CN104451339A - Low-nickel aging strengthening type iron-nickel based corrosion resistant alloy and preparation method thereof - Google Patents
Low-nickel aging strengthening type iron-nickel based corrosion resistant alloy and preparation method thereof Download PDFInfo
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- CN104451339A CN104451339A CN201410809009.7A CN201410809009A CN104451339A CN 104451339 A CN104451339 A CN 104451339A CN 201410809009 A CN201410809009 A CN 201410809009A CN 104451339 A CN104451339 A CN 104451339A
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- 239000000956 alloy Substances 0.000 title claims abstract description 74
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 73
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 60
- 230000032683 aging Effects 0.000 title claims abstract description 38
- 238000005728 strengthening Methods 0.000 title claims abstract description 27
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 24
- 238000002360 preparation method Methods 0.000 title claims description 7
- 238000005260 corrosion Methods 0.000 title abstract description 14
- 230000007797 corrosion Effects 0.000 title abstract description 12
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 title abstract description 10
- 239000011573 trace mineral Substances 0.000 claims abstract description 10
- 235000013619 trace mineral Nutrition 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims description 18
- 239000000463 material Substances 0.000 claims description 13
- 229910000831 Steel Inorganic materials 0.000 claims description 12
- 239000010959 steel Substances 0.000 claims description 12
- 238000011282 treatment Methods 0.000 claims description 12
- 238000002791 soaking Methods 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 8
- 229910052796 boron Inorganic materials 0.000 claims description 7
- 238000000265 homogenisation Methods 0.000 claims description 7
- 238000001192 hot extrusion Methods 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 229910052726 zirconium Inorganic materials 0.000 claims description 7
- 230000006698 induction Effects 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 238000001125 extrusion Methods 0.000 claims description 4
- 238000005097 cold rolling Methods 0.000 claims description 3
- 238000005098 hot rolling Methods 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract description 10
- 229910052719 titanium Inorganic materials 0.000 abstract description 10
- 230000008901 benefit Effects 0.000 abstract description 6
- 229910052804 chromium Inorganic materials 0.000 abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 abstract description 4
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 238000012545 processing Methods 0.000 abstract description 3
- 229910052758 niobium Inorganic materials 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 15
- 238000007669 thermal treatment Methods 0.000 description 12
- 239000010936 titanium Substances 0.000 description 12
- 239000011651 chromium Substances 0.000 description 11
- 239000010949 copper Substances 0.000 description 10
- 239000010955 niobium Substances 0.000 description 8
- 239000006104 solid solution Substances 0.000 description 7
- 229910052742 iron Inorganic materials 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000005265 energy consumption Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000005070 sampling Methods 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000003638 chemical reducing agent Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000009972 noncorrosive effect Effects 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 229910002555 FeNi Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000003889 chemical engineering Methods 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000023753 dehiscence Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000005065 mining Methods 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 239000007800 oxidant agent Substances 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
-
- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to a low-nickel aging strengthening type iron-nickel based corrosion resistant alloy. The alloy is prepared from the following components in percentage by weight: 36.0-42.0 percent of Ni, 19.0-25.0 percent of Cr, 3.0-6.0 percent of Mo, 1.0-3.50 percent of Cu, 1.5-3.0 percent of Ti, 0.2-0.6 percent of Al, less than or equal to 0.5 percent of Nb, less than or equal to 0.03 percent of C, less than or equal to 0.5 percent of Si, less than or equal to 0.5 percent of Mn, less than or equal to 0.0010 percent of S, less than or equal to 0.005 percent of P, 0.01-0.6 percent of trace elements and the balance of Fe. The alloy has high strength, high toughness and high corrosion resistance of existing iron-nickel based alloy. Compared with existing iron-nickel based alloy, the alloy has the advantages of better thermal processing performance and lower cost.
Description
Technical field
The present invention relates to a kind of metallic substance, particularly one low nickel ageing strengthening sections abros and preparation method.
Background technology
Ni-based structured material, except matrix element nickel, usually also containing beneficial elements such as chromium, molybdenum, niobium, tungsten, copper, iron, titanium and aluminium, can be used as superalloy or non-corrosive metal.Because the nickel content of nickel-base alloy is very high, massfraction is greater than 50%, and even up to 80%, therefore material cost is higher, has certain negative impact for large-scale promotion application.On the other hand, because in alloy, nickel content is too high, thermoplasticity is poor, and high temperature hot deformation resistance warm area that is comparatively large, that be applicable to distortion is narrower, and therefore difficulty of processing is very large, process costs is very high, is also a unfavorable factor for commercial introduction.Compared with nickel-base alloy, iron nickel base alloy part iron replaces more nickel, simultaneously still can containing beneficial elements such as higher or appropriate chromium, molybdenum, copper, titanium and aluminium, on the basis not changing stable austenite basal body structure, obtain different intensity, hardness and toughness plasticity by composition and process matching and control.And due to the downward of nickel content, even can turn down 30% (Fe+Ni >=50%), therefore there is obvious price advantage, in some application scenario, have greatly the gesture that can replace Langaloy, receive the extensive concern of academia and industry member.
Although the nickel content of iron nickel base alloy is much lower compared with nickel-base alloy, but in fact alloy content is still higher, cause that thermoplasticity is good not, high temperature hot deformation resistance is large, distortion warm area is narrow, compared with low alloy material, the hot-work difficulty of iron nickel base alloy is still comparatively large, and process costs is still higher.Therefore similar with Langaloy, iron nickel base alloy is still difficult to the manufacture technics tubing by hot-puncturing process usually, mostly can only by the mode tubulation of mechanical punching, only has minority can by the technique tubulation of hot extrusion.
On the other hand, for ageing strengthening type alloy, performance level and the microtexture of alloy are closely related, and as the morphology and distribution of grain size, carbide, the size of intermetallic compound and distribution etc., these factors control by thermal treatment process.The thermal treatment of general ageing strengthening sections nickel-base alloy is made up of solution treatment, intermediate treatment and ageing treatment.Major part alloy all needs these two requisite steps of ageing treatment after first solid solution.At present more existing research trial direct aging thermal treatments substitute the thermal treatment process needing two or more step, with shortened process, enhance productivity, reduce energy consumption, but not yet obtain and significantly break through.
Summary of the invention
The object of this invention is to provide a kind of low nickel ageing strengthening sections abros and preparation method, this alloy has high-strength, high-ductility, the high-corrosion resistance of existing Fe-Ni, and with existing Fe-Ni based compared with, have better hot workability, cost is lower.
Technical scheme of the present invention is:
Low nickel ageing strengthening sections abros, the weight percentage of each component of this alloy is: Ni:36.0 ~ 42.0%; Cr:19.0 ~ 25.0%; Mo:3.0 ~ 6.0%; Cu:1.0 ~ 3.50%; Ti:1.5 ~ 3.0%; Al:0.2 ~ 0.6%; Nb≤0.5%; C≤0.03%, Si≤0.5%, Mn≤0.5%; S≤0.0010; P≤0.005; Trace element 0.01 ~ 0.6%; Fe is surplus.
The good technical scheme of alloy of the present invention is, the weight percentage of each component of alloy is: Ni:38.0 ~ 42.0%; Cr:20.0 ~ 23.0%; Mo:3.0 ~ 6.0%; Cu:1.0 ~ 3.50%; Ti:1.5 ~ 3.0%; Al:0.3 ~ 0.6%; Nb≤0.5%; C≤0.03%, Si≤0.5%, Mn≤0.5%; S≤0.0010; P≤0.005; Trace element 0.01 ~ 0.6%; Fe is surplus.
Described trace element is V, Zr, B.
V:0.01 ~ 0.5%, Zr:0.01 ~ 0.1%, B:0.001 ~ 0.01% in described trace element.
The preparation method of low nickel ageing strengthening sections abros, each alloy compositions is got according to said ratio, vacuum induction melting, be cast into pole, esr becomes steel ingot, Homogenization Treatments, pipe, rod or sheet material are made in forge hot or hot rolling or hot extrusion, cold rolling or cold-drawn, heat-treat again: be incubated 2 ~ 20 hours in the air of 700 ~ 760 DEG C, be chilled to 620 ~ 680 DEG C with 40 ~ 60 DEG C of speed stoves hourly, then be incubated 2 ~ 20 hours.
Described Homogenization Treatments temperature is 1160 ~ 1190 DEG C, the time is 24 ~ 72 hours.
Heat forged temperature is 950 ~ 1150 DEG C, soaking time is 60 ~ 120 minutes; Hot-rolled temperature is 1000 ~ 1200 DEG C, soaking time is 60 ~ 120 minutes; Extrusion temperature 1000 ~ 1200 DEG C.
The summation of described two soaking time sections is no less than 10 hours.
The described heat treated time is no more than 20 hours.
The Main Function inventing each element in described alloy is as follows:
(1) Ni: the Ni of high level is the important foundation obtaining excellent anticorrosive performance, particularly anticorrosion stress-resistant and sulfide-stress cracking ability.Replace more Ni with part Fe, while reduction material cost, the stable austenitic matrix identical with nickel-base alloy can be obtained.
(2) Cr: relatively high Cr content is the guarantee obtaining erosion resistance, particularly improves the key of alloy anti-corrosion capability in Oxidant.But too high Cr content will promote the precipitation of σ phase, and then damage thermostability and the thermoplasticity of alloy.
(3) Mo: higher Mo content, mainly in order to improve the local corrosion abilities such as the resistance to spot corrosion of alloy, corrosion at a seam, especially improves the corrosive power of alloy in halide-ions, reductant.But too high Mo content can promote the precipitation of σ phase equally, be harmful to thermostability and the thermoplasticity of alloy.
(4) Cu: appropriate Cu content is conducive to improving the corrosion resistance of alloy in reductant.In addition there are some researches show Cu in some alloy through in can separate out rich Cu phase after the long-time timeliness of temperature, thus be of value to enduring quality, but in non-corrosive metal, there is not been reported in the performance of Cu this respect.
(5) Nb: Nb high in right amount can form ageing strengthening phase γ "-Ni
3nb, but too high Nb content can the undue segregation when as cast condition, considerably increases the difficulty of follow-up Homogenization Treatments.At the iron of Ni content " deficiency " in Ni-based or low nickelalloy, Nb is more to add as carbide forming element, reduces the formation of chromium carbide, ensures the solidity to corrosion of alloy.
(6) Ti, Al: a small amount of Ti, Al have desoxydatoin, the ageing strengthening effect adding alloy of appropriate Ti, Al has active effect, promotes ageing strengthening phase γ '-Ni
3effective precipitation of (Al, Ti), contributes to alloy and obtains high strength and high tenacity.On the other hand, because Ti, Al are easy scaling loss elements, too high Ti, Al can increase melting and remelting stage Composition Control and hot worked difficulty.
(7) Si, Mn: a small amount of Si, Mn have desoxydatoin, but in high alloy, Si, Mn are very responsive to the precipitation of harmful mesophase spherule, makes precipitated phase complicated and damages the thermostability of useful precipitated phase, adding control difficulty, usually need strict control.
(8) C: have solution strengthening effect, also can stable austenite matrix, but too high C content not only can damage the corrosion resistance nature of alloy, and is also harmful to welding property.
(9) V, Zr, B; The hot workability of healthy trace elements with household V, Zr, B and accurately proportioning alloy is of great benefit to.
Alloy of the present invention is at higher chromium, the molybdenum content of Fe-Ni based middle interpolation, obtain and optimize the main content such as Ni, Fe, Cr, Mo, Ti, Al simultaneously, the more Fe of special use replaces more Ni, add the technique elements such as V, Zr, B of trace simultaneously, to improve the hot-workability of alloy, reduce the tendency of hot tearing in hot procedure.Alloy of the present invention is ageing strengthening type FeNi-based austenitic alloy, by suitable thermal treatment, γ ' highly malleablized phase can be separated out, thus obtain higher intensity, hardness and toughness plasticity, simultaneously because nickel, chromium, molybdenum content are high, corrosion resistance nature is strong, and particularly stress corrosion dehiscence resistant is very capable.
Compared with alloy of the present invention or iron nickel base alloy Ni-based with solution strengthening type, intensity is higher and manufacture relatively large or comparatively complicated shape by aging strengthening model; Compared with the iron nickel base alloy of other ageing strengthening type, due to allocating into of micro-beneficial element, thermoplasticity improves, in hot procedure, hot cracking tendency reduces, the method of hot extrusion is more easily adopted to make thick-wall tube, overall craft performance is more excellent, and in addition owing to taking more low nickel content design, design of material cost declines to some extent; Compared with ageing strengthening type Langaloy, instead of part of nickel with more iron, but still have stable austenitic matrix structure, can also reach equal obdurability rank, more significant advantage significantly reduces material cost, and cost performance is very outstanding simultaneously.
Alloy of the present invention, compared with typical ageing strengthening sections nickel-base alloy, adopts low nickel content still can obtain equal high strength, high toughness plasticity, and outstanding corrosion resistance nature, and therefore material cost is lower; On the other hand, due to the interpolation of micro-beneficial element, thermoplasticity is obviously improved, and hot-work difficulty reduces, and lumber recovery improves, and hot-extrusion method even can be adopted to prepare seamless tubular goods, and processing performance has more advantage; In addition due to the heat treated employing of unique direct aging, thermal treatment process flow process shortens, and energy consumption reduces, and cost benefit significantly improves.
Alloy of the present invention, may be used for the fields such as various highly corrosive environments such as high sulfur-containing oil-gas exploitation, petrochemical complex, chemical engineering and oceanographic engineering, as for High Temperature High Pressure height sulfur-containing oil-gas Mining Equipment material, sulfur-containing oil-gas subsurface tool, key member, and completion drill collar etc.
Accompanying drawing explanation
Fig. 1 is that alloy of the present invention carries out aging heat treatment room-temperature mechanical property again after differing temps solid solution;
Fig. 2 is that alloy of the present invention is carrying out differing temps aging heat treatment room-temperature mechanical property after solid solution;
Fig. 3 is that alloy of the present invention contrasts through solid solution+timeliness and the heat treated room-temperature mechanical property of direct aging;
Fig. 4 is the metallographic structure of alloy of the present invention through solid solution+aging state;
Fig. 5 is the metallographic structure of direct aging state after alloy extrusion of the present invention.
Embodiment
One. embodiment
The weight percentage of a low nickel ageing strengthening sections abros component of the present invention is as shown in table 1:
Table 1
| Alloying constituent | Embodiment 1 | Embodiment 2 | Embodiment 3 |
| C | 0.027 | 0.015 | 0.0097 |
| Si | 0.101 | 0.160 | 0.207 |
| Mn | 0.337 | 0.229 | 0.135 |
| P | 0.0032 | 0.0028 | 0.0034 |
| S | 0.0010 | 0.0010 | 0.0010 |
| Cr | 20.80 | 21.76 | 22.91 |
| Ni | 38.41 | 40.23 | 41.35 |
| Mo | 5.20 | 4.16 | 3.18 |
| Nb | 0.397 | 0.283 | 0.188 |
| Ti | 2.81 | 2.20 | 1.88 |
| Al | 0.45 | 0.334 | 0.553 |
| V | 0.263 | 0.162 | 0.061 |
| Cu | 3.03 | 2.01 | 1.02 |
| Zr | 0.055 | 0.079 | 0.011 |
| B | 0.0043 | 0.0031 | 0.0061 |
| Fe | Surplus | Surplus | Surplus |
Low nickel ageing strengthening sections abros of the present invention, its preparation method is as follows:
Get each alloy compositions according to said ratio, vacuum induction melting, be cast into pole, esr becomes steel ingot, Homogenization Treatments, and described Homogenization Treatments temperature is 1160 ~ 1190 DEG C, the time is 24 ~ 72 hours.Forge hot or hot rolling or hot extrusion, heat forged temperature is 950 ~ 1150 DEG C, soaking time is 60 ~ 120 minutes; Hot-rolled temperature is 1000 ~ 1200 DEG C, soaking time is 60 ~ 120 minutes; Extrusion temperature 1000 ~ 1200 DEG C.Pipe, rod or sheet material are made in cold rolling or cold-drawn, then heat-treat: be incubated 2 ~ 20 hours in the air of 700 ~ 760 DEG C, be chilled to 620 ~ 680 DEG C, then be incubated 2 ~ 20 hours with 40 ~ 60 DEG C of speed stoves hourly.The summation of described two soaking time sections is no less than 10 hours, and described thermal treatment total time is no more than 20 hours, obtains low nickel ageing strengthening sections abros of the present invention.
Embodiment 1
Adopt vacuum induction melting alloy 500kg, be cast into the pole of Φ 170mm, then esr becomes the steel ingot of Φ 280mm, steel ingot number is N73, and alloy composition is in table 1.Steel ingot is placed in high temperature pit furnace and carries out homogenizing thermal treatment, the pole of Φ 100mm is made through forging, bar detects its tensile property, hardness and ballistic work after aging strengthening model, Linear cut sampling, processed sample, and performance is in table 2, and this material is used for the subsurface tool of oil-gas field.
Embodiment 2
Adopt vacuum induction melting alloy 1000kg, be cast into the pole of Φ 220mm, then esr becomes the steel ingot of Φ 380mm, steel ingot number is N74, and alloy composition is in table 1.Steel ingot is placed in high temperature pit furnace and carries out homogenizing thermal treatment, the pole of Φ 200mm is forged into through jumping-up pulling, bar detects its tensile property, hardness and ballistic work after aging strengthening model, Linear cut sampling, processed sample, and performance is in table 2, and this material is used for the subsurface tool of oil-gas field.
Embodiment 3
Adopt vacuum induction melting alloy 3000kg, be cast into the pole of Φ 250mm, then esr becomes the steel ingot of Φ 400mm, steel ingot number is N75, and alloy composition is in table 1.Steel ingot is placed in high temperature pit furnace and carries out homogenizing thermal treatment, through quick forging machine jumping-up pulling cogging, and the bar of Φ 230mm is made in radial forging machine forging, bar makes thick-walled tube through hot extrusion again, tubing detects its tensile property, hardness and ballistic work after aging strengthening model, Linear cut sampling, processed sample, performance is in table 2, and this material is used for the down-hole pipe in sour oil gas field.
Two. alloy property
1. the impact of thermal treatment alloy mechanical property, alloy structure
The room-temperature mechanical property of alloy of the present invention after different heat treatment is shown in Fig. 1-Fig. 3, and alloy using state of the present invention is generally aging state, solid solution can be adopted to add timeliness, also can adopt direct aging, to obtain high obdurability.Solid solution is adopted to add its metallographic structure of timeliness as described in Figure 4; Adopt its metallographic structure of direct aging as described in Figure 5.By contrast, direct aging thermal treatment can shortened process, save energy consumption, raise the efficiency, be more recommendable treatment process.
2. mechanical property tests
Table 2 mechanical property
Claims (9)
1. a low nickel ageing strengthening sections abros, it is characterized in that, the weight percentage of each component of this alloy is:
Ni：36.0～42.0％；
Cr：19.0～25.0％；
Mo：3.0～6.0％；
Cu：1.0～3.50％；
Ti：1.5～3.0％；
Al：0.2～0.6％；
Nb≤0.5％；C≤0.03％；Si≤0.5％；Mn≤0.5％；S≤0.0010；P≤0.005；
Trace element 0.01 ~ 0.6%;
Fe is surplus.
2. alloy according to claim 1, is characterized in that, the weight percentage of each component of this alloy is:
Ni：38.0～42.0％；
Cr：20.0～23.0％；
Mo：3.0～6.0％；
Cu：1.0～3.50％；
Ti：1.5～3.0％；
Al：0.3～0.6％；
Nb≤0.5％；C≤0.03％、Si≤0.5％、Mn≤0.5％；S≤0.0010；P≤0.005；
Trace element 0.01 ~ 0.6%;
Fe is surplus.
3. alloy according to claim 1 and 2, is characterized in that: described trace element is V, Zr, B.
4. alloy according to claim 3, is characterized in that: V:0.01 ~ 0.5%, Zr:0.01 ~ 0.1%, B:0.001 ~ 0.01% in described trace element.
5. the preparation method of low nickel ageing strengthening sections abros, it is characterized in that: get each alloy compositions according to the arbitrary described proportioning of claim 1-3, vacuum induction melting, is cast into pole, and esr becomes steel ingot, Homogenization Treatments, forge hot or hot rolling or hot extrusion, pipe, rod or sheet material are made in cold rolling or cold-drawn, then heat-treat: be incubated 2 ~ 20 hours in the air of 700 ~ 760 DEG C, be chilled to 620 ~ 680 DEG C with 40 ~ 60 DEG C of speed stoves hourly, then be incubated 2 ~ 20 hours.
6. method according to claim 5, is characterized in that: described Homogenization Treatments temperature is 1160 ~ 1190 DEG C, the time is 24 ~ 72 hours.
7. method according to claim 5, is characterized in that: heat forged temperature is 950 ~ 1150 DEG C, soaking time is 60 ~ 120 minutes; Hot-rolled temperature is 1000 ~ 1200 DEG C, soaking time is 60 ~ 120 minutes; Extrusion temperature 1000 ~ 1200 DEG C.
8. method according to claim 5, is characterized in that: the summation of described two soaking time sections is no less than 10 hours.
9. method according to claim 5, is characterized in that: the described heat treated time is no more than 20 hours.
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