CN104846237A - Manufacturing method of Ni-Fe-Cr-Mo anticorrosive alloy tube blank - Google Patents
Manufacturing method of Ni-Fe-Cr-Mo anticorrosive alloy tube blank Download PDFInfo
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- CN104846237A CN104846237A CN201510177582.5A CN201510177582A CN104846237A CN 104846237 A CN104846237 A CN 104846237A CN 201510177582 A CN201510177582 A CN 201510177582A CN 104846237 A CN104846237 A CN 104846237A
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Abstract
The invention relates to a manufacturing method of an Ni-Fe-Cr-Mo anticorrosive alloy tube blank, wherein the manufacturing method comprises the following steps: I, electroslag ingot smelting: smelting an Ni-Fe-Cr-Mo alloy into an electroslag ingot, wherein the content of B in the electroslag ingot is 0.003-0.008%; II, electroslag ingot surface treatment: removing defects such as cracks, scabs and concave pits visible to naked eyes on the surface of the electroslag ingot; III, homogenization treatment: placing the electroslag ingot in a high-temperature annealing furnace, carrying out heat preservation at the temperature of 1220-1260 DEG C, and after the temperatures of an electroslag ingot core and surface are uniform thoroughly, carrying out heat preservation for 12-24 h again, wherein the charging temperature is less than or equal to 400 DEG C and the heating up speed is less than or equal to 100 DEG C/h; and IV, cogging forging: discharging the electroslag ingot after homogenization treatment out of the high-temperature annealing furnace, transferring into a heating furnace of a cogging workshop, after the temperatures of the electroslag ingot core and surface are uniform and consistent, discharging out of the furnace, carrying out temperature grabbing and fast forging into the anticorrosive alloy tube blank. The anticorrosive alloy tube blank manufactured by the manufacturing method of the Ni-Fe-Cr-Mo anticorrosive alloy tube blank has high hot workability and high corrosion resistance.
Description
Technical field
The present invention relates to a kind of manufacture method of non-corrosive metal pipe, particularly relate to a kind of manufacture method of Ni-Fe-Cr-Mo type non-corrosive metal pipe.
Background technology
Common iron abros mainly contains Ni-Fe-Cr alloy, Ni-Fe-Cr-Mo alloy and Ni-Fe-Cr-Mo-Cu alloy three major types, wherein Ni-Fe-Cr-Mo type alloy is owing to being rich in Mo element, compared to Ni-Fe-Cr type alloy, it has more excellent anti-spot corrosion, crevice corrosion, stress corrosion dehiscence resistant ability and intensity is high, plasticity and toughness mate good mechanical property, is widely used in multiple harsh corrosive environment.The industry fields such as such as apparatus for desulfurizing exhaust gas, papermaking, offshore platform equipment, chemical industry equipment, phosphoric acid production vapour generator, heat exchanger, in addition, the type non-corrosive metal is also subject to the extensive concern in peracidity exploitation of oil-gas field field as tubing and casing material.
But, because the alloying level of this Ni-Fe-Cr-Mo type non-corrosive metal is high, and the Mo element playing solution strengthening and raising corrosion resisting property belongs to easy segregation element, in alloy graining process, the a large amount of segregation of Mo element is in interdendritic, interdendritic and dendrite is caused to do Mo Elemental redistribution uneven, this will significantly reduce the hot-workability of As-cast Microstructure, and then cause the cogging hot-work difficulty of alloy cast ingot to strengthen, in the cogging production process of alloy cast ingot, repeatedly occur because Hot Working Crack causes pipe to scrap phenomenon, pipe lumber recovery is lower, manufacturing cost significantly rises.Meanwhile, Mo element also can increase the susceptibility separated out mutually between σ phase, the equal poisonous metal of μ in a large amount of segregation in interdendritic, these intermetallic phases can jeopardize the corrosion resistance of alloy, in alloy, Mo concentration lower region is also easier to corrosion simultaneously, if this segregation structural state is left in alloy finished product (tubing and casing), then serious quality problems may be caused in its actual use procedure.Therefore, the hot workability and the solidity to corrosion that improve Ni-Fe-Cr-Mo type non-corrosive metal are a vital task of this alloy industry production instantly and key point in the urgent need to address.
Summary of the invention
The object of the invention is to a gram above-mentioned deficiency for the manufacture method of existing Ni-Fe-Cr-Mo type non-corrosive metal pipe, the invention provides the manufacture method of a kind of alloy pipe stock hot workability and the high Ni-Fe-Cr-Mo type non-corrosive metal pipe of solidity to corrosion.
The weight percent of the chemical composition of Ni-Fe-Cr-Mo type non-corrosive metal of the present invention consists of:
C ≤0.015%， Cr 21~24.0%， Mo 6.0~8.0%， Fe 18.0~21.0%，
Cu 1.5~2.0%， Co ≤3.0%， W ≤1.5%， Si ≤0.5%， Mn ≤0.5%，
S≤0.003%, P≤0.03%, all the other are Ni and inevitable impurity.
(wherein C, Si and Mn are impurity elements in steel, Co and W improves solidity to corrosion element, and interpolation can improve solidity to corrosion, but increases cost, be not very large, can add and can not add with raising solidity to corrosion and processibility relation.）
One of the present invention improves Ni-Fe-Cr-Mo type non-corrosive metal hot workability and corrosion proof method, and concrete technical scheme comprises:
(1) ESR ingot is smelted
Described Ni-Fe-Cr-Mo type non-corrosive metal is smelted into ESR ingot through vacuum induction smelting+esr bigeminy technique, and the B content in ESR ingot controls in 0.003 ~ 0.008% scope.
This alloy is high-grade non-corrosive metal, alloy content is high, impurity element such as S, P, O, H etc. have considerable influence to its corrosion resisting property, therefore, adopt " vacuum induction+esr " smelting process can improve its purity, and provide good as-cast structure, for the forging hot-work of follow-up alloy cast ingot provides good organization foundation.Because B element has strengthening crystal boundary, puies forward heavy alloyed heat resistance and improve the effect of hot workability, for useful alloying element, but B too high levels can make it increase in austenite grain boundary segregation, form the boride eutectic of low melting point, alloy performance has adverse influence, therefore, the B content in ESR ingot controls in 0.003 ~ 0.008% scope better.
(2) ESR ingot surface treatment
By machining remove ESR ingot surface crackle, scab, the naked eyes visual defects such as pit.(naked eyes visual defects refers to close-ups ESR ingot surface; Crackle must all remove, and crackle is also clean through emery wheel reconditioning; ESR ingot surface treatment method: mainly adopt the crackle of emery wheel local thinning surface, scab, the naked eyes visual defects such as pit.）
(3) homogenize process
ESR ingot is placed in high-temperature annealing furnace, be incubated at 1220 ~ 1260 DEG C of temperature, until ESR ingot heart portion and skin temperature all thoroughly after (according to ESR ingot diameter specifications, time is estimated according to 0.5min/mm all thoroughly), continue insulation 12 ~ 24h again, to dissolve the precipitated phase in alloy, eliminate element dendritic segregation.Wherein charging temperature≤400 DEG C, that heat-up rate control is≤100 DEG C/h(optimum is 80 DEG C/h).
(4) cogging forging
ESR ingot after the process that homogenizes is gone out high-temperature annealing furnace, proceed to fast in the process furnace of cogging workshop, surface temperature control when ESR ingot enters process furnace is at>=900 DEG C, the furnace temperature of process furnace treats that material temperature degree controls at 1150 ~ 1190 DEG C, due to Ni-Fe-Cr-Mo type non-corrosive metal ESR ingot to Heating temperature and soaking time very responsive, the long period is incubated under high temperature, easily cause alloy burning, thermoplasticity significantly reduces, and then cause forging crack phenomenon, therefore, the cogging forging temperature of ESR ingot answers conservative control, namely homogenization temperature (
) with wait to expect furnace temperature (
) should relational expression be met
.ESR ingot after the process that homogenizes is gone out high-temperature annealing furnace, proceed to fast in the process furnace of cogging workshop, surface temperature control when ESR ingot enters process furnace is at >=900 DEG C, the furnace temperature of process furnace treats that material temperature degree controls at 1150 ~ 1190 DEG C, after ESR ingot homogeneous temperature is consistent, come out of the stove and carry out robbing the fast forging of temperature, be forged into non-corrosive metal pipe.
Further, for Ni-Fe-Cr-Mo type non-corrosive metal ingot casting, the dendritic segregation of Mo element is the most serious, therefore, the process that homogenizes mainly eliminates Mo segregation, because its atomic radius is large, Elements Diffusion ability is more weak, soaking time depends primarily on the segregation degree of Mo element, velocity of diffusion and dendrite interval, when Mo element segregation COEFFICIENT K (ratio of the most high-content of interdendritic element and the minimum content of the dry element of dendrite) reaches 1.0 ~ 1.10, the dendritic segregation basically eliminate of Mo element just can be thought.
Beneficial effect of the present invention is:
By adopting manufacture method provided by the invention, effectively eliminate Mo in alloy, Cr, elements such as w dendritic segregation, reduce the precipitation susceptibility of phase between σ phase, μ equal poisonous metal, add preferably useful alloy element B simultaneously, improve the high-temp plastic of alloy, effectively stopped ingot formation cracking phenomena, improve lumber recovery, lumber recovery is increased to more than 85% by 68%.Secondly, for alloy cast ingot cogging provides as-cast structure that is homogeneous, segregation-free, the solidity to corrosion of alloy is improved.In addition, compared with traditional " ingot casting high temperature homogenization, cooling, heat back into stove, cogging " technique, the invention enables homogenize, cogging forges two production processes and can be connected continuously, ensure that the continuity of rhythm of production, saved energy consumption, the production cycle shortens, improve production efficiency.
specific embodiment:
Below in conjunction with embodiment, explanation is further explained to one raising Ni-Fe-Cr-Mo type non-corrosive metal hot workability provided by the present invention and corrosion proof method, but this concrete enforcement is not limited to following embodiment.
embodiment one
(1) ESR ingot is smelted
The chemical component weight per-cent of the present embodiment alloy:
C 0.011%, Cr 22.0%, Mo 6.8%, Fe 19.4%, Cu 1.7%, W 0.5%, Si 0.45%, Mn 0.43%, S 0.001%, P 0.008%, Ni surplus.Alloy is smelted through vacuum induction+esr bigeminy technique, and obtain the ESR ingot of tonne φ 350mm specification, the B content in ESR ingot is 0.0041%.
(2) ESR ingot surface treatment
By machining remove ESR ingot surface crackle, scab, pit naked eyes visual defects.
(3) homogenize process
High-temperature annealing furnace is warming up to 300 DEG C, ESR ingot is put into high-temperature annealing furnace, be warming up to 1230 DEG C with the speed of 100 DEG C/h, insulation 24h(wherein comprises time 2h all thoroughly, and 21h homogenizes the time).
(4) cogging forging
ESR ingot after the process that homogenizes is gone out high-temperature annealing furnace, directly proceed in the process furnace of cogging workshop, surface temperature when ESR ingot enters process furnace is 950 DEG C, the furnace temperature of process furnace treats that material temperature degree controls at 1150 DEG C, after ESR ingot homogeneous temperature is consistent, cogging of coming out of the stove is forged, and final forging temperature is 910 DEG C.Pipe (the φ 225mm specification) surface quality obtained through above-mentioned technique is good, does not find forge crack defect.
embodiment two
(1) ESR ingot is smelted
The chemical component weight per-cent of the present embodiment alloy:
C 0.009%， Cr 23.5%， Mo 7.3%， Fe 20.5%， Cu 1.7%，
Co 0.8% ， W 1.2%， Si 0.39%， Mn 0.48%， S 0.0012%，
P 0.015%, Ni surplus.Alloy is smelted through vacuum induction+esr bigeminy technique, and obtain tonne φ 350mm specification ESR ingot, the B content in ESR ingot is 0.0063%.
(2) ESR ingot surface treatment
By machining remove ESR ingot surface crackle, scab, the naked eyes visual defects such as pit.
(3) homogenize process
High-temperature annealing furnace is warming up to 400 DEG C, ESR ingot is put into high-temperature annealing furnace, be warming up to 1260 DEG C with the speed of 80 DEG C/h, insulation 14h(wherein comprises time 2h all thoroughly, and 12h homogenizes the time).
(4) cogging forging
ESR ingot after the process that homogenizes is gone out high-temperature annealing furnace, directly proceed in the process furnace of cogging workshop, surface temperature when ESR ingot enters process furnace is 920 DEG C, the furnace temperature of process furnace treats that material temperature degree controls at 1165 DEG C, after ESR ingot homogeneous temperature is consistent, cogging of coming out of the stove is forged, and final forging temperature is 915 DEG C.
Pipe (the φ 230mm specification) surface quality obtained through above-mentioned technique is good, does not find forge crack defect.
Various embodiments of the present invention homogenize process front and back segregation than K value test result data table as shown in table 1, and K value, about more close to 1, illustrates that element dendritic segregation is eliminated more thorough.
Table 1
As seen from Table 1, the segregation coefficient K of Mo, Cr, W element is 0.95-1.08.
By ASTM G48 standard in the FeC1 of 6%
3carry out corrosion test to the embodiment of the present invention forward and backward alloy that homogenizes in testing liquid, adopt weight-loss method to measure the erosion rate of alloy, the embodiment of the present invention to homogenize before and after process solidity to corrosion contrast in table 2.
Table 2
As seen from Table 2, the erosion rate of alloy pig is 0.0238-0.0245g/m
2h.
Claims (7)
1. a manufacture method for Ni-Fe-Cr-Mo type non-corrosive metal pipe, it comprises following step successively:
ismelt ESR ingot
Ni-Fe-Cr-Mo type non-corrosive metal is smelted into ESR ingot through vacuum induction smelting+esr bigeminy technique, and the B content in ESR ingot controls in 0.003 ~ 0.008% scope;
iIeSR ingot surface treatment
By machining remove ESR ingot surface crackle, scab, pit naked eyes visual defects;
iIIhomogenize process
ESR ingot is placed in high-temperature annealing furnace, is incubated at 1220 ~ 1260 DEG C of temperature, until ESR ingot heart portion and skin temperature all thoroughly after, then continue insulation 12 ~ 24h, to dissolve the precipitated phase in alloy, eliminate element dendritic segregation; Wherein charging temperature≤400 DEG C, heat-up rate controls as≤100 DEG C/h;
iVcogging is forged
ESR ingot after the process that homogenizes is gone out high-temperature annealing furnace, proceed to fast in the process furnace of cogging workshop, surface temperature control when ESR ingot enters process furnace is at >=900 DEG C, the furnace temperature of process furnace treats that material temperature degree controls at 1150 ~ 1190 DEG C, after ESR ingot homogeneous temperature is consistent, come out of the stove and carry out robbing the fast forging of temperature, be forged into non-corrosive metal pipe.
2. the manufacture method of Ni-Fe-Cr-Mo type non-corrosive metal pipe according to claim 1, is characterized in that; Step
iIIhomogenize in process, ESR ingot is after the process that homogenizes, and Mo element segregation COEFFICIENT K reaches 1.0 ~ 1.10.
3., according to the manufacture method of described Ni-Fe-Cr-Mo type non-corrosive metal pipe arbitrary in claim 1 or 2, it is characterized in that; Step
iVin cogging forging, homogenization temperature (
) with wait to expect furnace temperature (
) should relational expression be met
, final forging temperature controls more than 900 DEG C.
4. the manufacture method of Ni-Fe-Cr-Mo type non-corrosive metal pipe according to claim 3, is characterized in that; Step
iVin cogging forging, homogenization temperature (
) with wait to expect furnace temperature (
) should relational expression be met
, final forging temperature controls more than 900 DEG C.
5., according to the manufacture method of described Ni-Fe-Cr-Mo type non-corrosive metal pipe arbitrary in claim 1 or 2, it is characterized in that: step
iIIhomogenize in process, it is 79-81 DEG C/h that heat-up rate controls.
6. the manufacture method of Ni-Fe-Cr-Mo type non-corrosive metal pipe according to claim 3, is characterized in that; Step
iIIhomogenize in process, it is 79-81 DEG C/h that heat-up rate controls.
7. the manufacture method of Ni-Fe-Cr-Mo type non-corrosive metal pipe according to claim 4, is characterized in that; Step
iIIhomogenize in process, it is 79-81 DEG C/h that heat-up rate controls.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113088761A (en) * | 2021-02-21 | 2021-07-09 | 江苏汉青特种合金有限公司 | Ultrahigh-strength corrosion-resistant alloy and manufacturing method thereof |
| CN113492151A (en) * | 2021-07-16 | 2021-10-12 | 山西太钢不锈钢股份有限公司 | Manufacturing method of iron-nickel-based alloy hot-rolled coil |
| CN115233012A (en) * | 2022-07-19 | 2022-10-25 | 山西太钢不锈钢股份有限公司 | Manufacturing method of nickel-based high-temperature alloy hot rolled plate |
| CN117535559A (en) * | 2024-01-10 | 2024-02-09 | 北京北冶功能材料有限公司 | Low-density nickel-based high-temperature alloy foil and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103361518A (en) * | 2013-06-11 | 2013-10-23 | 太原钢铁(集团)有限公司 | Nickel-based seamless pipe for ultra supercritical boiler and manufacturing method thereof |
| CN103866163A (en) * | 2014-03-14 | 2014-06-18 | 钢铁研究总院 | Nickel-chromium-cobalt-molybdenum heat resisting alloy and pipe manufacturing process thereof |
| CN103993202A (en) * | 2014-05-20 | 2014-08-20 | 太原钢铁(集团)有限公司 | Nickel-based alloy for tubes of boiler of ultra-supercritical power station and preparation method thereof |
-
2015
- 2015-04-15 CN CN201510177582.5A patent/CN104846237A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103361518A (en) * | 2013-06-11 | 2013-10-23 | 太原钢铁(集团)有限公司 | Nickel-based seamless pipe for ultra supercritical boiler and manufacturing method thereof |
| CN103866163A (en) * | 2014-03-14 | 2014-06-18 | 钢铁研究总院 | Nickel-chromium-cobalt-molybdenum heat resisting alloy and pipe manufacturing process thereof |
| CN103993202A (en) * | 2014-05-20 | 2014-08-20 | 太原钢铁(集团)有限公司 | Nickel-based alloy for tubes of boiler of ultra-supercritical power station and preparation method thereof |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113088761A (en) * | 2021-02-21 | 2021-07-09 | 江苏汉青特种合金有限公司 | Ultrahigh-strength corrosion-resistant alloy and manufacturing method thereof |
| CN113492151A (en) * | 2021-07-16 | 2021-10-12 | 山西太钢不锈钢股份有限公司 | Manufacturing method of iron-nickel-based alloy hot-rolled coil |
| CN115233012A (en) * | 2022-07-19 | 2022-10-25 | 山西太钢不锈钢股份有限公司 | Manufacturing method of nickel-based high-temperature alloy hot rolled plate |
| CN115233012B (en) * | 2022-07-19 | 2023-08-11 | 山西太钢不锈钢股份有限公司 | Manufacturing method of nickel-based superalloy hot rolled plate |
| CN117535559A (en) * | 2024-01-10 | 2024-02-09 | 北京北冶功能材料有限公司 | Low-density nickel-based high-temperature alloy foil and preparation method and application thereof |
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Application publication date: 20150819 |