CN104195404A - Wide-temperature-range high-strength constant-elasticity alloy and preparation method thereof - Google Patents
Wide-temperature-range high-strength constant-elasticity alloy and preparation method thereof Download PDFInfo
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Abstract
The invention belongs to the field of alloy steel and in particular relates to wide-temperature-range high-strength constant-elasticity alloy and a preparation method thereof. The alloy is high in strength and low in elastic modulus temperature coefficient at the temperature (-60 DEG C to 400 DEG C). The alloy comprises the following chemical components in percentage by weight: 34.0%-39.0% of Ni, 12.0%-18.0% of Co, 2.3%-3.0% of Ti, 0.3%-0.8% of Al, 0.30%-0.80% of Si, 0.2%-0.6% of Mn, less than 0.05% of C, less than 0.02% of P, less than 0.02% of S and the balance of Fe, wherein the sum of W and 2Mo is 5.0%-10.0%. The preparation method comprises the following steps: performing vacuum induction melting on alloy electrode bars; performing vacuum self-consuming remelting; forging square billets and hotly rolling; coldly rolling and performing vacuum aging heat treatment. By optimizing the alloy elements and adjusting the preparation process, the strength of Fe-Ni-Co alloy is further enhanced in the relatively wide temperature range, and meanwhile, the elastic modulus temperature coefficient of the alloy is reduced.
Description
Technical field
The invention belongs to ferrous metals Material Field, be specifically related to a kind of wide temperature range high strength constant modulus alloy and preparation method thereof, this alloy has high strength and low elastic modulus temperature factor at wide temperature range (60 ℃～400 ℃).
Background technology
Sensitive components in high precision instrument instrument is used part constant modulus alloy conventionally, and to guarantee that instrument keeps higher precision in certain temperature range, and constant modulus alloy temperature coefficient of the elastic modulus has determined its use temperature scope., there is the shortcomings such as use temperature is narrow, hot strength is not enough in traditional 3J1,3J53 and Cr13 alloy; Although Nb base constant modulus alloy 55NbTiAl use temperature wide ranges, its temperature coefficient of the elastic modulus is large, cannot meet accuracy of instrument requirement.
It is high that the Fe-Ni-Co developing is in recent years associated golden use temperature, but intensity and Young's modulus are low, are difficult to meet service requirements.The Fe-Ni-Co that has introduced Nb, Ti alloying in Chinese invention patent application CN1305021A is associated gold, and its alloying constituent is: Ni 30～45%, and Co 5～20%, Nb 2～6%, and Ti 0.5～3%, and Cr 0.5～5%, Si≤0.5%, C≤0.5%, surplus is Fe; This alloy hardens by Precipitation, has improved the intensity of alloy when keeping wide use temperature, and this alloy is within the scope of-60 ℃～260 ℃, and temperature coefficient of the elastic modulus is lower than 40 * 10
-6/ ℃, intensity, higher than 1250MPa, has been improved Fe-Ni-Co and has been associated golden use properties, but use temperature can only arrive 260 ℃; Meanwhile, because the alloy of this invention contains a large amount of Nb elements and solution strengthening element Cr, so in its dispersion-strengthened mutually, be mainly γ ＂ phase, only contain a small amount of γ ' phase.
In prior art, alloying constituent contains a large amount of Nb elements, and solution strengthening element is Cr, and in its strengthening phase, major part is γ ＂ phase, and the γ ＇ of a part.By comparison, the present invention, by the optimization of alloying element and preparation technology's adjustment, not containing Nb element, makes alloy strengthening of the present invention mutually not containing γ ＂ phase in alloying constituent; In alloy, added solid solution element W/Mo (CN1305021A is completely different with prior art), by W/Mo solution strengthening effect, and γ ＇ dispersion-strengthened action, jointly improve alloy strength.Make the present invention in wide temperature range, further improve Fe-Ni-Co and be associated golden intensity, reduce its temperature coefficient of the elastic modulus simultaneously.
Summary of the invention
The object of the present invention is to provide a kind of wide temperature range high strength constant modulus alloy and preparation method thereof.
For achieving the above object, technical scheme of the present invention is as follows:
A wide temperature range high strength constant modulus alloy, the chemical composition of this alloy (wt.%) is Ni 34.0～39.0%, Co 12.0～18.0%, Ti 2.3～3.0%, Al 0.3～0.8%, and Si 0.3～0.8%, and Mn 0.2～0.6%, C < 0.05%, P < 0.02%, S < 0.02%, surplus is Fe, wherein, W+2Mo 5.0～10.0.
This alloy adopts following steps preparation: vacuum induction melting alloy electrode rod+vacuum consumable remelting → forging square billet and hot rolling → cold rolling and vacuum aging thermal treatment.
This alloy has following mechanical property:
In the temperature range of-60～400 ℃, its tensile strength Rm is greater than 1350MPa, and elongation at break δ is greater than 2.5%, temperature coefficient of the elastic modulus β
elower than 25 * 10
-6/ ℃.
The microtexture of this alloy is the austenitic matrix with magnetostrictive effect, and the γ ' phase of the dispersion-strengthened that forms of Ti, Al and Ni, Co.
A preparation method for wide temperature range high strength constant modulus alloy, comprises the steps:
A) melting: utilize vacuum induction melting alloy, be cast into consumable electrode rod, vacuum tightness≤1 * 10
-1pa, consumable electrode rod is through vacuum consumable remelting, fusion process vacuum tightness≤1 * 10
-2pa, further degassed and refinement inclusion size obtains the ingot that strips off the skin;
B) cogging, heat are pricked: the ingot that strips off the skin is lower than 600 ℃ of shove charges, and cogging is forged into square billet, is then rolled into band;
C) cold rolling, thermal treatment: hot rolled band is cold rolling one-tenth cold rolling strap after annealing, and the deflection requirement according to final use, through solution hardening, is cold-rolled to final size, finally cold-rolled steel sheet is carried out to vacuum aging thermal treatment.
In step a, Fe, Ni, Co, W directly put into sweet pot as once reinforced; Ti, Al, Si, Mn put into vacuum induction batch hopper as secondary charging, and after all raw materialization is clear, refining is 2～10 minutes, and the vacuum chamber at vacuum induction furnace is cast into consumable electrode rod by molten steel afterwards.
In step b, forging temperature is 1050～1150 ℃, and forging soaking time is 40～60min.
In step b, hot-rolled temperature is 1080～1130 ℃, and the hot rolling heat holding time is insulation 30～60min.
In step b, quenching temperature is 950～1050 ℃, and thermal treatment temp is 650～750 ℃, and thermal treatment soaking time is 3～5h.
Beneficial effect of the present invention is:
Embodiment
Below in conjunction with embodiment, the specific embodiment of the present invention is described in further detail.
Overall technical architecture of the present invention is: first, utilize magnetostriction principle, make Fe-Ni-Co be associated gold and in wide temperature range, obtain low temperature coefficient of the elastic modulus, and then add wherein W/Mo element, by solution strengthening, improve Fe-Ni-Co alloy strength; Add appropriate Ti, Al, in ag(e)ing process, diffusion-precipitation strengthening phase (γ '), further improves alloy over-all properties simultaneously.After optimized alloy composition, through melting-forging-hot rolling-cold rolling and thermal treatment, make alloy strip steel rolled stock there is high strength, high use temperature and low elastic modulus temperature factor in wide temperature range (60 ℃～400 ℃).
Wide temperature range high strength constant modulus alloy of the present invention, its chemical composition (wt.%) is Ni 34.0～39.0%, Co 12.0～18.0%, Ti 2.3～3.0%, Al 0.3～0.8%, and Si 0.3～0.8%, and Mn 0.2～0.6%, C < 0.05%, P < 0.02%, S < 0.02%, surplus is Fe, wherein, W+2Mo 5.0～10.0.
The effect of above-mentioned each alloying element and the design considerations of moiety are as follows:
Ni: austenite former, after adding, produce magnetostrictive effect, be the basis that alloy produces permanent elasticity energy;
Co: austenite former, add Co and can significantly carry heavy alloyed Curie temperature, expand alloy use temperature scope;
W, Mo: ferrite former, add W, Mo, mainly play solution strengthening effect.The interpolation of W, Mo, causes alloy lattice distortion, hinders dislocation motion, improves alloy strength;
Ti, Al: form the γ ' phase of dispersion-strengthened with Ni, Co, regulate permanent elasticity energy and the mechanical property of alloy, suitably reduce Ti, Al content can improve alloy Curie temperature;
Si, Mn: add Si, can improve alloy rupture ductility, improve alloy notch susceptibility; Add Mn, can improve alloy processing characteristics;
C, P, S: as impurity element, content is more low better.
Above-mentioned wide temperature range high strength constant modulus alloy preparation method's technical process comprises vacuum induction melting alloy electrode rod+vacuum consumable remelting → forging square billet and hot rolling → cold rolling and vacuum aging thermal treatment.
The preparation method of wide temperature range high strength constant modulus alloy of the present invention, comprises the steps:
1, melting
Utilize vacuum induction melting alloy, be cast into consumable electrode rod, vacuum tightness≤1 * 10
-1pa, will strictly control the scaling loss amount of alloying element in fusion process, make the Composition Control of alloy within scope of design.Wherein, Fe, Ni, Co, W directly put into sweet pot as once reinforced; Ti, Al, Si, Mn, La, Zr, B put into vacuum induction batch hopper as secondary charging, refining 2～10min after all raw materialization is clear, and the vacuum chamber at vacuum induction furnace is cast into electrode bar by molten steel afterwards.Electrode bar is through vacuum consumable remelting, fusion process vacuum tightness≤1 * 10
-2pa, further degassed and refinement inclusion size obtains the ingot that strips off the skin.
2, cogging, heat are pricked
Strip off the skin ingot lower than 600 ℃ of shove charges, and temperature rise rate determines by the size of the ingot that strips off the skin, and after 1050～1150 ℃ of insulation 40～60min, cogging is forged into square billet.After 1080～1130 ℃ of insulation 30～60min, be rolled into band again.
3, cold rolling, thermal treatment
Hot rolled band is cold rolling one-tenth cold rolling strap after annealing, according to the deflection requirement of final use, through 950～1050 ℃ of solution hardening, is cold-rolled to final size, and last cold-rolled steel sheet carries out vacuum aging thermal treatment through 650～750 ℃ of insulation 3～5h.
The wide temperature range high strength constant modulus alloy that this patent relates to, to add appropriate W, Ti, Al on Fe-Ni-Co is the basis of constant elastic alloy, in wide temperature range, keep low elastic modulus temperature factor and high strength, expand the use temperature scope of instrument, improve the precision of instrument.
Embodiment:
The wide temperature range high strength constant modulus alloy that adopts chemical composition of the present invention to prepare, its chemical composition (embodiment 1, embodiment 2, embodiment 3, embodiment 4) as shown in table 1.The chemical analysis results of 4 kinds of composition alloys of vacuum induction melting is as shown in table 2:
The chemical composition of table 1 molten alloy (wt.%)
| Element | Ni | Co | W | Mo | Ti | Al | Si | Mn | C | P | S | W+2Mo | Fe |
| Embodiment 1 | 39.0 | 12.0 | 5.0 | - | 3.0 | 0.32 | 0.79 | 0.21 | 0.009 | 0.008 | 0.007 | 5.0 | More than |
| Embodiment 2 | 37.1 | 16.2 | 7.1 | - | 2.6 | 0.35 | 0.45 | 0.35 | 0.017 | 0.012 | 0.008 | 7.1 | More than |
| Embodiment 3 | 36.0 | 16.5 | 5.2 | 2.1 | 2.7 | 0.39 | 0.30 | 0.59 | 0.011 | 0.010 | 0.012 | 9.8 | More than |
| Embodiment 4 | 34.0 | 18.0 | 3.1 | 2.9 | 2.3 | 0.8 | 0.62 | 0.42 | 0.014 | 0.009 | 0.010 | 8.9 | More than |
The complete processing that the alloy of mentioned component is adopted: above-mentioned wide temperature range high strength constant modulus alloy preparation method's technical process comprises vacuum induction melting alloy electrode rod+vacuum consumable remelting → forging square billet and hot rolling → cold rolling and vacuum aging thermal treatment.Concrete technology parameter, as shown in table 2.
The processing parameter of table 2 molten alloy
Physics, the mechanical property of the Fe-Ni-Co sound stage width temperature range high strength constant modulus alloy of preparing through above-mentioned technique are shown in Table 3, and alloy is greater than 1500MPa at room temperature tensile strength Rm, and elongation at break δ is greater than 3%; In the time of 400 ℃, tensile strength Rm is greater than 1450MPa, and elongation at break δ is greater than 2.5%; In the time of 450 ℃, tensile strength Rm is greater than 1350MPa, and elongation at break δ is greater than 2.5%; Meanwhile, this alloy in the temperature range of-60～400 ℃, its temperature coefficient of the elastic modulus | β
e| lower than 25 * 10
-6/ ℃, alloy material has good intensity and toughness, has the potentiality at applied at elevated temperature.
Table 3Fe-Ni-Co-W alloy physics, mechanical property
Claims (9)
1. a wide temperature range high strength constant modulus alloy, is characterized in that:
The chemical composition of this alloy (wt.%) is Ni 34.0～39.0%, Co 12.0～18.0%, and Ti 2.3～3.0%, and Al 0.3～0.8%, Si 0.3～0.8%, Mn 0.2～0.6%, C < 0.05%, P < 0.02%, S < 0.02%, surplus is Fe, and wherein, W+2Mo 5.0～10.0.
2. wide temperature range high strength constant modulus alloy as claimed in claim 1, is characterized in that:
This alloy adopts following steps preparation: vacuum induction melting alloy electrode rod+vacuum consumable remelting → forging square billet and hot rolling → cold rolling and vacuum aging thermal treatment.
3. wide temperature range high strength constant modulus alloy as claimed in claim 1, is characterized in that:
This alloy has following mechanical property:
In the temperature range of-60～400 ℃, its tensile strength Rm is greater than 1350MPa, and elongation at break δ is greater than 2.5%, temperature coefficient of the elastic modulus β
elower than 25 * 10
-6/ ℃.
4. wide temperature range high strength constant modulus alloy as claimed in claim 1, is characterized in that:
The microtexture of this alloy is the austenitic matrix with magnetostrictive effect, and the γ ' phase of the dispersion-strengthened that forms of Ti, Al and Ni, Co.
5. a preparation method for wide temperature range high strength constant modulus alloy as claimed in claim 1, is characterized in that:
Comprise the steps:
A) melting: utilize vacuum induction melting alloy, be cast into consumable electrode rod, vacuum tightness≤1 * 10
-1pa, consumable electrode rod is through vacuum consumable remelting, fusion process vacuum tightness≤1 * 10
-2pa, further degassed and refinement inclusion size obtains the ingot that strips off the skin;
B) cogging, heat are pricked: the ingot that strips off the skin is lower than 600 ℃ of shove charges, and cogging is forged into square billet, is then rolled into band;
C) cold rolling, thermal treatment: hot rolled band is cold rolling one-tenth cold rolling strap after annealing, and the deflection requirement according to final use, through solution hardening, is cold-rolled to final size, finally cold-rolled steel sheet is carried out to vacuum aging thermal treatment.
6. preparation method as claimed in claim 5, is characterized in that:
In step a, Fe, Ni, Co, W directly put into sweet pot as once reinforced; Ti, Al, Si, Mn put into vacuum induction batch hopper as secondary charging, and after all raw materialization is clear, refining is 2～10 minutes, and the vacuum chamber at vacuum induction furnace is cast into consumable electrode rod by molten steel afterwards.
7. preparation method as claimed in claim 5, is characterized in that:
In step b, forging temperature is 1050～1150 ℃, and forging soaking time is 40～60min.
8. preparation method as claimed in claim 5, is characterized in that:
In step b, hot-rolled temperature is 1080～1130 ℃, and the hot rolling heat holding time is insulation 30～60min.
9. preparation method as claimed in claim 5, is characterized in that:
In step b, quenching temperature is 950～1050 ℃, and thermal treatment temp is 650～750 ℃, and thermal treatment soaking time is 3～5h.
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101280381A (en) * | 2008-05-29 | 2008-10-08 | 钢铁研究总院 | Constant modulus alloy having wide zone and small frequency temperature coefficient |
| CN101280396A (en) * | 2008-05-29 | 2008-10-08 | 钢铁研究总院 | Constant modulus alloy having magnetic induction and low frequency temperature coefficient |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU662612A1 (en) * | 1977-04-06 | 1979-05-15 | Предприятие П/Я Р-6209 | Iron-base dispersion-hardening alloy |
-
2014
- 2014-09-12 CN CN201410466857.2A patent/CN104195404B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101280381A (en) * | 2008-05-29 | 2008-10-08 | 钢铁研究总院 | Constant modulus alloy having wide zone and small frequency temperature coefficient |
| CN101280396A (en) * | 2008-05-29 | 2008-10-08 | 钢铁研究总院 | Constant modulus alloy having magnetic induction and low frequency temperature coefficient |
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