JP4278060B2 - Spherical vanadium carbide-containing low thermal expansion material excellent in wear resistance and method for producing the same - Google Patents
Spherical vanadium carbide-containing low thermal expansion material excellent in wear resistance and method for producing the same Download PDFInfo
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Description
本発明は耐摩耗性に優れた球状バナジウム炭化物含有低熱膨張材料及びこの製造方法に関する。
本発明の目的は、鉄−ニッケル合金や鉄−ニッケル−コバルト合金基地中に、高硬度の球状バナジウム炭化物を晶出・分散させることにより、低熱膨張性に加えて、高耐摩耗性を示す低熱膨張材料及びこの製造方法を提供することにある。
The present invention relates to a spherical vanadium carbide-containing low thermal expansion material excellent in wear resistance and a method for producing the same.
The object of the present invention is to provide a low heat exhibiting high wear resistance in addition to low thermal expansion by crystallizing and dispersing high hardness spherical vanadium carbide in an iron-nickel alloy or iron-nickel-cobalt alloy base. The object is to provide an intumescent material and a method of manufacturing the same.
近年、超精密加工を達成するために、要求される加工精度がミクロンオーダーからサブミクロンオーダーにまで高まっている。このような超精密加工を実現するには、精密加工機械の精度が問題となる。
精密加工機械の精度の維持・向上には、温度による精密加工機械の寸法変化を抑制することが必要である。このために、精密加工機械を構成する材料として、温度による寸法変化の少ない材料、即ち低熱膨張材料が使用されている。
In recent years, in order to achieve ultra-precision machining, the required machining accuracy has increased from the micron order to the submicron order. In order to realize such ultra-precision machining, the precision of precision machining machines becomes a problem.
In order to maintain and improve precision of precision processing machines, it is necessary to suppress dimensional changes of precision processing machines due to temperature. For this reason, a material having a small dimensional change due to temperature, that is, a low thermal expansion material is used as a material constituting the precision processing machine.
低熱膨張材料としては、インバー（Ｆｅ−３６．５％Ｎｉ）やスーパーインバー（３２％Ｎｉ−５％Ｃｏ−Ｆｅ）が知られている。
インバーの熱膨張係数は、室温付近で約１．２×１０−６／Ｋ、スーパーインバーの熱膨張係数は、室温付近で約０．１×１０−６／Ｋであり、温度による寸法変化が少ないことから、標準尺や測量尺などの測定機器に用いられてきた。
しかしながら、インバーやスーパーインバーなどの低熱膨張材料は、切削加工性が悪く、高い寸法精度の製品を効率的に製造することが困難であった。また鋳造性が悪く、鋳造品として使用されることは少なかった。
Invar (Fe-36.5% Ni) and Super Invar (32% Ni-5% Co-Fe) are known as low thermal expansion materials.
The thermal expansion coefficient of Invar is about 1.2 × 10 −6 / K near room temperature, and the thermal expansion coefficient of Super Invar is about 0.1 × 10 −6 / K near room temperature. Because of its small number, it has been used in measuring instruments such as standard scales and surveying scales.
However, low thermal expansion materials such as Invar and Super Invar have poor machinability, and it has been difficult to efficiently produce products with high dimensional accuracy. In addition, castability was poor, and it was rarely used as a cast product.
一方、インバーなどの二元系合金やスーパーインバーなどの三元系合金に、各種元素を添加することにより、上記欠点の解消を目指した低熱膨張材料が提案されている。
例えば、特許文献１には、Ｃ：０．５％超〜１．５％未満、Ｓｉ：０．５％〜１．５％、Ｍｎ：１．０％以下、Ｎｉ：２５．０％〜３２．０％、Ｃｏ：６．５％超〜１３．０％からなり、前記組成においてＮｉ＋Ｃｏの範囲が３３．０％〜４０．０％未満、残部は鉄及び不可避的元素からなる低熱膨張材料が開示されている。
特許文献２には、Ｃ：０．３〜２．５％、Ｓｉ：０．８％以下、Ｍｎ：１．０％以下、Ｎｉ：２５〜４０％、Ｃｏ：９．０％以下であって、ＮｉとＣｏとの合計量が３３〜４３％、ＭｇまたはＣａを０．１％以下、希土類元素を０．２％以下、Ｎｂ，Ｔｉ，Ｚｒ，ＴａおよびＨｆから選択される少なくとも１種の炭化物形成元素を２．０％以下含有し、残部Ｆｅおよび不純物からなる低熱膨張材料が開示されている。
On the other hand, a low thermal expansion material has been proposed that aims to eliminate the above-mentioned drawbacks by adding various elements to binary alloys such as Invar and ternary alloys such as Super Invar.
For example, in
In
しかしながら、インバー、スーパーインバー、或いは特許文献１及び２に開示される従来の低熱膨張材料は、低熱膨張性を示すものの、耐摩耗性に劣り、機械的強度に優れた低熱膨張材料ではなかった。
本発明の解決課題は、耐摩耗性などの機械的強度に優れた低熱膨張材料及びこの製造方法を提供することである。
However, Invar, Super Invar, or the conventional low thermal expansion materials disclosed in
The problem to be solved by the present invention is to provide a low thermal expansion material excellent in mechanical strength such as wear resistance and a method for producing the same.
請求項１に係る発明は、合金原料として、Ｃ：１．５〜４．０重量％、Ｖ：６〜１５重量％、Ｓｉ：０．２〜４．０重量％、Ｎｉ：２０〜３７重量％、残部鉄（Ｆｅ）及び不可避不純物を含有し、組織中に球状のバナジウム炭化物を晶出させてなることを特徴とする球状バナジウム炭化物含有低熱膨張材料に関する。
請求項２に係る発明は、Ｃｏ：０．０１〜１６重量％の合金原料を含有することを特徴とする請求項１に記載の球状バナジウム炭化物含有低熱膨張材料に関する。
請求項３に係る発明は、Ｃ：１．５〜４．０重量％、Ｖ：６〜１５重量％、Ｓｉ：０．２〜４．０重量％、Ｎｉ：２０〜３７重量％、残部鉄（Ｆｅ）及び不可避不純物からなる合金原料を１７７３〜２０２３Ｋで溶解して、組織中に球状のバナジウム炭化物を晶出させることを特徴とする球状バナジウム炭化物含有低熱膨張材料の製造方法に関する。
請求項４に係る発明は、前記合金原料が、Ｃｏ：０．０１〜１６重量％の合金原料を含有することを特徴とする請求項３に記載の球状バナジウム炭化物含有低熱膨張材料の製造方法に関する。
The invention according to
The invention according to
The invention according to
Invention, the alloy raw material, C o according to claim 4: 0.01 to 16 manufacturing method of spheroidal vanadium carbide containing low thermal expansion material according to
本発明に係る低熱膨張材料及びこの製造方法は、鉄−ニッケル合金や鉄−ニッケル−コバルト合金基地中に、高硬度の球状バナジウム炭化物を晶出・分散させているので、低熱膨張材料として汎用されているインバーやスーパーインバーなどと略同等の低熱膨張性を有するとともに、インバーやスーパーインバーなどの低熱膨張材料が持ち合わせていない高耐摩耗性を示す低熱膨張材料及びこの製造方法を提供することができる。 The low thermal expansion material and the manufacturing method according to the present invention are widely used as a low thermal expansion material because high hardness spherical vanadium carbide is crystallized and dispersed in an iron-nickel alloy or iron-nickel-cobalt alloy base. It is possible to provide a low thermal expansion material having a low thermal expansion property substantially equal to that of invar, super invar, etc., and exhibiting high wear resistance not possessed by low thermal expansion materials such as invar and super invar, and a method for manufacturing the same. .
以下、本発明に係る耐摩耗性に優れた球状バナジウム炭化物含有低熱膨張材料及びこの製造方法について詳述する。
本発明に係る球状バナジウム炭化物含有低熱膨張材料は、Ｃ：１．５〜４．０重量％、Ｖ：６〜１５重量％、Ｓｉ：０．２〜４．０重量％、Ｎｉ：２０〜３７重量％、残部鉄（Ｆｅ）及び不可避不純物からなる。
Hereinafter, the spherical vanadium carbide-containing low thermal expansion material excellent in wear resistance according to the present invention and the production method thereof will be described in detail.
The spherical vanadium carbide-containing low thermal expansion material according to the present invention has C: 1.5 to 4.0 wt%, V: 6 to 15 wt%, Si: 0.2 to 4.0 wt%, Ni: 20 to 37 % By weight, balance iron (Fe) and inevitable impurities.
Ｃ及びＶは、球状のバナジウム炭化物を晶出させるために配合される。
炭素（Ｃ）の含有量は、１．５〜４．０重量％、好ましくは１．９〜３．５重量％、より好ましくは２．１〜３．３重量％とされる。
Ｃの含有量が１．５重量％未満の場合、球状化不良のバナジウム炭化物が多くなり、１．５重量％を超えるとバナジウム炭化物の球状化が安定化する。
Ｃの含有量が４．０重量％を超えると、一部のＣはＦｅ−Ｃ系板状炭化物（セメンタイト）となり、機械的強度が低下する場合がある。
C and V are blended to crystallize spherical vanadium carbide.
The carbon (C) content is 1.5 to 4.0% by weight, preferably 1.9 to 3.5% by weight, and more preferably 2.1 to 3.3% by weight.
When the content of C is less than 1.5% by weight, the amount of vanadium carbide with poor spheroidization increases, and when it exceeds 1.5% by weight, the spheroidization of vanadium carbide is stabilized.
When the C content exceeds 4.0% by weight, a part of C becomes Fe—C type plate-like carbide (cementite), and the mechanical strength may decrease.
バナジウム（Ｖ）の含有量は、６．０〜１５重量％、好ましくは８〜１４重量％、より好ましくは、９〜１３．５重量％とされる。
Ｖの含有量が６．０重量％未満の場合、バナジウム炭化物を球状で晶出させることができず、１５重量％を超えて配合しても、それ以上の効果は期待できず、逆に偏析を起しやすくなり、いずれの場合も好ましくない。
また、球状のバナジウム炭化物は、ＶとＣの原子数比が約１：１（重量比４．２５：１）であるため、Ｖの含有量がＣの含有量の３〜６重量倍、好ましくは３．５〜５．５重量倍、より好ましくは約４重量倍になるように配合するとよい。
The content of vanadium (V) is 6.0 to 15% by weight, preferably 8 to 14% by weight, and more preferably 9 to 13.5% by weight.
If the V content is less than 6.0% by weight, the vanadium carbide cannot be crystallized in a spherical shape, and even if it exceeds 15% by weight, no further effect can be expected and conversely segregation. In any case, it is not preferable.
Also, since the spherical vanadium carbide has an atomic ratio of V to C of about 1: 1 (weight ratio of 4.25: 1), the V content is preferably 3 to 6 times the C content, preferably May be blended so as to be 3.5 to 5.5 times by weight, more preferably about 4 times by weight.
ケイ素（Ｓｉ）は溶解鋳造性、或いは耐摩耗性などの機械的特性向上のために配合される。
ケイ素（Ｓｉ）は溶解時の酸化防止と脱酸および鋳造性確保のために配合される。Ｓｉの含有量は０．２〜４．０重量％、好ましくは０．５〜４．０重量％、より好ましくは０．５〜２．０重量％とされる。この理由は、０．２重量％未満の場合、Ｖの歩留りを悪化させるためにＳｉ含有による効果を発揮することができず、一方、４．０重量％を超えると耐摩耗性が低下してしまい、いずれの場合も好ましくない。
Silicon (Si) is blended to improve mechanical properties such as melt castability or wear resistance.
Silicon (Si) is blended for the purpose of preventing oxidation during dissolution, deoxidation, and ensuring castability. The Si content is 0.2 to 4.0% by weight, preferably 0.5 to 4.0% by weight, and more preferably 0.5 to 2.0% by weight. The reason for this is that if it is less than 0.2% by weight, the effect of Si content cannot be exerted in order to deteriorate the yield of V. On the other hand, if it exceeds 4.0% by weight, the wear resistance decreases. In any case, it is not preferable.
ニッケル（Ｎｉ）は熱膨張係数の低下のために配合される。
Ｎｉの含有量は２０〜３７重量％、好ましくは２０〜３５重量％、より好ましくは２３〜３５重量％とされる。この理由は、Ｎｉの含有量が２０重量％未満の場合、熱膨張係数が高値となり好ましくなく、３７重量％を超えて含有すると、室温以下のような低温度域での熱膨張係数が高値となり、いずれの場合も好ましくない。
Nickel (Ni) is blended to reduce the thermal expansion coefficient.
The Ni content is 20 to 37% by weight, preferably 20 to 35% by weight, and more preferably 23 to 35% by weight. The reason for this is that when the Ni content is less than 20% by weight, the thermal expansion coefficient becomes high, which is not preferable. When the Ni content exceeds 37% by weight, the thermal expansion coefficient in a low temperature region such as room temperature or lower becomes high. In either case, it is not preferable.
以上の合金元素が主成分である鉄（Ｆｅ）に含有させる必須成分である。 The above alloy elements are essential components to be contained in iron (Fe) as a main component.
さらに、本発明では上記した必須成分に加えて、Ｍｎ：０．０４〜０．３重量％、Ｃｏ：０．０１〜１６重量％及びＭｇ：０．０１〜０．１重量％からなる群から選択される一種以上の合金原料を含有することができる。 Further, in the present invention, in addition to the above-mentioned essential components, Mn: 0.04 to 0.3% by weight, Co: 0.01 to 16% by weight, and Mg: 0.01 to 0.1% by weight One or more selected alloy raw materials can be contained.
マンガン（Ｍｎ）を含有すると、耐摩耗性などの機械的特性をより向上することができる。
マンガン（Ｍｎ）を含有すると、耐摩耗性などの機械的特性をより向上することができる。 Ｍｎの含有量は０．０４〜０．３重量％、好ましくは０.０４〜０．２５重量％、より好ましくは０.０４〜０．２重量％とされる。
この理由は、０．０４重量％未満の含有量では、耐摩耗性などの機械的特性を向上させることができず、また０．３重量％を超えて含有すると、熱膨張係数が高値となるため、いずれの場合も好ましくない。
When manganese (Mn) is contained, mechanical properties such as wear resistance can be further improved.
When manganese (Mn) is contained, mechanical properties such as wear resistance can be further improved. The Mn content is 0.04 to 0.3% by weight, preferably 0.04 to 0.25% by weight, more preferably 0.04 to 0.2% by weight.
This is because if the content is less than 0.04% by weight, mechanical properties such as wear resistance cannot be improved. If the content exceeds 0.3% by weight, the thermal expansion coefficient becomes high. Therefore, it is not preferable in either case.
コバルト（Ｃｏ）を含有すると、熱膨張係数を低下させることができる。
Ｃｏの含有量は０．０１〜１６重量％、好ましくは０．１〜１２重量％、より好ましくは１〜１２重量％とされる。
この理由は、０．０１重量％未満の含有量では、熱膨張率の低減効果が低く、また１６重量％を超えて含有すると、逆に室温以下のような低温度域での熱膨張係数が高値となるため、いずれの場合も好ましくない。
When cobalt (Co) is contained, the thermal expansion coefficient can be lowered.
The Co content is 0.01 to 16% by weight, preferably 0.1 to 12% by weight, more preferably 1 to 12% by weight.
The reason for this is that when the content is less than 0.01% by weight, the effect of reducing the thermal expansion coefficient is low, and when the content exceeds 16% by weight, the thermal expansion coefficient in a low temperature region such as room temperature or less is conversely Since it becomes a high price, it is not preferable in any case.
マグネシウム（Ｍｇ）を含有すると、バナジウム炭化物の球状化を促進することができる。
Ｍｇの含有量は０．０１〜０．１重量％、好ましくは０．０２〜０．０８重量％、より好ましくは０．０３〜０．０８重量％とされる。この理由は０．０１重量％未満の場合にはバナジウム炭化物の球状化を促進することができず、また０．１重量％を超えることはマグネシウムの酸化物が多く散在することになり材質上好ましくない。
When magnesium (Mg) is contained, spheroidization of vanadium carbide can be promoted.
The Mg content is 0.01 to 0.1% by weight, preferably 0.02 to 0.08% by weight, and more preferably 0.03 to 0.08% by weight. The reason for this is that when the amount is less than 0.01% by weight, spheroidization of vanadium carbide cannot be promoted, and when it exceeds 0.1% by weight, a large amount of magnesium oxide is scattered, which is preferable in terms of material. Absent.
尚、本発明では、上記した成分にＰ及びＳを含有しても構わない。
リン（Ｐ）の含有量は０．０２〜０．１重量％、好ましくは０．０２〜０．０８重量％、より好ましくは０．０２〜０．０６重量％とされる。この理由は、０．０１重量％未満にすることは現在用いる材料上困難なことであり、一方、０．１重量％を超えると偏析や脆性を起すために、いずれの場合も好ましくない。
硫黄（Ｓ）の含有量は０．００６〜０．０８重量％、好ましくは０．０１５〜０．０５重量％とされる。この理由は、０．００６重量％未満にすることは現在用いる材料上困難なことであり、０．０８重量％を超えると、ＭｎＳ（硫化マンガン）を晶出しやすくなり、脆性を起すために、いずれの場合も好ましくない。
In the present invention, P and S may be contained in the above components.
The phosphorus (P) content is 0.02 to 0.1% by weight, preferably 0.02 to 0.08% by weight, and more preferably 0.02 to 0.06% by weight. The reason for this is that it is difficult to use less than 0.01% by weight of the material currently used. On the other hand, if it exceeds 0.1% by weight, segregation and brittleness are caused.
The content of sulfur (S) is 0.006 to 0.08% by weight, preferably 0.015 to 0.05% by weight. The reason for this is that it is difficult to use less than 0.006% by weight on the material currently used. If it exceeds 0.08% by weight, MnS (manganese sulfide) is easily crystallized, and brittleness is caused. In either case, it is not preferable.
さらに、本発明では上記した各成分に加えて、（ａ）Ｍｏ：０．５〜４．０重量％、（ｂ）Ｔａ、Ｔｉ、Ｗ、Ｎｂからなる群から選択される少なくとも二種以上の合金元素：０．５〜３．５重量％、（ｃ）Ｃａ、Ｂａ、Ｓｒからなる群から選択される少なくとも二種以上の合金元素：０．０１〜０．１重量％、の（ａ）〜（ｃ）の中から選択された一以上の合金元素を配合することができる。 Further, in the present invention, in addition to the above-described components, (a) Mo: 0.5 to 4.0% by weight, (b) at least two or more selected from the group consisting of Ta, Ti, W, and Nb Alloy element: 0.5 to 3.5% by weight, (c) At least two or more kinds of alloy elements selected from the group consisting of Ca, Ba and Sr: 0.01 to 0.1% by weight (a) One or more alloy elements selected from (c) can be blended.
本発明に係る球状バナジウム炭化物含有低熱膨張材料を製造するには、上記組成からなる合金原料を、気泡化反応温度で溶解した後、鋳造すればよい。
気泡化反応温度は１７７３〜２０７３Ｋ、好ましくは１７７３〜１９５０Ｋ、より好ましくは１８７３〜１９５０Ｋである。
溶解温度が１７７３Ｋ未満であると、球状バナジウム炭化物が形成されず、非球状バナジウム炭化物がマトリックス中に晶出するために、耐摩耗性を向上することができない。また、処理溶湯の流動性が悪化し、鋳造することが困難となる。
溶解温度が２０７３Ｋを超えると、球状バナジウム炭化物の形成には影響を与えないが、合金原料の歩留まりが悪化する場合がある。
In order to produce the spherical vanadium carbide-containing low thermal expansion material according to the present invention, the alloy raw material having the above composition may be melted at the aeration reaction temperature and then cast.
The bubble formation reaction temperature is 1773-2073K, preferably 1773-1950K, more preferably 1873-1950K.
When the melting temperature is less than 1773 K, spherical vanadium carbide is not formed, and non-spherical vanadium carbide crystallizes in the matrix, so that the wear resistance cannot be improved. Moreover, the fluidity | liquidity of a process molten metal deteriorates and it becomes difficult to cast.
If the melting temperature exceeds 2073 K, the formation of spherical vanadium carbide is not affected, but the yield of alloy raw materials may deteriorate.
さらに、Ｍｇを含有させる場合、前述のように他の合金原料とともに気泡化反応温度で溶解した後、鋳造しても構わないが、球状バナジウム炭化物の晶出を促進させるために、Ｍｇを除く上記組成からなる合金原料を、気泡化反応温度で溶解した後、Ｍｇを添加して鋳造を行うことが好ましい。
Ｍｇは沸点（１３７３Ｋ）が比較的低いために、１７７３〜２０７３Ｋの溶湯中では気泡となる。Ｍｇ添加により、積極的に溶湯中にＭｇ気泡の微細な球状空間を分散させ、この気泡の球状空間に共有結合性の球状バナジウム炭化物を優先的に晶出させることで、球状バナジウム炭化物の晶出を促進させ、さらに球状バナジウム炭化物をマトリックス中に均一に分散させることができる。この理由により、Ｍｇは炭化物の球状化能が極めて高く、本合金には重要な要素である。
Ｍｇは、純マグネシウム、Ｍｇ合金、Ｍｇの塩化物、Ｍｇのフッ化物等を使用することができ、Ｍｇ合金としては、塊状又はブリケットのＭｇ−Ｎｉ、Ｍｇ−Ｆｅ、Ｍｇ−Ｓｉ−Ｆｅ、Ｍｇ−Ｃｕ、Ｍｇ−Ａｌなどを例示することができる。
Furthermore, when Mg is contained, it may be cast after melting at the bubble forming reaction temperature together with other alloy raw materials as described above, but in order to promote crystallization of spherical vanadium carbide, the above except for Mg It is preferable to carry out casting by adding Mg after melting the alloy raw material having the composition at the bubble formation reaction temperature.
Since Mg has a relatively low boiling point (1373K), it becomes bubbles in the melt of 1773-2073K. By adding Mg, the fine spherical space of Mg bubbles is positively dispersed in the molten metal, and the spherical vanadium carbide having a covalent bond is preferentially crystallized in the spherical space of the bubbles, thereby crystallizing the spherical vanadium carbide. And can further disperse the spherical vanadium carbide uniformly in the matrix. For this reason, Mg has an extremely high ability to spheroidize carbides and is an important factor for this alloy.
Mg may be pure magnesium, Mg alloy, Mg chloride, Mg fluoride, etc., and Mg alloy such as bulk or briquette Mg—Ni, Mg—Fe, Mg—Si—Fe, Mg -Cu, Mg-Al, etc. can be illustrated.
上記組成からなる球状バナジウム炭化物含有低熱膨張材料は、常法に準じて、鋳型内に溶湯を注ぎ込み、その後冷却する鋳放しにより得ることができる。
また、１２７３Ｋ〜１４２３Ｋに加熱後水中に急冷する熱処理を施すことも可能である。熱処理を施すことによって、鋳放しにより製造した場合に比べて、熱膨張係数を低下させることができ、低熱膨張性を向上させることができる。
The spherical vanadium carbide-containing low thermal expansion material having the above composition can be obtained by casting as molten metal is poured into a mold and then cooled according to a conventional method.
Moreover, it is also possible to perform the heat processing which quenches rapidly in water after heating to 1273K-1423K. By performing the heat treatment, the thermal expansion coefficient can be reduced and the low thermal expansion can be improved as compared with the case of manufacturing by casting.
本発明に係る球状バナジウム炭化物含有低熱膨張材料は、基地中に硬質な炭素粒子である球状バナジウム炭化物が略均一に分散して含まれている。このために、低熱膨張性を示すとともに、耐摩耗性などの機械的特性に優れた低熱膨張材料である。 The spherical vanadium carbide-containing low thermal expansion material according to the present invention contains spherical vanadium carbide, which is hard carbon particles, dispersed in a substantially uniform manner in the matrix. For this reason, it is a low thermal expansion material that exhibits low thermal expansion and is excellent in mechanical properties such as wear resistance.
以下、実施例を示して本発明をより詳細に説明する。但し、本発明は以下の実施例により何ら限定されるものではない。 Hereinafter, the present invention will be described in more detail with reference to examples. However, the present invention is not limited to the following examples.
表１に記載した組成に従い、実施例１〜２６の各試料を以下の方法で調製した。
まず各合金元素を、５ｋｇ高周波誘導炉（マグネシア坩堝）を用いて１９２３Ｋに昇温して溶解した。１８７３Ｋで鋳型内（試料部サイズ:６０×７０×１０ｍｍ）に溶湯を注ぎ込み、その後冷却する鋳放しにより、ミクロ組織観察試験片、機械的試験片（５５×５５×１０ｍｍ）及び耐摩耗性試験片（２５×５０×１０ｍｍ）を採取した。
また、熱処理試料は上記溶解鋳造により得られた試料を１２７３Ｋ〜１４２３Ｋに加熱後水中に急冷することで得た。
According to the composition described in Table 1, each sample of Examples 1 to 26 was prepared by the following method.
First, each alloy element was melted by raising the temperature to 1923 K using a 5 kg high-frequency induction furnace (magnesia crucible). The molten metal is poured into the mold (sample size: 60 × 70 × 10 mm) at 1873K, and then cooled, and the microstructure is examined, a mechanical specimen (55 × 55 × 10 mm), and an abrasion resistance specimen. (25 × 50 × 10 mm) was collected.
The heat-treated sample was obtained by heating the sample obtained by the above melt casting to 1273K-1423K and then rapidly cooling it in water.
尚、比較例１としては、ＳＳ４００と呼称される一般構造用圧延鋼材（ＪＩＳ Ｇ−３１０１）を、比較例２としては、インバー（Ｆｅ−３６％Ｎｉ）を、比較例３としてはスーパーインバー（Ｆｅ−３２％Ｎｉ−５％Ｃｏ）を、比較例４としては、黒鉛鋼系低熱膨張材（Ｆｅ−０．２〜１．０％Ｃ−３６％Ｎｉ）を、それぞれ用いた。 In addition, as comparative example 1, rolled steel for general structure called SS400 (JIS G-3101), as comparative example 2, invar (Fe-36% Ni), as comparative example 3, super invar ( Fe-32% Ni-5% Co) and, as Comparative Example 4, a graphite steel low thermal expansion material (Fe-0.2 to 1.0% C-36% Ni) was used.
［試験例１：光学顕微鏡観察］
ミクロ組織の観察のために、上記調製した各実施例の供試材の側部より１２ｍｍ部を切断して、研磨後、光学顕微鏡で観察した。
各実施例の顕微鏡写真をそれぞれ図１〜２１に示す。尚、図１〜２１中、（Ａ）は鋳放しにより製造した試料の顕微鏡写真であり、（Ｂ）は熱処理を施して製造した試料の顕微鏡写真である。
[Test Example 1: Optical microscope observation]
In order to observe the microstructure, a 12 mm portion was cut from the side portion of the specimen of each of the above-prepared examples, polished, and then observed with an optical microscope.
The micrographs of each example are shown in FIGS. 1 to 21, (A) is a photomicrograph of a sample manufactured by casting, and (B) is a photomicrograph of a sample manufactured by heat treatment.
図１〜２１に示されるように、実施例の各試料では、組織中に球状のバナジウム炭化物が晶出していることが確認された。 As shown in FIGS. 1 to 21, it was confirmed that spherical vanadium carbide crystallized in the structure in each sample of the example.
［試験例２：硬さ試験（ＨＶ）］
実施例１〜２６及び比較例１〜４の試料のビッカーズ硬さを測定した。結果を表２に記載する。
[Test Example 2: Hardness test (HV)]
The Vickers hardness of the samples of Examples 1 to 26 and Comparative Examples 1 to 4 was measured. The results are listed in Table 2.
［試験例３：硬さ試験（ＨＲＣ）］
実施例１〜２６の試料の硬度を、「ロックウェル硬さ（ＨＲ）」の「Ｃスケール」（ＨＲＣ）を用いて測定した。試験方法は、「ＪＩＳ Ｚ−２２４５」に示される「ロックウェル硬さ試験方法」（ダイヤモンド圧子又は球圧子を用いて、まず基準荷重を加え、次に試験荷重を加え、再び基準荷重に戻したとき、前後２回の基準荷重における圧子の侵入深さの差によって定義式から求める）に準じて試験を行った。結果を表２に記載する。
[Test Example 3: Hardness test (HRC)]
The hardness of the samples of Examples 1 to 26 was measured using “C scale” (HRC) of “Rockwell hardness (HR)”. The test method is “Rockwell hardness test method” shown in “JIS Z-2245” (using a diamond indenter or a ball indenter, first applying a reference load, then applying a test load, and then returning to the reference load again. The test was carried out according to the definition formula) by the difference in penetration depth of the indenter at the reference load twice before and after. The results are listed in Table 2.
表２に示されるとおり、本発明に係る球状バナジウム炭化物含有低熱膨張材料は、比較例の低熱膨張材料に比べて、硬度が高いことが確認された。 As shown in Table 2, it was confirmed that the spherical vanadium carbide-containing low thermal expansion material according to the present invention has higher hardness than the low thermal expansion material of the comparative example.
［試験例３：耐摩耗試験］
理研−大越式迅速摩耗試験機（ＪＴトーシ株式会社製）を用いて、以下の条件で摩耗試験を行った。尚、この摩耗試験機は、回転円盤を平面試料に押し付けて摩耗させ、そのときの摩耗痕の体積から摩耗量を測定する試験機である。
（摩耗試験条件）
荷重：1kgf，2kgf，4kgf
摩擦速度：0.59ｍ/min，1.09ｍ/min，2.28ｍ/min
摩擦相手材：Ｓ45Ｃ未処理
摩擦距離：600ｍ
無潤滑、大気中
[Test Example 3: Wear resistance test]
Using a RIKEN-Ogoshi quick wear tester (manufactured by JT Toshi Co., Ltd.), a wear test was performed under the following conditions. This wear tester is a tester for measuring the amount of wear from the volume of wear marks at the time when a rotating disk is pressed against a flat sample to be worn.
(Wear test conditions)
Load: 1kgf, 2kgf, 4kgf
Friction speed: 0.59m / min, 1.09m / min, 2.28m / min
Friction material: S45C untreated Friction distance: 600m
No lubrication, in the atmosphere
耐摩耗試験の結果を図２２〜２７に示す。図２２〜２７に示されるように、各実施例の試料はいずれも、比較例１〜４の試料に比べて摩耗量が少なく、耐摩耗性に優れることが確認された。 The results of the abrasion resistance test are shown in FIGS. As shown in FIGS. 22 to 27, it was confirmed that each of the samples of each example had a smaller wear amount and excellent wear resistance than the samples of Comparative Examples 1 to 4.
また、図２８〜３０に、耐摩耗試験に供した各試料の摩耗体積と、ロックウェル硬さ試験の結果の相関関係を示す。
耐摩耗試験の全ての条件下において、硬度が高い試料ほど摩耗量が少なく、硬度と摩耗性との間に相関関係が見られた。
28 to 30 show the correlation between the wear volume of each sample subjected to the wear resistance test and the results of the Rockwell hardness test.
Under all conditions of the wear resistance test, the higher the hardness of the sample, the smaller the wear amount, and a correlation was found between the hardness and the wear resistance.
［試験例４：熱膨張率の測定］
熱膨張率測定機（ブルカーエイエックスエス(株)製、ＴＤ5020Ｓ）を用いて、以下の条件で熱膨張率を測定した。
（熱膨張率測定条件）
示差熱膨張計：水平示差熱検出方式
基準試料：アルミナ
加熱速度：２０Ｋ/ｍｉｎ
測定試料長さ：２０ｍｍ
荷重：１０ｇ
測定温度範囲：室温より４７８Ｋ（２０５℃）まで
測定雰囲気：大気中
[Test Example 4: Measurement of thermal expansion coefficient]
The thermal expansion coefficient was measured under the following conditions using a thermal expansion coefficient measuring machine (Bruker AXS Co., Ltd., TD5020S).
(Thermal expansion coefficient measurement conditions)
Differential thermal dilatometer: Horizontal differential heat detection method Reference sample: Alumina Heating rate: 20K / min
Measurement sample length: 20mm
Load: 10g
Measurement temperature: measured up 478K (205 ℃) than room Atmosphere: in the air
各試料の、３２３〜３７３Ｋの平均熱膨張率、３０３〜３７３Ｋの平均熱膨張率、３０３〜４７３Ｋの平均熱膨張率を、表３に示す。
また図３１〜３６に、各試料の熱膨張率の測定結果を示す。
Table 3 shows the average thermal expansion coefficient of 323 to 373 K, the average thermal expansion coefficient of 303 to 373 K, and the average thermal expansion coefficient of 303 to 473 K of each sample.
Moreover, the measurement result of the thermal expansion coefficient of each sample is shown in FIGS.
図３１は、実施例５，９，１８，２４と比較例２〜４の平均熱膨張率を示すグラフである。
図３１に示されるように、本発明に係る低熱膨張材料は、汎用の低熱膨張材料である比較例２〜４と略同等の低熱膨張性を示すことが分かる。比較例２や３は、低温域では膨張係数が低いが、高温域になるほど膨張係数が大きくなる傾向にある。本発明に係る低熱膨張材料は、高温域においても、低温域と略同等の膨張係数を示すことが分かる。
FIG. 31 is a graph showing average thermal expansion coefficients of Examples 5, 9, 18, and 24 and Comparative Examples 2 to 4.
As FIG. 31 shows, it turns out that the low thermal expansion material which concerns on this invention shows the low thermal expansion property substantially equivalent to Comparative Examples 2-4 which are general purpose low thermal expansion materials. In Comparative Examples 2 and 3, the expansion coefficient is low in the low temperature range, but the expansion coefficient tends to increase as the temperature increases. It can be seen that the low thermal expansion material according to the present invention exhibits an expansion coefficient substantially equal to that in the low temperature range even in the high temperature range.
図３２は、実施例５、１２〜１４の平均熱膨張率を示すグラフである。
図３３は、実施例２、８〜１１の平均熱膨張率を示すグラフである。
図３４は、実施例１５〜２０の平均熱膨張率を示すグラフである。
図３５は、実施例２１〜２５の平均熱膨張率を示すグラフである。
図３６は、各実施例における、コバルト添加量と平均熱膨張率との関係を示すグラフである。
図３２〜３５に示されるように、コバルトを添加することによって、熱膨張係数が低下して、低熱膨張性が向上することが確認された。コバルトの添加量が多いほど、特に高温域における熱膨張係数の低下に効果があることが分かった。
FIG. 32 is a graph showing the average coefficient of thermal expansion of Examples 5 and 12-14.
FIG. 33 is a graph showing the average coefficient of thermal expansion of Examples 2 and 8 to 11.
FIG. 34 is a graph showing the average thermal expansion coefficients of Examples 15 to 20.
FIG. 35 is a graph showing an average coefficient of thermal expansion of Examples 21 to 25.
FIG. 36 is a graph showing the relationship between the cobalt addition amount and the average coefficient of thermal expansion in each example.
As shown in FIGS. 32 to 35, it was confirmed that by adding cobalt, the thermal expansion coefficient is lowered and the low thermal expansion is improved. It has been found that the greater the amount of cobalt added, the more effective is the reduction in the coefficient of thermal expansion, particularly at high temperatures.
図３７は、実施例１〜５の平均熱膨張率を示すグラフである。
図３７に示されるように、ニッケルの含有量を高めることによって、高温域における熱膨張係数を低下できることが分かる。
FIG. 37 is a graph showing the average thermal expansion coefficients of Examples 1 to 5.
As shown in FIG. 37, it can be seen that the thermal expansion coefficient in the high temperature region can be lowered by increasing the nickel content.
図３８は、実施例５〜７の平均熱膨張率を示すグラフである。
図３８に示されるように、炭素含有量が増加するほど、熱膨張率が低下することが分かる。
FIG. 38 is a graph showing the average thermal expansion coefficients of Examples 5 to 7.
As FIG. 38 shows, it turns out that a coefficient of thermal expansion falls, so that carbon content increases.
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