought superalloy part, the thermoplasticity of improving difficult wrought superalloy part and prevention and forge the cracking in hot procedure.
Background technology
When the difficult wrought superalloy part of preparation, specifically, in the forging hot procedure of difficult wrought superalloy part, resistance to deformation is large, and the texturing temperature interval is narrow, hot-workability is poor, easy cracking in the thermal processing distortion process, need to increase the polishing number of times and the hot-work fire just can be become a useful person, thus reduced difficult wrought superalloy part lumber recovery, increased energy consumption and labour cost, even cause scrapping of whole steel ingot or blank, cause huge financial loss.
Summary of the invention
For the deficiencies in the prior art, one of purpose of the present invention is to solve in above-mentioned prior art the one or more problems that exist.
The object of the invention is to improve difficult wrought superalloy clarity, improve ingot quality by optimizing smelting, casting process parameters and ingot shape, thereby improve difficult wrought superalloy thermoplasticity, and be incubated treatment process in forging hot procedure, adopt arc anvil (or V-type anvil) draw out technique and the prevention of die forging jumping-up moulding process to forge the hot procedure cracking, to reduce production costs and to improve lumber recovery, prepare qualified product.
According to an aspect of the present invention, a kind of difficult wrought superalloy is provided, the composition of described difficult wrought superalloy is by weight percentage: 0%≤C≤0.1%, 16.5%≤Cr≤19.5%, 13.5%≤Co≤16.0%, 1.0%≤W≤2.0%, 2.5%≤Mo≤3.5%, 2.0%≤Al≤3.0%, 4.5%≤Ti≤5.5%, 0%≤Fe≤1.0%, 0.01%≤B≤0.03%, 0%≤Zr≤0.06%, 0%≤S≤0.002%, 0%≤Si≤0.15%, 0%≤Mn≤0.15%, surplus is Ni and other inevitable impurity.
The composition of described difficult wrought superalloy is by weight percentage: C is that 0.075%, Cr is that 18.0%, Co is that 15.0%, W is that 1.5%, Mo is that 3.0%, Al is that 2.5%, Ti is that 5%, B is that 0.02%, Zr is 0.04%, and surplus is Ni and other inevitable impurity.
According to an aspect of the present invention, provide a kind of described method of preparation method of difficult wrought superalloy part to comprise the steps: (a) melting, melting obtains the alloy of following composition: 0%≤C≤0.1%, 16.5%≤Cr≤19.5%, 13.5%≤Co≤16.0%, 1.0%≤W≤2.0%, 2.5%≤Mo≤3.5%, 2.0%≤Al≤3.0%, 4.5%≤Ti≤5.5%, 0%≤Fe≤1.0%, 0.01%≤B≤0.03%, 0%≤Zr≤0.06%, 0%≤S≤0.002%, 0%≤Si≤0.15%, 0%≤Mn≤0.15%, surplus is Ni and other inevitable impurity; (b) casting, adopt the top teeming process casting; (c) remelting, melting voltage is 22V-30V, the melting electric current is that 2000A-3000A, molten drop speed are drip/s of 3/s-6, and adopts water-cooled and the type of cooling of filling helium gas cooling and combining, and with helium pressure, is that the 100Pa-200Pa explained hereafter goes out the remelting steel ingot; (d) hot-work is forged: before forging after Heating Steel Ingots is come out of the stove, the insulation treatment process is set, described insulation treatment process for sprinkling one deck glass powder on the pure aluminium silicate insulating cotton, after making surface of steel ingot bonding one deck pure aluminium silicate insulating cotton be incubated processing, adopt, without tensile stress arc anvil, steel ingot is carried out to draw out.
Melting step in described preparation method comprises the charging by batches step, in the charging by batches step of described melting, except 1/3 Al, Ti of 1/3 C of easy scaling loss pantogen material C piece weight and starting material Al bar weight and micro alloying element B, Zr raw material, time shove charge of other element raw material homogeneous, with the stove unslaked lime of packing into, after the desulfurization removing nitric deoxygenation refining completes, add 1/3 Al, Ti of 1/3 C of easy scaling loss pantogen material C piece weight and starting material Al bar weight, tap and within first 5 minutes, add B, Zr raw material.
Ingot shape in casting step process in described preparation method is
The ingot mould used in casting step process in described preparation method scalded with molten steel, and top adds hot topping, and sprue gate and insulated feeder distance are less than 300mm, keep molten steel to become under plume.
Reflow step in described preparation method obtains
the remelting steel ingot.
Hot-work forging step in described preparation method comprises to be processed rear and carries out carrying out many fiery inferior repetitions without the step of tensile stress arc anvil draw out being incubated.
After described preparation method also has been included in the hot-work forging, by the steel ingot draw out extremely
2mm, the line cutting is removed steel ingot end to end and segmentation, obtains
blank, with R=20mm car chamfering, after described insulation treatment process, adopt the swage collar pier thick, obtain
the blank of 2mm * 100 ± 2mm, be of a size of after preparing machining
the little diskware of difficult wrought superalloy.
The accompanying drawing explanation
Fig. 1 is the vacuum induction melting graphic representation according to the embodiment of the present invention.
Embodiment
Below, describe embodiments of the invention in detail with reference to concrete example.
Exemplary embodiment of the present invention provides a kind of difficult wrought superalloy.The composition of this difficulty wrought superalloy is by weight percentage: 0%≤C≤0.1%, 16.5%≤Cr≤19.5%, 13.5%≤Co≤16.0%, 1.0%≤W≤2.0%, 2.5%≤Mo≤3.5%, 2.0%≤Al≤3.0%, 4.5%≤Ti≤5.5%, 0%≤Fe≤1.0%, 0.01%≤B≤0.03%, 0%≤Zr≤0.06%, 0%≤S≤0.002%, 0%≤Si≤0.15%, 0%≤Mn≤0.15%, surplus is Ni and other inevitable impurity.
Preferably, the composition of difficult wrought superalloy of the present invention is by weight percentage: C is that 0.075%, Cr is that 18.0%, Co is 15.0%, W is that 1.5%, Mo is that 3.0%, Al is that 2.5%, Ti is 5%, B is that 0.02%, Zr is 0.04%, and surplus is Ni and other inevitable impurity.
Difficult wrought superalloy of the present invention is the nickel base superalloy of the difficulty distortion of a kind of high A1, Ti content, there is good tensile strength, high temperature resistant persistence and resistance to fatigue, particularly there is high strength, oxidation-resistance and structure stability more than 900 ℃, be mainly used to manufacture high thrust-weight ratio, high-efficiency engine turbine diskware, also can be used to manufacture whole gas turbine rotor, working temperature can reach 980 ℃.Because the alloying level of difficult wrought superalloy is high, especially its A1 and Ti content summation can be up to 7.5%, and the γ ' phase content of formation reaches 45% left and right, and this causes the easy component segregation of difficult wrought superalloy and thermal processing distortion difficulty, easy to crack.
The present invention also provides a kind of preparation method of difficult wrought superalloy part, and this preparation method comprises melting, casting, remelting and hot-work forging.
At first, melting obtains the alloy of following composition: 0%≤C≤0.1%, 16.5%≤Cr≤19.5%, 13.5%≤Co≤16.0%, 1.0%≤W≤2.0%, 2.5%≤Mo≤3.5%, 2.0%≤Al≤3.0%, 4.5%≤Ti≤5.5%, 0%≤Fe≤1.0%, 0.01%≤B≤0.03%, 0%≤Zr≤0.06%, 0%≤S≤0.002%, 0%≤Si≤0.15%, 0%≤Mn≤0.15%, surplus is Ni and other inevitable impurity.
Preferably, the electrode melting type of furnace adopted in fusion process can be 3000 pounds of vacuum induction furnaces, selected high-quality high pure metal starting material when vacuum induction melting, and purpose is to reduce the harmful element content that starting material are brought into.
Preferably, at when filling with substance in smelting furnace, except 1/3 Al(of 1/3 C of easy scaling loss pantogen material C piece weight and starting material Al bar weight hereinafter to be referred as 1/3C and 1/3Al), Ti and micro alloying element (B, Zr etc.) raw material, time shove charge of other element raw material homogeneous, with the stove unslaked lime of packing into, and press tight loose principle charging, prevent from building bridge in fusion process.Give the electrification material when reach≤1Pa of suction, and adopt the low power material.After starting material fusing fully, carry out the great-power electromagnetic stirring, 1520 ℃ of-1540 ℃ of high temperature desulfurizings, extend soaking time, to reach the purpose of denitrogenation deoxidation.In the melting later stage, after the desulfurization removing nitric deoxygenation refining completes, add easy scaling loss element 1/3C, 1/3Al, Ti, tap and within first 5 minutes, add micro alloying element (B, Zr etc.) raw material, specifically see Fig. 1.
Specifically, from the vacuum induction melting process curve shown in Fig. 1, can find out, add in batches raw material, and low power step type ground heats up in fusion process.Specifically, the power in minute some stages raises temperature, temperature insulation for some time of every rising, for example, and insulation 20min, this can make alloy raw material material well under low power, in the situation that do not increase cost, improves smelting quality.
In the charging by batches step of described melting, except easy scaling loss element 1/3C, 1/3Al, Ti and the raw materials such as micro alloying element B, Zr, time shove charge of other element raw material homogeneous, with the stove unslaked lime of packing into, temperature is increased to smelting temperature subsequently, treats that raw material carries out refining after all melting under the superpower of about 300KW.
Specifically, as shown in fig. 1, complete the refining of desulfurization removing nitric deoxidation under 1520 ℃-1540 ℃.In the melting later stage, add easy scaling loss element 1/3C, extend soaking time, be incubated 60 minutes subsequently under the power condition of 150 ± 5KW, conjunctiva subsequently for the first time has a power failure, under the power condition of 150 ± 5KW, insulation is 60 minutes, purpose is deoxidation, denitrogenation, and raising steel clarity at night, reach the purpose of refining, the conjunctiva that has a power failure for the first time is because the Al in the subsequent smelting operation, Ti adds the process of the heat release that is a fierceness, power failure conjunctiva purpose is to allow temperature lower, make Al, Ti adds fashionable, reduce its fierce degree, prevent splash and excess Temperature, cause follow-up smelting operation temperature to control difficulty.Have a power failure conjunctiva for the first time after the past period, continue to heat up, under 1520 ℃-1540 ℃, add 1/3Al, Ti element, be incubated 5 minutes, after insulation under the power condition of the 150 ± 5KW of 20 minutes, temperature adjustment subsequently for the second time has a power failure subsequently.Under the power condition of the 150 ± 5KW of 20 minutes, the impurity elements such as oxygen, nitrogen can be further sloughed in insulation, improve the molten steel purity, the temperature adjustment that has a power failure for the second time is to prepare for the temperature of subsequent operations tapping, and then the adjustment molten steel temperature is that follow-up charged tapping creates conditions.After this, applying argon gas, after treating that argon gas reaches 26665Pa, prepare tapping, within first 5 minutes, adds B, Zr raw material in tapping, charged tapping at the temperature of 1400 ℃-1430 ℃.
Preferably, the parameter adopted according to the casting process of the optimization of the embodiment of the present invention can be as follows: ingot shape is
the top teeming process cast; Ingot mould must scald with molten steel, and clean rustless, top adds hot topping; Cast in charged tapping under vacuum, pouring gate and insulated feeder distance are less than 300mm, keep molten steel to become under plume, control casting rate and filling quality; Casting rear mold cool time need be greater than 1h.
So far, exemplary embodiment according to the present invention by optimizing melting, that the casting process parameter obtains the low high clarity of nitrogen hypoxemia of low-sulfur is the second best in quality
electrode bar.
Electrode bar needs polishing, while optionally being necessary, can carry out carrying out vacuum arc remelting after surperficial car light and the appropriate filled end of excision.According to the present invention, can adopt the vacuum arc remelting furnace that model is VAR660P7Ti.
The method of polishing and car light can be used those skilled in the art's technique means commonly used, as long as can meet the demand to the quality of steel.
Preferably, controlling melting voltage in the vacuum arc remelting process is that 22V-30V, melting electric current are that 2000A-3000A, molten drop speed are drip/s of 3/s-6, and adopt water-cooled and fill the type of cooling that helium gas cooling combines and carry out cooling, wherein, helium pressure is 100Pa-200Pa, produces the second best in quality of the tiny and low component segregation of original structure crystal grain after remelting
the vacuum arc remelting steel ingot.
Subsequently, steel ingot is of a size of after pulling out skin
left and right, carry out the thermal treatment of 1150 ℃ * 40h homogenizing and make ingot composition further even, reduces microsegregation.
In ensuing hot-work forging process, before can adopting 2000 tons of fast forging forging equipments to forge after Heating Steel Ingots is come out of the stove, sprinkle the glass powder that one deck fusing point is 1000 ℃ of left and right on the pure aluminium silicate insulating cotton, make surface of steel ingot bonding one deck pure aluminium silicate insulating cotton be incubated processing, to slow down the radiating rate of steel ingot, make resting in the temperature range that is applicable to the hot-work forging deformation of steel ingot energy long period, insulation increases every fire time deflection, and employing is carried out draw out without tensile stress arc anvil (or V-type anvil) to steel ingot, the prevention surface cracking.Many fire, draw out extremely to repeat after insulation is processed to there is no tensile stress arc anvil (or V-type anvil)
left and right.Then line cutting remove steel ingot end to end and segmentation (
± 2mm), after car chamfering (R=20mm), insulation process (the same), adopt the swage collar pier thick (
± 2mm * 100 ± 2mm), improve difficult wrought superalloy thermoplasticity and prevention hot procedure cracking, prepare qualified product, size after machining
According to the preparation method of the embodiment of the present invention by forging hot procedure, being incubated treatment process, adopt arc anvil (or V-type anvil) draw out technique and the prevention of die forging jumping-up moulding process to forge the cracking in hot procedure, reduce production cost and improved lumber recovery, prepared qualified product.
Improve difficult wrought superalloy clarity, improve ingot quality by the processing parameter of optimizing in melting, casting process parameter and hot-work forging process according to the preparation method of the embodiment of the present invention, thereby improve difficult wrought superalloy thermoplasticity.
Although with reference to embodiments of the invention, specifically described exemplary embodiment of the present invention, those skilled in the art will appreciate that without departing from the spirit and scope of the present invention, can make various forms of changes to embodiment.
Claims (9)
1. a difficult wrought superalloy, is characterized in that, the composition of described difficult wrought superalloy is by weight percentage: 0%≤C≤0.1%, 16.5%≤Cr≤19.5%, 13.5%≤Co≤16.0%, 1.0%≤W≤2.0%, 2.5%≤Mo≤3.5%, 2.0%≤Al≤3.0%, 4.5%≤Ti≤5.5%, 0%≤Fe≤1.0%, 0.01%≤B≤0.03%, 0%≤Zr≤0.06%, 0%≤S≤0.002%, 0%≤Si≤0.15%, 0%≤Mn≤0.15%, surplus is Ni and other inevitable impurity.
2. difficult wrought superalloy as claimed in claim 1, it is characterized in that, the composition of described difficult wrought superalloy is by weight percentage: C is that 0.075%, Cr is 18.0%, Co is 15.0%, W is that 1.5%, Mo is that 3.0%, Al is 2.5%, Ti is 5%, B is that 0.02%, Zr is 0.04%, and surplus is Ni and other inevitable impurity.
3. the preparation method of a difficult wrought superalloy part, is characterized in that, described method comprises the steps:
(a) melting, melting obtains the alloy of following composition: 0%≤C≤0.1%, 16.5%≤Cr≤19.5%, 13.5%≤Co≤16.0%, 1.0%≤W≤2.0%, 2.5%≤Mo≤3.5%, 2.0%≤Al≤3.0%, 4.5%≤Ti≤5.5%, 0%≤Fe≤1.0%, 0.01%≤B≤0.03%, 0%≤Zr≤0.06%, 0%≤S≤0.002%, 0%≤Si≤0.15%, 0%≤Mn≤0.15%, surplus is Ni and other inevitable impurity;
(b) casting, adopt the top teeming process casting;
(c) remelting, melting voltage is 22V-30V, the melting electric current is that 2000A-3000A, molten drop speed are drip/s of 3/s-6, and adopts water-cooled and the type of cooling of filling helium gas cooling and combining, and with helium pressure, is that the 100Pa-200Pa explained hereafter goes out the remelting steel ingot;
(d) hot-work is forged: before forging after Heating Steel Ingots is come out of the stove, the insulation treatment process is set, described insulation treatment process for sprinkling one deck glass powder on the pure aluminium silicate insulating cotton, after making surface of steel ingot bonding one deck pure aluminium silicate insulating cotton be incubated processing, adopt, without tensile stress arc anvil, steel ingot is carried out to draw out.
4. preparation method as claimed in claim 3, melting step in described preparation method comprises the charging by batches step, in the charging by batches step of described melting, except 1/3 Al, Ti of 1/3 C of easy scaling loss pantogen material C piece weight and starting material Al bar weight and micro alloying element B, Zr raw material, time shove charge of other element raw material homogeneous, with the stove unslaked lime of packing into, after the desulfurization removing nitric deoxygenation refining completes, add 1/3 Al, Ti of 1/3 C of easy scaling loss pantogen material C piece weight and starting material Al bar weight, tap and within first 5 minutes, add B, Zr raw material.
5. preparation method as claimed in claim 3, is characterized in that, the ingot shape in the casting step process in described preparation method is
6. preparation method as claimed in claim 5, is characterized in that, the ingot mould used in the casting step process in described preparation method scalded with molten steel, and top adds hot topping, and sprue gate and insulated feeder distance are less than 300mm, keep molten steel to become under plume.
7. preparation method as claimed in claim 3, is characterized in that, the reflow step in described preparation method obtains
the remelting steel ingot.
8. preparation method as claimed in claim 3, is characterized in that, the hot-work forging step in described preparation method comprises to be processed rear and carries out carrying out many fiery inferior repetitions without the step of tensile stress arc anvil draw out being incubated.
9. preparation method as claimed in claim 3, is characterized in that, after described preparation method also has been included in the hot-work forging, by the steel ingot draw out extremely
the line cutting is removed steel ingot end to end and segmentation, obtains
blank, with R=20mm car chamfering, after described insulation treatment process, adopt the swage collar pier thick, obtain
blank, be of a size of after preparing machining
the little diskware of difficult wrought superalloy.
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| CN104826969A (en) * | 2015-05-25 | 2015-08-12 | 无锡市派克重型铸锻有限公司 | Method for forging 500-Kg-level GH3230 high-temperature alloy |
| CN106424501A (en) * | 2016-07-26 | 2017-02-22 | 厦门虹鹭钨钼工业有限公司 | Sheath-based difficult-to-deform material multidirectional swaging method |
| CN107709586A (en) * | 2015-08-12 | 2018-02-16 | 山阳特殊制钢株式会社 | It is laminated moulding Ni base superalloy powder |
| CN108179322A (en) * | 2018-01-31 | 2018-06-19 | 攀钢集团江油长城特殊钢有限公司 | A kind of difficult deformation cobalt base superalloy plank of high lanthanum content and preparation method thereof |
| CN108285998A (en) * | 2018-03-29 | 2018-07-17 | 冯满 | A kind of high-temperature alloy steel |
| CN113862520A (en) * | 2021-08-26 | 2021-12-31 | 北京钢研高纳科技股份有限公司 | GH4720Li high-temperature alloy for aero-engine forged blade, preparation method and application thereof, and alloy ingot |
| CN114799005A (en) * | 2022-05-06 | 2022-07-29 | 任超群 | Forging method of homogeneous fine-grain high-temperature alloy disc |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103952593A (en) * | 2014-04-21 | 2014-07-30 | 西北工业大学 | K4169 high-temperature alloy |
| CN103952593B (en) * | 2014-04-21 | 2016-04-06 | 西北工业大学 | A kind of K4169 superalloy |
| CN104826969A (en) * | 2015-05-25 | 2015-08-12 | 无锡市派克重型铸锻有限公司 | Method for forging 500-Kg-level GH3230 high-temperature alloy |
| CN107709586A (en) * | 2015-08-12 | 2018-02-16 | 山阳特殊制钢株式会社 | It is laminated moulding Ni base superalloy powder |
| CN106424501A (en) * | 2016-07-26 | 2017-02-22 | 厦门虹鹭钨钼工业有限公司 | Sheath-based difficult-to-deform material multidirectional swaging method |
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| CN108179322B (en) * | 2018-01-31 | 2019-09-24 | 攀钢集团江油长城特殊钢有限公司 | A kind of preparation method of the difficult deformation cobalt base superalloy plate of high lanthanum content |
| CN108285998A (en) * | 2018-03-29 | 2018-07-17 | 冯满 | A kind of high-temperature alloy steel |
| CN113862520A (en) * | 2021-08-26 | 2021-12-31 | 北京钢研高纳科技股份有限公司 | GH4720Li high-temperature alloy for aero-engine forged blade, preparation method and application thereof, and alloy ingot |
| CN114799005A (en) * | 2022-05-06 | 2022-07-29 | 任超群 | Forging method of homogeneous fine-grain high-temperature alloy disc |
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