CN1396291A - Process for preparing steel-base composite feinforced by particles generated in-situ locally - Google Patents
Process for preparing steel-base composite feinforced by particles generated in-situ locally Download PDFInfo
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- CN1396291A CN1396291A CN 02109101 CN02109101A CN1396291A CN 1396291 A CN1396291 A CN 1396291A CN 02109101 CN02109101 CN 02109101 CN 02109101 A CN02109101 A CN 02109101A CN 1396291 A CN1396291 A CN 1396291A
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Abstract
A process for preparing steel-base composite material reinforced by the particles generated in-situ locally includes such steps as proportioning powdered Al, C and Ti, stirring for 4-48 hr, die pressing under 200-800 MPa to obtain the prepared block, vacuum heating for self-spreading synthesis reaction to generate particles in situ, putting the block at the position where casting is needed to be reinforced, and casting molten steel and at 1450 deg.C.
Description
Technical field: the present invention relates to the preparation technology of metal-base composites, particularly relate to the preparation technology of base steel composite material and local composite abrasion resistance material.
Background technology: metal-base composites is owing to have a high strength, high ratio modulus, wear-resisting, heat-resisting, multiple excellent comprehensive performances such as fatigue performance is good, a present front subject focus that has become common people and paid close attention to.Up to now, the enhancing mode of steel-based composite material mainly contains and adds particle and endogenetic particle, add the particle complex process, cost an arm and a leg, and add particle and matrix wettability, physics and chemical compatibility are all poor, can cause producing interface pollution with engage bad, form interfacial reaction layer and branch inhomogeneous, be easy to segregation in a series of problems that are difficult to overcome such as crystal boundaries, thereby reinforced effects is undesirable.Endogenetic particle substantially all is whole compound, and the impelling strength of matrix steel reduces greatly, thereby has limited the steel-based composite material promotion and application.
The common methods of preparation in-situ endogenic particles reiforced metal-base composition mainly contains XD method, contact reaction method.XD method (United States Patent (USP), U.S.Patent No.4710348) can regard two stages as: the fs reaction generates enhanced granule, subordinate phase is distributed to enhanced granule in the metallic solution and goes, and master operation is: powder process-mixing-moulding-degasification-sintering-melting-casting.This method technique is stronger, and the difficulty height is difficult for grasping, and is mainly used to make matrix materials such as particle enhanced Al base, Ti base.(Chinese patent, the patent No.: master operation 93104814) is contact reaction method: powder process-mixing-moulding-adding alloy liquid melting-casting.Contact reaction method makes the particle wild phase react generation when molten alloy liquid, has simplified technology.During this method operation higher technique is arranged, technology is difficult to grasp during actual production, and can only prepare the overall enhanced matrix material.Contact reaction method is mainly used to make Al base, Zn based composites.
XD method, contact reaction method all be not used to prepare in-situ endogenic particle enhanced steel iron base composite material, and all were whole recombining process, and this technology---the self propagating high temperature synthesis method has been given prominence to local compound and in-situ endogenic particle enhancing advantage in the type.At present, do not see the interior self propagating high temperature synthesis method of type as yet and prepare the report that the in-situ locally endogenetic particle strengthens steel-based composite material.
Technology contents: the purpose of this invention is to provide that a kind of technology is simple, with low cost, the preparation method of the steel-base composite feinforced by particles generated in-situ locally that is easy to promote the use of.This method and whole composite algorithm have the difference of essence, it is not just to have formed the particle wild phase before cast, but after the matrix molten steel pours into casting mold, generate enhanced granule in the local self propagating high temperature building-up reactions that takes place of casting mold, and be distributed in equably in the matrix, solidify the back and just can make steel-base composite feinforced by particles generated in-situ locally.Because this self-propagating high-temperature reaction in is to take place in type, successfully solved in the whole composite algorithm owing to form the problem that the high-load adding of alloying element of wild phase causes the Molten Steel Flow difference, stability, the reliability of technology are improved greatly, further improved production efficiency.Saved whole compound required a large amount of valuable alloy on the other hand, thereby the local base steel composite material that strengthens of the low cost of making, mass-producing commercial production becomes possibility.Another free-revving engine of this invention is to keep having improved the over-all properties deficiency of single matrix steel grade on the basis of the original feature performance benefit of matrix steel, really accomplishes effective combination that material is tough, embodies the design philosophy that uses the best steel to make the knife's edge.
The technical scheme of this invention is: react at the inner synthetic particle wild phase of self propagating high temperature that takes place of casting mold through the reaction prefabricated block after the vacuum stripping, thereby prepare the method for steel-base composite feinforced by particles generated in-situ locally, it is characterized in that technological process comprises in the preparation of reaction prefabricated block and the type from spreading two stages of in-situ synthesized reaction.
1) preparation of prefabricated section may further comprise the steps:
A. prefabricated section is formed: prefabricated section is made up of pulverous Al, C and Ti, Al content (wt%) 1%～50%, and the atomic ratio of C and Ti is: 0.6～1.4, its size range is 0.01 μ m～200 μ m;
B. batch mixing: the above-mentioned starting material that prepare are packed in the stirrer, stirred 4～48 hours, mix:
C. compression moulding: the starting material that mix are put into mould, compression moulding at room temperature, pressure range is 200～800Mpa;
D. the vacuum stripping of prefabricated section is handled: the prefabricated section that suppresses is put into the heating under vacuum device, vacuum tightness 〉=10
-1MPa is heated to 100～400 ℃, degasification 1～4h with the heating rate of 5～40 ℃/min;
2) spread the original position synthesis particle wild phase in certainly:
A. casting mold requires: casting mold water content＜4% that the molten steel casting is adopted, ventilation property＞100;
B. the matrix molten steel requires: for the synthetic particle wild phase of prefabricated section generation self propagating high temperature provides the molten steel temperature of heat to exist
More than 1450 ℃;
C. the placement of prefabricated section in casting mold: need the enhanced position to place the Al-Ti-C prefabricated section of vacuum degassing processing at foundry goods;
D. the casting matrix molten steel makes local granule enhancing base steel composite material.
High-temperature molten steel is poured into casting mold, and the synthetic particle wild phase of the original position self propagating high temperature of prefabricated section in the initiation type is prepared the local base steel composite material that strengthens.
The present invention compares with present existing technology has following outstanding advantage:
1) technology is simple, and is with low cost, is easy to apply, and carries out the mass-producing commercial production.The invention is characterized in and successfully prepare the in-situ locally particle reinforced steel-base composite material, its method is different from whole composite algorithm, the heat that makes full use of high-temperature molten steel causes from spreading building-up reactions, the melting with molten steel of the process that generates the particle wild phase is separated, and be merged together with cast molding, and local self propagating high temperature building-up reactions takes place in type, thereby significantly reduced the required a large amount of valuable alloying element of formation particle wild phase, reduced cost; Successfully solved the problem that whole composite algorithm makes the base steel composite material poor impact toughness, technology stability, reliability are improved greatly.
2) the particle wild phase in-situ endogenic in steel solution in the compound position among the present invention, wettability is good, the interface is in conjunction with good, distribution disperse and be distributed in intracrystalline, and played the effect of crystal grain thinning, simultaneously compound position combine with original steel also good, and add poor, the easy pollution of wettability that particle produces, interface in conjunction with bad, particle is poly-partially, easily is distributed in defectives such as crystal boundary.Therefore, the present invention is the whole or local breakthrough that strengthens base steel composite material of preparation particle.Opened up a new road for the whole or local enhancing of particle, pushing effect has been played in the development and the renewal of particulate reinforced composite; The present invention simultaneously can satisfy the service requirements under the various operating modes, and can significantly improve casting quality by the cast molding intricate casting.The particle enhanced steel iron base composite material of the processing method of prior art preparation, the particle wild phase all is to form in the molten steel fusion process, has influenced the flowability of molten steel greatly, and easily produces a large amount of being mingled with and defective such as misrun.And particle wild phase of the present invention is to form from spreading in-situ endogenic in casting mold after the molten steel melting, does not influence the flowability of molten steel, has improved the quality of foundry goods, can fundamentally address these problems.Thereby solved the key issue of long-term puzzlement particles reiforced metal-base composition scientific and technical research.
3) method of the present invention produce the enhanced granule size between 0.5 μ m～5 μ m, generally about 2 μ m, tiny, the rounding of particle, for subsphaeroidal, surface clean is evenly distributed, and is distributed in intracrystalline, has obviously improved the particulate strengthening effect.
4) preparation method of the present invention makes local from spreading steel-base composite feinforced by particles generated in-situ, enhanced granule is to cause self-propagating reaction and in-situ endogenic in the part of casting mold by high temperature matrix molten steel, wettability is good, need uniform distribution in the enhanced scope in the foundry goods part, reinforced effects is remarkable, when not influencing the intrinsic advantage of matrix steel, improved the mechanical property and the wear resistance of matrix material greatly, have good application prospects and market potential.With manganese steel is matrix, and macrohardness (HRC), microhardness (HV) and wear resistance that the in-situ locally particle of preparation strengthens manganese steel are greatly improved, and its wear resistance is 2.1 times of matrix manganese steel, sees Table 1.
Table 1 matrix manganese steel and performance of composites are relatively
Material microhardness (HV) macrohardness (HRC) wear resistance (ε)
Matrix manganese steel 368＜15 1
Matrix material 820 34 2.1
Annotate: wearability test is that 15N, grit size are to carry out under the 25 μ m wear working conditions in load.
This method is that the preparation method of the steel-base composite feinforced by particles generated in-situ locally that is easy to promote the use of and XD method and contact reaction method are essentially different, be that the particle wild phase is neither formed before melting, neither in fusion process, react generation, but cause the self propagating high temperature building-up reactions generation particle wild phase of Al-C-Ti prefabricated section in the casting mold by the heat of high-temperature molten steel.The present invention solved successfully that the particle wild phase content that whole composite algorithm exists is low, reinforced effects is not obvious and since the adding of a large amount of alloying elements cause the Molten Steel Flow difference and wholely compoundly not needing to cause compound position poor toughness and can not use and waste problems such as valuable and near resource and particle, stability, the reliability of technology are improved greatly, further improved production efficiency.Thereby the low cost of making, mass-producing commercial production in-situ locally particle reinforced steel-base composite material become possibility.Another purpose of this invention is to obtain different sites and have high rigidity simultaneously, resistance to wear structured material with high impact toughness, thereby has solved single composite hardness and flexible contradiction.
Description of drawings:
Fig. 1 (a) TiC (30vol%) granule partial strengthens the manganese steel composite material tissue
(b) TiC (30vol%) granule partial strengthens the power spectrum of manganese steel composite material TiC
Fig. 2 (a) TiC (40vol%) granule partial strengthens 45# steel composite material tissue
(b) TiC (40vol%) granule partial strengthens the power spectrum of 45# steel composite material TiC
Fig. 3 (a) TiC (50vol%) granule partial strengthens 45# steel composite material tissue
(b) figure (a) C unit vegetarian noodles scanning
(c) figure (a) Al unit vegetarian noodles scanning
(d) figure (a) Ti unit vegetarian noodles scanning
(e) figure (a) Fe unit vegetarian noodles scanning
Fig. 4 (a) TiC (70vol%) granule partial strengthens the manganese steel composite material tissue
(b) TiC (30vol%) granule partial strengthens the power spectrum of manganese steel composite material
Fig. 5 (a) TiC (35vol%) granule partial strengthens the manganese steel composite material tissue
(b) TiC (35vol%) granule partial strengthens the power spectrum of manganese steel composite material TiC
Embodiment:
Embodiment 1
Produce TiC (30vol%) granule partial and strengthen manganese steel composite material
Get Al powder (74 μ m, 99.9%), Ti powder (29 μ m, 99.5%), C powder (50 μ m, 99.6%), matrix is a manganese steel.Above three kinds of powder are pressed C: Ti=1: 1 (atom), the ratio of Al content 5wt%, mix, on 10 tons of pressing machinees, be pressed into the cylinder shape reaction prefabricated block of φ 20 * 10 then, reaction prefabricated block be placed on carry out the vacuum stripping processing in the heating under vacuum device, vacuum degassed prefabricated section is placed into the casting mold medium casting needs the enhanced position, melting manganese steel, it is poured into casting mold make prefabricated section, self-propagating reaction takes place, make the TiC granule partial after solidifying and strengthen manganese steel composite material.Its macrohardness (HRC) 〉=35; Microhardness (HV) 〉=800.
Embodiment 2
Produce TiC (70vol%) granule partial and strengthen the 45# steel composite material
Get Al powder (74 μ m, 99.9%), Ti powder (29 μ m, 99.5%), C powder (50 μ m, 99.6%), matrix 45# steel.Above three kinds of powder are pressed C: Ti=1: 1 (atom), the proportioning of Al content 5wt%, mix, on 10 tons of pressing machinees, be pressed into the cylinder shape reaction prefabricated block of φ 20 * 10, reaction prefabricated block is placed on carries out vacuum stripping in the heating under vacuum device and handle, it is placed into the casting mold medium casting needs enhanced position, melting 45# steel, it is poured in the casting mold, strengthen the 45# steel composite material thereby make prefabricated section generation self-propagating reaction make the TiC granule partial.Its macrohardness (HRC) 〉=40; Microhardness (HV) 〉=1200.
Embodiment 3
Produce TiC (40vol%) granule partial and strengthen manganese steel composite material
Get Al powder (29 μ m, 99.6%), Ti powder (44 μ m, 99.5%), C powder (50 μ m, 99.6%), matrix manganese steel.Above three kinds of powder are pressed C: Ti=1: 1 (atom), the ratio of Al content 40wt%, mix, on 10 tons of pressing machinees, be pressed into the cylinder shape reaction prefabricated block of φ 20 * 10 then, reaction prefabricated block is placed on carries out vacuum stripping in the heating under vacuum device and handle and to be placed into the casting mold medium casting and to need the enhanced position, melting 45# steel, it is poured in the casting mold, make prefabricated section generation self-propagating reaction, prefabricated section is fully reacted, strengthen manganese steel composite material thereby make TiC (40vol%) granule partial.
Embodiment 4
Produce TiC (60vol%) granule partial and strengthen manganese steel composite material
Get Al powder (44 μ m, 99.6%), Ti powder (25 μ m, 99.5%), C powder (25 μ m, 99.6%), the matrix magnesium alloy is a manganese steel.Above three kinds of powder are pressed C: Ti=1: 1 (atom), the proportioning of Al content 15wt% mixes, and is pressed into the cylinder shape reaction prefabricated block of φ 20 * 10 on 10 tons of pressing machinees, reaction prefabricated block is placed in the heating under vacuum device, degasification 2h takes out reaction prefabricated block, it is placed into the casting mold medium casting needs the enhanced position, melting 45# steel, it is poured in the casting mold, make prefabricated section generation self-propagating reaction, strengthen manganese steel composite material thereby make TiC (30wt%) granule partial.Its its macrohardness (HRC) 〉=38; Show and be hardness (HV) 〉=900.Compare wear resistance ε 〉=2.0 with matrix manganese steel.
Claims (1)
1. steel-base composite feinforced by particles generated in-situ locally preparation method is characterized in that technological process comprises in preparation feedback prefabricated section and the type from spreading two stages of in-situ synthesized reaction:
1) preparation of prefabricated section may further comprise the steps:
A. prefabricated section is formed: prefabricated section is made up of pulverous Al, C and Ti, Al content (wt%) 1%～50%, C and Ti
Atomic ratio be: 0.6～1.4, its size range is 0.1 μ m～200 μ m,
B. batch mixing: the above-mentioned starting material that prepare are packed in the stirrer, stirred 4～48 hours, mix;
C. compression moulding: the starting material that mix are put into mould, compression moulding at room temperature, pressure range is 200～800Mpa;
D. the vacuum stripping of prefabricated section is handled: the prefabricated section that suppresses is put into the heating under vacuum device, vacuum tightness 〉=10
-1MPa is heated to 100～400 ℃, degasification 1～4h with the heating rate of 5～40 ℃/min;
2) spread the original position synthesis particle wild phase in the type certainly:
A. casting mold requires: casting mold water content＜4% that the molten steel casting is adopted, ventilation property＞100.
B. the matrix molten steel requires: be prefabricated section generation self propagating high temperature building-up reactions, generate the particle wild phase enough heats are provided that molten steel temperature guarantees more than 1450 ℃.
C. the placement of prefabricated section in casting mold: need the enhanced position to place the Al-Ti-C prefabricated section of vacuum degassing processing at foundry goods.
D. the casting matrix molten steel prepares local granule enhancing base steel composite material.
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1318637C (en) * | 2005-01-10 | 2007-05-30 | 山东科技大学 | Method for preparing intermetallic compound powder cored filament material for electric arc spraying |
| CN1327028C (en) * | 2004-09-03 | 2007-07-18 | 吉林大学 | Surface or local gradient reinforced wear resistant manganese steel composite material and preparing process |
| CN101161374B (en) * | 2007-11-27 | 2010-08-11 | 吉林大学 | Reactant composition for preparing multiple phase confusion TiB2-TiC ceramic particle gradient enhancement metal-based complex material |
| CN102205406A (en) * | 2011-05-11 | 2011-10-05 | 西安科技大学 | In-situ synthesized Al3Ti particle surface-reinforced aluminum-base compound cylinder sleeve and manufacturing method thereof |
| CN102240794A (en) * | 2011-06-29 | 2011-11-16 | 北京交通大学 | Method for manufacturing steel-based particle reinforced composite anti-wear piece |
| CN103831421A (en) * | 2014-03-26 | 2014-06-04 | 铜仁学院 | Method for preparing local enhancement aluminum matrix composite |
| CN103949648A (en) * | 2014-05-08 | 2014-07-30 | 吉林大学 | Preparation method of high-strength high-toughness bionic-function surface wear resistance composite material |
| CN104493169A (en) * | 2014-12-26 | 2015-04-08 | 中国科学院长春光学精密机械与物理研究所 | Ceramic particle local reinforced metal heat sink and preparing method thereof |
| 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 |
-
2002
- 2002-01-27 CN CN 02109101 patent/CN1212414C/en not_active Expired - Lifetime
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1327028C (en) * | 2004-09-03 | 2007-07-18 | 吉林大学 | Surface or local gradient reinforced wear resistant manganese steel composite material and preparing process |
| CN1318637C (en) * | 2005-01-10 | 2007-05-30 | 山东科技大学 | Method for preparing intermetallic compound powder cored filament material for electric arc spraying |
| CN101161374B (en) * | 2007-11-27 | 2010-08-11 | 吉林大学 | Reactant composition for preparing multiple phase confusion TiB2-TiC ceramic particle gradient enhancement metal-based complex material |
| CN102205406A (en) * | 2011-05-11 | 2011-10-05 | 西安科技大学 | In-situ synthesized Al3Ti particle surface-reinforced aluminum-base compound cylinder sleeve and manufacturing method thereof |
| CN102205406B (en) * | 2011-05-11 | 2012-08-08 | 西安科技大学 | In-situ synthesized Al3Ti particle surface-reinforced aluminum-base compound cylinder sleeve and manufacturing method thereof |
| CN102240794A (en) * | 2011-06-29 | 2011-11-16 | 北京交通大学 | Method for manufacturing steel-based particle reinforced composite anti-wear piece |
| CN102240794B (en) * | 2011-06-29 | 2013-01-23 | 北京交通大学 | Method for manufacturing steel-based particle reinforced composite anti-wear piece |
| CN103831421A (en) * | 2014-03-26 | 2014-06-04 | 铜仁学院 | Method for preparing local enhancement aluminum matrix composite |
| CN103949648A (en) * | 2014-05-08 | 2014-07-30 | 吉林大学 | Preparation method of high-strength high-toughness bionic-function surface wear resistance composite material |
| CN104493169A (en) * | 2014-12-26 | 2015-04-08 | 中国科学院长春光学精密机械与物理研究所 | Ceramic particle local reinforced metal heat sink and preparing method thereof |
| 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 |
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