CN109594032A - A method of improving alloy coat impact resistance - Google Patents
A method of improving alloy coat impact resistance Download PDFInfo
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- CN109594032A CN109594032A CN201811352269.0A CN201811352269A CN109594032A CN 109594032 A CN109594032 A CN 109594032A CN 201811352269 A CN201811352269 A CN 201811352269A CN 109594032 A CN109594032 A CN 109594032A
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- coating
- impact resistance
- interface
- alloy coat
- maximum shear
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/12—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the method of spraying
- C23C4/129—Flame spraying
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
- C23C4/067—Metallic material containing free particles of non-metal elements, e.g. carbon, silicon, boron, phosphorus or arsenic
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Application Of Or Painting With Fluid Materials (AREA)
Abstract
The invention discloses a kind of methods for improving alloy coat impact resistance, belong to amorphous alloy coating technical field.This method is to carry out coating impact test to alloy coat, under shock loading, make the concentrated position of the maximum shear stress far from coating and basal body interface by adjusting coating layer thickness, so that the probability that Interface Cracking occurs for coating be mitigated or eliminated, improves alloy coat impact resistance.Define coating impact resistance and coating layer thickness relational expression be Δ=| z/tc- 1 |, when the value of Δ is closer to 0, closer to the interface of coating and substrate, interface is easier to crack the concentrated position of maximum shear stress；When the value of Δ is far from 0, Interface Cracking can be mitigated or eliminated.The present invention provides important scientific basis for design impact resistance coating.
Description
Technical field
The present invention relates to amorphous alloy coating technical fields, and in particular to a kind of side for improving alloy coat impact resistance
Method.
Background technique
Alloy coat be usually be to increase wearability, intensity or hardness etc. of matrix and prepare, coating as structural material,
Impact property be evaluate its in loading process safety, reliability and validity important indicator.The impact of coating, which is cracked, goes
For the difficult point for being always research, about analyzing the damage mechanisms of its cracking to the alloy coat that has excellent performance of preparation usage to Guan Chong
It wants.However, in the past few decades, the impact behavior for studying coating is very limited.
Amorphous alloy coating has wear-and corrosion-resistant and neutron absorption capability, these unique characteristics make amorphous alloy coating exist
The industries such as aerospace, petrochemical industry, atomic energy are applied widely.But amorphous alloy coating has very poor impact resistance
Can, the interface for being specifically reflected in coating and substrate produces serious cracking.
In impact process, shear stress can be generated below contact surface.For shallow layer, the shearing force of generation is contacted
Mainly undertaken by substrate.In contrast, for thick coating, shear stress is largely focused on coating rather than substrate.And
Other coatings have also discovered the similar phenomenon with thickness correlation: Interface Cracking is not observed in 300 μm of coatings, and in 500 μ
M coating just observes very serious cracking.These are the result shows that the degree of cracking is sensitive to coating layer thickness.Therefore, in order to design
The excellent crystalline state of impact property or amorphous alloy coating out, should further investigate the relevance of coating layer thickness and impact injury, to
Seek to design high-impact can alloy coat.
Summary of the invention
It cracks to solve the impact of coating under shock environment, improves the impact flexibility of coating, it is an object of the invention to
A kind of method for improving alloy coat impact resistance is provided, this method can be used for preparing the painting of the high impact resistance under shock environment
Layer.
The technical solution adopted in the present invention is as follows:
A method of alloy coat impact resistance is improved, this method is to carry out coating impact test to alloy coat,
Under shock loading, make the concentrated position of the maximum shear stress far from coating and basal body interface by adjusting coating layer thickness, thus
The probability that Interface Cracking occurs for coating is mitigated or eliminated, improves alloy coat impact resistance.
In this method, the relational expression for defining coating impact resistance and coating layer thickness is formula (1), is sentenced according to formula (1)
Determine the impact resistance of coating.
Δ=| z/tc-1| (1)；
In formula (1): Δ indicates coating impact resistance degree of cracking；Z is the corresponding depth of the maximum shear stress, and unit is μm；
tcFor coating layer thickness, unit is μm.
In formula (1), when the value of Δ is closer to 0, the concentrated position of maximum shear stress is closer to coating and substrate
Interface, interface is easier to crack；When the value of Δ is far from 0, Interface Cracking can be mitigated or eliminated；The value of Δ is bigger, alloy
The impact resistance of coating is better.
The method of the present invention is applicable not only to improve the impact resistance of crystalline coatings, is also applied for improving amorphous coating layer
Impact resistance.
Design Mechanism of the present invention is as follows:
The method of the present invention is to make the maximum shear stress concentrated position far from boundary by adjusting coating layer thickness under shock loading
Face, so that the probability that Interface Cracking occurs for coating be mitigated or eliminated.
In impact process, the maximum shear stress can be generated below contact surface, the concentrated position of the maximum shear stress from
The interface of coating and substrate is closer, then the more easy rapid generation cracking of coating.Thus defined formula Δ=| z/tc- 1 | to indicate
The relationship of coating shock resistance cracking performance and coating layer thickness, when Δ level off to 0 when, i.e., maximum shear stress acts on coating/substrate
Interface, interface is then cracked rapidly.When Δ is far from 0, Interface Cracking can be mitigated or eliminated.
The material of impact specimen in the method for the present invention is the coating of different-thickness.
The present invention has the beneficial effect that:
1, make shear stress concentrated position far from interface by adjusting coating layer thickness, so that amorphous alloy painting be mitigated or eliminated
The probability of Interface Cracking occurs for layer.
2, the design method is easy to implement, easy to operate, and high impact-resistant performance requirement can be met in shock environment.
Detailed description of the invention
Fig. 1 is the FeCrMnMoWBCSi amorphous alloy coating XRD spectrum of different-thickness.
Fig. 2 is the maximum shear stress τ of Fe base amorphous alloy coating under shock loadingmaxWith the contour of position (r/a, z/a)
Line profile figure, the peak value τ of maximum shear stresscritAt the z ≈ 0.5a of underface.
Fig. 3 be formula Δ=| z/tc- 1 | and tcRelational graph.
Fig. 4 is the Fe base amorphous alloy coating of different-thickness in impact energy 21.6J lower section SEM photograph.
Fig. 5 is the addition Al of different-thickness2O3The stainless steel coating of particle is in impact energy 21.6J lower section SEM photograph.
Fig. 6 is the stainless steel coating of the addition SiC particulate of different-thickness in impact energy 21.6J lower section SEM photograph.
Specific embodiment
The present invention is described in detail with reference to the accompanying drawings and embodiments.
The present invention defines the relational expression (1) of coating impact resistance and coating layer thickness, determines the resistance to of coating according to formula (1)
Impact property.
Δ=| z/tc-1| (1)；
In formula (1): Δ indicates coating impact resistance degree of cracking；Z is the corresponding depth of the maximum shear stress, and unit is μm；
tcFor coating layer thickness, unit is μm.
In following example 1-7, coated substrate is carbon steel, and iron is prepared on matrix using supersonic flame spraying technology
Base amorphous alloy coating (Fe49.7Cr18Mn1.9Mo7.4W1.6B15.2C3.8Si2.4(with atomic percentage)).Supersonic flame spraying
Al is added in the amorphous powdered alloy used2O3Particle, additive amount are the 15% of amorphous powdered alloy weight.Coating layer thickness is respectively
200 μm, 300 μm, 400 μm, 500 μm, 600 μm, 700 μm and 800 μm.
Make to improve the impact resistance of alloy coat by adjusting coating layer thickness (as shown in Figure 1) under shock loading
The maximum shear stress concentrated position (as shown in Figure 2) is far from coating and basal body interface, so that coating, which is mitigated or eliminated, occurs interface
The probability of cracking.
As shown in figure 3, when Δ value level off to 0 when, i.e., maximum shear stress acts on coating/substrate interface, and interface is then rapid
It cracks.When Δ is far from 0, Interface Cracking can mitigate, and even be eliminated.
Embodiment 1:
Choose with a thickness of 600 μm of coating, calculate Δ=| z/tc- 1 |=0.07, value is close to 0, i.e. maximum shear
Close to interface, Fig. 4 (e) fully confirms 600 μm of coatings and serious cracking has occurred stress.
Embodiment 2:
Choose with a thickness of 700 μm of coating, calculate Δ=| z/tc- 1 |=0.24, it is greater than embodiment 1, i.e. maximum shear
Far from interface, Fig. 4 (f) fully confirms 700 μm of coating interface crackings and is mitigated stress.
Embodiment 3:
Choose with a thickness of 800 μm of coating, calculate Δ=| z/tc- 1 |=0.35, it is greater than embodiment 1, i.e. maximum shear
Far from interface, Fig. 4 (g) fully confirms 800 μm of coating interface crackings and further mitigates stress.
Embodiment 4:
Choose with a thickness of 500 μm of coating, calculate Δ=| z/tc- 1 |=0.20, it is greater than embodiment 1, i.e. maximum shear
Far from interface, Fig. 4 (d) fully confirms 500 μm of coating interface crackings and is mitigated stress.
Embodiment 5:
Choose with a thickness of 400m coating, calculate Δ=| z/tc- 1 |=0.53, it is greater than embodiment 1, i.e. maximum shear
Far from interface, Fig. 4 (c) fully confirms 400m coating interface cracking and completely eliminates stress.
Embodiment 6:
Choose with a thickness of 300 μm of coating, calculate Δ=| z/tc- 1 |=1.03, it is greater than embodiment 1, i.e. maximum shear
Far from interface, Fig. 4 (b) fully confirms 300 μm of coating interface crackings and completely eliminates stress.
Embodiment 7:
Choose with a thickness of 200 μm of coating, calculate Δ=| z/tc- 1 |=2.05, it is greater than embodiment 1, i.e. maximum shear
Far from interface, Fig. 4 (a) fully confirms 200 μm of coating interface crackings and completely eliminates stress.
It can be seen from the experiment effect data of above embodiments 1-7 when the value of Δ is closer to 0, the easier hair in interface
Raw cracking；When the value of Δ is far from 0, Interface Cracking can be mitigated or eliminated；The value of Δ is bigger, and the impact resistance of alloy coat is got over
It is good.
Embodiment 8:
In the present embodiment, substrate is ordinary carbon steel, and thermal spraying is prepared for that Al is added2O3The stainless steel coating of particle, in which:
Sprayed on material used is that Al is added in powder of stainless steel2O3Particle, the chemical component of powder of stainless steel are Fe44.6Cr28Mn0.8
Mo2.5C7.6Si2.4Ni14.1(with atomic percentage), Al2O3Particle additive amount is the 15% of powder of stainless steel weight.It calculates
The Δ value of 500 μm of coatings is closest to 0, i.e., the maximum shear stress is close to interface, and crack most serious.When Δ is far from 0, cracking subtracts
It is slow even to be eliminated.Fig. 5 (d) fully confirms 500 μm of coating interface cracking most serious.Fig. 5 (c), Fig. 5 (e), Fig. 5 (f) and Fig. 5
(g) when confirming Δ respectively far from 0,400 μm, 600 μm, 700 μm and 800 μm coating crackings are mitigated.Fig. 5 (a) and Fig. 5
(b) when confirming Δ farther away from 0 respectively, 200 μm and 300 μm of coating crackings are completely eliminated.
Embodiment 9:
In the present embodiment, substrate is ordinary carbon steel, and the FeCrMnMoCSiNi of the addition SiC particulate of thermal spraying preparation is stainless
Steel coating calculates the Δ of 500 μm of coatings closest to 0, i.e., the maximum shear stress is close to interface, and crack most serious.Δ is separate
0, cracking, which slows down, even to be eliminated.Fig. 6 (c) fully confirms 500 μm of coating interface cracking most serious.Fig. 6 (a) and Fig. 6 (b) is respectively
When confirming Δ far from 0,200 μm and 300 μm of coating crackings are completely eliminated.
Claims (4)
1. a kind of method for improving alloy coat impact resistance, it is characterised in that: this method is to carry out coating to alloy coat
Impact test makes the concentrated position of the maximum shear stress far from coating and matrix under shock loading by adjusting coating layer thickness
Alloy coat impact resistance is improved so that the probability that Interface Cracking occurs for coating be mitigated or eliminated in interface.
2. the method according to claim 1 for improving alloy coat impact resistance, it is characterised in that: fixed in this method
The relational expression of adopted coating impact resistance and coating layer thickness is formula (1), and the impact resistance of coating is determined according to formula (1).
Δ=| z/tc-1| (1)；
In formula (1): Δ indicates coating impact resistance degree of cracking；Z is the corresponding depth of the maximum shear stress, and unit is μm；tcTo apply
Thickness degree, unit are μm.
3. the method according to claim 2 for improving alloy coat impact resistance, it is characterised in that: in formula (1), when
When the value of Δ is closer to 0, closer to the interface of coating and substrate, interface is easier to open the concentrated position of maximum shear stress
It splits；When the value of Δ is far from 0, Interface Cracking can be mitigated or eliminated；The value of Δ is bigger, and the impact resistance of alloy coat is better.
4. the method according to claim 2 for improving alloy coat impact resistance, it is characterised in that: this method is suitable for
Improve the impact resistance of crystalline state or amorphous coating layer.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112359311A (en) * | 2020-09-23 | 2021-02-12 | 中国科学院金属研究所 | Method for reducing longitudinal cracks of thermal spraying super stainless steel coating |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001056934A (en) * | 1999-08-18 | 2001-02-27 | Sony Corp | Production of magnetic recording medium |
| CN1616706A (en) * | 2004-09-03 | 2005-05-18 | 吉林大学 | Surface or local gradient reinforced wear resistant manganese steel composite material and preparing process |
| CN101859337A (en) * | 2010-06-04 | 2010-10-13 | 中国地质大学（北京） | Method for evaluating cracking of brazing diamond abrasive grain alloy layer |
| CN107794484A (en) * | 2016-08-29 | 2018-03-13 | 中国科学院金属研究所 | A kind of anti-skidding amorphous alloy coating of wear-and corrosion-resistant and preparation method thereof |
| CN108699664A (en) * | 2016-02-25 | 2018-10-23 | 新日铁住金株式会社 | The high-strength hot-dip galvanized steel sheet of impact resistance fissility and processing department excellent corrosion resistance |
-
2018
- 2018-11-14 CN CN201811352269.0A patent/CN109594032A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001056934A (en) * | 1999-08-18 | 2001-02-27 | Sony Corp | Production of magnetic recording medium |
| CN1616706A (en) * | 2004-09-03 | 2005-05-18 | 吉林大学 | Surface or local gradient reinforced wear resistant manganese steel composite material and preparing process |
| CN101859337A (en) * | 2010-06-04 | 2010-10-13 | 中国地质大学（北京） | Method for evaluating cracking of brazing diamond abrasive grain alloy layer |
| CN108699664A (en) * | 2016-02-25 | 2018-10-23 | 新日铁住金株式会社 | The high-strength hot-dip galvanized steel sheet of impact resistance fissility and processing department excellent corrosion resistance |
| CN107794484A (en) * | 2016-08-29 | 2018-03-13 | 中国科学院金属研究所 | A kind of anti-skidding amorphous alloy coating of wear-and corrosion-resistant and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| DAVID W. WHEELER: "Observations and Characterization of Damage in Diamond Coatings Due to Impact Loading", 《JOURNAL OF THE AMERICAN CERAMIC SOCIETY》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112359311A (en) * | 2020-09-23 | 2021-02-12 | 中国科学院金属研究所 | Method for reducing longitudinal cracks of thermal spraying super stainless steel coating |
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Application publication date: 20190409 |