CN103114232A - Rare-earth modified steel-bonded hard alloy and preparation method - Google Patents
Rare-earth modified steel-bonded hard alloy and preparation method Download PDFInfo
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- CN103114232A CN103114232A CN201310091944XA CN201310091944A CN103114232A CN 103114232 A CN103114232 A CN 103114232A CN 201310091944X A CN201310091944X A CN 201310091944XA CN 201310091944 A CN201310091944 A CN 201310091944A CN 103114232 A CN103114232 A CN 103114232A
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Abstract
The invention discloses a rare-earth modified steel-bonded hard alloy and a preparation method thereof. The rare-earth modified steel-bonded hard alloy is prepared from the following raw materials by weight percent: 48-50% of TiC powder, 13-15% of Mn powder, 1.5-3.0% of Mo powder, 1.0-2.0% of Ni powder, 1.0-1.3% of graphite powder, 0.2-0.5% of La2O3 powder and the balance of reduced iron powder. The preparation method comprises the following steps of: ball-milling and mixing the materials which are prepared by weight percent, spray-drying and pelleting, pressing and molding under a certain pressure, vacuum-sintering at 1400-1430 DEG C and preserving the heat for 1-3hours, and cooling along with the furnace. The rare-earth modified steel-bonded hard alloy prepared by the invention is low in porosity, high in density and high in anti-bending strength; and the preparation method is simple in process, short in sintering period, low in process cost, and is applicable to industrial production.
Description
Technical field
The present invention relates to a kind of Steel Bond Hard Alloy and preparation method thereof, relate in particular to a kind of rare earth modified Steel Bond Hard Alloy and preparation method.
Background technology
Steel Bond Hard Alloy is as Binder Phase, matrix material take refractory carbide as hard phase with steel.The advantage separately of its existing Wimet and steel matrix has again high rigidity, high-wearing feature and the high strength of Wimet concurrently, has simultaneously workability, heat-treatability, forging property and the weldability of steel, has filled up blank between the two.Steel Bond Hard Alloy has consisted of the over-all properties advantage of own uniqueness, the over-all properties of this excellence makes it have the field of particular requirement to have broad application prospects at the surveying instruments such as tool die material, wear-resisting and damping part, high temperature resistant and corrosion resistant member, impact and broken instrument, cutlery, amount jig and defence and military material, navigation, aerospace material etc. to material proportion and over-all properties.
In metallic carbide, titanium carbide has high rigidity, anti-oxidant, corrosion-resistant, proportion is little, Heat stability is good and excellent physical and chemical performance, and Grain growth trend is little in sintering process, and is generally rounded, for alloy provides good use properties, it is a kind of more satisfactory hard phase.
The Steel Bond Hard Alloy density of existing bibliographical information is lower, and bending strength is lower, can not be advantageously applied in the industrial production of the standardized component such as blade and wear part, has restricted the expansion of its Application Areas.
Summary of the invention
The object of the present invention is to provide the rare earth modified Steel Bond Hard Alloy that a kind of density is high, bending strength is high.
Another object of the present invention is to provide the preparation method of the rare earth modified Steel Bond Hard Alloy that a kind of technique is simple, cost is low.
Rare earth modified Steel Bond Hard Alloy provided by the invention is prepared from by by weight percentage following raw material: TiC powder 48-50%, Mn powder 13-15%, Mo powder 1.5-3.0%, Ni powder 1.0-2.0%, Graphite Powder 99 1.0-1.3%, La
2O
3Powder 0.2-0.5%, surplus is reduced iron powder.
As improvement, rare earth modified Steel Bond Hard Alloy of the present invention is prepared from by by weight percentage following raw material: TiC powder 48-50%, Mn powder 13-15%, Mo powder 2.0-3.0%, Ni powder 1.0-2.0%, Graphite Powder 99 1.2-1.3%, La
2O
3Powder 0.4-0.5%, surplus is reduced iron powder.
The preparation method of above-mentioned rare earth modified Steel Bond Hard Alloy comprises the following steps:
(1) batching is by described component and weight percent batching;
(2) ball milling mixes, and the powder for preparing is put into ball grinder carry out ball milling;
(3) compression moulding, the powder that ball milling is good carries out spray-drying process, makes pressed compact under certain pressure;
(4) vacuum sintering, after 1400-1430 ℃ of lower vacuum sintering and being incubated 1-3 hour, furnace cooling.
As improvement, the described La of step (1)
2O
3The powder footpath is less than 45mm, and the reduced iron powder particle diameter is less than 75mm.
As improvement, the described ball grinder of step (2) is stainless cylinder of steel, and take Stainless Steel Ball as grinding element, take alcohol as ball-milling medium, ratio of grinding media to material is 5:1.
As improvement, the described Ball-milling Time of step (2) is 18-20 hour.
As improvement, the described compression moulding pressure of step (3) is 200-500MPa.
As improvement, the described vacuum sintering of step (4) is carried out under 0.5Pa at low vacuum.
The present invention is by adding La
2O
3Suppress growing up of crystal grain, and played the effect of dispersion-strengthened.Due to La
2O
3Chemical property is active, under sintering temperature, and La
2O
3Can with the metal-powder interface on impurity and oxide film effect, play the effect that purifies the interface, help the improvement of wettability, thereby be conducive to the process of densification, reach the purpose that reduces porosity, and the raising that reduces to help bending strength of porosity.La
2O
3Powder content can play the rare earth reinforced effect between 0.2% and 0.5%, therefore intensity and the density of Steel Bond Hard Alloy of the present invention are improved, and more than bending strength can reach 1700MPa, density reached more than 97.4%.
The rare earth modified Steel Bond Hard Alloy porosity that the present invention obtains is low, and density is high, and crystal grain is tiny, homogeneous microstructure, and bending strength is high, and mechanical property is good.Simultaneously, preparation method's technique of the present invention is simple, easy to operate, the sintering period is short, process costs is low, be suitable for suitability for industrialized production.
Description of drawings
Fig. 1 is the typical gold phase constitution photo (1500 *) of rare earth modified Steel Bond Hard Alloy of the present invention.
Embodiment
Rare earth modified Steel Bond Hard Alloy of the present invention is the TiC powder of 48-50% by weight percent, the Mn powder of 13-15%, the Mo powder of 1.5-3.0%, the Ni powder of 1.0-2.0%, the Graphite Powder 99 of 1.0-1.3%, the La of 0.2-0.5%
2O
3Powder, all the other are prepared from for reduced iron powder.In order to reach better density and bending strength, prepare by following weight percent: TiC powder 48-50%, Mn powder 13-15%, Mo powder 2.0-3.0%, Ni powder 1.0-2.0%, Graphite Powder 99 1.2-1.3%, La
2O
3Powder 0.4-0.5%, all the other are reduced iron powder.
Rare earth modified Steel Bond Hard Alloy of the present invention prepares by following step.At first prepare burden, wherein La
2O
3The powder footpath is preferably less than 45mm, and the reduced iron powder particle diameter can make powder better reach alloying in mechanical milling process preferably less than 75mm like this.
Ball milling mixes and can carry out according to a conventional method, the powder for preparing is put into ball grinder carry out ball milling.Preferably use stainless steel jar mill, take Stainless Steel Ball as grinding element, take alcohol as ball-milling medium, ratio of grinding media to material is 5:1.Ball-milling Time is preferably 18-20 hour so that powder better realize alloying and granularity tiny and even.
The powder that ball milling is good carries out spray-drying process according to a conventional method, makes pressed compact under certain pressure.Pressure is preferably 200-500MPa, and powder compact density is further improved.
After 1400-1430 ℃ of lower vacuum sintering and being incubated 1-3 hour, furnace cooling.Sintering temperature is vital.Sintering temperature is during lower than 1400 ℃, and sintered compact shrinks not, can't obtain the higher Steel Bond Hard Alloy of density; Burning easily occuring during higher than 1430 ℃, cause carbide grain too to grow up, affects the performance of Steel Bond Hard Alloy.
Vacuum sintering is preferably in low vacuum to be carried out under 0.5Pa, can greatly reduce and avoid the volatilization loss of metal.
In above-mentioned weight percentage ranges and under processing condition, the present invention has prepared following rare earth modified Steel Bond Hard Alloy, now illustrates with embodiment.
Embodiment 1
Prepare in the steps below rare earth modified Steel Bond Hard Alloy of the present invention:
(1) batching: with purity greater than 99.99%, particle diameter is less than the La of 45mm
2O
3Powder, purity greater than 98.5%, particle diameter is less than the reduced iron powder of 75mm, the TiC powder, the Mn powder, the Mo powder, Ni powder and Graphite Powder 99, by following weight percent batching: TiC 48%, and Mn 14%, and Mo 1.5%, and Ni 2.0%, and C 1.0%, La
2O
30.2%, surplus is Fe;
(2) ball milling mixes: take Stainless Steel Ball as grinding element, ratio of grinding media to material is 5:1, take alcohol as ball-milling medium, the powder for preparing is put into stainless steel jar mill carry out ball milling, and Ball-milling Time is 18 hours;
(3) compression moulding: the powder that ball milling is good carries out spray-drying process, makes pressed compact under 200MPa pressure;
(4) vacuum sintering: vacuum tightness is evacuated to lower than after 0.5Pa in the vacuum sintering furnace chamber, furnace cooling at 1400 ℃ of sintering and after being incubated 1 hour.
The rare earth modified Steel Bond Hard Alloy that obtains, the obvious refinement of its microstructure (as Fig. 1), crystal grain is tiny, and homogeneous microstructure, hardness value are HRC66.5, and density is 97.4%, and bending strength is 1700MPa.
Press the rare earth modified Steel Bond Hard Alloy of the method steps Preparation Example 2-5 of embodiment 1, its difference is ingredients by weight per-cent, Ball-milling Time, compression moulding pressure, sintering temperature and soaking time, list in table 1, the parameters such as the hardness value of the rare earth modified Steel Bond Hard Alloy of acquisition, density, bending strength see Table 1.
Table 1
| ? | Embodiment 2 | Embodiment 3 | Embodiment 4 | Embodiment 5 |
| TiC | 48% | 50% | 48% | 49% |
| Mn | 13% | 15% | 13% | 13% |
| Mo | 3.0% | 3.0% | 2.0% | 2.0% |
| Ni | 1.0% | 1.0% | 2.0% | 1.5% |
| C | 1.3% | 1.2 % | 1.3% | 1.3% |
| La 2O 3 | 0.5% | 0.4% | 0.5% | 0.4% |
| Fe | Surplus | Surplus | Surplus | Surplus |
| Ball-milling Time | 20 hours | 19 hours | 18 hours | 18 hours |
| Compression moulding pressure | 500MPa | 400MPa | 400MPa | 400MPa |
| Sintering temperature | 1430℃ | 1420℃ | 1420℃ | 1420℃ |
| Soaking time | 3 hours | 2 hours | 1 hour | 1 hour |
| Hardness value | HRC68.5 | HRC67.5 | HRC68.2 | HRC68 |
| Density | 98.5% | 98.2% | 98.8% | 98.2% |
| Bending strength | 1800MPa | 1760MPa | 1780MPa | 1740MPa |
Claims (8)
1. rare earth modified Steel Bond Hard Alloy is characterized in that being prepared from by by weight percentage following raw material: TiC powder 48-50%, Mn powder 13-15%, Mo powder 1.5-3.0%, Ni powder 1.0-2.0%, Graphite Powder 99 1.0-1.3%, La
2O
3Powder 0.2-0.5%, surplus is reduced iron powder.
2. rare earth modified Steel Bond Hard Alloy according to claim 1 is characterized in that being prepared from by by weight percentage following raw material: TiC powder 48-50%, Mn powder 13-15%, Mo powder 2.0-3.0%, Ni powder 1.0-2.0%, Graphite Powder 99 1.2-1.3%, La
2O
3Powder 0.4-0.5%, surplus is reduced iron powder.
3. the preparation method of claim 1 or 2 described rare earth modified Steel Bond Hard Alloy is characterized in that comprising the following steps:
(1) batching is by described component and weight percent batching;
(2) ball milling mixes, and the powder for preparing is put into ball grinder carry out ball milling;
(3) compression moulding, the powder that ball milling is good carries out spray-drying process, makes pressed compact under certain pressure;
(4) vacuum sintering, after 1400-1430 ℃ of lower vacuum sintering and being incubated 1-3 hour, furnace cooling.
4. the preparation method of rare earth modified Steel Bond Hard Alloy claimed in claim 3, is characterized in that the described La of step (1)
2O
3The powder footpath is less than 45mm, and the reduced iron powder particle diameter is less than 75mm.
5. the preparation method of rare earth modified Steel Bond Hard Alloy claimed in claim 3, is characterized in that the described ball grinder of step (2) is stainless cylinder of steel, and take Stainless Steel Ball as grinding element, take alcohol as ball-milling medium, ratio of grinding media to material is 5:1.
6. the preparation method of rare earth modified Steel Bond Hard Alloy claimed in claim 3, is characterized in that the described Ball-milling Time of step (2) is 18-20 hour.
7. the preparation method of rare earth modified Steel Bond Hard Alloy claimed in claim 3, is characterized in that the described compression moulding pressure of step (3) is 200-500MPa.
8. the preparation method of rare earth modified Steel Bond Hard Alloy claimed in claim 3 is characterized in that the described vacuum sintering of step (4) carries out under 0.5Pa at low vacuum.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103627943A (en) * | 2013-12-09 | 2014-03-12 | 株洲硬质合金集团有限公司 | TiC series steel bond hard alloy |
| CN104195408A (en) * | 2014-09-23 | 2014-12-10 | 江苏汇诚机械制造有限公司 | Preparation method of ultrahigh-manganese steel based TiC steel bond hard alloy |
| CN104232965A (en) * | 2014-09-23 | 2014-12-24 | 江苏汇诚机械制造有限公司 | Preparation method of TiC high-speed steel-based steel-bonded hard alloy |
| CN104232966A (en) * | 2014-09-23 | 2014-12-24 | 江苏汇诚机械制造有限公司 | Preparation method of TiC high-wear-resistant steel-bonded hard alloy |
| CN104294073A (en) * | 2014-09-23 | 2015-01-21 | 江苏汇诚机械制造有限公司 | Preparation method of modified high-manganese steel base TiC steel bonded carbide |
| CN105331841A (en) * | 2014-08-16 | 2016-02-17 | 江苏汇诚机械制造有限公司 | Preparation method of titanium carbide steel-bonded alloy |
| CN105420587A (en) * | 2014-08-23 | 2016-03-23 | 江苏汇诚机械制造有限公司 | Preparation method for TiC high-boron low alloy high-speed steel-based steel bonded cemented alloy |
| CN105441775A (en) * | 2014-08-23 | 2016-03-30 | 江苏汇诚机械制造有限公司 | Preparation method of (TiV)C steel bond hard alloy |
| CN108588539A (en) * | 2018-01-11 | 2018-09-28 | 芜湖市金贸流体科技股份有限公司 | A kind of corrosion resisting stainless steel precise forming technique |
| CN112301295A (en) * | 2020-10-28 | 2021-02-02 | 常熟市电力耐磨合金铸造有限公司 | Steel bonded hard alloy and preparation method and application thereof |
| CN116445823A (en) * | 2023-03-16 | 2023-07-18 | 常熟市电力耐磨合金铸造有限公司 | TiC-based high manganese steel bonded hard alloy with high hardness and high toughness and preparation method thereof |
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Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103627943A (en) * | 2013-12-09 | 2014-03-12 | 株洲硬质合金集团有限公司 | TiC series steel bond hard alloy |
| CN105331841A (en) * | 2014-08-16 | 2016-02-17 | 江苏汇诚机械制造有限公司 | Preparation method of titanium carbide steel-bonded alloy |
| CN105420587A (en) * | 2014-08-23 | 2016-03-23 | 江苏汇诚机械制造有限公司 | Preparation method for TiC high-boron low alloy high-speed steel-based steel bonded cemented alloy |
| CN105441775A (en) * | 2014-08-23 | 2016-03-30 | 江苏汇诚机械制造有限公司 | Preparation method of (TiV)C steel bond hard alloy |
| CN105420587B (en) * | 2014-08-23 | 2017-12-22 | 江苏汇诚机械制造有限公司 | A kind of preparation method of TiC high-boron low-alloy high-speed steels base steel bonded carbide |
| CN104195408A (en) * | 2014-09-23 | 2014-12-10 | 江苏汇诚机械制造有限公司 | Preparation method of ultrahigh-manganese steel based TiC steel bond hard alloy |
| CN104232965A (en) * | 2014-09-23 | 2014-12-24 | 江苏汇诚机械制造有限公司 | Preparation method of TiC high-speed steel-based steel-bonded hard alloy |
| CN104232966A (en) * | 2014-09-23 | 2014-12-24 | 江苏汇诚机械制造有限公司 | Preparation method of TiC high-wear-resistant steel-bonded hard alloy |
| CN104294073A (en) * | 2014-09-23 | 2015-01-21 | 江苏汇诚机械制造有限公司 | Preparation method of modified high-manganese steel base TiC steel bonded carbide |
| CN108588539A (en) * | 2018-01-11 | 2018-09-28 | 芜湖市金贸流体科技股份有限公司 | A kind of corrosion resisting stainless steel precise forming technique |
| CN112301295A (en) * | 2020-10-28 | 2021-02-02 | 常熟市电力耐磨合金铸造有限公司 | Steel bonded hard alloy and preparation method and application thereof |
| CN116445823A (en) * | 2023-03-16 | 2023-07-18 | 常熟市电力耐磨合金铸造有限公司 | TiC-based high manganese steel bonded hard alloy with high hardness and high toughness and preparation method thereof |
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Application publication date: 20130522 |