CN109457091A - A method of preparing coarse-grain Fe-Mn-Si base marmem - Google Patents

A method of preparing coarse-grain Fe-Mn-Si base marmem Download PDF

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CN109457091A
CN109457091A CN201811193766.0A CN201811193766A CN109457091A CN 109457091 A CN109457091 A CN 109457091A CN 201811193766 A CN201811193766 A CN 201811193766A CN 109457091 A CN109457091 A CN 109457091A
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grain
minutes
base marmem
marmem
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CN109457091B (en
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彭华备
雍立秋
王勇宁
文玉华
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Sichuan University
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/01—Shape memory effect

Abstract

The invention discloses a kind of methods for preparing coarse-grain Fe-Mn-Si base marmem, belong to marmem field.Austenite grain average-size >=1 millimeter of Fe-Mn-Si base marmem prepared by the present invention.Specific step is as follows: (1) first handling Fe-Mn-Si base marmem 5 minutes to 1 hour at 1260 DEG C ~ 1300 DEG C；(2) following treatment process is then recycled not less than primary: being cooled to 1100 DEG C ~ 1200 DEG C with 0.1 DEG C of per minute ~ 10 DEG C of speed per minute and is handled 5 minutes to 30 minutes；Then 1260 DEG C ~ 1300 DEG C are heated to 0.1 DEG C of per minute ~ 10 DEG C of speed per minute and handled 5 minutes to 1 hour；(3) water cooling is to room temperature after being finally cooled to 1150 DEG C ~ 1200 DEG C with 0.1 DEG C of per minute ~ 5 DEG C of speed per minute.

Description

A method of preparing coarse-grain Fe-Mn-Si base marmem
Technical field
The present invention relates to marmem fields, and in particular to a kind of ferrimanganic silicon substrate shape for preparing coarse austenite grain The method of shape memory alloys.The austenite average grain size of the Fe-Mn-Si base marmem of this method preparation is not less than 1 Millimeter.
Background technique
Ferrimanganic silicon-base alloy has many advantages, such as low in cost, handling ease and good welding performance, therefore since self-discovery just The extensive concern of domestic and foreign scholars is attracted.But the polycrystalline of not specially treated deformation processing (hot rolling, cold rolling or cold drawing) The recoverable strain of ferrimanganic silicon-base alloy only 2% or so, is not achieved the requirement of engineer application.Currently, (deformation at room temperature adds for training 650 DEG C of repetitive processes nearby annealed), the austenite high-temperature particles near 700 DEG C and thermo-mechanical processi these three sides Method is also only capable of its recoverable strain being increased to 4-5%.Meanwhile all there is deformation process in these processing, not only increase and be prepared into This, and complex-shaped element is difficult to carry out.In the recent period, Wen Yuhua et al. is prepared for by the method for casting after annealing processing Stretch training-free casting ferrimanganic silicon-base alloy (Y.H. Wen, et al., Nature that recoverable strain reaches 7.6% Communications, 2014,5:4964).But there are power compared with deformation processing alloy for casting ferrimanganic silicon-base alloy Learn performance difference and the low problem of recovery stress.Therefore, how under conditions of exempting from training, in the deformation processing of good mechanical performance It is that ferrimanganic silicon-base alloy still needs to solve the problems, such as at present that high recoverable strain is obtained in alloy.Peng Huabei etc. utilizes high temperature ferrite Shape memory effect (the H.B. of deformation processing ferrimanganic silicon-base alloy is significantly improved in the case where exempting from training condition to austenite transformation Peng, et al., Metallurgical and Materials Transactions A, 2016, 7: 3277- 3283).Their patent ZL201410102165.X also discloses this method.But they also indicate that deformation processing Fe- 19.38Mn-5.29Si-8.98Cr-4.83Ni(number represents weight percent, similarly hereinafter) alloy in experience high temperature ferrite to Austria Since the crystallite dimension of austenite is smaller (about 110 microns) after the transformation of family name's body, maximum recoverable strain at this time is also 5% or so (H.B. Peng, et al., Advanced Engineering Materials, 2018,20:1700741).Therefore, How exempt from training under conditions of, in the deformation processing ferrimanganic silicon-base alloy of good mechanical performance obtain not less than 6% can be extensive Complex strain is still to still need to solve the problems, such as at present.
Currently, deformation processing ferrimanganic silicon-base alloy recoverable strain is that crystallite dimension is smaller the main reason for being lower than 6%.And The recoverable strain of training-free casting ferrimanganic silicon-base alloy is exactly that austenite grain is coarse up to 7.6% major reason, can Up to 1mm or more (Y.H. Wen, et al., Nature Communications, 2014,5:4964).Therefore, it obtains thick Big austenite grain is the precondition for the recoverable strain that deformation processing ferrimanganic silicon-base alloy is realized not less than 6%.However, The method of roughening austenite grain mainly improves solid solution temperature and extends the solution treatment time at present.But due to iron Manganese silicon-base alloy stacking fault energy is low, and annealing twin is easily formed, this results in the above method that can not effectively increase austenite grain (H.B. Peng, et al.. Materials Science and Engineering A, 2018,712:37-49).
Summary of the invention
In view of the problems of the existing technology, the present invention provides a kind of side for preparing coarse-grain Fe-Mn-Si base marmem Method.
The present invention prepares coarse-grain Fe-Mn-Si base marmem, and specific step is as follows: (1) first by ferrimanganic silicon substrate shape Memorial alloy is handled 5 minutes to 1 hour at 1260 DEG C ~ 1300 DEG C；(2) following treatment process is then recycled not less than primary: with 0.1 DEG C of per minute ~ 10 DEG C of speed per minute is cooled to 1100 DEG C ~ 1200 DEG C and handles 5 minutes to 30 minutes；Then with 0.1 DEG C per minute ~ 10 DEG C of speed per minute be heated to 1260 DEG C ~ 1300 DEG C and handle 5 minutes to 1 hour；(3) finally with 0.1 DEG C Water cooling is to room temperature after DEG C speed per minute is cooled to 1150 DEG C ~ 1200 DEG C per minute ~ 5.The ferrimanganic silicon substrate shape memory closes Gold is single-phase high temperature ferrite at 1260 DEG C ~ 1300 DEG C, and at 1100 DEG C ~ 1200 DEG C is single phase austenite.Ferrimanganic silicon substrate The high temperature ferrite of alloy is easily changed into austenite, therefore final room temperature texture is based on austenite.Step (2) of the present invention Repeatedly phase of the austenite to high temperature ferritic transformation when exactly changing and heat to austenite using high temperature ferrite when cooling Change process first obtains coarse grains even the high temperature ferrite of monocrystalline.And there are two the purposes of step (3): (1) high by control Cooling velocity when warm ferrite changes to austenite, reduces austenite number of nuclei, so that it is coarse to prepare austenite grain Fe-Mn-Si base marmem；(2) retain the defect that high temperature ferrite is generated to austenite transformation (to be conducive to improve shape Memory effect) and inhibit the formation of annealing twin, so that Fe-Mn-Si base marmem be allowed to obtain more excellent shape Memory effect.
To obtain coarseer austenite grain, the circulating treatment procedure of above-mentioned steps (2) is preferably not below three times.This hair Austenite grain average-size >=1 millimeter of the Fe-Mn-Si base marmem of bright preparation.The ferrimanganic silicon substrate shape memory Alloy contains Fe, Mn, Si and Cr element, and includes one of Ni, Ti, Nb, Cu, Co, V, Mo, Al, C and N element or a variety of, The weight percent content of each element in alloy are as follows: Mn 12 ~ 32%, Si 4 ~ 7%, Cr 0 ~ 14%, Ni 0 ~ 8%, Ti 0 ~ 1%, Nb It 0 ~ 2%, Cu 0 ~ 1%, Co 0 ~ 2%, V 0 ~ 2%, Mo 0 ~ 2%, Al 0 ~ 3%, C 0 ~ 0.2%, N 0 ~ 0.2%, Yu Wei Fe and can not keep away The impurity exempted from.
The present invention has the advantage that (1) normative heat treatment equipment can complete preparation process.(2) deformation prepared adds The austenite grain of work ferrimanganic silicon-base alloy is coarse, and recoverable strain reaches 6.5% or more.(3) without complicated deformation plus annealing Process, the processing suitable for complex parts.
Specific embodiment
Below with reference to embodiment, the invention will be further described.It is worth noting that the embodiment provided cannot understand Person skilled in the art for limiting the scope of the invention, the field makes the present invention according to the content of aforementioned present invention Some nonessential modifications and adaptations still should belong to the scope of the present invention.
The weight percent of each element of the selected cold rolling state Fe-Mn-Si base marmem of embodiment are as follows: Mn 19.2%, Si 5.6%, Cr 10.1%, Ni 4.8%, C 0.01%, Yu Wei Fe and inevitable impurity.When temperature is higher than At 1260 DEG C, which is single-phase high temperature ferrite；When temperature is lower than 1178 DEG C, which is single phase austenite.
The concrete processing procedure of embodiment 1 is as follows: (1) first handling 15 minutes at 1270 DEG C；(2) following processing is then recycled Process is twice: being cooled to 1150 DEG C with 5 DEG C of speed per minute and handles 10 minutes；Then with 5 DEG C of speed heating per minute It is handled 15 minutes to 1270 DEG C；(3) water cooling is to room temperature after being finally cooled to 1160 DEG C with 1 DEG C of speed per minute.
The concrete processing procedure of embodiment 2 is as follows: (1) first handling 10 minutes at 1270 DEG C；(2) following processing is then recycled Process four times: being cooled to 1120 DEG C with 8 DEG C of speed per minute and handle 10 minutes；Then with 8 DEG C of speed heating per minute It is handled 20 minutes to 1270 DEG C；(3) water cooling is to room temperature after being finally cooled to 1170 DEG C with 0.5 DEG C of speed per minute.
Austenite average grain size is characterized using metallographic method.Recoverable strain, specific steps are characterized using bending method are as follows: Then alloy is restored 5 points in 600 DEG C of heating by first 10 DEG C of bending deformation 13% more than Ms (martensite start) point by alloy Clock finally measures the recoverable strain of alloy.The austenite average grain size of embodiment 1 has reached 1.8 millimeters, can restore to answer Change has reached 7.1%.The austenite average grain size of embodiment 2 has reached 3.1 millimeters, and recoverable strain has reached 7.7%.On It states result and clearly illustrates that the present invention is successfully prepared the coarse Fe-Mn-Si base marmem of austenite grain, can restore Strain has reached level (Y.H. Wen, the et al., Nature of training-free casting Fe-Mn-Si base marmem Communications, 2014,5:4964).

Claims (5)

1. a kind of method for preparing coarse-grain Fe-Mn-Si base marmem, which is characterized in that specific step is as follows:
(1) first Fe-Mn-Si base marmem is handled 5 minutes to 1 hour at 1260 DEG C ~ 1300 DEG C；
(2) following treatment process is then recycled not less than primary: being cooled to 0.1 DEG C of per minute ~ 10 DEG C of speed per minute 1100 DEG C ~ 1200 DEG C and processing 5 minutes to 30 minutes；Then 1260 are heated to 0.1 DEG C of per minute ~ 10 DEG C of speed per minute DEG C ~ 1300 DEG C and processing 5 minutes to 1 hour；
(3) water cooling is to room temperature after being finally cooled to 1150 DEG C ~ 1200 DEG C with 0.1 DEG C of per minute ~ 5 DEG C of speed per minute.
2. a kind of method for preparing coarse-grain Fe-Mn-Si base marmem according to claim 1, which is characterized in that iron Manganese silicon substrate marmem is single-phase high temperature ferrite at 1260 DEG C ~ 1300 DEG C, and is single-phase at 1100 DEG C ~ 1200 DEG C Austenite.
3. a kind of method for preparing coarse-grain Fe-Mn-Si base marmem according to claim 1, which is characterized in that step Suddenly the circulating treatment procedure of (2) is not less than three times.
4. a kind of method for preparing coarse-grain Fe-Mn-Si base marmem according to claim 1, which is characterized in that warp Austenite grain average-size >=1 millimeter of Fe-Mn-Si base marmem after this method processing.
5. a kind of method for preparing coarse-grain Fe-Mn-Si base marmem according to claim 1 or 2 or 3 or 4, special Sign is that the Fe-Mn-Si base marmem contains Fe, Mn, Si and Cr element, and include Ni, Ti, Nb, Cu, Co, V, One of Mo, Al, C and N element or a variety of, the weight percent content of each element in alloy are as follows: Mn 12 ~ 32%, Si 4 ~ 7%, Cr 0 ~ 14%, Ni 0 ~ 8%, Ti 0 ~ 1%, Nb 0 ~ 2%, Cu 0 ~ 1%, Co 0 ~ 2%, V 0 ~ 2%, Mo 0 ~ 2%, Al 0 ~ 3%, C 0 ~ 0.2%, N 0 ~ 0.2%, Yu Wei Fe and inevitable impurity.
CN201811193766.0A 2018-10-15 2018-10-15 Method for preparing coarse-grain Fe-Mn-Si-based shape memory alloy Expired - Fee Related CN109457091B (en)

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109913764A (en) * 2019-04-10 2019-06-21 四川大学 A method of improving ferrimanganic alumel memory performance stability
CN113930693A (en) * 2021-10-14 2022-01-14 哈尔滨工程大学 Fe-Mn-Al-Ni-Cu super-elastic alloy and preparation method thereof

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CN107699667A (en) * 2017-09-21 2018-02-16 四川大学 A kind of method for preparing magnetic Fe-Mn-Si base marmem
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109913764A (en) * 2019-04-10 2019-06-21 四川大学 A method of improving ferrimanganic alumel memory performance stability
CN113930693A (en) * 2021-10-14 2022-01-14 哈尔滨工程大学 Fe-Mn-Al-Ni-Cu super-elastic alloy and preparation method thereof

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