CN102181791A - In-situ TiC dispersion-strengthened austenitic heat-resistant steel and preparation method thereof - Google Patents
In-situ TiC dispersion-strengthened austenitic heat-resistant steel and preparation method thereof Download PDFInfo
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- CN102181791A CN102181791A CN 201110075639 CN201110075639A CN102181791A CN 102181791 A CN102181791 A CN 102181791A CN 201110075639 CN201110075639 CN 201110075639 CN 201110075639 A CN201110075639 A CN 201110075639A CN 102181791 A CN102181791 A CN 102181791A
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Abstract
The invention relates to a novel in-situ synthetic TiC dispersion-strengthened austenitic heat-resistant steel material and a preparation method thereof. The TiC-containing heat-resistant steel is prepared from the following alloy components in percentage by mass: 18.0-25.0% of Cr, 8.0-30.0% of Ni, 0.05-3.0% of C, 1.0-12.0% of Ti and the balance of Fe. The heat-resistant steel can also comprise less than 3.0% of Mo, less than 1.0% of Al, less than 1.0% of Nb and less than 1.0% of V. The new process combining in-situ fusion casting and electroslag remelting is used for preparing the TiC-containing austenitic heat-resistant steel. Compared with the existing electroslag remelting, the TiC particles in the heat-resistant steel provided by the invention are distributed in a more uniform way and have smaller size. The TiC-containing austenitic heat-resistant steel subjected to electroslag remelting has high strength, excellent heat resistance and excellent wear resistance, and can be used for parts serving at high temperature on industrial products and equipment in metallurgy, machinery, automobiles, petrochemical industry and the like.
Description
Technical field
The present invention relates to synthetic TiC dispersion-strengthened austenite heat-resistance steel of a kind of novel original position and preparation method thereof.
Background technology
Prior art: in industries such as metallurgy, space flight, oil and chemical industry, many equipment of at high temperature working and component all need good resistance toheat, as steam boiler, the steam turbine of thermal power plant, and the jet engine of aircraft industry etc.The material that these at high temperature are on active service need bear various load, as stretch, crooked, reverse, fatigue and impact etc., this just needs the plasticity that they have certain high temperature intensity and adapt to it.In addition, they also contact with high-temperature vapour, air or combustion gas, and this just needs them to have sufficiently high chemical stability.
Austenite heat-resistance has excellent toughness and plasticity, resistance to elevated temperatures and machinability, is widely used in actual industrial.But compare with other high temperature steel, austenitic heat-resistance steel not only intensity is low, wears no resistance and can not improve its intensity by thermal treatment, thereby limited it in industrial application.The preparation technology of TiC dispersion-strengthened steel commonly used adopts the original position fusion casting usually at present.The original position fusion casting by means of traditional casting technique, by add the prefabricated section that contains Ti and C component in melt, generates TiC particle wild phase by reaction in according to thermodynamic principles.Original position synthetic TiC enhanced granule have Thermodynamically stable, size tiny, be evenly distributed and clean with basal body interface and combine characteristics such as good.The original position fusion casting prepares the dispersed particle-strengthened steel of TiC and has that preparation technology is simple relatively, low cost of manufacture, is easy to realize characteristics such as suitability for industrialized production and practical application, thereby has development potentiality and be used widely.But (TiC is 4.93gcm because the density difference of TiC density and steel fusant is big
-3, steel is 7.8gcm
-3), this can cause TiC particulate come-up and reunite, cause the skewness of TiC particle in matrix.In addition, the increase of TiC granule content can make the increase of melt viscosity and reduce the flowability of melt, finally causes being prone in the ingot casting metallurgical problems such as loose, pore, and these casting flaws have restricted the development and the application of TiC dispersion-strengthened steel to a certain extent.Esr is a kind of secondary refining technology, the integrated metallurgical castingprocesses that the collection steel secondary refining combines with directional freeze.Because the removal of high temperature sludge liquid is mingled with the good crystallization condition of effect and water mold, the prepared steel ingot of esr has good purity, and as-cast structure is careful evenly, premium propertiess such as non-metallic inclusion small and dispersed.Therefore, esr is widely used on steel grades such as superior alloy steel, die steel, rapid steel, high temperature steel and superalloy.
Summary of the invention
The purpose of this invention is to provide that a kind of original position synthesis particle is tiny, TiC dispersion-strengthened austenite heat-resistance steel and preparation method thereof is evenly distributed.
Technical solution of the present invention is: the dispersed particle-strengthened austenitic heat-resistance steel of a kind of TiC, composition quality percentage ratio is: Cr:18.0～25.0%, Ni:8.0～30.0%, C:0.05～3.0%, Ti:1.0～12.0%, Fe surplus.Austenitic heat-resistance steel of the present invention may further include, Mo, Al, Nb and V, and the mass percent of each component is Cr:18.0～25.0%, Ni:8.0～30.0%, C:0.05～3.0%, Ti:1.0～12.0%, Mo:＜3.0%, Al:＜1.0%, Nb:＜1.0%, V:＜1.0%, the Fe surplus.
A kind of method for preparing the dispersed particle-strengthened austenitic heat-resistance steel of above-mentioned TiC, preparation process be, the prefabricated section of preparation titaniferous and carbon, and this prefabricated section is formed by the iron powder between 100～200 orders, titanium valve and carbon dust mixed compaction; Add Cr, Ni, alloy furnace charges such as C, Fe at medium-frequency induction furnace, after treating that above-mentioned furnace charge melts fully, be heated to 1550-1700 ℃, required prefabricated section is added in the stove, after treating that prefabricated section reaction, fusing are finished, leave standstill insulation 5min, the pouring metal melt in the stove is gone into to obtain to be used for the consumable electrode that esr is handled in the ready-made in advance sand mo(u)ld, carry out esr then and handle in electroslag furnace, electroslag remelting process is: adopt (25%～30%) Al
2O
3+ (55%～65%) CaF
2+ (20%～5%) TiO
2Slag system is set packing ratio=0.4～0.6 setting voltage 20-30 volt, sets electric current 5000-6500 ampere; The ESR ingot that finally obtains is processed into section bar with the thermal deformation method, and the temperature of processing is 950-1150 ℃.
The novel process that this invention adopts original position fusion casting and esr to combine has prepared the austenite heat-resistance steel that a kind of performance is good, cost is low, intensity is high, resistance toheat is good.Mechanics material property, high-temperature oxidation resistance and the creep property of this TiC of containing austenitic heat-resistance steel all are better than matrix high temperature steel, and this TiC of containing high temperature steel can be used for the component that the needs on Industrial products such as metallurgy, machinery, automobile and petrochemical complex and the equipment at high temperature are on active service.
Beneficial effect: the present invention has following performance characteristics: 1. the material alloys composition is accurate, and ingot quality is good, good compactness, purity height, do not have casting flaws such as loose, the follow-up hot-work rate height of becoming a useful person; 2. original position TiC even particle distribution, particle is tiny, and is strong with basal body binding force; 3. the adjustability of performance promptly can change matrix according to service requirements, forms the material of different performance (intensity, hardness, plasticity and resistance toheat); 5. mechanical strength height, wear-resistant, anti-oxidant and creep resistance, over-all properties are better than matrix high temperature steel.The present invention can be used for the component that the needs on Industrial products such as metallurgy, machinery, automobile and petrochemical complex and the equipment at high temperature are on active service.
Description of drawings
The prepared TiC of Fig. 1 the present invention strengthens the steel metallographic structure.
Fig. 2 is TiC size distribution and pattern in the TiC dispersion-strengthened austenitic heat-resistance steel before the electroslag of the present invention.
Fig. 3 strengthens TiC size distribution and shape appearance figure in the steel for the prepared TiC of the present invention.
Fig. 4 strengthens steel and matrix high temperature steel antioxidant property comparison diagram for the prepared TiC of the present invention.
Fig. 5 strengthens steel and matrix high temperature steel creep-resistant property comparison diagram for the prepared TiC of the present invention.
Embodiment
Table has been listed the mechanical property of some materials for the performance characteristics of material that this invention is described in each following table, wear-resistant, anti-oxidant and creep-resistant property:
Listed the composition of two kinds of alloys in the table 1, first alloy is a kind of typical austenite heat-resistance alloy, and second alloy then is the TiC dispersion-strengthened austenitic heat-resistance steel for preparing by the present invention, and its content is all within the composition range of this invention regulation.
The chemical ingredients (wt%) of two kinds of alloys of table 1
Listed the mechanical property of these two kinds of alloys in the table 2, as seen from the table, in the austenite heat-resistance alloy, added the TiC particle after, can make the intensity of alloy obtain by a relatively large margin raising.
The ambient temperature mechanical properties of two kinds of alloys of table 2
Listed the mechanical behavior under high temperature of these two kinds of alloys in the table 3, as seen from the table, in the austenite heat-resistance alloy, added the TiC particle after, can make the hot strength of alloy obtain by a relatively large margin raising, expanded the upper limit of its use temperature.
The mechanical behavior under high temperature of two kinds of alloys of table 3
Listed the abrasion loss of these measured on the MM2000 wear testing machine two kinds of alloys in the table 4.Test conditions is: 1. friction pair adopts the GCr15 steel, 2. oil lubrication, and 3. linear velocity 0.94m/s, 4. test period is 20 minutes, 5. load 150N.By the table as seen, in the austenite heat-resistance alloy, added the TiC particle after, the abrasion resistance properties of alloy is significantly improved.
The wear volume (mm3) of two kinds of alloys of table 4 behind wearing and tearing 20min under the 150N load
Fig. 3 is the high temperature oxidation weightening finish curve of 800 ℃ of following two kinds of alloys, and as seen from the figure, the rate of oxidation that does not contain TiC particulate austenitic heat-resistance steel is 0.93mgcm
-2Down, the rate of oxidation that contains the high temperature steel of TiC then drops to 0.4mgcm
-2, illustrate that adding the TiC particle can make the antioxidant property of alloy obtain by a relatively large margin raising.Fig. 4 is the creep curve of the following two kinds of alloys of 650 ℃/100MPa, and as seen from the figure, the creep speed that does not contain TiC particulate austenitic heat-resistance steel is 6.9 * 10
-9S
-1, the creep speed that contains the high temperature steel of TiC then drops to 1.2 * 10
-9S
-1, illustrate that having added the creep-resistant property that can make alloy behind the TiC particle in austenitic heat-resistance steel obtains by a relatively large margin raising.
Embodiment 1: a kind of original position is synthesized TiC dispersion-strengthened austenitic heat-resistance steel, it is characterized in that composition quality percentage ratio is: 1.08%C+18%Cr+9%Ni+4%Ti, surplus is Fe.The prefabricated section of preparation titaniferous and carbon: with granularity be iron powder, titanium valve and carbon dust between 200 orders by the mixed of claim 1, and be compacted into piece; After medium-frequency induction furnace adds the matrix alloy furnace charge, treats that above-mentioned furnace charge melts fully, be heated to 1580 ℃, the gained prefabricated section is added in the stove, prefabricated section is fused in the furnace charge; Pouring metal melt in the stove is gone in the ready-made in advance model; Steel ingot carries out esr, and electroslag remelting process is: adopt 30%Al
2O
3+ 60%CaF
2+ 10%TiO
2Slag system, packing ratio=0.5; 20 volts of setting voltages are set 6000 amperes in electric current, use the steel ingot that one step process makes and are processed into section bar with the thermal deformation method, and the temperature of processing is 950-1150 ℃.
Embodiment 2: a kind of original position is synthesized TiC dispersion-strengthened austenitic heat-resistance steel, it is characterized in that composition quality percentage ratio is: 1.8%C+18%Cr+14%Ni+2.5%Mo+7%Ti, surplus is Fe.The prefabricated section of preparation titaniferous and carbon: with granularity be iron powder, titanium valve and carbon dust between 200 orders by the mixed of claim 1, and be compacted into piece; Add the matrix alloy furnace charge at medium-frequency induction furnace, be heated to 1600 ℃, treat that above-mentioned furnace charge melts fully after, the gained prefabricated section is added in the stove, prefabricated section is fused in the furnace charge; Pouring metal melt in the stove is gone in the ready-made in advance model; Steel ingot carries out esr, and electroslag remelting process is: adopt 30%Al
2O
3+ 65%CaF
2+ 5%TiO
2Slag system, packing ratio=0.4～0.6,25 volts of setting voltages are set 6000 amperes in electric current; Use the steel ingot that one step process makes and be processed into section bar with the thermal deformation method, the temperature of processing is 950-1150 ℃.
Embodiment 3: a kind of original position is synthesized TiC dispersion-strengthened austenitic heat-resistance steel, it is characterized in that composition quality percentage ratio is: 1.3%C+25%Cr+20%Ni+2.0%Mo+1.0%Nb+6%Ti, surplus is Fe.The prefabricated section of preparation titaniferous and carbon: with granularity be iron powder, titanium valve and carbon dust between 200 orders by the mixed of claim 1, and be compacted into piece; Add the matrix alloy furnace charge at medium-frequency induction furnace, be heated to 1600 ℃, treat that above-mentioned furnace charge melts fully after, the gained prefabricated section is added in the stove, prefabricated section is fused in the furnace charge; Pouring metal melt in the stove is gone in the ready-made in advance model; Steel ingot carries out esr, and electroslag remelting process is: adopt 30%Al
2O
3+ 65%CaF
2+ 5%TiO
2Slag system, packing ratio=0.4,30 volts of setting voltages are set 6500 amperes in electric current; Use the steel ingot that one step process makes and be processed into section bar with the thermal deformation method, the temperature of processing is 950-1150 ℃.
Claims (3)
1. an original position TiC dispersion-strengthened austenitic heat-resistance steel is characterized in that, mass percent is Cr:18.0 ~ 25.0%, Ni:8.0 ~ 30.0%, C:0.05 ~ 3.0%, Ti:1.0 ~ 12.0%, Fe surplus.
2. the dispersed particle-strengthened austenitic heat-resistance steel of TiC as claimed in claim 1 is characterized in that described austenitic heat-resistance steel also comprises, Mo, Al, Nb and V, and the mass percent of each component is Cr:18.0 ~ 25.0%, Ni:8.0 ~ 30.0%, C:0.05 ~ 3.0%, Ti:1.0 ~ 12.0%, Mo:＜3.0%, Al:＜1.0%, Nb:＜1.0%, V:＜1.0%, the Fe surplus.
3. the preparation method of the dispersed particle-strengthened austenitic heat-resistance steel of the described TiC of claim 1 is characterized in that step is:
A. preparation contains the prefabricated section of ferrotitanium carbon: according to titanium, carbon mass ratio is 4:(0.8 ~ 1), the iron powder that adds titanium carbon dust total mass 10 ~ 60% therein mixes and is compacted into piece, and the granularity of used powder is 100 ~ 200 orders;
B. the content with Ti among the step a is benchmark, according to Cr, the Ni mass ratio is the ratio of 18.0 ~ 25.0:8.0 ~ 30.0, calculate the Cr in the dispersed particle-strengthened austenitic heat-resistance steel, the final content of Ni, as preparation austenitic heat-resistance steel matrix alloy furnace charge Cr, the add-on of Ni, according to C mass percent 0.2 ~ 2.0% scope, determine the final content of C in the dispersed particle-strengthened austenitic heat-resistance steel, and calculate the final content of the required Fe of dispersed particle-strengthened austenitic heat-resistance steel, C and the final content of Fe deduct the add-on of the C and the Fe that are used for preparing the prefabricated section that contains ferrotitanium carbon among the step a in the dispersed particle-strengthened austenitic heat-resistance steel that is obtained by aforementioned calculation, promptly obtain C and Fe add-on that intermediate frequency is smelted preparation austenitic heat-resistance steel matrix alloy furnace charge;
C. add the matrix alloy furnace charge at medium-frequency induction furnace, after treating that above-mentioned furnace charge melts fully, be heated to 1550-1700 ℃, add step a gained prefabricated section, after treating that prefabricated section reaction, fusing are finished, leave standstill and descend to be incubated 5min, the pouring metal melt in the stove is gone in the ready-made in advance sand mo(u)ld at 1550-1700 ℃;
D. the steel ingot that step c is obtained carries out esr, and described electroslag slag charge is by Al
2O
3, CaF
2And TiO
2Form, the mass percent of electroslag slag charge component is: 25% ~ 30% Al
2O
3, 55% ~ 65% CaF
2, 20% ~ 5% TiO
2, set packing ratio=0.4 ~ 0.6, setting voltage 20-30 volt is set electric current 5000-6500 ampere;
E. the ESR ingot that steps d is obtained is forged with the thermal deformation method and is processed into section bar, hot processing temperature 950-1150 ℃.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105463328A (en) * | 2015-12-10 | 2016-04-06 | 安徽相邦复合材料有限公司 | In-situ mixed particle reinforcement steel-based composite material and preparing method thereof |
| CN110952028A (en) * | 2019-12-19 | 2020-04-03 | 广东省材料与加工研究所 | Cr-Ni series austenite heat-resistant steel with enhanced phase precipitated in interior and preparation method thereof |
| CN111304555A (en) * | 2020-03-31 | 2020-06-19 | 广东省材料与加工研究所 | In-situ endogenously precipitated ceramic particle reinforced Cr-Mn-Ni-C-N austenitic heat-resistant steel and preparation method and application thereof |
| CN113249631A (en) * | 2021-03-25 | 2021-08-13 | 江苏省沙钢钢铁研究院有限公司 | Die casting heating furnace slide block and manufacturing method thereof |
| CN113584382A (en) * | 2021-07-06 | 2021-11-02 | 广东省科学院新材料研究所 | Iron-based ceramic composite material and preparation method and application thereof |
| CN113930656A (en) * | 2021-09-16 | 2022-01-14 | 华中科技大学 | N-ODS steel for fusion reactor and preparation method thereof |
| CN115838903A (en) * | 2022-12-09 | 2023-03-24 | 中国核动力研究设计院 | Nano mixture dispersed high-strength heat-resistant ferrite steel and application thereof |
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Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN105463328A (en) * | 2015-12-10 | 2016-04-06 | 安徽相邦复合材料有限公司 | In-situ mixed particle reinforcement steel-based composite material and preparing method thereof |
| CN110952028A (en) * | 2019-12-19 | 2020-04-03 | 广东省材料与加工研究所 | Cr-Ni series austenite heat-resistant steel with enhanced phase precipitated in interior and preparation method thereof |
| CN110952028B (en) * | 2019-12-19 | 2020-12-08 | 广东省材料与加工研究所 | Cr-Ni series austenite heat-resistant steel with enhanced phase precipitated in interior and preparation method thereof |
| WO2021121021A1 (en) * | 2019-12-19 | 2021-06-24 | 广东省科学院材料与加工研究所 | Cr-ni austenitic heat-resistant steel with endogenous precipitated reinforced phase, preparation method therefor and use thereof |
| CN111304555A (en) * | 2020-03-31 | 2020-06-19 | 广东省材料与加工研究所 | In-situ endogenously precipitated ceramic particle reinforced Cr-Mn-Ni-C-N austenitic heat-resistant steel and preparation method and application thereof |
| CN113249631A (en) * | 2021-03-25 | 2021-08-13 | 江苏省沙钢钢铁研究院有限公司 | Die casting heating furnace slide block and manufacturing method thereof |
| CN113584382A (en) * | 2021-07-06 | 2021-11-02 | 广东省科学院新材料研究所 | Iron-based ceramic composite material and preparation method and application thereof |
| CN113930656A (en) * | 2021-09-16 | 2022-01-14 | 华中科技大学 | N-ODS steel for fusion reactor and preparation method thereof |
| CN115838903A (en) * | 2022-12-09 | 2023-03-24 | 中国核动力研究设计院 | Nano mixture dispersed high-strength heat-resistant ferrite steel and application thereof |
| CN115838903B (en) * | 2022-12-09 | 2023-09-26 | 中国核动力研究设计院 | Nano-mixture-dispersed high-strength heat-resistant ferritic steel and application thereof |
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Application publication date: 20110914 |