CN108570617A - A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method - Google Patents

A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method Download PDF

Info

Publication number
CN108570617A
CN108570617A CN201810589776.XA CN201810589776A CN108570617A CN 108570617 A CN108570617 A CN 108570617A CN 201810589776 A CN201810589776 A CN 201810589776A CN 108570617 A CN108570617 A CN 108570617A
Authority
CN
China
Prior art keywords
casting
powder
alloy
temperature
iron
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
CN201810589776.XA
Other languages
Chinese (zh)
Inventor
罗丰华
牟楠
温家飞
闵小兵
严淑群
王哲
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Central South University
Original Assignee
Central South University
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Central South University filed Critical Central South University
Priority to CN201810589776.XA priority Critical patent/CN108570617A/en
Publication of CN108570617A publication Critical patent/CN108570617A/en
Priority to CN201910403308.3A priority patent/CN109972054A/en
Withdrawn legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C22C33/06—Making ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)

Abstract

The mass percentage of a kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method, alloy each element is Cr：9.0~13.0, B：2.6~2.9, C：0.7~0.9, Nb：0.4~0.8, V：The content of 0.4~0.8, Mn are less than 0.3, Er：0.03~0.8, S, P：≤ 0.01, surplus Fe；Wherein C, B gross mass percentage composition are：3.3~3.6；C/Cr content ratios：0.06~0.08；The gross mass percentage composition of Nb, V is：0.5~1.0.The preparation of Fe carbonic acid bait powder compacts is first got out, alloying ingredient, melting and Metamorphism treatment carry out melting, casting and heat treatment.Ingot casting integral hardness prepared by the present invention reaches HRC65.8~70.4, and impact flexibility reaches 13.1~16.9J/cm2, bending strength reaches 1328~1571MPa.

Description

A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method
Technical field
The invention belongs to high-hardness and wear-resistant cast-iron fields, and it is solid to be related to a kind of fine hard phase and supersaturation that rare earth erbium is rotten Solution, martensitic matrix phase wear and corrosion resistant cast iron alloy and its component preparation method, can be widely used for electric power, metallurgy, machine Mechanical wearing piece manufacture in the industries such as tool, chemical industry.
Technical background
Fe-Cr-B-C abrasion resistant casting alloys are mainly with Fe2B or M2B is hard phase, has good toughness and high rigidity, height Corrosion resistance, melting-casting manufacturability is good, has very wide application prospect.
Metamorphism treatment is to improve one of Fe-Cr-B-C alloy structures and mechanical property effective ways.Alterant is according to effect The elements such as strong carbon, nitrogen, sulfide formation element, such as Ti, V, and strong constitutional supercooling element, such as surface active element can be divided into Rare earth (RE), Mg etc..
Rare earth element is gathered on the solid growth interface of liquid, and limitation crystal grain is grown up, to improve the hardness of alloy, intensity and resistance to Mill property；And thinning microstructure, so that boride suspension shape and graininess distribution is occurred, improves impact flexibility.Research shows that：In Fe-Cr- The cerium (Ce) of addition 0.6% can make impact flexibility improve 86.4% in B-C alloys.Add the mixing alterant of 1.0% (Ce+La) Into Fe-Cr-B alloys, the hardness of alloy increases to 70.2HRC by 52HRC, and impact flexibility is by 3.36J/cm2It is increased to 6.38J/cm2。
RE Modified can rare earth alloy or rare-earth wires single Modification Manners, can also take compound modification treatment, i.e., with N, The mixture of the elements such as Ti, V, Mg, Si and rare earth is as alterant.Silicon Mg mixed rare-earth alterant (RE-Si-Mg) is most common It is composite inoculating method, some researches show that：Fe-Cr-B-C alloys impact toughness after RE-Si-Mg is rotten is higher than not rotten premise 72.2%；After RE-Ti goes bad and is heat-treated, impact flexibility improves 1.8 times；Through RE-Mg go bad impact flexibility improve 34.6%；Desmachyme all disappears after RE-Ti-N is rotten, and toughness improves 133.3%；Through RE-Mg-V-Ti Metamorphism treatments Afterwards, impact flexibility reaches 15.6J/cm2；After RE-Ti-Si-V Metamorphism treatments, impact flexibility reaches 12J/cm2More than.
These using the method for RE Modified all there are one common difficulty, i.e. the pure rare earth, rare earth alloy of high activity or multiple Close rare earth material.Due to the high activity of rare earth so that the tissue of alloy, performance are difficult to control after alterant itself or Metamorphism treatment System, modification effect are difficult to ensure.
Document 1：LM cathodes research-emission principle and present Research [D] Beijing University of Technology, 2001：pp44-50.Carbonization La2O3The chemical balance of-Mo alloys：
3Mo2C(s)+La2O3(s)=2La (s, l)+3CO (g)+6Mo
Due to Mo2The effect of C, the reduction reaction free enthalpy variation for generating simple substance La is small very much, to reaction product La With the also high 10 several orders of magnitude of the equilibrium partial pressure of CO.When temperature is higher than 1673K, i.e., 1400 DEG C, CO partial pressures are less than E-9atm When, reaction equation can carry out to the right automatically, i.e. reduction generates simple substance La.
Patent document 2：The antifriction alloy hardness of 105695884 B of Authorization Notice No. CN, preparation are HRC66~70, impact 4~9J/cm of toughness2.The hardness of such alloy is higher, but impact flexibility is insufficient, and intensity index is relatively low, and bending strength is relatively low, 346~477MPa ranges limit the occasion that the Alloyapplication is big in some external loads, impact resistance is needed to act on.
Document 3：The rapid cooling organization and performance of eutectic Fe-Cr-B-C alloys, casting, 2017,66 (10):1053~1056. The rapid cooling tissue of as cast condition Fe-Cr-B-C alloys by martensite+retained austenite matrix and along the continuous net-shaped distribution of crystal boundary (Fe, Cr)2(B,C)+(Fe,Cr)23(B,C)6Hard phase composition.The microhardness of rapid cooling tissue matrix phase is 800~880HV, hard Phase microhardness is 1150~1400HV, macrohardness HRC68, and impact flexibility reaches 13.6J/cm2；And it is moved back through 960 DEG C of@2h After fire, matrix is changed into ferrite and nodular cementite, hard phase (Fe, Cr)2(B, C) and (Fe, Cr)23(B,C)6On a small quantity There is suspension, cenotype (Fe, Cr) occur in dissolving, regional area3(B, C), matrix phase microhardness is 330~400HV after annealing, Hard phase is 850~1250HV, and macrohardness is reduced to HRC46, and impact flexibility is reduced to 3.4J/cm2.3 acquired results of document Reflect that the hardness of matrix phase plays significant role to the hardness and impact flexibility of such material；Using high temperature solid solution quenching-low temperature Temper, is improved the solid solubility of matrix phase and the possibility of hardness, referenced patent document 2, such alloy after Overheating Treatment, There is the possibility promoted in aspect of performance such as impact flexibility.
Invention content
The object of the present invention is to provide a kind of rare earth erbium toughening high hard alloy and its casting and heat treatment methods.This method is adopted Use Er2O3For alterant, carbide, boride in high temperature melting state Fe-Cr-B-C alloys, which have, promotes high activity Er first The thermodynamic condition that element is formed, and form compound containing Er in C, B so that casting alloy structure refinement, carbon boride break Netted and presentation graininess distribution；After heat treatment, matrix is that the polynary supersaturated solid solution of high rigidity, martensite etc. are non-equilibrium Phase so that alloy has good toughness, high rigidity and higher intensity index.
Er2O3Powder, which is added directly into melt, can float with clinker and cause Er loss of elements, to lose modification effect, Therefore the present invention uses Er2O3Powder and iron powder after mixing, are molded into powder compact, then with Fe-Cr-B-C casting alloys one Play fusing.Er2O3The weight ratio of powder and iron powder substantially 1:5~20, that is, form the mixing pressure of Fe-4.16~14.58wt.%Er Block.The too high levels of the too low then Fe of Er amounts, can influence burdening calculation；And Er too high levels then green compact forming difficulty.Wherein Er2O3Powder is white amorphous powder, Er2O3Content is more than 99.0%, therefore is not strict with to its purity and granularity. Fe powder is reduction Fe powder or water atomization Fe powder, can contain the member in the alloying element or impurity ranges in modified cast iron in Fe powder Element, such as Ni, V, Cr, being subject to does not influence briquette forming and influence burdening calculation.
The high-wearing feature for the patent document 2 that the present invention selects, high corrosion-resistant Fe-Cr-B-C alloys are basic alloy, then are added Add 0.03~0.8%Er elements rotten.The multi-element eutectic alloy containing elements such as Fe, Cr, B, C, Nb, V, Er is formed, each element Mass percentage is Cr：9.0~13.0, B：2.6~2.9, C：0.7~0.9, Nb：0.4~0.8, V：0.4~0.8, Mn's Content is less than 0.3, Er：0.03~0.8, S, P：≤ 0.01, surplus Fe.Wherein C, B summation：3.3~3.6；C/Cr content ratios： 0.06~0.08；The summation of Nb, V are 0.5~1.0.
With reference to patent document 2, it is specific prepare alloy when, can be used ferrochrome (high-carbon, middle carbon, micro- carbon), ferro-boron, ferro-niobium, Vanadium iron, pure iron, etc. according to component requirements dispensing.Raw material and its composition are listed in table 1.
Table 1 can be applied to prepare the raw material and composition of invention alloy
The material composition of table 1 is not unique, and specific ingredient raw material obtained by reality determine.Wherein ferrochrome, Crome metal, ferro-boron, ferro-niobium and vanadium iron provide the content of Cr, B, Nb and V of invention alloy, and high carbon ferro-chrome is used for balancing C content.It is pure Iron can be electrical pure iron, electromagnetic pure iron or ingot iron.
The method specifically comprises the following steps：
(1)Fe-Er2O3Powder compact prepares
Using iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight ratio of powder and iron powder is substantially 1:5~20, that is, form the Fe-Er of Fe-4.16~14.58%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
(2) alloying ingredient, melting and Metamorphism treatment
After weighing good corresponding raw material according to the component requirements proportioning of Fe-Cr-B-C alloys, then add 0.03~0.8%Er Element is rotten.First by Fe-Er2O3Powder compact is positioned over furnace bottom, be then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and Pure iron.Induction furnace, vaccum sensitive stove etc. can be used carry out melting and prepares alloy.Fusion temperature is higher than 1520~1620 DEG C；Then it drops Low furnace power, after melt temperature is down to 1320~1380 DEG C, with the fine aluminium deoxidation of dispensing total amount 0.1~0.15%；Continue Heat preservation stands about 5~10 minutes.
(3) it casts
Ranging from 1280~1320 DEG C of cast temperature.Designed alloy has deep eutectic ingredient, is molded in normal sands Non-equilibrium matrix can be formed under the conditions of making, such as amorphous, nanocrystalline or martensitic structure.Since designed alloy is total Brilliant ingredient, melt have good mobility fine, can casting and forming by various methods, such as normal sands Mold casting or The special casting method such as model casting, lost foam casting, permanent mold casting, ceramic mold casting, die casting, centrifugal casting.In order to keep away Exempt from that thermal stress-cracking occurs, die sinking temperature will be less than 200 DEG C after having cast, and naturally cool to environment temperature.
(4) it is heat-treated
Casting is put into box stove heat, heating temperature is 950~1060 DEG C, and soaking time is 1~4h.Heat temperature raising Speed is no more than 10 DEG C/min.
After heat preservation, casting is quickly entered to 5~15% brine or buck quenching cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.
Then in 200~250 DEG C of 2~4h of temper, environment temperature is naturally cooled to.
Step (1) described iron powder is purity >=98.5%, the reduced iron powder or purity >=99.0% of -100 mesh of granularity, grain Spend the water-atomized iron powder of -100 mesh, or quite granularity contains a small amount of alloy iron powder for not influencing casting alloy ingredient.Also may be used To select the powder of smaller particle size, the compact strength with follow-up dispensing and furnace charge preparation is not influenced can be pressed by being subject to.
Step (1) is described to be uniformly mixed into mixed cartridge type batch mixing, V-type batch mixing or stir mixing, substantial uniform to realize .
Step (1) described green compact is die forming, and pressing pressure is 100~600MPa, and green compact size is unlimited.It can also adopt Take isostatic cool pressing method.
Step (2) is by Fe-Er2O3The purpose that powder compact is positioned over furnace bottom is：The substances such as ferrochrome, ferro-boron have than pure The low fusion temperature of iron, therefore can preferentially melt and be impregnated into the Fe-Er of bottom2O3Powder compact so that straight iron powder gradually melts Change, and releases Er2O3Powder particle.Er2O3Density be slightly above melt, about 8.64g/cm3, disperse in the melt Er2O3Particle is by Fe3C、Cr3C2Equal carbide restore to form active Er elements, and are reacted with C, B, are formed and are similar to Er (B, C)6 Compound.CO, the CO formed in reaction process2Equal gas molecules can be adsorbed on Er2O3Around particle, Er is driven2O3On particle It is floating so that Elemental redistribution is uniform, and modification effect improves.
By the metamorphism of Er, the reticular structure and Needle-shaped boride of distribution along crystal boundary disappear, and alloy is by primary crystal matrix phase It is formed with eutectic structure, this eutectic structure, which is interted by tiny matrix phase with hard phase, to be formed so that the intensity of alloy and punching Toughness is hit to be improved.
If Er2O3Powder is not previously prepared to be positioned over furnace bottom at briquetting, then is easy to float to bath surface, melt with clinker Surface oxygen content is high, Er2O3It is not easy to be reduced to form active Er, and loses modification effect.
The Fe3C、Cr3C2Equal carbide are formed by C and Fe element reactions when high carbon ferro-chrome and fusing, due to Fe3C、 Cr3C2The stability of equal carbide at high temperature is not so good as Mo2C, and the temperature melted is more than 1400 DEG C of reactions described in document 1 Temperature, the partial pressure of CO gases is also extremely low in melt；And the property of Er and La is much like, thus it is similar to document 1, it generates and lives The reduction reaction of property Er can carry out.EDS energy spectrum analysis, which also indicates that, contains Er elements in casting alloy object phase.
Step (4) is when hardening heat is 950~1060 DEG C, as hardening heat increases, some dissolving of hard phase Into matrix phase so that matrix phase volume fraction increases, while alloying element content also improves in matrix phase, can be formed after quenching The martensitic structure of more high rigidity.Hereby it is ensured that whole hardness and comprehensive performance.
The tissue of Fe-Cr-B-C alloys is cast mainly by hard phase (Fe2B or M2B etc.) and matrix phase (α or martensitic phase) Composition.The hardness of alloy depends primarily on the volume ratio of hard phase, i.e. hard phase is higher, and the hardness of material is bigger.But due to hard Matter is mutually excessive, and matrix phase intensity is relatively low, integral hardness can be caused to decline, toughness is insufficient.Therefore, in addition to hard phase and matrix phase Ratio is outside determinant, and the characteristic of matrix phase is also critically important.When hardening heat is less than 950 DEG C, hard phase can be analysed from matrix Go out so that material hardness declines, the reductions such as impact flexibility.Continue raising hardening heat and reach 1100 DEG C, office in casting can be caused Portion's burning so that alloy ductility declines.
The Fe-Cr-B-C alloys that the Er Modification Manners of the present invention are not limited to, can also be applied to other cast irons and C content are higher Smelting iron and steel is rotten, micronization processes.
The present invention be mainly characterized by directly use Er2O3Powder is mixed with iron powder, forms powder compact, rotten as Er elements Carrier.Utilize Fe in Fe-Cr-B-C alloy high-temp melts3C、Cr3C2The reduction of equal carbide forms active Er elements, and It is reacted with C, B, is formed and be similar to Er (B, C)6Compound, avoid the occurrence of that boride is netted and acicular texture, promote tiny total Crystalline substance organizes the formation of, and plays the rotten toughening effect of thinning microstructure.Pass through quenching-temper again so that the volume of matrix phase point Number, solid solubility and hardness increase, so as to improve the rapport between matrix phase and boron, carbon compound.Ingot casting integral hardness reaches To HRC65.8~70.4, impact flexibility reaches 13.1~16.9J/cm2, bending strength reaches 1328~1571MPa.
Description of the drawings
1 cast sturcture of Fig. 1 present examples schemes；
1 casting alloy X-ray diffracting spectrum of Fig. 2 present examples；
The EDS collection of illustrative plates and ingredient of 1 casting matrix phase of Fig. 3 present examples.
Specific implementation mode
The various method of smelting of the present invention, casting method are not limited by following examples, and any right in the present invention is wanted The improvement in range and variation for asking book claimed are all within protection scope of the present invention.
Select high carbon ferro-chrome, chromic carbide iron, crome metal, ferro-boron, ferro-niobium, vanadium iron, ingot iron, straight iron powder, Er2O3It is powder, pure Aluminium etc. is raw material, and alloy is configured in the composition range that invention requires.
Embodiment 1. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:5, that is, form the Fe-Er of Fe-14.58wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, chromic carbide iron, ferro-boron, ferro-niobium, vanadium iron, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is Raw material, composition range are as follows：Cr:10.0wt.%；B:2.9wt.%；C:0.7wt.%；Nb:0.4wt.%；V:0.2wt.%； Er:0.8wt.%；Impurity element control is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, because This is unlisted in table 2.
After weighing good corresponding raw material according to component requirements proportioning, using induction melting and sand mold die cast.Specific steps For：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1620 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1380 DEG C, with dispensing total amount 0.15% fine aluminium deoxidation；Continue heat preservation and stands about 10 minutes.Ranging from 1320 DEG C of cast temperature.Die sinking temperature is low after having cast In 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 950 DEG C, soaking time 4h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, casting is quickly entered to 5% brine hardening cooling.It should be stirred continuously in cooling procedure, Quench cooling time >=30min.Then in 200 DEG C of temper 4h, environment temperature is naturally cooled to.
Fig. 1 is casting alloy tissue, and based on Fe primary phases and eutectic phase, wherein eutectic phase is Fe phases and boron, carbon compound The eutectic structure of object；Fig. 2 is the X-ray diffracting spectrum of casting alloy, and display alloy substrate is α-Fe phases, and diffraction maximum is wider, And it is wider nearby at 65 °, therefore be the martensitic phase for having a large amount of Cr solid solutions, carbon, boron compound Fe2B、Fe3C and Cr23C6For base The complex chemical compound of plinth, and show Er (B, C)6Compound exists；Fig. 3 is casting alloy matrix phase EDS collection of illustrative plates and analysis As a result, as a result EDS can only show in alloy there are Er elements in the qualitative analysis of ingredient, illustrate Er2O3Work is produced with melt With, make Er elements occur alloying, play melt metamorphism.
Gained ingot casting integral hardness reaches HRC67.6, and impact flexibility reaches 14.5J/cm2, bending strength reach 1330MPa.
Embodiment 2. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:20, that is, form the Fe-Er of Fe-4.16wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, crome metal, ferro-boron, ferro-niobium, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is raw material, at Divide range as follows：Cr:10.0wt.%；B:2.7wt.%；C:0.7wt.%；Nb:0.5wt.%；Er:0.03wt.%；Impurity member Element control is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, therefore unlisted in table 2.
After weighing good corresponding raw material according to component requirements proportioning, vacuum induction melting and the casting of water cooling swage can be used It makes.The specific steps are：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium and pure iron.Fusing Temperature is 1520 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1320 DEG C, with dispensing total amount 0.1% Fine aluminium deoxidation；Continue heat preservation and stands about 5 minutes.Ranging from 1280 DEG C of cast temperature.Die sinking temperature will be less than 200 after having cast DEG C, naturally cool to environment temperature.
Then casting is put into box stove heat, heating temperature is 1050 DEG C, soaking time 1h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, casting is quickly entered to 15% brine hardening cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.Then in 250 DEG C of temper 2h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC68.7, and impact flexibility reaches 15.8J/cm2, bending strength reaches 1418MPa。
Embodiment 3. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:10, that is, form the Fe-Er of Fe-7.95wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, chromic carbide iron, ferro-boron, ferro-niobium, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is raw material, Composition range is as follows：Cr：10.0wt.%；B：2.7wt.%；C:0.8wt.%；Nb:0.6wt.%；Er:0.6wt.%；Impurity Control of element is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, therefore unlisted in table 2.
After good corresponding raw material being weighed according to component requirements proportioning, using induction melting and model casting, the specific steps are：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1580 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1320 DEG C, with dispensing total amount 0.12% fine aluminium deoxidation；Continue heat preservation and stands about 8 minutes.Ranging from 1280 DEG C of cast temperature.Die sinking temperature is wanted after having cast Less than 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 1000 DEG C, soaking time 2h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, casting is quickly entered to 10% brine hardening cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.Then in 220 DEG C of temper 3h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC69.9, and impact flexibility reaches 13.4J/cm2, bending strength reaches 1358MPa。
Embodiment 4. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:15, that is, form the Fe-Er of Fe-5.47wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, crome metal, ferro-boron, ferro-niobium, vanadium iron, ingot iron and above-mentioned Fe-Er2O3It is original to mix briquetting Material, composition range are as follows：Cr：11.0wt.%；B：2.7wt.%；C:0.7wt.%；Nb:0.2wt.%；V:0.4wt.%；Er: 0.5wt.%；Impurity element control is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, therefore not It is listed in Table 2.
After good corresponding raw material being weighed according to component requirements proportioning, using induction melting and sand casting, the specific steps are：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1600 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1340 DEG C, with dispensing total amount 0.13% fine aluminium deoxidation；Continue heat preservation and stands about 9 minutes.Ranging from 1280 DEG C of cast temperature.Die sinking temperature is wanted after having cast Less than 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 1060 DEG C, soaking time 2h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, the buck that casting is quickly entered to 5% quenches cooling.It should be stirred continuously in cooling procedure, Quench cooling time >=30min.Then in 220 DEG C of temper 2h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC67.0, and impact flexibility reaches 13.1J/cm2, bending strength reaches 1571MPa。
Embodiment 5. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:12, that is, form the Fe-Er of Fe-6.73Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, chromic carbide iron, ferro-boron, ferro-niobium, vanadium iron, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is Raw material, composition range are as follows：Cr：10.0wt.%；B：2.6wt.%；C：0.6wt.%；Nb：0.3wt.%；V：0.1wt.%； Er:0.2wt.%；Impurity element control is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, because This is unlisted in table 2.
After weighing good corresponding raw material according to component requirements proportioning, using induction melting and lost foam casting, specific steps It is as follows：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1600 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1325 DEG C, with dispensing total amount 0.12% fine aluminium deoxidation；Continue heat preservation and stands about 6 minutes.Ranging from 1285 DEG C of cast temperature.Die sinking temperature is wanted after having cast Less than 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 980 DEG C, soaking time 3h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, the buck that casting is quickly entered to 15% quenches cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.Then in 220 DEG C of temper 3h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC65.8, and impact flexibility reaches 16.9J/cm2, bending strength reaches 1328MPa。
Embodiment 6. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:8, that is, form the Fe-Er of Fe-9.72wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, chromic carbide iron, ferro-boron, ferro-niobium, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is raw material, Composition range is as follows：Cr：10.0wt.%；B：2.6wt.%；C：0.8wt.%；Nb：0.8wt.%；Er:0.3wt.%；Impurity Control of element is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, therefore unlisted in table 2.
It is specific to walk using vacuum induction melting and iron mould casting after weighing good corresponding raw material according to component requirements proportioning It is rapid as follows：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1590 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1325 DEG C, with dispensing total amount 0.14% fine aluminium deoxidation；Continue heat preservation and stands about 7 minutes.Ranging from 1290 DEG C of cast temperature.Die sinking temperature is wanted after having cast Less than 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 1020 DEG C, soaking time 2h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, the buck that casting is quickly entered to 10% quenches cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.Then in 220 DEG C of temper 3h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC70.4, and impact flexibility reaches 15.1J/cm2, bending strength reaches 1418MPa。
Embodiment 7. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:9, that is, form the Fe-Er of Fe-8.75wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, chromic carbide iron, ferro-boron, ferro-niobium, vanadium iron, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is Raw material, composition range are as follows：Cr：11.0wt.%；B：2.6wt.%；C：0.9wt.%；Nb：0.2wt.%；V：0.2wt.%； Er:0.10wt.%；Impurity element control is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, because This is unlisted in table 2.
After weighing good corresponding raw material according to component requirements proportioning, induction melting and lost foam casting can be used.Specific step It is rapid as follows：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1610 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1340 DEG C, with dispensing total amount 0.13% fine aluminium deoxidation；Continue heat preservation and stands about 8 minutes.Ranging from 1290 DEG C of cast temperature.Die sinking temperature is wanted after having cast Less than 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 1020 DEG C, soaking time 1h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, the buck that casting is quickly entered to 15% quenches cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.Then in 200 DEG C of temper 4h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC68.3, and impact flexibility reaches 13.5J/cm2, bending strength reaches 1520MPa。
Embodiment 8. uses iron powder and Er2O3Powder after mixing, is molded into powder compact.Er2O3The weight of powder and iron powder Than substantially 1:16, that is, form the Fe-Er of Fe-5.14wt.%Er2O3Mix briquetting.The carrier to go bad as rare earth Er.
Select high carbon ferro-chrome, chromic carbide iron, ferro-boron, ferro-niobium, vanadium iron, ingot iron and above-mentioned Fe-Er2O3Mixing briquetting is Raw material, composition range are as follows：Cr：13.0wt.%；B：2.6wt.%；C：0.8wt.%；Nb：0.6wt.%；V：0.4wt.%； Er:0.08wt.%；Impurity element control is shown in Table 2.The impurity such as a small amount of Al, Mn, N will not cause alloy property essence to change, because This is unlisted in table 2.
After weighing good corresponding raw material according to component requirements proportioning, using induction melting and lost foam casting, specific steps It is as follows：
By Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure iron. Fusion temperature is 1600 DEG C；Until completely melted, furnace power is reduced, after melt temperature is down to 1330 DEG C, with dispensing total amount 0.12% fine aluminium deoxidation；Continue heat preservation and stands about 6 minutes.Ranging from 1300 DEG C of cast temperature.Die sinking temperature is wanted after having cast Less than 200 DEG C, environment temperature is naturally cooled to.
Then casting is put into box stove heat, heating temperature is 980 DEG C, soaking time 2h.Heat temperature raising speed No more than 10 DEG C/min.After heat preservation, the buck that casting is quickly entered to 10% quenches cooling.It should constantly be stirred in cooling procedure It mixes, quenches cooling time >=30min.Then in 200 DEG C of temper 2h, environment temperature is naturally cooled to.
Gained ingot casting integral hardness reaches HRC68.4, and impact flexibility reaches 16.3J/cm2, bending strength reaches 1544MPa。
Casting alloy performance detection prepared by each embodiment is as described below：
1. pair example casting metal carries out hardness test using HR-150A Rockwell hardness machines, load 150Kg makes a call to five It is averaged after point, is listed in table 2.
2. pair example casting metal carries out impact flexibility test using JBS-300B shock machines, range 150J is beaten It is averaged after five samples, is listed in table 2.
3. pair example casting metal material electronics universal testing machine carries out three-point bending resistance experiment, sample size is 2 × 5 × The rectangular specimen of 50mm, span 30mm take the bending strength average value of three same treatment samples to be listed in table 2.
The ingredient of 2 embodiment of table and hardness, impact flexibility and bending strength

Claims (5)

1. a kind of rare earth erbium toughening high hard alloy, it is characterised in that：The mass percentage of alloy each element is Cr：9.0~ 13.0 B：2.6~2.9, C：0.7~0.9, Nb：0.4~0.8, V：The content of 0.4~0.8, Mn are less than 0.3, Er：0.03~ 0.8, S, P：≤ 0.01, surplus Fe；Wherein C, B gross mass percentage composition are：3.3~3.6；C/Cr content ratios：0.06~ 0.08；The gross mass percentage composition of Nb, V is：0.5~1.0.
2. casting and the heat treatment method of rare earth erbium toughening high hard alloy as described in claim 1, it is characterised in that including with Lower step：
(1)Fe-Er2O3Powder compact prepares
Using iron powder and Er2O3Powder after mixing, is molded into powder compact；Er2O3The weight ratio of powder and iron powder is 1:5~20, Form the Fe-Er of Fe-4.16~14.58%Er2O3Briquetting is mixed, the carrier to go bad as rare earth Er；
(2) alloying ingredient, melting and Metamorphism treatment
After weighing good corresponding raw material according to the component requirements proportioning of Fe-Cr-B-C alloys, then add 0.03~0.8%Er elements It is rotten：First by Fe-Er2O3Powder compact is positioned over furnace bottom, is then placed in ferrochrome, crome metal, ferro-boron, ferro-niobium, vanadium iron and pure Iron prepares alloy, 1520~1620 DEG C of fusion temperature using induction furnace melting；Then furnace power is reduced, melt temperature is dropped To after 1320~1380 DEG C, with the fine aluminium deoxidation of dispensing total amount 0.1~0.15%；Continue heat preservation and stands 5~10 minutes；
(3) it casts
Ranging from 1280~1320 DEG C of cast temperature, designed alloy has deep eutectic ingredient, in common sand casting item Non-equilibrium matrix can be formed under part, by various methods casting and forming, in order to avoid thermal stress-cracking occurs, cast Die sinking temperature is less than 200 DEG C afterwards, naturally cools to environment temperature；
(4) it is heat-treated
Casting is put into box stove heat, heating temperature is 950~1060 DEG C, and soaking time is 1~4h, heat temperature raising speed No more than 10 DEG C/min；After heat preservation, casting is quickly entered into 5~15% brine or buck quenching cools down, in cooling procedure It should be stirred continuously, quench cooling time >=30min；Then in 200~250 DEG C of 2~4h of temper, environment temperature is naturally cooled to Degree.
3. casting and the heat treatment method of rare earth erbium toughening high hard alloy as claimed in claim 2, it is characterised in that step (1) The iron powder is purity >=98.5%, the reduced iron powder or purity >=99.0% of -100 mesh of granularity, the water mist of -100 mesh of granularity Change iron powder, or quite granularity contains a small amount of alloy iron powder for not influencing casting alloy ingredient.It can also select smaller particle size Powder, the compact strength with not influencing follow-up dispensing and furnace charge and preparing can be pressed by being subject to.
4. casting and the heat treatment method of rare earth erbium toughening high hard alloy as claimed in claim 2, it is characterised in that step (1) It is described to be uniformly mixed into mixed cartridge type batch mixing, V-type batch mixing or stir mixing.
5. casting and the heat treatment method of rare earth erbium toughening high hard alloy as claimed in claim 2, it is characterised in that step (1) The green compact is die forming, and pressing pressure is 100~600MPa, or takes isostatic cool pressing method.
CN201810589776.XA 2018-06-08 2018-06-08 A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method Withdrawn CN108570617A (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
CN201810589776.XA CN108570617A (en) 2018-06-08 2018-06-08 A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method
CN201910403308.3A CN109972054A (en) 2018-06-08 2019-05-15 A kind of erbium toughening high hard alloy and its casting and heat treatment method

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201810589776.XA CN108570617A (en) 2018-06-08 2018-06-08 A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method

Publications (1)

Publication Number Publication Date
CN108570617A true CN108570617A (en) 2018-09-25

Family

ID=63572110

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201810589776.XA Withdrawn CN108570617A (en) 2018-06-08 2018-06-08 A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method

Country Status (1)

Country Link
CN (1) CN108570617A (en)

Similar Documents

Publication Publication Date Title
CN108707835A (en) A kind of rare-earth yttrium toughening high hard alloy and its casting and heat treatment method
CN108425072A (en) A kind of Rare Earth Lanthanum toughening high hard alloy and its casting and heat treatment method
CN108396249A (en) A kind of lanthanum carbonate toughening high hard alloy and its casting and heat treatment method
CN108570617A (en) A kind of rare earth erbium toughening high hard alloy and its casting and heat treatment method
CN108441777A (en) A kind of cerium toughening high hard alloy and its casting and heat treatment method
CN108441775A (en) A kind of carbonic acid erbium toughening high hard alloy and its casting and heat treatment method
CN109972054A (en) A kind of erbium toughening high hard alloy and its casting and heat treatment method
CN108570608A (en) A kind of rare earth strontium toughening high hard alloy and its casting and heat treatment method
CN108570618A (en) A kind of strontium nitrate toughening high hard alloy and its casting and heat treatment method
CN108570619A (en) A kind of yttrium carbonate toughening high hard alloy and its casting and heat treatment method
CN108754292A (en) A kind of strontium carbonate toughening high hard alloy and its casting and heat treatment method
CN108570621A (en) A kind of cerous carbonate toughening high hard alloy and its casting and heat treatment method
CN108570620A (en) A kind of yttrium nitrate toughening high hard alloy and its casting and heat treatment method
CN108707833A (en) A kind of erbium nitrate toughening high hard alloy and its casting and heat treatment method
CN108774706A (en) A kind of cerous nitrate toughening high hard alloy and its casting and heat treatment method
CN108707834A (en) A kind of lanthanum nitrate toughening high hard alloy and its casting and heat treatment method
CN109972053A (en) A kind of cerium toughening casting alloy and its preparation and heat treatment method
CN109972052A (en) A kind of strontium goes bad high hard alloy and its casting and heat treatment method
CN109972050A (en) A kind of yttrium toughened antiwear alloy and its casting and heat treatment method
CN108677104A (en) A kind of rare earth bait goes bad toughening high hardness alloy and its casting method
CN110106450A (en) A kind of lanthanum toughening high hard alloy and its casting and heat treatment method
CN108570622A (en) A kind of carbonic acid erbium goes bad toughening high hardness alloy and its casting method
CN108707812A (en) A kind of Al toughenings high hardness wear-resisting alloy and its casting and heat treatment method
CN108570609A (en) A kind of yttrium nitrate goes bad toughening high hardness alloy and its casting method
CN108570624A (en) A kind of cerium goes bad toughening high hardness alloy and its casting method

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
WW01 Invention patent application withdrawn after publication

Application publication date: 20180925

WW01 Invention patent application withdrawn after publication