JPWO2019188120A1 - Shot used for blasting - Google Patents
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- JPWO2019188120A1 JPWO2019188120A1 JP2020509793A JP2020509793A JPWO2019188120A1 JP WO2019188120 A1 JPWO2019188120 A1 JP WO2019188120A1 JP 2020509793 A JP2020509793 A JP 2020509793A JP 2020509793 A JP2020509793 A JP 2020509793A JP WO2019188120 A1 JPWO2019188120 A1 JP WO2019188120A1
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- 238000005422 blasting Methods 0.000 title claims abstract description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 50
- 229910052742 iron Inorganic materials 0.000 claims abstract description 24
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 23
- 239000000956 alloy Substances 0.000 claims abstract description 23
- 239000002245 particle Substances 0.000 claims description 50
- 239000000654 additive Substances 0.000 claims description 10
- 230000000996 additive effect Effects 0.000 claims description 10
- 229910052802 copper Inorganic materials 0.000 claims description 8
- 229910052759 nickel Inorganic materials 0.000 claims description 8
- 229910000734 martensite Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910052796 boron Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 230000000694 effects Effects 0.000 description 31
- 235000019589 hardness Nutrition 0.000 description 22
- 238000000034 method Methods 0.000 description 13
- 230000000171 quenching effect Effects 0.000 description 13
- 239000002184 metal Substances 0.000 description 12
- 229910052751 metal Inorganic materials 0.000 description 12
- 238000010791 quenching Methods 0.000 description 12
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 10
- 229910052760 oxygen Inorganic materials 0.000 description 10
- 239000001301 oxygen Substances 0.000 description 10
- 239000002994 raw material Substances 0.000 description 10
- 230000007423 decrease Effects 0.000 description 8
- 229910052748 manganese Inorganic materials 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 229910052710 silicon Inorganic materials 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 5
- 238000004140 cleaning Methods 0.000 description 4
- 238000001816 cooling Methods 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000005469 granulation Methods 0.000 description 4
- 230000003179 granulation Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910001562 pearlite Inorganic materials 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 238000009692 water atomization Methods 0.000 description 3
- 238000005266 casting Methods 0.000 description 2
- 239000011361 granulated particle Substances 0.000 description 2
- 230000005484 gravity Effects 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000011347 resin Substances 0.000 description 2
- 229920005989 resin Polymers 0.000 description 2
- 238000012795 verification Methods 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000001739 density measurement Methods 0.000 description 1
- 239000012153 distilled water Substances 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 239000012768 molten material Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 238000007873 sieving Methods 0.000 description 1
- 239000012798 spherical particle Substances 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 235000019587 texture Nutrition 0.000 description 1
Images
Classifications
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- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/06—Metallic powder characterised by the shape of the particles
- B22F1/065—Spherical particles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B24—GRINDING; POLISHING
- B24C—ABRASIVE OR RELATED BLASTING WITH PARTICULATE MATERIAL
- B24C11/00—Selection of abrasive materials or additives for abrasive blasts
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
- C22C33/0271—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5% with only C, Mn, Si, P, S, As as alloying elements, e.g. carbon steel
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
- B22F2009/0828—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid with water
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2200/00—Crystalline structure
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Nanotechnology (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Abstract
本開示は、ブラスト加工に用いられるショットであって、添加元素としてC:0.20〜0.50質量%、Si:0.50〜1.10質量%、及びMn:0.50〜1.15質量%を含む鉄基合金からなり、Siに対するCの質量比が0.30〜0.75、Mnに対するCの質量比が0.30〜0.75、及びMnに対するSiの質量比が0.70〜1.60であり、ビッカース硬さがHV400〜800である、ショットに関する。The present disclosure is a shot used for blasting, in which C: 0.20 to 0.50% by mass, Si: 0.50 to 1.10% by mass, and Mn: 0.50 to 1. It is composed of an iron-based alloy containing 15% by mass, and the mass ratio of C to Si is 0.30 to 0.75, the mass ratio of C to Mn is 0.30 to 0.75, and the mass ratio of Si to Mn is 0. For shots of .70 to 1.60 and Vickers hardness of HV400 to 800.
Description
本開示は、ブラスト加工に用いられるショットに関する。 The present disclosure relates to shots used for blasting.
鋳造後の鋳造物の砂落とし、金属製品のバリ取り、錆等のスケールの除去、などに、ショットブラストは用いられている。ショットブラストはショットと呼ばれる粒子を被加工物に向けて投射する加工方法である。ショットとしては、鉄系の粒子を用いることが多い。 Shot blasting is used for removing sand from castings after casting, deburring metal products, and removing scales such as rust. Shot blasting is a processing method in which particles called shots are projected toward a work piece. Iron-based particles are often used as shots.
特許文献1には、添加元素としてC:0.80〜1.10質量%、Si:0.50〜1.00質量%、Mn:0.50〜1.00質量%、Cr:0.10〜0.30質量%を含み、残部がFe(不可避不純物を含む)であるショットが開示されている。ショットは、ショットブラストに適さないサイズに損耗されるまで繰り返し使用されるため、より損耗の少ない(寿命が長い)ショットの登場が望まれている。 Patent Document 1 describes as additive elements C: 0.80 to 1.10% by mass, Si: 0.50 to 1.00% by mass, Mn: 0.50 to 1.00% by mass, Cr: 0.10. Shots containing ~ 0.30% by weight and the balance being Fe (containing unavoidable impurities) are disclosed. Since shots are used repeatedly until they are worn to a size that is not suitable for shot blasting, it is desired that shots with less wear (longer life) be introduced.
また、ショットの硬さは、ワークの物性やショットブラストの目的に合わせて選択されている。多様な硬さを持つショットを製造する製造方法の確立が望まれている。 The hardness of the shot is selected according to the physical characteristics of the work and the purpose of shot blasting. It is desired to establish a manufacturing method for manufacturing shots having various hardnesses.
本開示は上記事情に鑑みてなされたものであり、研掃効率が損なわれ難いため寿命が長く、かつ多様な硬さを有するショットを提供することを目的とする。 The present disclosure has been made in view of the above circumstances, and an object of the present invention is to provide a shot having a long life and various hardness because the cleaning efficiency is not easily impaired.
本開示の一形態に係るショットは、ブラスト加工に用いられるショットである。当該ショットは、添加元素としてC:0.20〜0.50質量%、Si:0.50〜1.10質量%、及びMn:0.50〜1.15質量%を含む鉄基合金からなる。また、当該ショットにおいて、Siに対するCの質量比(C/Si)は0.30〜0.75、Mnに対するCの質量比(C/Mn)が0.30〜0.75、Mnに対するSiの質量比(Si/Mn)が0.70〜1.60、である。そして、当該ショットのビッカース硬さはHV400〜800(JIS Z 2244:2009にて規定)である。 The shot according to one form of the present disclosure is a shot used for blasting. The shot is composed of an iron-based alloy containing C: 0.25 to 0.50% by mass, Si: 0.50 to 1.10% by mass, and Mn: 0.50 to 1.15% by mass as additive elements. .. Further, in the shot, the mass ratio of C to Si (C / Si) was 0.30 to 0.75, the mass ratio of C to Mn (C / Mn) was 0.30 to 0.75, and the mass ratio of Si to Mn was 0.30 to 0.75. The mass ratio (Si / Mn) is 0.70 to 1.60. The Vickers hardness of the shot is HV400 to 800 (specified in JIS Z 2244: 2009).
一実施形態において、CとSiとMnの合計含有量(C+Si+Mn)は1.80〜2.40質量%であってもよい。 In one embodiment, the total content of C, Si and Mn (C + Si + Mn) may be 1.80 to 2.40% by mass.
一実施形態において、鉄基合金は、さらにCr、Ni、Cu、Mo、Al、B、V、Nb及びTiからなる群より選択される少なくとも1種の元素を0.30〜1.0質量%含んでいてもよい。 In one embodiment, the iron-based alloy further comprises 0.30 to 1.0% by mass of at least one element selected from the group consisting of Cr, Ni, Cu, Mo, Al, B, V, Nb and Ti. It may be included.
一実施形態において、ショットは実質的に焼戻マルテンサイト相から形成されていてもよい。 In one embodiment, the shot may be substantially formed from the tempered martensite phase.
一実施形態において、ブローホールを有する粒子の数はショット全体の5%以下であってもよい。 In one embodiment, the number of particles with blow holes may be 5% or less of the total shot.
一実施形態において、粒子の長手方向の長さをL、長手方向に直行する方向における最大径をSとした場合に、L/Sが2.0以上となる粒子の数は、ショット全体の5%以下であってもよい。 In one embodiment, when the length of the particles in the longitudinal direction is L and the maximum diameter in the direction orthogonal to the longitudinal direction is S, the number of particles having an L / S of 2.0 or more is 5 for the entire shot. It may be less than or equal to%.
本開示の一形態により、研掃効率が損なわれ難いため寿命が長く、かつ多様な硬さを有するショットが提供される。 According to one embodiment of the present disclosure, a shot having a long life and various hardness is provided because the cleaning efficiency is not easily impaired.
本開示の一形態に係るショットは、添加元素としてC、Si及びMnを含む4成分系の鉄基合金からなるショットである。あるいは、本開示の一形態に係るショットは、鉄基合金からなる粒子を含み、当該鉄基合金が添加元素としてC、Si及びMnを含む、ショットである、ということもできる。当該ショット(鉄基合金)には、その他の不可避不純物が含まれていてもよい。 The shot according to one embodiment of the present disclosure is a shot made of a four-component iron-based alloy containing C, Si and Mn as additive elements. Alternatively, it can be said that the shot according to one embodiment of the present disclosure is a shot containing particles made of an iron-based alloy, and the iron-based alloy contains C, Si, and Mn as additive elements. The shot (iron-based alloy) may contain other unavoidable impurities.
以下に、水アトマイズ法にてショットを製造する場合を例に、一実施形態のショットについて詳しく説明する。なお、以下の説明における%は特に断りのない限り、質量%を示す。 Hereinafter, the shot of one embodiment will be described in detail by taking the case of producing a shot by the water atomizing method as an example. Unless otherwise specified,% in the following description indicates mass%.
<溶融工程>
所定の組成となるように秤量したショットの原料(Fe、C、Si、Mn等)を溶解炉に投入し、1600〜1750℃に加熱して溶解して溶湯とする。<Melting process>
Raw materials for shots (Fe, C, Si, Mn, etc.) weighed so as to have a predetermined composition are put into a melting furnace and heated to 1600 to 1750 ° C. to melt them into a molten metal.
Feはショットの基となる元素である。 Fe is the element that is the basis of the shot.
Cは、硬さに影響を及ぼす元素である。C濃度が高くなるとショットが硬くなるため研掃能力が高くなるが、Cの濃度に比例して靱性が低下する。靱性の低下は寿命の低下に繋がる。ショットとして求められる硬さと寿命を考慮し、鉄基合金中のCの含有量は0.20〜0.50質量%であるが、0.30〜0.45質量%であってもよく、0.35〜0.45質量%であってもよい。 C is an element that affects hardness. As the C concentration increases, the shot becomes harder and the cleaning ability increases, but the toughness decreases in proportion to the C concentration. A decrease in toughness leads to a decrease in life. Considering the hardness and life required as a shot, the content of C in the iron-based alloy is 0.25 to 0.50% by mass, but it may be 0.30 to 0.45% by mass, and is 0. It may be 35 to 0.45% by mass.
Siには原料溶湯中の酸素を除去する効果がある。原料溶湯中に含まれる酸素は、アトマイズ法による造粒時に、粒子の球状化を阻害する。Si濃度が高いと脱酸効果が高くなるため球状の粒子を得やすくなるが、Siの濃度に比例して靱性が低下する。また、原料溶湯中の酸素を除去することで、ブローホールと呼ばれる内部欠陥を減少させることができる。Cにも脱酸効果はあるが、寿命を考慮すると、脱酸効果を十分に得られる量のCを添加することは困難である。脱酸効果と寿命を考慮し、鉄基合金中のSiの含有量は0.50〜1.10質量%であるが、0.55〜1.05質量%であってもよく、0.60〜1.00質量%であってもよい。 Si has the effect of removing oxygen in the molten metal of the raw material. Oxygen contained in the molten metal inhibits the spheroidization of particles during granulation by the atomizing method. When the Si concentration is high, the deoxidizing effect is high, so that spherical particles can be easily obtained, but the toughness decreases in proportion to the Si concentration. Further, by removing oxygen in the molten metal, it is possible to reduce internal defects called blow holes. C also has a deoxidizing effect, but considering the life, it is difficult to add an amount of C that can sufficiently obtain the deoxidizing effect. Considering the deoxidizing effect and the life, the content of Si in the iron-based alloy is 0.50 to 1.10% by mass, but it may be 0.55 to 1.05% by mass, and 0.60. It may be ~ 1.00% by mass.
Mnには造粒した粒子の焼き入れ性を向上させる効果と、TTT線図におけるパーライトノーズを右側にシフトさせて臨界冷却速度を下げる効果とがある。焼き入れを行うことで、ショットとして求められる硬さを得ることができる。焼き入れによって粒子の組織が変態するが、この際に均質かつ微細な結晶粒を有する組織にすることが求められる。このような組織が得られるよう焼き入れ条件を調整するが、ショットのような細かい粒子の場合は、繊細な焼き入れ条件の調整が必要とされている。合金中にMnを添加することで、焼き入れ条件の許容値が広がり、条件の調整がし易くなる。これにより、造粒した粒子の全体に亘って、均質かつ微細(例えば、2〜10μm)な結晶粒を有する組織を導入し易くなる。その結果、靱性に優れた粒子となるため、ショットの寿命が向上する。しかし、Mnは高価な金属の為、濃度を高くするとショットの製造コストの増大に繋がる。焼き入れ効果とコストを考慮し、鉄基合金中のMnの含有量は0.50〜1.15質量%であるが、0.55〜1.00質量%であってもよく、0.60〜0.95質量%であってもよい。 Mn has the effect of improving the quenchability of the granulated particles and the effect of shifting the pearlite nose in the TTT diagram to the right to lower the critical cooling rate. By quenching, the hardness required for a shot can be obtained. The structure of the particles is transformed by quenching, and at this time, it is required to have a structure having homogeneous and fine crystal grains. The quenching conditions are adjusted so that such a structure can be obtained, but in the case of fine particles such as shots, it is necessary to adjust the quenching conditions delicately. By adding Mn to the alloy, the allowable value of quenching conditions is widened, and the conditions can be easily adjusted. This facilitates the introduction of a structure having homogeneous and fine (for example, 2 to 10 μm) crystal grains throughout the granulated particles. As a result, the particles have excellent toughness, so that the life of the shot is improved. However, since Mn is an expensive metal, increasing the concentration leads to an increase in the production cost of shots. Considering the quenching effect and cost, the content of Mn in the iron-based alloy is 0.50 to 1.15% by mass, but may be 0.55 to 1.00% by mass, 0.60. It may be ~ 0.95% by mass.
さらに、鉄基合金中のCの含有量をa質量%、Siの含有量をb質量%、Mnの含有量をc質量%とした時に、添加元素であるC、Si及びMnのそれぞれの相乗効果を考慮すると、各質量比等は以下のとおりである。
a/b(Siに対するCの質量比)は0.30〜0.75であるが、0.35〜0.60であってもよく、0.40〜0.50であってもよい。
a/c(Mnに対するCの質量比)は0.30〜0.75であるが、0.35〜0.60であってもよく、0.40〜0.50であってもよい。
b/c(Mnに対するSiの質量比)は0.70〜1.60であるが、0.80〜1.40であってもよく、0.90〜1.20であってもよい。
a+b+c(CとSiとMnの合計含有量)は1.80〜2.40質量%であることが好ましいが、1.85〜2.25質量%であってもよく、1.90〜2.10質量%であってもよい。Further, when the content of C in the iron-based alloy is a mass%, the content of Si is b mass%, and the content of Mn is c mass%, the synergies of the additive elements C, Si, and Mn are obtained. Considering the effect, each mass ratio and the like are as follows.
Although a / b (mass ratio of C to Si) is 0.30 to 0.75, it may be 0.35 to 0.60 or 0.40 to 0.50.
Although a / c (mass ratio of C to Mn) is 0.30 to 0.75, it may be 0.35 to 0.60 or 0.40 to 0.50.
The b / c (mass ratio of Si to Mn) is 0.70 to 1.60, but may be 0.80 to 1.40 or 0.99 to 1.20.
The a + b + c (total content of C, Si, and Mn) is preferably 1.80 to 2.40% by mass, but may be 1.85 to 2.25% by mass, and 1.90 to 2.25% by mass. It may be 10% by mass.
前記鉄基合金は、さらにCr、Ni、Cu、Mo、Al、B、V、Nb及びTiからなる群より選択される少なくとも1種の元素を含んでいてもよい。これら他の添加元素はSi及びMnの効果を補完する目的で添加され、添加によって以下に示す効果が得られる。ただし、これら他の添加元素濃度が高すぎると、硬さの低下、寿命の低下、球状化の不足、などの不具合が発生する傾向がある。そのため、鉄基合金中のこれら他の添加元素の含有量(複数の元素を添加した場合はその合計含有量)を0.30〜1.0質量%となるように調整してもよい。 The iron-based alloy may further contain at least one element selected from the group consisting of Cr, Ni, Cu, Mo, Al, B, V, Nb and Ti. These other additive elements are added for the purpose of complementing the effects of Si and Mn, and the effects shown below can be obtained by the addition. However, if the concentration of these other additive elements is too high, problems such as a decrease in hardness, a decrease in life, and insufficient spheroidization tend to occur. Therefore, the content of these other additive elements in the iron-based alloy (when a plurality of elements are added, the total content thereof) may be adjusted to be 0.30 to 1.0% by mass.
Crには、焼き入れ性を向上させる効果と、TTT線図におけるパーライトノーズを右側にシフトさせて臨界冷却速度を下げる効果とがある。Crの濃度が低すぎるとこれらの効果が十分に得られず、高すぎるとショットの靱性が低下する傾向がある。これらを考慮して、鉄基合金中のCrの含有量を0.3〜1.0質量%となるように調整してもよい。 Cr has an effect of improving hardenability and an effect of shifting the pearlite nose in the TTT diagram to the right to lower the critical cooling rate. If the concentration of Cr is too low, these effects cannot be sufficiently obtained, and if it is too high, the toughness of the shot tends to decrease. In consideration of these, the Cr content in the iron-based alloy may be adjusted to be 0.3 to 1.0% by mass.
Ni及びCuには、酸素による球状化阻害を抑制しつつ、焼き入れ性及び寿命を向上させる効果がある。Ni及びCuの濃度が低すぎるとこれらの効果が十分に得られず、高すぎると靱性が低下する傾向がある。これらを考慮して、鉄基合金中のNi及びCuの合計含有量を0.4〜1.0質量%となるように調整してもよい。なお、Cuに比べてNiの方が上記効果の発現に若干優れるが、高価な材料であるため、効果とコストを考慮してNiとCuの組成比は決定される。 Ni and Cu have the effect of improving hardenability and life while suppressing inhibition of spheroidization by oxygen. If the concentrations of Ni and Cu are too low, these effects cannot be sufficiently obtained, and if they are too high, the toughness tends to decrease. In consideration of these, the total content of Ni and Cu in the iron-based alloy may be adjusted to be 0.4 to 1.0% by mass. Although Ni is slightly superior to Cu in exhibiting the above effects, it is an expensive material, so the composition ratio of Ni and Cu is determined in consideration of the effects and cost.
Moには、組織や硬さの粒子毎のばらつきを低減させる効果と、焼き入れ性の向上の効果と、TTT線図におけるパーライトノーズを右側にシフトさせて臨界冷却速度を下げる効果と、がある。Moの濃度が低すぎるとこれらの効果が十分に得られない傾向がある。また、Moは高価な材料であるため、Moの濃度が高すぎると、コストの上昇によるデメリットの方が、これらの効果が得られるメリットよりも大きくなる。これらを考慮して、鉄基合金中のMoの含有量を0.1〜0.3質量%となるように調整してもよい。 Mo has the effect of reducing the variation of each particle in structure and hardness, the effect of improving hardenability, and the effect of shifting the pearlite nose in the TTT diagram to the right to lower the critical cooling rate. .. If the concentration of Mo is too low, these effects tend not to be sufficiently obtained. Further, since Mo is an expensive material, if the concentration of Mo is too high, the demerit due to the increase in cost becomes larger than the merit that these effects can be obtained. In consideration of these, the content of Mo in the iron-based alloy may be adjusted to be 0.1 to 0.3% by mass.
Alには、原料溶湯中の酸素を除去して粒子の球状化を促進する効果と、ブローホールを低減させる効果と、がある。Alの濃度が低すぎるとこれらの効果が十分に得られず、高すぎると逆に球状化が阻害される傾向がある。これらを考慮して、鉄基合金中のAlの含有量を0.04〜0.12質量%となるように調整してもよい。 Al has an effect of removing oxygen in the molten metal of the raw material to promote spheroidization of particles and an effect of reducing blow holes. If the concentration of Al is too low, these effects cannot be sufficiently obtained, and if it is too high, spheroidization tends to be inhibited. In consideration of these, the content of Al in the iron-based alloy may be adjusted to be 0.04 to 0.12% by mass.
Bには、焼き入れ性を向上させる効果と、寿命を向上させる効果と、がある。Bの濃度が低すぎるとこれらの効果が十分に得られず、高すぎると逆に寿命が低下する傾向がある。これらを考慮して、鉄基合金中のBの含有量を0.01〜0.05質量%となるように調整してもよい。 B has an effect of improving hardenability and an effect of improving the life. If the concentration of B is too low, these effects cannot be sufficiently obtained, and if it is too high, the life tends to be shortened. In consideration of these, the content of B in the iron-based alloy may be adjusted to be 0.01 to 0.05% by mass.
V、Nb及びTiには、寿命を向上させる効果がある。これらの元素の濃度が低すぎると当該効果が十分に得られず、高すぎると逆に寿命が低下する傾向がある。これらを考慮して、鉄基合金中のV、Nb及びTiの合計含有量を0.05〜0.5質量%となるように調整してもよい。 V, Nb and Ti have the effect of improving the life. If the concentration of these elements is too low, the effect cannot be sufficiently obtained, and if the concentration is too high, the life tends to be shortened. In consideration of these, the total content of V, Nb and Ti in the iron-based alloy may be adjusted to be 0.05 to 0.5% by mass.
<造粒工程>
原料溶湯を溶解槽底部のノズルから落下させ、この溶湯に向けて高圧水を噴射することで、造粒物(球状体)を得る。<Granulation process>
A granulated product (spherical body) is obtained by dropping the raw material molten metal from a nozzle at the bottom of the melting tank and injecting high-pressure water toward the molten metal.
原料溶湯中の酸素は、造粒の際に粒子の球状化を阻害する要因となる。一実施形態のショットは、原料としてSiを含む溶湯から形成される。Siによって原料溶湯中の酸素が除去されるため、そのような原料を用いることで粒子の球状化を促進することができる。 Oxygen in the molten metal becomes a factor that inhibits the spheroidization of particles during granulation. The shot of one embodiment is formed from a molten metal containing Si as a raw material. Since oxygen in the molten raw material is removed by Si, spheroidization of particles can be promoted by using such a raw material.
また、原料溶湯中の酸素は、ブローホールの原因となる。ブローホールとは、原料溶湯中の酸素が原料の凝固時に大気中に放出されず、粒子の内部に気泡として内包されることで生じるものである。原料としてSiを用いることで、原料溶湯中の酸素が除去され、ブローホールを低減させることができる。 In addition, oxygen in the molten metal causes blow holes. Blow holes are generated when oxygen in the molten raw material is not released into the atmosphere when the raw material is solidified, but is contained as bubbles inside the particles. By using Si as a raw material, oxygen in the molten material can be removed and blow holes can be reduced.
<焼き入れ工程>
上記のとおり生成される造粒物にはCが含有されているため、Feに比べて硬い。しかし、ショットとして用いるにはさらに硬さを向上させる必要がある。造粒工程で製造した造粒物をロータリーキルン等により乾燥させた後に、800〜900℃に加熱し、1時間程度保持した後、水中に投下して焼入れを行う。これにより、造粒物の硬さを増大させることができる。<Quenching process>
Since the granulated product produced as described above contains C, it is harder than Fe. However, it is necessary to further improve the hardness in order to use it as a shot. The granulated product produced in the granulation step is dried by a rotary kiln or the like, heated to 800 to 900 ° C., held for about 1 hour, and then dropped into water for quenching. Thereby, the hardness of the granulated product can be increased.
造粒物にはMnが含有されているため、焼き入れ性が改善されている。また、当該造粒物では、TTT線図におけるパーライトノーズが右側にシフトしているため臨界冷却速度が低下している。さらに、焼き入れを行った際、造粒物の組織が微細化するため靱性が向上する。即ち、このような造粒物は、損耗の少ない(寿命が長い)ショットとして用ることができる。 Since the granulated product contains Mn, the hardenability is improved. Further, in the granulated product, the pearlite nose in the TTT diagram is shifted to the right, so that the critical cooling rate is lowered. Further, when quenching is performed, the structure of the granulated product becomes finer, so that the toughness is improved. That is, such a granulated product can be used as a shot with less wear (longer life).
<焼き戻し工程>
焼き入れ工程を経た造粒物を300〜600℃で0.5〜2.0時間程度加熱し、その後徐冷することにより焼き戻しを行う。これにより、造粒物を所望の硬度に調整することができるとともに、焼入れ工程により低下した造粒物の靭性を向上させることができる。<Tempering process>
The granulated product that has undergone the quenching step is heated at 300 to 600 ° C. for about 0.5 to 2.0 hours, and then slowly cooled to perform tempering. Thereby, the granulated product can be adjusted to a desired hardness, and the toughness of the granulated product lowered by the quenching step can be improved.
焼き入れ工程及び焼き戻し工程を経ることで、造粒物には微細で且つ均一な組織が導入される。特に、一実施形態のショットに含まれる粒子の組織は、実質的に焼戻マルテンサイト相から主として形成される。焼戻マルテンサイト相における結晶粒サイズは0.5〜10μm程度である。このような組織を持つ粒子は、ブラスト加工の際に衝撃荷重が繰り返し加えられても、靱性が高いため損耗が抑制される。 By going through the quenching step and the tempering step, a fine and uniform structure is introduced into the granulated product. In particular, the texture of the particles contained in the shot of one embodiment is substantially formed primarily from the tempered martensite phase. The crystal grain size in the tempered martensite phase is about 0.5 to 10 μm. Particles having such a structure have high toughness even when an impact load is repeatedly applied during blasting, so that wear is suppressed.
<分級工程>
振動篩等を用いて焼き入れ工程後の造粒物を篩にかける。これにより所定の径を有する粒子を分級する。<Classification process>
Sieve the granulated product after the quenching process using a vibrating sieve or the like. As a result, particles having a predetermined diameter are classified.
<回収工程>
分級された粒子の形状や硬度等を検査する工程を経て、所定の径を有する粒子を含むショットが得られる。<Recovery process>
Through the steps of inspecting the shape, hardness, etc. of the classified particles, a shot containing particles having a predetermined diameter can be obtained.
一実施形態のショット(粒子)のビッカース硬さは、HV400〜800である。なお、ブラスト加工性及び寿命の観点から、HVは400〜650であってもよく、400〜500であってもよい。HVの標準偏差はHV50以下とすることができる。一実施形態のショットは特定の組成を有するため、ショットとして十分な硬さを有し、かつ粒子毎の硬さのばらつきが極めて小さい。硬さのばらつきが極めて小さいことにより、ブラスト加工の際に仕上がり品質が安定する。 The Vickers hardness of the shot (particle) of one embodiment is HV400-800. From the viewpoint of blast workability and life, the HV may be 400 to 650 or 400 to 500. The standard deviation of HV can be HV50 or less. Since the shot of one embodiment has a specific composition, it has sufficient hardness as a shot, and the variation in hardness for each particle is extremely small. Due to the extremely small variation in hardness, the finished quality is stable during blasting.
一実施形態のショットにおいて、粒子の長手方向の長さをL、前記長手方向に直行する方向における最大径をSとした場合に、L/Sが2.0以上となる粒子の数はショット全体の5%以下であってもよい。一実施形態のショットは特定の組成を有するため、均等に球状化された粒子が多く含まれており、ブラスト加工の際に仕上がり品質が安定する。当該粒子の数は、ショット全体の1%以下であってもよく、0.1%以下であってもよい。 In the shot of one embodiment, when the length of the particles in the longitudinal direction is L and the maximum diameter in the direction orthogonal to the longitudinal direction is S, the number of particles having an L / S of 2.0 or more is the entire shot. It may be 5% or less of. Since the shot of one embodiment has a specific composition, it contains a large amount of uniformly spheroidized particles, and the finished quality is stable during blasting. The number of the particles may be 1% or less of the whole shot, or 0.1% or less.
一実施形態のショットにおいて、ブローホールを有する粒子の数はショット全体の5%以下であってもよい。ここで、ブローホールを有する粒子とは、断面における気泡の面積割合が断面の面積の10%以上であり、且つ気泡の壁面がなだらかなものを指す。ブローホールはブラスト加工の際にショットが破損する起点となる。一実施形態のショットは特定の組成を有するため、ブローホールを有する粒子の数が極めて少なく寿命が長い。当該粒子の数は、ショット全体の3%以下であってもよく、1%以下であってもよい。 In the shot of one embodiment, the number of particles having blow holes may be 5% or less of the total shot. Here, the particles having blow holes mean that the area ratio of the bubbles in the cross section is 10% or more of the area of the cross section, and the wall surface of the bubbles is gentle. The blow hole is the starting point for shot damage during blasting. Since the shot of one embodiment has a specific composition, the number of particles having blow holes is extremely small and the life is long. The number of the particles may be 3% or less of the entire shot, or 1% or less.
一実施形態のショットにおいて、クラックを有する粒子の数はショット全体の5%以下であってもよい。ここで、クラックを有する粒子とは、断面における亀裂の長さが亀裂の幅の3倍以上であり、且つ亀裂の長さが断面における最少直径の20%以上の長さであるものを指す。クラックはブラスト加工の際にショットが破損する起点となる。一実施形態のショットは特定の組成を有するため、クラックを有する粒子の数が極めて少なく寿命が長い。当該粒子の数は、ショット全体の3%以下であってもよく、1%以下であってもよい。 In the shot of one embodiment, the number of particles having cracks may be 5% or less of the total shot. Here, the particle having a crack means that the length of the crack in the cross section is 3 times or more the width of the crack and the length of the crack is 20% or more of the minimum diameter in the cross section. The crack is the starting point for the shot to be damaged during the blasting process. Since the shot of one embodiment has a specific composition, the number of particles having cracks is extremely small and the life is long. The number of the particles may be 3% or less of the entire shot, or 1% or less.
一実施形態のショットにおいて、含まれる粒子の平均粒子径は0.1〜1.5mmであってもよい。平均粒子径がこの範囲内であるとショットの寿命が長くなる傾向がある。ここで、平均粒子径とは、JIS Z 8801基準ふるいを使用したふるい分けにより測定される値である。平均粒子径は、0.1〜1.0mmであってもよく、0.15〜0.75mmであってもよく、0.2〜0.45mmであってもよい。 In the shot of one embodiment, the average particle size of the contained particles may be 0.1 to 1.5 mm. If the average particle size is within this range, the life of the shot tends to be long. Here, the average particle size is a value measured by sieving using a JIS Z 8801 standard sieve. The average particle size may be 0.1 to 1.0 mm, 0.15 to 0.75 mm, or 0.2 to 0.45 mm.
一実施形態のショットの見かけ密度は7.45g/cm3以上であってもよい。これにより、ブラスト加工の際における被加工物への衝突エネルギーを得易くなるため、被加工物を十分に研掃し易い。The apparent density of the shots of one embodiment may be 7.45 g / cm 3 or more. This makes it easier to obtain collision energy with the work piece during blasting, so it is easy to sufficiently grind the work piece.
[実施例]
次に、一実施形態のショットの効果を確認するための試験結果について説明する。
まず、表1の配合比を有する鉄基合金からなる種々のショットを、水アトマイズ法を用いて作製した。表1におけるXは、Cr、Ni、Cu、Mo、Al、B、V、Nb及びTiからなる群より選択される添加元素の含有量(合計の含有量)を示す。[Example]
Next, the test results for confirming the effect of the shot of one embodiment will be described.
First, various shots made of iron-based alloys having the compounding ratios shown in Table 1 were prepared by using the water atomization method. X in Table 1 indicates the content (total content) of the additive element selected from the group consisting of Cr, Ni, Cu, Mo, Al, B, V, Nb and Ti.
得られた粒子を分級して所望の粒子径(φ0.3mm、φ0.6mm、φ1.0mm)を有するショットを得た。なお、各粒子径を有するショットはそれぞれ下記のようにして準備した。
φ0.3mm:0.425mmの篩を通過し、0.355mmの篩上に残留したもの。
φ0.6mm:0.710mmの篩を通過し、0.600mmの篩上に残留したもの。
φ1.0mm:1.180mmの篩を通過し、1.000mmの篩上に残留したもの。The obtained particles were classified to obtain shots having desired particle diameters (φ0.3 mm, φ0.6 mm, φ1.0 mm). The shots having each particle size were prepared as follows.
φ0.3 mm: Passed through a 0.425 mm sieve and remained on a 0.355 mm sieve.
φ0.6 mm: Passed through a 0.710 mm sieve and remained on a 0.600 mm sieve.
φ1.0 mm: Passed through a 1.180 mm sieve and remained on a 1.000 mm sieve.
(1)ビッカース硬さの測定
ショットの粒子を樹脂に埋め込んだ後、断面中心が表面に露出するように研磨した。10個のショットに対して前述の規格(JIS Z 2244:2009)に準じてビッカース硬さを測定し、その平均値をショットの硬さとした。結果を表2に示す。(1) Measurement of Vickers hardness After the shot particles were embedded in the resin, they were polished so that the center of the cross section was exposed on the surface. The Vickers hardness was measured for 10 shots according to the above-mentioned standard (JIS Z 2244: 2009), and the average value was taken as the hardness of the shots. The results are shown in Table 2.
(2)見かけ密度の測定
JIS Z0311:2004に準じて測定した。具体的には、比重瓶(容積:50ml)にショットを約10g装入し、質量を測定した。次いで、比重瓶に蒸留水を装入し、内部の気泡を除去した後、質量を測定した。これらの質量から見かけ密度を演算した。この操作を2回行い、その平均値をショットの見かけ密度とした。結果を表2に示す。(2) Measurement of apparent density Measurement was performed according to JIS Z0311: 2004. Specifically, about 10 g of shots was placed in a specific gravity bottle (volume: 50 ml), and the mass was measured. Next, distilled water was charged into a specific gravity bottle to remove air bubbles inside, and then the mass was measured. The apparent density was calculated from these masses. This operation was performed twice, and the average value was taken as the apparent density of the shot. The results are shown in Table 2.
(3)欠陥(ブローホール)の検証
ショットの粒子を樹脂に埋め込んだ後、断面中心が表面に露出するように研磨した。100個のショットに対して断面を投影機によって観察し、欠陥として前述のブローホールが存在するショットの数を計測してその割合を算出した。結果を表2に示す。(3) Verification of defects (blow holes) After the shot particles were embedded in the resin, they were polished so that the center of the cross section was exposed on the surface. The cross section of 100 shots was observed with a projector, the number of shots in which the above-mentioned blow hole was present as a defect was measured, and the ratio was calculated. The results are shown in Table 2.
(4)真球度の検証
ショットの粒子をガラス平板に広げた後、100個のショットに対して、粒子の長手方向の長さL、前記長手方向に直行する方向における最大径Sをマイクロスコープにより観察した。そして、L/Sが2.0以上となる粒子の数を計測し、その割合(粒子形状不良率)を算出した。結果を表2に示す。(4) Verification of sphericity After spreading the particles of the shot on a glass plate, the length L in the longitudinal direction of the particles and the maximum diameter S in the direction orthogonal to the longitudinal direction are measured for 100 shots with a microscope. Observed by. Then, the number of particles having an L / S of 2.0 or more was measured, and the ratio (particle shape defect rate) was calculated. The results are shown in Table 2.
(5)寿命の評価
製造したショット100gを寿命試験装置(Ervin製:The Test Ervin Machine)に投入し、投射速度60m/sで鋼材(HRC65)に向けて投射した。投射後のショットを回収し、回収したショットを篩(0.300mm、0.500mm又は0.850mm)で分級し、篩に残ったショットの重さを秤量した。篩上に残ったショットが10gとなるまでこの操作を繰り返し、この試験により得られた衝突回数とショットの残留率の関係を示す曲線を積分し、この数値を寿命値とした。結果を表2に示す。(5) Evaluation of life The 100 g of the manufactured shot was put into a life test device (manufactured by Ervin: The Test Ervin Machine) and projected toward a steel material (HRC65) at a projection speed of 60 m / s. The shots after projection were collected, the collected shots were classified by a sieve (0.300 mm, 0.500 mm or 0.850 mm), and the weight of the shots remaining on the sieve was weighed. This operation was repeated until the amount of shots remaining on the sieve was 10 g, and the curve showing the relationship between the number of collisions obtained by this test and the residual rate of shots was integrated, and this value was used as the lifetime value. The results are shown in Table 2.
比較例は、従来の組成をもつショットである。実施例1〜10のショットは、比較例のショットに比べて長寿命であることがわかった。 A comparative example is a shot having a conventional composition. It was found that the shots of Examples 1 to 10 had a longer life than the shots of Comparative Example.
また、実施例1及び比較例それぞれのショットの断面を走査型電子顕微鏡にて観察した。図1に示すように、実施例のショットにおいては、微細化された焼戻マルテンサイト相から主として形成された組織が観察されたのに対し、比較例のショットにおいては、微細化されていないマルテンサイト相から主として形成された組織が観察された。 In addition, the cross sections of the shots of Example 1 and Comparative Example were observed with a scanning electron microscope. As shown in FIG. 1, in the shot of the example, the structure mainly formed from the refined tempered martensite phase was observed, whereas in the shot of the comparative example, the unrefined martensite was observed. Tissues formed primarily from the site phase were observed.
一実施形態のショットは、研掃に必要な硬さを有しており、且つ寿命が長いため、工業的価値は極めて大である。このショットは、あらゆるブラスト加工に用いることができる。 The shot of one embodiment has a hardness required for cleaning and has a long life, so that it has an extremely large industrial value. This shot can be used for any blasting process.
一実施形態のショットの製造方法として水アトマイズ法を例に説明したが、ガスアトマイズ法やディスクアトマイズ法等の別の方法を採用してもよい。 Although the water atomization method has been described as an example of the shot production method of one embodiment, another method such as a gas atomization method or a disc atomization method may be adopted.
Claims (6)
添加元素としてC:0.20〜0.50質量%、Si:0.50〜1.10質量%、及びMn:0.50〜1.15質量%を含む鉄基合金からなり、
前記Siに対する前記Cの質量比が0.30〜0.75、前記Mnに対する前記Cの質量比が0.30〜0.75、及び前記Mnに対する前記Siの質量比が0.70〜1.60であり、
ビッカース硬さがHV400〜800である、ショット。A shot used for blasting
It is composed of an iron-based alloy containing C: 0.25 to 0.50% by mass, Si: 0.50 to 1.10% by mass, and Mn: 0.50 to 1.15% by mass as additive elements.
The mass ratio of the C to the Si is 0.30 to 0.75, the mass ratio of the C to the Mn is 0.30 to 0.75, and the mass ratio of the Si to the Mn is 0.70 to 1. 60
A shot with a Vickers hardness of HV400-800.
When the length of the particles in the longitudinal direction is L and the maximum diameter in the direction orthogonal to the longitudinal direction is S, the number of particles having an L / S of 2.0 or more is 5% or less of the entire shot. The shot according to any one of claims 1 to 5.
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JP2018061997 | 2018-03-28 | ||
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PCT/JP2019/009328 WO2019188120A1 (en) | 2018-03-28 | 2019-03-08 | Shot used for blast processing |
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JP (1) | JP7205535B2 (en) |
CN (1) | CN111278603A (en) |
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Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2670281A (en) * | 1949-10-14 | 1954-02-23 | American Wheelabrator & Equipm | Steel shot for blast cleaning, blast peening, and the like |
JPS56152909A (en) * | 1980-04-30 | 1981-11-26 | Nippon Beenaito Kk | Manufacture of metallic particle |
JPS579855A (en) * | 1980-06-20 | 1982-01-19 | Ito Kiko Kk | Steel shot |
JPH02228448A (en) * | 1989-02-28 | 1990-09-11 | Daido Steel Co Ltd | High strength and high toughness steel shot |
Family Cites Families (1)
Publication number | Priority date | Publication date | Assignee | Title |
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CN105861922B (en) * | 2016-04-28 | 2017-09-29 | 淄博大亚金属科技股份有限公司 | One kind surface treatment high life steel ball and preparation method thereof |
-
2019
- 2019-03-08 US US16/981,460 patent/US20210069864A1/en not_active Abandoned
- 2019-03-08 WO PCT/JP2019/009328 patent/WO2019188120A1/en active Application Filing
- 2019-03-08 DE DE112019000550.2T patent/DE112019000550T5/en active Pending
- 2019-03-08 CN CN201980005353.1A patent/CN111278603A/en active Pending
- 2019-03-08 JP JP2020509793A patent/JP7205535B2/en active Active
- 2019-03-21 TW TW108109769A patent/TW201942381A/en unknown
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2670281A (en) * | 1949-10-14 | 1954-02-23 | American Wheelabrator & Equipm | Steel shot for blast cleaning, blast peening, and the like |
JPS56152909A (en) * | 1980-04-30 | 1981-11-26 | Nippon Beenaito Kk | Manufacture of metallic particle |
JPS579855A (en) * | 1980-06-20 | 1982-01-19 | Ito Kiko Kk | Steel shot |
JPH02228448A (en) * | 1989-02-28 | 1990-09-11 | Daido Steel Co Ltd | High strength and high toughness steel shot |
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US20210069864A1 (en) | 2021-03-11 |
CN111278603A (en) | 2020-06-12 |
WO2019188120A1 (en) | 2019-10-03 |
DE112019000550T5 (en) | 2020-10-08 |
TW201942381A (en) | 2019-11-01 |
JP7205535B2 (en) | 2023-01-17 |
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