CN101613843B - Component design method of multi-component bulk iron-based amorphous alloy material - Google Patents
Component design method of multi-component bulk iron-based amorphous alloy material Download PDFInfo
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Abstract
The invention discloses a component design method of a multi-component bulk iron-based amorphous alloy material, and relates to an amorphous alloy material and provides a component design method of a multi-component bulk iron-based amorphous alloy material with high glass forming capability. The component design method comprises the following steps of: according to influences of different elements to precipitated phases, defining proper elements from thermodynamics database as adding elements, calculating a Fe-C longitudinal section pseudo-binary diagram by using Thermol-calc commercial phase diagram calculation software; adjusting the temperature and component coordinate of the pseudo-binary diagram, leading the carbon content coordinate range to contain eutectic points and determining component lines from the pseudo-binary diagram; observing initial phases near a liquid phase line and precipitated phases near the temperature of nasal tip, judging whether to meet the requirements of being beneficial to amorphously forming the precipitated phases, if so, selecting carbon atom content near the eutectic points, determining final components, calculating a phase fraction diagram, further obtaining data of precipitation amount of all the phases, and finally preparing amorphous alloy according to components; and if no, returning.
Description
Technical field
The present invention relates to a kind of amorphous alloy material, especially relate to a kind of composition design method of multicomponent bulk iron-based amorphous alloy material of high glass forming ability.
Background technology
Metallic glass normally is cooled to molten metal to solidify below the glass transformation temperature and before forming core and crystallization formation.Common metal and alloy all want crystallization to form crystal when liquid cooled is got off.Yet, had been found that some metal and alloy when rate of cooling is enough fast, the extreme viscid state in the time of when solidifying, can keeping liquid state, thus suppressing crystallization, this rate of cooling need reach p.s. 10 usually
4～10
6The order of magnitude of K.In order to obtain so high rate of cooling, molten metal or alloy can only be sprayed onto on the extraordinary conductive substrate of heat conduction.The alloy of Huo Deing is a non-crystaline amorphous metal like this, but size is very little.Therefore, previously obtd amorphous alloy material all is that molten metal or alloy are ejected into the strip that obtains on the copper roller of high speed rotating, or is cast to the thin slice that obtains in the cold substrate and powder etc.Looked for recently have the non-crystaline amorphous metal of stronger inhibition crystallizing power, so just can utilize lower rate of cooling to suppress crystallization.If under very low rate of cooling, can suppress crystallization, then can make larger sized non-crystaline amorphous metal.
Non-crystaline amorphous metal, especially Fe-based amorphous alloy since being found, just have been subjected to material scholar and physicist's extensive concern always.Its reason be iron-base large-block amorphous alloy in the middle of various noncrystal and crystal systems, have high strength, high rigidity, high anti-corrosion, have characteristics such as good toughness and soft magnetic performance.Since iron-base large-block amorphous alloy comes out, improve amorphous formation ability, obtain large-sized non-crystaline amorphous metal and be always one of major objective that people lay siege to.The Status of development of iron-based soft magnetic non-crystaline amorphous metal is taught ([1] Duwez and C.H.Lin:Amorphous ferromagnetic phase inFe-C-P Alloys.J.Appl.Phys.38 from U.S. Duwez in 1967,4096 (1967)) taken the lead in since success develops Fe-P-C and be soft magnetic amorphous strip, many scientists have paid a large amount of effort in the process of synthetic new iron-based non-crystaline amorphous metal with excellent soft magnetic performance.U.S. AlliedSignal companies in 1979 develop the plane flow Cast Strip technology in non-crystaline amorphous metal broadband, and release Fe base, Co base, the Fe-Ni base system row amorphous alloy strips of name Metglass in nineteen eighty-two.The people such as Yashizawa of FDAC metal company in 1988 develop FeCuNbSiB nano-crystal soft magnetic alloy Finemet with low cost by the crystallization processing on the non-crystaline amorphous metal basis, have high magnetic strength and the high magnetic permeability of cobalt base amorphous alloy, high saturated magnetic strength and low-loss characteristics of Fe-based amorphous alloy concurrently.Nineteen ninety, people such as Makino develop FeMB (M=Zr, Hf, Nb) nanometer crystal alloy Nanoperm, its saturation induction density is higher than 1.5T.1998, people such as the WillardMA of the U.S. ([2] M.A.Willard, D.E.Laughlin, M.E.McHenry, D.Thoma, K.Sickafus, J.O.Cross and V.G.Harris:Structure and magnetic properties of (Fe
0.5Co
0.5)
88Zr
7B
4Cu
1Nanocrystalline alloys.J.Appl.Phys.84,6773 (1998)) announced and can be used for pyritous FeCoZrBCu nano-crystal soft-magnetic Hitperm that its magnetic induction density is higher than 2.0T.Since the nineties in 20th century, the exploitation of iron-based soft magnetic block non-crystaline amorphous metal obtains sizable progress.These alloys can be divided into following five big main systems:
①Fe-(Al，Ga，Sn)-(P，C，B，Si，Ge)；
②Fe-(Co，Ni)-M-B(M＝Zr，Hf，Ti，V，Nb，Ta，Mo，W)；
③Fe-Co-Ln-B-M(M＝Cr，V，Hf，W，Mo，Nb，Ta，Zr)；
④Fe-(Cr，Mo，Ni，Nb)-(Al，Ga)-(P，C，B)；
⑤Fe-(Co，Ni)-B-Si-(Zr，Nb)。
At present, the research and development of iron-based soft magnetic block non-crystaline amorphous metal have entered a new period.There is a class Fe-based amorphous alloy not manifest magnetic characteristic in room temperature or more than the room temperature, so be known as no magnetic non-crystaline amorphous metal. the overall dimension of the Fe-based amorphous alloy that obtains with copper mold casting has reached 16mm, and is named as " amorphous steel ".Amorphous steel has good development prospect and researching value as non-magnetic material and structured material.Amorphous steel at room temperature is no magnetic properties and has characteristics such as high rigidity, height is anti-corrosion, can be used as a kind of novel special purpose material.Because raw materials used is not precious metal, the amorphous phase of preparation price and other system is than much cheap, so amorphous steel is expected to replace the crystal ferrous materials in some occasion., will be in the non-crystal system a kind of of future in engineering applications to be arranged most more, open up road as structured material in actual application in engineering for large block amorphous because its good amorphous crystallized ability, preparation technology is easy.
People such as Luo Chongyang ([3] Luo Chongyang, Pan Mingxiang, Kou Shengzhong, Zhao Deqian, Wang Weihua: the formation of Fe56Mn5Cr7Mo12Er2C12B6 amorphous steel. Science Bulletin 3,50 (2005)) reported the formation of Fe56Mn5Cr7Mo12Er2C12B6 amorphous steel.
Yet up to the present, though proposed the theory of numerous relevant amorphous formation aspects, but can really apply to also almost not having of amorphous component design aspect, some Forecasting Methodologies before also only are applicable to the composition that constituent element is less, and design is also felt simply helpless for the multicomponent especially amorphous component more than the quaternary.
Summary of the invention
The object of the present invention is to provide a kind of composition design method of multicomponent bulk iron-based amorphous alloy material of high glass forming ability, the present invention also is applicable to the composition design of the bulk amorphous alloys of other matrixes.
The present invention considers the thermodynamics and kinetics factor of the whole process of setting of alloy solution, from the cluster condensate depression, the primary phase motivating force, aspects such as the pre-precipitated phase kinetics in CCT or TTT curve nose temperature place (sizableness is in about 80% melting temperature) derive the composition design method of non-crystaline amorphous metal
The present invention includes following steps:
1) according to of the influence of different elements to precipitated phase, from the thermodynamic data storehouse, define suitable element as adding element, go out the pseudo-binary phase diagram in Fe-C vertical section with the commercial calphad computed in software of Thermol-calc;
2) adjust the temperature and the component coordinate scope of the pseudo-binary phase diagram in Fe-C vertical section, and make the carbon content coordinate range comprise eutectic point, from the pseudo-binary phase diagram in Fe-C vertical section, be specified to separated time, wherein, Fe is as matrix, and C reduces the most important element of Fe fusing point, and other elements add as disturbance term;
3) observe near primary phase of liquidus line and near the precipitated phase the nose temperature, see the requirement of whether satisfying the precipitated phase that helps amorphous formation,, should avoid the preferential generation of following phase: FCC_A1, CARBIDE, MC promptly at the liquidus line place; Allow the following tendency that becomes primary phase mutually: BCC, HCP_A2, MB, the nose temperature place of CCT or TTT curve should avoid the generation of following phase: FCC_A1, and MC allows following tending to mutually generate: M
7C
3, M
23C
6, M
6C, MB;
4) if satisfy step 3), then near eutectic point, choose carbon content, determine the ultimate constituent, calculate phase fraction (BPW) figure, further obtain each data of the amount of separating out mutually, prepare non-crystaline amorphous metal according to composition at last;
If do not satisfy step 3), then return step 1).
In step 1), described element is Fe-based amorphous element, wherein, the part element comprise little atomic element (C, N, Si, S, P) and transition metal (Ti, V, Cr, Mn, Co, Ni, Zr, Nb, Mo, Hf, Ta, W).
In step 2) in, described carbon content is 10%～20% to be advisable by carbon atom percentage ratio preferably.
The present invention is applicable to the non-crystaline amorphous metal of other systems.
Can use software and the database with identity function for thermodynamic (al) calculating, BPW figure also can have other composition-temperature relation figure to substitute.
Existing amorphous component has been carried out checking and utilized this method to design a series of new amorphous components.
Have various cluster structures in the alloy solution, wherein take as the leading factor to have high symmetric icosahedron cluster, its local highly dense heap configurational energy effectively reduces the free energy of liquid phase.Mostly cluster is the multiple twin of FCC structure, consider overall configuration for the contribution that reduces free energy greater than the part, below fusing point, cluster is sacrificed short range order and is reconstituted the FCC with long-range Mi Dui, structures such as HCP or BCC.According to expression of free energy: G=H-TS, the reduction of the S that the reduction of filling up H that free volume is brought bigger between cluster brings more than long-range order obtains being suitable for the following configuration of melting temperature thereby reduce the system free energy.
The shape of CCT and TTT curve is the coefficient result of kinetics and thermodynamics, viscosity owing to system more than nose temperature (sizableness is in about 80% melting temperature) is very little, the forming core crystallization mainly is the process by thermodynamic control, condensate depression is big more, the forming core motivating force is also big more, and crystallization velocity is also just fast more.Below the nose temperature, the viscosity of system has increased several magnitude, and the forming core crystallisation process of this moment is by kinetic control, and temperature is low more, and atomic diffusion speed is more little, causes a low crystallization velocity.Obviously,, tackle this two aspect and consider simultaneously for the forming process of amorphous, to whole process of setting analysis, indispensable.
Comprise composition and structure mutually, whole process of setting is accompanied by the change procedure of precipitated phase composition and structure, at first tackles all precipitated phases of system and does systematic research.The method that combines with calculating by experiment, for ferrous alloy, learn main precipitated phase comprise sosoloid mutually with compound mutually, and all can be used as the expansion of Fe-C alloy phase handled, mainly comprised FCC, HCP_A3, BCC_A2, CEMENTITE, CARBIDE, M
7(C, B)
3, M
23(C, B)
6, MC, MB wherein M represent alloying element, and these all exist with the form of sosoloid or alloy carbide mutually.
For the sosoloid phase, can be added on and have simultaneously among α-Fe and the γ-Fe or single alloying element with big solubleness.On the one hand, can cause the lattice unstability.Be exactly that the bond distance who satisfies the formation of large size cluster does not wait requirement on the other hand.What distortion caused that unstability has outstanding contributions to γ-Fe solid solution lattice is elements such as Ni, Co, Mn, Cr, and that α-Fe solid solution lattice distortion is caused that unstability has outstanding contributions is Al, V, Mo, W, Cr, elements such as Co.The process of the formation by understanding cluster can know that the configuration that energy is minimum should approach dense arrangement as far as possible.The stability of cluster is relevant with how much formations of atom, and the new coplanar bonding mode of the always former tetrahedron of adatom is more strong on energy.As there being the FCC phase in the primary phase, cluster can preferentially change the FCC structure into by twin when reduced size, thereby reduces its surface energy and strain energy.According to the energy barrier principle, corresponding to different primary phases, the stability of cluster is followed successively by (high to low): BCC, HCP, FCC.
For carbide, carbide forming element by by force to a little less than be followed successively by:
Zr，Ti，Nb，V，W，Mo，Cr，Mn，Fe。
The structural information of each element carbide, the carbide that should avoid having the FCC simple configuration is separated out, and infers that thus adding element can only arrive W.When carbon content was low, the strong carbide forming element preferentially formed carbide; When carbon content is higher, weak carbide forming element also will form carbide, as W, Mo, Cr, along with the increase of carbon content, form successively (Fe, W, Mo)
6C, (Fe, Cr)
23C
6, (Fe, Cr)
7C
3, Fe
3C.
Add carbide forming element and must follow following principle:
1. add the strong carbide forming element, suppress austenite and separate out.
2. carbide forming element in adding suppresses austenite and separates out, and forms the complex construction carbide at nose temperature place.
3. the adding rare earth element further slows down carbide and separates out, but can promote the generation of austenite and rare earth carbide simultaneously, so should add on a small quantity.
The present invention has analyzed the influence of part element to alloy by Theoretical Calculation and experimental verification, and the electrochemistry and the physical properties of comprehensive element can roughly be classified to it:
1) be fit to add or only be fit to a small amount of element that adds:
The reduction meta is that the element of eutectic temperature is: Mo, Mn, W, Si, Ni, Cu, Co.
The element that forms complicated carbide is: Cr, Mo.
Solidify is that the bigger transition metal of partition ratio is: Mn, Cr.
The non-compound formation element that forms short range order bunch with C is: RE.
The element that reduces carbon activity is: Mn, Cr, Mo, V, W.
2) be not suitable for adding or be not suitable for a large amount of elements that add:
The strong carbide forming element is: Hf, Zr, Ti, Ta, Nb.
The raising meta is that the element of eutectic temperature is: Al, V, Ti.
The element that improves carbon activity in the iron liquid is: Al, Si, Cu, Ni, Co.
The too small element of partition ratio is when solidifying: V, Ti.
At the liquidus line place, consider the thermodynamics factor, should avoid the preferential generation of following phase: FCC_A1, CARBIDE, MC.Allow the following tendency that becomes primary phase mutually: BCC, HCP_A2, MB.
The nose temperature place of CCT or TTT curve considers kinetic factor, should avoid following phase: FCC_A1, MC.Allow following tendency mutually generate: M
7C
3, M
23C
6, M
6C, MB.
The amorphous that the present invention proposes forms the influence that mechanism and composition design method have taken into full account the each side factor, and is widely applicable, comparatively effective at present for the composition design that multicomponent is large block amorphous.It is big that the Fe-based amorphous alloy that obtains has hardness, the intensity height, and characteristics such as erosion resistance is strong, but scarcely have magnetic.
Description of drawings
Fig. 1 is FeCr
10Mo
12B
8C is a Fe-C multicomponent alloy vertical cross-section phasor.In Fig. 1, X-coordinate is carbon atomic percentage conc C/at.%, and ordinate zou is temperature T emperature/K; Symbol representative successively from top to bottom among the figure: L liquid phase; BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA); MoB 1 (Mo): 1 (B); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); CARBIDE 3.0 (CR, FE, MO, W): 1.0 (C); M23C620 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C).
Fig. 2 is Fe
55Cr
10Mo
12B
8C
16Multicomponent alloy phase fraction figure.In Fig. 2, X-coordinate is temperature T emperatrue/K, and ordinate zou is phase fraction (BPW); Symbol from left to right is expressed as successively among the figure: BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); MoB 1 (Mo): 1 (B); FCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 1.0 (C, N, VA); CARBIDE 3.0 (CR, FE, MO, W): 1.0 (C); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); The L liquid phase; HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA).
Fig. 3 is FeCr
18Mo
16B
8C is a Fe-C multicomponent alloy vertical cross-section phasor.In Fig. 3, X-coordinate is carbon atomic percentage conc C/at.%, and ordinate zou is temperature T emperature/K; Symbol representative successively from top to bottom among the figure: L liquid phase; HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA); MoB 1 (Mo): 1 (B); M7C37.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); CARBIDE 3.0 (CR, FE, MO, W): 1.0 (C); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); M6C2.0 (CO, FE, NI): 2.0 (MO, NB, W): 2.0 (CO, CR, FE, MO, NB, NI, V, W): 1.0 (C).
Fig. 4 is Fe
46Cr
18Mo
16B
8C
12Multicomponent alloy phase fraction figure.In Fig. 4, X-coordinate is temperature T emperatrue/K, and ordinate zou is phase fraction (BPW); Symbol from left to right is expressed as successively among the figure: BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); MoB 1 (Mo): 1 (B); HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA); M7C37.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); The L liquid phase.
Fig. 5 is FeCr
18Mo
18W
2B
7C is a Fe-C multicomponent alloy vertical cross-section phasor.In Fig. 5, X-coordinate is carbon atomic percentage conc C/at.%, and ordinate zou is temperature T emperature/K; Symbol representative successively from top to bottom among the figure: L liquid phase; BCC1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA); MoB 1 (Mo): 1 (B); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); M6C2.0 (CO, FE, NI): 2.0 (MO, NB, W): 2.0 (CO, CR, FE, MO, NB, NI, V, W): 1.0 (C); MC 1.0 (MO, W): 1.0 (C, N); M2B 2.0 (CO, CR, FE, MO, NB, NI, V, W): 1.0 (B).
Fig. 6 is Fe
43Cr
18Mo
18W
2B
7C
12Multicomponent alloy phase fraction figure.In Fig. 6, X-coordinate is temperature T emperatrue/K, and ordinate zou is phase fraction (BPW); Symbol from left to right is expressed as successively among the figure: BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); MoB 1 (Mo): 1 (B); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); The L liquid phase.
Fig. 7 is FeCr
14Mo
10W
2B
9C is a Fe-C multicomponent alloy vertical cross-section phasor.In Fig. 7, X-coordinate is carbon atomic percentage conc C/at.%, and ordinate zou is temperature T emperature/K; Symbol representative successively from top to bottom among the figure: L liquid phase; BCC1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); MoB 1 (Mo): 1 (B); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); MC 1.0 (MO, W): 1.0 (C, N); Fe2B 2.0 (Fe): 1.0 (B).
Fig. 8 is Fe
53Cr
14Mo
10W
2B
9C
12Multicomponent alloy phase fraction figure.In Fig. 8, X-coordinate is temperature T emperatrue/K, and ordinate zou is phase fraction (BPW); Symbol from left to right is expressed as successively among the figure: and M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); MC 1.0 (MO, W): 1.0 (C, N); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); MoB 1 (Mo): 1 (B); BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); CARBIDE 3.0 (CR, FE, MO, W): 1.0 (C); The L liquid phase.
Fig. 9 is FeCr
16Mo
12Al
2B
7C is a Fe-C multicomponent alloy vertical cross-section phasor.In Fig. 9, X-coordinate is carbon atomic percentage conc C/at.%, and ordinate zou is temperature T emperature/K; Symbol representative successively from top to bottom among the figure: L liquid phase; BCC1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); HCP 2.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, SI, TI, V, W): 0.5 (C, N, VA); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); MoB 1 (Mo): 1 (B); CARBIDE 3.0 (CR, FE, MO, W): 1.0 (C); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); MC 1.0 (MO, W): 1.0 (C, N); Fe2B 2.0 (Fe): 1.0B); M3C2 3.0 (CR, MO, V, W): 2.0 (C).
Figure 10 is Fe
49Cr
16Mo
12A
L2B
7C
14Multicomponent alloy phase fraction figure.In Figure 10, X-coordinate is temperature T emperatrue/K, and ordinate zou is phase fraction (BPW); Symbol from left to right is expressed as successively among the figure: and M3C2 3.0 (CR, MO, V, W): 2.0 (C); M23C6 20 (CO, CR, FE, MN, NI, V): 3 (CO, CR, FE, MN, MO, NI, V, W): 6 (C); BCC 1.0 (AL, CO, CR, CU, FE, MG, MN, MO, NB, NI, P, S, SI, TI, V, W): 3.0 (C, N, VA); MoB1 (Mo): 1 (B); M7C3 7.0 (CO, CR, FE, MN, MO, NI, V, W): 3.0 (C); CARBIDE 3.0 (CR, FE, MO, W): 1.0 (C); The L liquid phase.
Embodiment
Enumerate several embodiment that utilize method of the present invention to design bulk iron-based amorphous composition below.
Embodiment 1:FeCr
10Mo
12B
8The C system
Step 1: from the thermodynamic data storehouse, define element of Fe, Cr, Mo, C, B, go out the pseudo-binary phase diagram in Fe-C vertical section with the commercial calphad computed in software of Thermol-calc.
Step 2: adjust range of views, make the scope of C content coordinate comprise eutectic point just, as shown in Figure 1.
Step 3: can be observed near the primary phase of liquidus line is HCP, at the eutectic point place MoB phase is arranged, and with HCP, BCC, M7C3 are pre-precipitated phase in the interval range more than hypereutectic some nose temperature, satisfies the requirement that each precipitated phase is crossed size between the cold-zone substantially.
Step 4: choose the C 16at% place of hypereutectic a little point, determine composition, calculate BPW figure, obtain each amount of separating out in process of setting, as shown in Figure 2.Can see having a small amount of FCC to separate out mutually, other reach requirement substantially.
Step 5: the Fe-based amorphous alloy of present embodiment is made up of Fe, Cr, Mo, C, B and Y element, each elements atomic percentage is: Fe 54～58%, Cr 8%～10%, Mo 12%, C 14%～16%, B 8%, Y2%, prepare burden after being converted into weight percent.With highly purified batching arc melting in the argon gas of titanium absorption, make it to mix, cooling obtains ingot casting.Then mother alloy is moved on to the suction blowhole, evenly the fusing back sucks in the copper mold once more, has prepared the non-crystal bar of diameter 3mm.
Embodiment 2:FeCr
18Mo
16B
8The C system
Step 1: from the thermodynamic data storehouse, define element of Fe, Cr, Mo, C, B, calculate the pseudo-binary phase diagram in Fe-C vertical section with Thermol-calc.
Step 2: adjust range of views, make the scope of C content coordinate comprise eutectic point just, as shown in Figure 3.
Step 3: can be observed near the primary phase of liquidus line is HCP
3, through generating the BCC phase after the little condensate depression, in the interval range more than hypereutectic some nose temperature with HCP, BCC, M
23C
6Be pre-precipitated phase, satisfy the requirement that each precipitated phase is crossed size between the cold-zone substantially.
Step 4: choose the C 12at% place of hypereutectic a little point, determine composition, calculate BPW figure, obtain each amount of separating out in process of setting, as shown in Figure 4.Can see and reach requirement on a large scale.
Step 5: the Fe-based amorphous alloy of present embodiment is made up of Fe, Cr, Mo, W, C, B and Y element, each elements atomic percentage is: Fe 44～48%, Cr 16%～18%, Mo 16%, C 10%～12%, B 8%, Y2%, prepare burden after being converted into weight percent.With highly purified batching arc melting in the argon gas of titanium absorption, make it to mix, cooling obtains ingot casting.Then mother alloy is moved on to the suction blowhole, evenly the fusing back sucks in the copper mold once more, has prepared the non-crystal bar of diameter 3mm.
Embodiment 3:FeCr
18Mo
18W
2B
7The C system
Step 1: from the thermodynamic data storehouse, define element of Fe, Cr, Mo, W, C, B, calculate the pseudo-binary phase diagram in Fe-C vertical section with Thermol-calc.
Step 2: adjust range of views, make the scope of C content coordinate comprise eutectic point just, as shown in Figure 5.
Step 3: can be observed near the primary phase of liquidus line is BCC and HCP
3, through generating the MoB phase after the little condensate depression, in the interval range more than hypereutectic some nose temperature with HCP, BCC, M
23C
6, M6C is pre-precipitated phase, satisfies the requirement that each precipitated phase is crossed size between the cold-zone substantially.
Step 4: choose the C 12at% place of hypereutectic a little point, determine composition, calculate BPW figure, obtain each amount of separating out in process of setting, as shown in Figure 6.Reach requirement on a large scale as can be seen.
Step 5: the Fe-based amorphous alloy of present embodiment is made up of Fe, Cr, Mo, W, C, B and Y element, each elements atomic percentage is: Fe 48～52%, Cr 16%～18%, Mo 18%, W 2%, C 10%～12%, B 8%, Y2%, prepare burden after being converted into weight percent.With highly purified batching arc melting in the argon gas of titanium absorption, make it to mix, cooling obtains ingot casting.Then mother alloy is moved on to the suction blowhole, evenly the fusing back sucks in the copper mold once more, has prepared the non-crystal bar of diameter 3mm.
Embodiment 4:FeCr
14Mo
10W
2B
9The C system
Step 1: from the thermodynamic data storehouse, define element of Fe, Cr, Mo, W, C, B, calculate the pseudo-binary phase diagram in Fe-C vertical section with Thermol-calc.
Step 2: adjust range of views, make the scope of C content coordinate comprise eutectic point just, as shown in Figure 7.
Step 3: can be observed near the primary phase of liquidus line is M
7C
3, through generating the MoB phase after the little condensate depression, in the interval range more than hypereutectic some nose temperature with M
23C
6, MoB, M
7C
3Be pre-precipitated phase, satisfy the requirement that each precipitated phase is crossed size between the cold-zone substantially.
Step 4: choose the C 12at% place of hypereutectic a little point, determine composition, calculate BPW figure, obtain each amount of separating out in process of setting, as shown in Figure 8.Reach requirement on a large scale as can be seen.
Step 5: the Fe-based amorphous alloy of present embodiment is made up of Fe, Cr, Mo, W, C, B and Y element, each elements atomic percentage is: Fe 51～55%, Cr 12%～14%, Mo 10%, C 10%～12%, B 9%, Y 2%, prepare burden after being converted into weight percent.With highly purified batching arc melting in the argon gas of titanium absorption, make it to mix, cooling obtains ingot casting.Then mother alloy is moved on to the suction blowhole, evenly the fusing back sucks in the copper mold once more, has prepared the non-crystal bar of diameter 3mm.
Embodiment 5:FeCr
16Mo
12Al
2B
7The C system
Step 1: from the thermodynamic data storehouse, define element of Fe, Cr, Mo, Al, C, B, calculate the pseudo-binary phase diagram in Fe-C vertical section with Thermol-calc.
Step 2: adjust range of views, make the scope of C content coordinate comprise eutectic point just, as shown in Figure 9.
Step 3: can be observed near the primary phase of liquidus line is HCP and BCC
3, generating M through after the little condensate depression
7C
3Phase, in the interval range more than hypereutectic some nose temperature with M
23C
6, MoB, M
7C
3Be pre-precipitated phase, satisfy the requirement that each precipitated phase is crossed size between the cold-zone substantially.
Step 4: choose the C 14at% place of hypereutectic a little point, determine composition, calculate BPW figure, obtain each amount of separating out in process of setting, as shown in figure 10.Reach requirement on a large scale as can be seen.
Step 5: the Fe-based amorphous alloy of present embodiment is made up of Fe, Cr, Mo, Al, C, B and Y element, each elements atomic percentage is: Fe 47～51%, Cr 14%～16%, Mo 12%, Al 2%, C 12%～14%, B 7%, Y 2%, prepare burden after being converted into weight percent.With highly purified batching arc melting in the argon gas of titanium absorption, make it to mix, cooling obtains ingot casting.Then mother alloy is moved on to the suction blowhole, evenly the fusing back sucks in the copper mold once more, has prepared the non-crystal bar of diameter 3mm.
Each element to out of phase influence referring to table 1.
Claims (2)
1. the composition design method of multicomponent bulk iron-based amorphous alloy material is characterized in that may further comprise the steps:
1) according to of the influence of different elements to precipitated phase, from the thermodynamic data storehouse, define suitable element as adding element, go out the pseudo-binary phase diagram in Fe-C vertical section with the commercial calphad computed in software of Thermol-calc, described element is Fe-based amorphous element, wherein, the part element comprises little atomic element: C, N, Si, S, P and transition metal: Ti, V, Cr, Mn, Co, Ni, Zr, Nb, Mo, Hf, Ta, W;
2) adjust the temperature and the component coordinate scope of the pseudo-binary phase diagram in Fe-C vertical section, and make the carbon content coordinate range comprise eutectic point, from the pseudo-binary phase diagram in Fe-C vertical section, be specified to separated time, wherein, Fe is as matrix, and C reduces the most important element of Fe fusing point, and other elements add as disturbance term;
3) observe near primary phase of liquidus line and near the precipitated phase the nose temperature, see the requirement of whether satisfying the precipitated phase that helps amorphous formation,, should avoid the preferential generation of following phase: FCC_A1, CARBIDE, MC promptly at the liquidus line place; Allow the following tendency that becomes primary phase mutually: BCC, HCP_A2, MB, the nose temperature place of CCT or TTT curve should avoid the generation of following phase: FCC_A1, and MC allows following tending to mutually generate: M
7C
3, M
23C
6, M
6C, MB;
4) if satisfy step 3), then near eutectic point, choose carbon content, determine the ultimate constituent, calculate phase fraction figure, further obtain each data of the amount of separating out mutually, prepare non-crystaline amorphous metal according to composition at last;
If do not satisfy step 3), then return step 1).
2. the composition design method of multicomponent bulk iron-based amorphous alloy material as claimed in claim 1 is characterized in that in step 2) in, described carbon content is 10%～20% by carbon atom percentage ratio.
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| CN105950946B (en) * | 2016-07-01 | 2017-11-21 | 广西大学 | A kind of method that high-entropy alloy composition design is carried out based on segregation situation between constituent element |
| CN106756639A (en) * | 2016-11-23 | 2017-05-31 | 江西省电力设备总厂 | A kind of block Fe-based amorphous alloy and preparation method thereof |
| CN111681716A (en) * | 2020-06-19 | 2020-09-18 | 国电锅炉压力容器检验有限公司 | Component optimization design method of 617 nickel-based superalloy |
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1341771A (en) * | 2001-08-10 | 2002-03-27 | 大连理工大学 | Large-block amorphous alloy component design method |
| CN1514035A (en) * | 2002-12-31 | 2004-07-21 | 中国科学院物理研究所 | Iron base large block non crystalline alloy |
| CN1563444A (en) * | 2004-04-05 | 2005-01-12 | 吉林大学 | Method for designing components of large piece of non-crystalline alloy |
| CN1603445A (en) * | 2004-11-04 | 2005-04-06 | 哈尔滨工业大学 | Iron-base bulk amorphous alloy with high glass-forming ability |
| CN101033530A (en) * | 2007-04-16 | 2007-09-12 | 安泰科技股份有限公司 | Ferrum-base block non-crystalline alloy material |
| CN101215679A (en) * | 2008-01-08 | 2008-07-09 | 厦门大学 | Nonmagnetic iron-base block amorphous alloy and preparation method thereof |
-
2009
- 2009-07-24 CN CN200910112258XA patent/CN101613843B/en not_active Expired - Fee Related
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1341771A (en) * | 2001-08-10 | 2002-03-27 | 大连理工大学 | Large-block amorphous alloy component design method |
| CN1514035A (en) * | 2002-12-31 | 2004-07-21 | 中国科学院物理研究所 | Iron base large block non crystalline alloy |
| CN1563444A (en) * | 2004-04-05 | 2005-01-12 | 吉林大学 | Method for designing components of large piece of non-crystalline alloy |
| CN1603445A (en) * | 2004-11-04 | 2005-04-06 | 哈尔滨工业大学 | Iron-base bulk amorphous alloy with high glass-forming ability |
| CN101033530A (en) * | 2007-04-16 | 2007-09-12 | 安泰科技股份有限公司 | Ferrum-base block non-crystalline alloy material |
| CN101215679A (en) * | 2008-01-08 | 2008-07-09 | 厦门大学 | Nonmagnetic iron-base block amorphous alloy and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 吕俊等.Fe-Zr-B非晶合金的机械合金化制备与非晶化机制研究.《金属功能材料》.2006,第13卷(第2期), * |
| 李福山.Fe基软磁非晶态合金的研究.《郑州大学学报(工学版)》.2002,第23卷(第4期),30-32. * |
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