CN105177414A - Nickel-carbon-ferrum-based powder metallurgy alloy and preparation method thereof - Google Patents
Nickel-carbon-ferrum-based powder metallurgy alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a nickel-carbon-ferrum-based powder metallurgy alloy and a preparation method thereof. The alloy comprises, by weight, 1-7% of nickel, 0.4-1% of carbon and 92-94.6% of ferrum. The manufacturing process comprises the steps of (1), ball-milling and mixing, wherein ball-milling and mixing are carried out on materials of the nickel, the carbon and the ferrum, the ratio of grinding media to the materials is 1-3 to 1, the rotation speed of a spherical tank is set to range from 200 r/min to 400 r/min, and the ball-milling times ranges from 6 hours to 8 hours; (2), placing the materials which have undergone ball-milling and mixing in the step (1) into a die to carry out pressing formation; (3), burying the materials pressed and formed in the step (2) into fire-resistant sand, sintering the materials for 1-2 hours at 1100-1200 DEG C and then naturally cooling the materials in a furnace to obtain the nickel-carbon-ferrum-based powder metallurgy alloy, wherein the protective atmosphere is composed of 90-100% N2 and 0-10% H2 in the sintering process. According to the invention, the nickel and the carbon are added into ferrum-based powder metallurgy alloy, the appropriate ball-milling process is adopted, the microstructure of the alloy manufactured through the method is good, the porosity is small, pores are balled, the grain size is small, the rigidity is high, the tensile strength is high and the plasticity is good.
Description
Technical field
The present invention relates to ferrous based powder metallurgical field, particularly a kind of powder metallurgy low alloy steel and preparation method thereof increasing nickel, carbon.
Background technology
Powder metallurgy technology has a lot of unique advantage in the research and development and materials processing of material, and wherein topmost advantage is as follows:
(1) alloy material prepared by powder metallurgy technology has very unique chemistry and physicals compared to the material of the preparation of traditional technology.The material that conventional casting methods and mechanical means cannot be prepared and the workpiece (as Wimet, function ceramics etc.) that a lot of difficulty melts metal can be realized by powder metallurgy technology.
(2) can change the addition of composition in alloy and element in the process prepared at mmaterial easily, the element added in the alloy can divide and plays respective characteristic, prepares the alloy material with premium properties.
(3) powder metallurgy technology is a kind of technology of near-net-shape, utilizes powder metallurgy technology can realize the shaping of various complicated shape, and the nothing that simultaneously can realize material is cut and few machining, and the utilization ratio of material can reach more than 95%.Therefore powder metallurgy technology have that cost is low, efficiency high and be a kind of green manufacture technology.
Powder metallurgy low alloy steel is exactly adopt the mode of powder metallurgy that a certain amount of enhancing element (as nickel, manganese, chromium etc.) is joined (Fe >=90wt%) in iron powder, and adds the alloy system that a certain amount of carbon forms as requested.The success of the stephanoporate oil-retaining bearing that the thirties in last century is prepared by powder metallurgy technology makes powder metallurgy low alloy steel be widely used.To phase at beginning of the sixties in last century Fe-C, the powder metallurgy low alloy steel product of Fe-Cu occupies its leading position, the mechanical property of the alloy after these sintering is poor, and tensile strength major part concentrates between 150-300MPa, but can compare favourably with the performance of cast member at that time.Arrived the mid-1960s Fe-Ni-Cu, Fe-Ni-Mo alloy system to be widely used, its tensile strength can reach 200-500MPa.Up to the present, along with the improvement of powder metallurgical technique (powder preparation, element variation, forming technology, sintering process), the performance of powder metallurgy low alloy steel has had larger lifting.
The alloy prepared adding C element subsequently in Fe-Ni not only reduces the cost of sintered metal product, also obtain good performance simultaneously, after quenching, its tensile property can more than 800MPa, but after quenching, the plasticity of alloy is not significantly improved.
Fe-Ni-C system powder metallurgy is widely used because it has good mechanical property, but on Ni and C in Fe-Ni-C system mmaterial on the impact of iron-base powder metallurgical product performance and the Changeement of microstructure less, both at home and abroad to having done large quantifier elimination in ferrous based powder metallurgical mechanical property, and the intensity of alloy and hardness are obtained for larger improvement, but the plasticity being aimed at iron-base powder metallurgy material does not obtain lifting clearly, mould sex factor to Addition ofelements to iron-base powder metallurgy material also not explain relatively fully and research simultaneously, up to the present its range of application is still restricted.
Summary of the invention
The object of the invention is by the mechanical property of Fe-Ni-C system powder metallurgy low alloy steel and the research of microtexture, expect to find rational proportioning, a kind of intensity and the plasticity that can either improve material are provided, the ferrous based powder metallurgical Alloy And Preparation Method of the production cost of material can be reduced again.
The concrete technical scheme of the present invention is as follows:
The invention provides a kind of nickel carbon ferrous based powder metallurgical alloy, comprise the raw material of following weight percent: Ni-(1-7) wt%, C-(0.4-1) wt%, Fe-(92-94.6) wt%;
Preferably, the raw material of following weight percent is comprised: Ni-(5-7) wt%, C-(0.6-1) wt%, Fe-(92-94.4) wt%;
Be more preferably, comprise the raw material of following weight percent: Ni-7wt%, C-1wt%, Fe-92wt%.
The present invention also provides the preparation method of above-mentioned nickel carbon ferrous based powder metallurgical alloy, comprises the following steps:
(1) ball milling mixing: nickel source, carbon source and source of iron are carried out ball milling mixing, and ratio of grinding media to material is (1-3): 1, and spherical tank rotating speed is 200r/min-400r/min, and Ball-milling Time is 6-8 hour;
(2) material described step (1) obtained loads mould, press forming;
(3) be embedded in fire-resistant sand by the mould of press forming in step (2), sinter 1-2h at 1100 DEG C-1200 DEG C after, furnace cooling obtains nickel carbon ferrous based powder metallurgical alloy, and in sintering process, protective atmosphere is (90-100) %N
2+ (0-10) %H
2.
Wherein, 0.8% Zinic stearas (ZnSt2) is also comprised as releasing agent in the mixture of step (1), because Zinic stearas almost can all decompose when temperature is 850 DEG C, so it is little to add the impact of Zinic stearas on agglomerated material performance and structure.
The present invention does not have special restriction to nickel source, carbon source and source of iron, preferably uses carbonyl nickel powder, oildag and LAP100.29 water-atomized iron powder to be respectively nickel source, carbon source and source of iron.
In the present invention special restriction is not had, as long as can play well-mixed ball mill device all within protection scope of the present invention to the device of ball milling mixing.The present invention preferably adopts horizontal ball mill to carry out ball milling.The material of the present invention to ball mill does not have concrete restriction.Preferably, ball mill tank material and steel ball material are stainless steel.
In the present invention, concrete restriction be there is no to the batch of ball milling mixing, can need to set suitable ball milling mixed batch according to the difference of ball mill device or preparation.500g material is preferably adopted to be a batch mixing batch in the present invention.
Protective atmosphere is not adopted, air atmosphere in step of the present invention (1) ball milling mixing process.In sintering process in step (3), protective atmosphere can be 90%N
2+ 10%H
2, or be nitrogen.
The present invention increases nickel element, carbon in ferrous based powder metallurgical, and the alloy microtexture of manufacture is better, and porosity is less, hole nodularization, and grain-size is less, and hardness is high, and tensile strength is large, and plasticity is good, and cost is lower simultaneously, is highly advantageous to and applies.
Accompanying drawing explanation
Fig. 1 is Fe-Ni-C system of the present invention powder metallurgy low alloy steel hole metallograph; Wherein, (a) 0.6wt%C, 1wt%Ni; (b) 0.6wt%C, 4wt%Ni; (c) 0.6wt%C, 7wt%Ni; (d) 1.0wt%C, 1wt%Ni; (e) 1.0wt%C, 4wt%Ni; (f) 1.0wt%C, 7wt%Ni.
Fig. 2 is Fe-Ni-C powder metallurgy low alloy steel crystal grain metallograph of the present invention; Wherein, (a) 0.4wt%C, 7wt%Ni; (b) 0.6wt%C, 7wt%Ni; (c) 0.8wt%C, 7wt%Ni; (d) 1.0wt%C, 3wt%Ni; (e) 1.0wt%C, 5wt%Ni; (f) 1.0wt%C, 7wt%Ni;
Fig. 3 is Fe-Ni-C powder metallurgy low alloy steel metallographic structure figure of the present invention; Wherein, (a) 1.0wt%C, 3wt%Ni; (b) 1.0wt%C, 5wt%Ni; (c) 1.0wt%C, 7wt%Ni; (d) 1.0wt%C, 8wt%Ni;
Fig. 4 is the metallographic structure figure under 500 times, Fe-Ni-C powder metallurgy low alloy steel of the present invention; Wherein, (a) Fe-7Ni-0.4C, (b) Fe-7Ni-0.6C, (c) Fe-7Ni-0.8C, (d) Fe-7Ni-1.0C;
Fig. 5 is Fe-Ni-C powder metallurgy low alloy steel metallographic structure figure of the present invention; Wherein, (a) 2wt%Ni, 0.8wt%C; (b) 3wt%Ni, 0.8wt%C; (c) 2wt%Ni, 1.0wt%C; (d) 3wt%Ni, 1.0wt%C; (e) 3wt%Ni, 1.0wt%C;
Fig. 6 is Fe-Ni-C Tensile fracture cross-section morphology figure of the present invention; Wherein, (a) 7wt%Ni, 0.4wt%C; (b) 3wt%Ni, 1.0wt%C; (c) 7wt%Ni, 1.0wt%.
Embodiment
Below in conjunction with the embodiment in the present invention; technical scheme in the embodiment of the present invention is clearly and completely described; obviously; described embodiment is only the present invention's part embodiment; instead of whole embodiments. based on the embodiment in the present invention; those of ordinary skill in the art, not making the every other embodiment obtained under creative work prerequisite, belong to the scope of protection of the invention.
Embodiment 1
(1) LAP100.29 water-atomized iron powder is adopted to be starting material, adopt oildag and carbonyl nickel powder respectively as the interpolation raw material of carbon, nickelalloy element, according to the proportions nickel carbon iron-based material (surplus is iron) in table 1, add the Zinic stearas (ZnSt that massfraction is 0.8%
2) as releasing agent.
(2) ball milling mixing: be batch mixing batch with step (1) 500g material during batch mixing; powder adopts horizontal ball mill to carry out ball milling; ball milling tank body material is stainless steel; steel ball material is stainless steel; ratio of grinding media to material is 2: 1; spherical tank rotating speed is set to 200r/min, and Ball-milling Time 8 hours, does not adopt protective atmosphere.
(3) material in step (2) is loaded mould, press forming.
(4) be embedded in the fire-resistant sand in sintering oven by material in step (3), sintering temperature is 1120 DEG C, and sintering time is two hours, and sintering protective atmosphere is 90%N
2+ 10%H
2, sample furnace cooling after finally sintering.
1, carbon, nickel content are on the impact of iron-base powder metallurgy material mechanical property
Through detection, different nickel, carbon content on the impact of iron-base powder metallurgy material mechanical property in table 1.
The different nickel of table 1, carbon content are on the impact of iron-base powder metallurgy material mechanical property
Results and analysis:
(1) impact of different carbon, nickel content alloy hardness:
As can be seen from Table 1, when carbon content is constant along with the increase of nickel content, the changes in hardness of alloy is comparatively complicated.When carbon content is 0.4wt% and 0.6wt%, along with the increase of nickel content, the hardness of alloy presents the trend first increasing and reduce afterwards, with carbon content be 0.4wt% and 0.6wt% unlike, when carbon content is 0.8wt% and 1.0wt%, when nickel content is 1%wt-3wt%, the hardness of alloy first increases rear reduction, and when nickel content is higher than 3wt%, the hardness of alloy increases along with the increase of nickel content, when nickel content reaches 8wt%, the hardness of alloy starts to reduce.The hardness of alloy Fe-7Ni-1.0C reaches the highest, is 85.3HRB, compared with the hardness of alloy Fe-7Ni-0.4C, Fe-7Ni-0.6C, Fe-7Ni-0.8C, improves 12.3HRB, 10HRB and 6.1HRB respectively.Keep nickel content constant, the hardness of alloy increases along with the increase of carbon content.
(2) carbon, nickel content are on the impact of iron-base powder metallurgy material tensile strength:
When nickel content is 0.4wt% and 0.6wt%, the tensile strength of alloy increases along with the increase of nickel content, and when nickel content is 0.8wt%, the tensile strength of alloy starts to reduce.When carbon content is 0.8wt% and 1.0wt%, when nickel content is 1%wt ~ 3wt%, the tensile strength of alloy is first increase rear reduction equally, when nickel content is more than 3wt%, the hardness of alloy increases along with the increase of nickel content, when nickel content is 7wt%, the tensile strength of alloy all reaches maximum value, the tensile strength of its interalloy Fe-7Ni-1.0C is the highest, for 511Mpa is compared with alloy Fe-7Ni-0.4C, Fe-7Ni-0.6C, Fe-7Ni-0.8C, tensile strength improves 61MPa, 53Mpa and 41MPa respectively.When nickel content is constant, the tensile strength of sintered alloy increases along with the increase of carbon content.
(3) nickel, carbon content are on the impact of iron-base powder metallurgy material elongation at break:
Conventional cast material, when intensity increases, plasticity can reduce accordingly.But there will be different phenomenons in powder metallurgy, that is exactly while intensity increases, and the plasticity of material is also in increase.The elongation of the increase alloy along with nickel content when carbon content is 0.4wt% and 0.6wt% is increasing gradually, when nickel content is 8wt%, the elongation of alloy reaches maximum value, be 5.18%, but elongation only improve only 0.03%. when carbon content is 0.6wt%, 0.8wt% and 1.0wt% compared with when being 7wt% with nickel content, when nickel content is 1wt% ~ 4wt%, the elongation of alloy presents the trend first increasing and reduce afterwards, when nickel content is more than 4wt%, the elongation of alloy increases along with the increase of nickel content.Alloy Fe-7Ni-1.0C elongation is 4.66%, elongation declines and reduces 0.36%, 0.19% and 0.06% and 0.09% respectively compared with alloy Fe-7Ni-0.4C, Fe-7Ni-0.6C, Fe-7Ni-0.6C, Fe-8Ni-1.0C, and elongation change scope is also little.When nickel content is constant, along with carbon content increases, alloy elongation reduces, and therefore the elongation adding alloy material of carbon plays weakening effect.
By above carbon, nickel content to the mechanical property research of iron-base powder metallurgy material, consider the over-all properties of alloy material, the best performance of Fe-7Ni-1.0C alloy, hardness and intensity are respectively 85.3HRB, 511MPa, and now elongation is 4.66%.
2, Micro-Structure Analysis
What Fig. 1 provided is be respectively Fe-0.4C-7Ni, Fe-0.6C-7Ni, Fe-0.8C-7Ni, Fe-1.0C-3Ni, Fe-1.0C-5Ni, the metallograph (polishing state) of Fe-1.0C-7Ni, under the condition that nickel content is constant, along with carbon content is increased to 1.0wt% from 0.4wt%, from Fig. 1 (a), (b), c () and (f) can be found out, pore dimension increases, increasing number, the connectedness of hole increases, but it is rounder and more smooth that hole becomes, this is because the increase when nickel content is identical along with carbon content is gathered in around iron powder and nickel powder particle on the one hand, carbon is diffused in ferrite, hole is left in original position, be on the other hand because carbon powder particle and ferrous powder granules vary in size, the particle re-arrangement that Kirkendall effect causes occur in sintering process and forms larger hole.The increase of hole and the irregular of shape, the intensity of alloy and plasticity play the effect of weakening.
Comparison diagram 1 (d), (e) and (f), can find out, under the condition that carbon content is constant, along with the increase of nickel content, the size of hole reduces gradually, and the connectedness between hole reduces.Due to the increase of nickel element, rich austenitic can be formed, promote the diffusion between iron powder, there is stronger sintering activation, pore dimension can be made to shrink and promote hole nodularization simultaneously.As can be seen from Fig. 1 equally, the hole quantity that increase along with nickel content is gathered in grain boundaries increases, this is because the increase of nickel content causes too much carbon to be diffused in austenite timely, causes to there is more carbon at grain boundaries and remain, thus occurs more less holes at grain boundaries.
Therefore, as seen from Figure 1 after adding nickel, the pore dimension in tissue and porosity are in reduction, and nickel and adding of carbon can promote hole nodularization, and the plasticity of this alloy serves promoter action.With adds separately compared with carbon, add elongation at break and the intensity increase of alloy after nickel element; With adds separately compared with nickel element, add carbon in iron-based, the intensity of alloy increases, but elongation reduction, and the change of this and hole has close relationship.
The metallographic structure figure of what Fig. 2 provided is respectively Fe-0.4C-7Ni, Fe-0.6C-7Ni, Fe-0.8C-7Ni, Fe-1.0C-3Ni, Fe-1.0C-5Ni, Fe-1.0C-7Ni.Known on the impact of iron-base powder metallurgy material grain fineness number according to carbon content, the increase grain size along with carbon content increases.But can find out from Fig. 2 (a), 2 (b), 2 (c) and 2 (f), after adding nickel element in iron powder, along with the increase of carbon content, the grain-size in metallographic structure reduces.This is that this just causes α with γ phase in heat-processed to coexist, and which prevent the growth 2 compared with large grain size in phase transition process because adding of nickel impels the phase transformation in tissue to occur in different temperature and different regions.Along with the increase of nickel content, Fig. 2 (d), 2 (e) and 2 (f) are the metallographs of Fe-1.0C-3Ni, Fe-1.0C-5Ni, Fe-1.0C-7Ni, grain-size in tissue is reduce equally, this is due to the increase along with nickel content, second-phase Fu Nie district is there is in tissue, hinder the diffusion of crystal boundary, meanwhile, nickel content increase make grain boundaries exist more less holes, so when carbon content is constant, along with the increase of nickel content, grain-size is reduce equally.
What Fig. 3 provided is Fe-3Ni-1.0C, Fe-5Ni-1.0C, Fe-7Ni-1.0C and Fe-8Ni-1.0C metallograph.As can be seen from Figure 3, rich austenitic has all been there is in tissue, and along with austenitic content rich in the increase tissue of carbon content increases, this is because nickel diffusion when solid state sintering is very slow, by the sintering processing of routine, nickel element is difficult to diffusion evenly, so along with the increase of nickel content, alloy Zhong Funie district content increases.Around rich austenitic, carbon content is higher, be organized as martensite, this is adding due to nickel, reduce the content of carbon in eutectoid, so along with the increase of nickel, more carbon is piled up around rich austenitic, and the sintered blank after compacting at high temperature sinters and belongs to a kind of heat treatment process, so when the material after sintering is in process of cooling subsequently, form martensite around rich austenitic.Martensite belongs to hard phase, and to notch sensitive, and the hole in tissue is breach, the existence of rich austenitic can improve the susceptibility of martensite to breach, thus close the hardness and the tensile strength that improve alloy, rich austenitic has good plasticity, so the elongation of alloy equally also increases simultaneously.When nickel content is increased to 8wt%, as shown in Fig. 3 (d), the area in Fu Nie district increases further, and the hardness of alloy and tensile strength start to reduce.
Fig. 4 metallographic structure figure that to be Fe-7Ni-0.4C, Fe-7Ni-0.6C, Fe-7Ni-0.8C, Fe-7Ni-1.0C magnification be under 500 times.Can find from figure, all martensite is there is around rich austenitic, when carbon content is 0.4wt%, martensite content around rich austenitic is less, along with the increase of carbon content, the martensite content around rich austenitic increases, so when nickel content is identical, hardness and the tensile strength of alloy increase along with the increase of carbon content, and the change of elongation in contrast.
To carbon, nickel content in the curve of the Effect on Mechanical Properties of iron-base powder metallurgy material, two special points are there are, alloy Fe-3Ni-0.8C and Fe-3Ni-1.0C respectively, reduce in the hardness of this place's alloy and tensile strength, we analyze in the metallographic structure of these two kinds of alloys for this reason, explain the reason of its intensity and hardness reduction.
That Fig. 5 provides is Fe-2Ni-0.8C, Fe-3Ni-0.8C, the metallographic structure figure of Fe-2Ni-1.0C and Fe-3Ni-1.0C. Fig. 5 (a), mainly based on perlite in (c) metallographic structure, there is not rich austenitic, but there is rich austenitic when nickel content is increased to 3%wt in metallographic structure, after 500 times are amplified to the metallographic structure of Fe-3Ni-1.0C alloy, as shown in Fig. 5 (e), around Fu Nie district, martensite content is less, therefore rich austenitic starts to occur to be the hardness of alloy Fe-3Ni-0.8C and Fe-3Ni-1.0C and the reason of tensile strength reduction.
Fig. 6 is the cross-section morphology figure of Fe-7Ni-0.4C, Fe-3Ni-1.0C and Fe-7Ni-1.0C sample respectively.Can find out that in Fig. 6 (a) section forms primarily of the hole of dimple, a small amount of river shape decorative pattern and some amount, dimple is more and darker, belong to ductile rupture, after carbon content is increased to 1.0wt%, as shown in Fig. 6 (b), compared with alloy Fe-7Ni-0.4C alloy Fe-7Ni-1.0C cross-section morphology on dimple quantity reduce, cleavage surface increases, hole quantity increases, and the plasticity of Fe-7Ni-1.0C reduces.As can be seen from Fig. 6 (c), the section of figure Fe-3Ni-1.0C alloy is by hole, and river shape decorative pattern and dimple form, the dimple comparatively small amt on section, river shape decorative pattern is in the majority, alloy belongs to brittle rupture, and along with nickel content is increased to 7wt%, Fe-7Ni-1.0C alloy is compared with Fe-3Ni-1.0C, hole quantity on fracture reduces, dimple quantity increases, and Alloy Fracture presents dimple, cleavage river decorative pattern comprehensive characteristics, and alloy Fe-7Ni-1.0C is quasi-cleavage crack.
Therefore, the nickel different by Micro-Structure Analysis and carbon are on the impact of the hole of ferrous based powder metallurgical low alloy steel, grain-size and phase transformation, ultimate analysis on the impact of ferrous based powder metallurgical low alloy steel fracture apperance, draws the fracture mode of sample in nickel and carbon content. conclusion is as follows:
(1) to finding in the porosity research of agglomerated material, keep nickel content constant, along with the increase of carbon content, porosity increases, and the degree of hole nodularization strengthens, and the hole of nodularization is unfavorable for the diffusion of crackle, facilitates the plasticity of material to a certain extent.Keep carbon content constant, along with the increase of nickel, increase in tissue along the hole that grain boundaries is little, and distribution is relatively more even, porosity reduces, and the intensity of this alloy and plasticity all play the effect of promotion.
(2) finding the grain-size research of agglomerated material, after adding carbon dust and nickel powder in iron powder, grain fineness number increases, and after this means that carbon and nickel add simultaneously, crystal grain obtains refinement, and intensity and the plasticity of alloy all serve promoter action simultaneously.
(3) find when studying the affecting of metallographic structure of carbon and nickel content alloy, along with nickel content increases, content of pearlite in alloy increases, and has occurred rich austenitic in tissue, and along with the increase of nickel content, rich austenitic content is also in increase.Around rich austenitic, there is martensite, and along with the increase of carbon content, the martensite content around rich austenitic is also in increase.
(4) fracture apperance of alloy is observed and is found, when nickel content is 7wt%, along with the increase of carbon content, the dimple quantity on Alloy Fracture reduces, and alloy becomes quasi-cleavage crack from ductile rupture.Be 1.0wt% in carbon content, along with the increase of nickel content, on alloy section, the quantity of dimple increases, and river shape decorative pattern reduces, and Alloy Fracture presents dimple, cleavage river decorative pattern comprehensive characteristics, and material becomes quasi-cleavage crack from brittle rupture, and alloy plasticity increases.
Above-mentioned embodiment is intended to illustrate that the present invention can be professional and technical personnel in the field and realizes or use; modifying to above-mentioned embodiment will be apparent for those skilled in the art; therefore the present invention includes but be not limited to above-mentioned embodiment; any these claims or specification sheets of meeting describes; meet and principle disclosed herein and novelty, the method for inventive features, technique, product, all fall within protection scope of the present invention.
Claims (7)
1. a nickel carbon ferrous based powder metallurgical alloy, is characterized in that, comprises the raw material of following weight percent: Ni-(1-7) wt%, C-(0.4-1) wt%, Fe-(92-94.6) wt%.
2. nickel carbon ferrous based powder metallurgical alloy according to claim 1, is characterized in that, comprise the raw material of following weight percent: Ni-(5-7) wt%, C-(0.6-1) wt%, Fe-(92-94.4) wt%.
3. nickel carbon ferrous based powder metallurgical alloy according to claim 1, is characterized in that, comprise the raw material of following weight percent: Ni-7wt%, C-1wt%, Fe-92wt%.
4. the preparation method of nickel carbon ferrous based powder metallurgical alloy as described in claim 1-3 any one, is characterized in that, comprise the following steps:
(1) ball milling mixing: nickel source, carbon source and source of iron are carried out ball milling mixing, and ratio of grinding media to material is (1-3): 1, and spherical tank rotating speed is 200r/min-400r/min, and Ball-milling Time is 6-8 hour;
(2) mixture obtained in described step (1) is loaded mould, press forming;
(3) be embedded in fire-resistant sand by the module of press forming in step (2), sinter 1-2h at 1100 DEG C-1200 DEG C after, furnace cooling obtains nickel carbon ferrous based powder metallurgical alloy, and in sintering process, protective atmosphere is (90-100) %N
2+ (0-10) %H
2.
5. the preparation method of nickel carbon ferrous based powder metallurgical alloy according to claim 4, is characterized in that, also comprise the Zinic stearas of mixture 0.8wt% in the mixture that step (1) obtains.
6. the preparation method of nickel carbon ferrous based powder metallurgical alloy according to claim 4, it is characterized in that, described nickel source, carbon source and source of iron are respectively carbonyl nickel powder, oildag and LAP100.29 water-atomized iron powder.
7. the preparation method of nickel carbon ferrous based powder metallurgical alloy according to claim 4, it is characterized in that, step (1) ball milling mixing process is carried out in air atmosphere.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106312059A (en) * | 2016-10-11 | 2017-01-11 | 广东粤海华金科技股份有限公司 | Powder metallurgy sintering method of non-magnetic steel structural component |
| JP7467904B2 (en) | 2019-12-16 | 2024-04-16 | 株式会社レゾナック | Sintered alloy and method for producing the same |
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